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ANNUAL REPORT<br />
2 0 0 6<br />
FACULTY OF<br />
MATERIALS- AND GEO-SCIENCES<br />
- 1 -
ANNUAL REPORT<br />
2 0 0 6<br />
FACULTY OF<br />
MATERIALS- AND GEO-SCIENCES
Annual Report<br />
2006<br />
Faculty 11<br />
<strong>Material</strong>s- and Geo-Sciences<br />
<strong>Material</strong>s Science:<br />
Petersenstraße 23 • L2 01 • 64287 Darmstadt<br />
Phone: +49 (0) 6151 / 16 - 5377 • Fax: +49 (0) 6151 / 16 - 5551<br />
http://www.tu-darmstadt.de/fb/ms/<br />
Applied Geosciences:<br />
Schnittspahnstraße 9 • B2 01/02 • 64287 Darmstadt<br />
Phone: +49 (0) 6151 / 16 - 2571 • Fax: +49 (0) 6151 / 16 - 6539<br />
http://www.tu-darmstadt.de/fb/geo/<br />
For further information contact:<br />
Dr. Joachim Brötz, Phone: +49 (0) 6151 / 16 - 4392; eMail: broetz@tu-darmstadt.de<br />
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Contents<br />
I. PREFACE 4<br />
II. INSTITUTE OF MATERIALS SCIENCE 8<br />
Physical Metallurgy.................................................................8<br />
Ceramics Group ...................................................................15<br />
<strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong>...............................................19<br />
Surface Science ...................................................................23<br />
Thin films ..............................................................................28<br />
Dispersive Solids ..................................................................31<br />
Structure Research...............................................................36<br />
Chemical Analytics ...............................................................44<br />
Theoretical <strong>Material</strong>s Science ..............................................49<br />
<strong>Material</strong>s Modelling...............................................................52<br />
<strong>Material</strong>s for Renewable Energies........................................54<br />
Joint Research Laboratory Nanomaterials ...........................56<br />
Collaborative Research Center (SFB) ..................................58<br />
Reports of Research Activities 61<br />
Diploma Theses 110<br />
PhD Theses 112<br />
Mechanical Workshop 113<br />
III. INSTITUTE OF APPLIED GEOSIENCES 114<br />
Physical Geology and Global Cycles..................................114<br />
Hydrogeology .....................................................................117<br />
Engineering Geology ..........................................................118<br />
Applied Sedimentology.......................................................122<br />
Geo-Resources and Geo-Hazards .....................................125<br />
Geomaterials Science ........................................................128<br />
Technical Petrology ............................................................131<br />
Environmental Mineralogy ..................................................135<br />
Reports of Research Activities 137<br />
Diploma Theses 161<br />
Magister Theses 161<br />
PhD Theses 161<br />
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Preface<br />
The year 2006 of the Department of <strong>Material</strong>s- and Geo-Sciences was characterized by a<br />
stabilisation of the Geo-Sciences and a shift of severe structural changes to the Institute of<br />
<strong>Material</strong>s Science. In addition, our Dean Prof. Heinz von Seggern resigned due to health<br />
problems on March 31 and was succeeded by Prof. W. Jaegermann. We all would like to<br />
thank Prof. v. Seggern for his efforts. Finally, the target agreement was signed mid of<br />
2006; however some different opinions on the future of the departments were still not<br />
settled at this time. The development of students’ and graduate numbers for <strong>Material</strong>s- and<br />
Geo-Science are shown in Fig. 1.<br />
Fig. 1 Number of graduates (diplomas and doctorates) in <strong>Material</strong>s- and Geo-Sciences at<br />
Darmstadt University of Technology over the last 7 years<br />
After the appointment of Prof. Hans-Joachim Kleebe in January 2006 as head of the<br />
Geomaterials Group following Prof. Wolfgang Müller, all chairs of the Institute of Geo-<br />
Science are now assigned. The new crew has defined new directions in research and<br />
education at the TU Darmstadt. More information about the achievements of the year 2006<br />
are given below.<br />
In <strong>Material</strong>s Science the reoccupation of professorships substituting the first fo<strong>und</strong>ing<br />
generation after retirement or appointment to other institutions is still a major challenge.<br />
Hartmut Fuess who was the first professor of the newly fo<strong>und</strong>ed Department of <strong>Material</strong>s<br />
Science in 1989 was retired in Oct. 2006. Prof. Dr. Dr. h. c. Fuess was head of the<br />
Structural Research Division and succeeded to built-up a nationally and internationally<br />
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highly recognized research lab on structural research. Especially, the powder diffraction<br />
facilities located at national laboratories in Hamburg and Munich (DESY and FRM II) were<br />
used in cooperation by many guests from Germany and other institutions abroad. In<br />
addition, Prof. Fuess served for several years as dean of the Department of <strong>Material</strong>s<br />
Science and after unification with Geoscience of the Department of <strong>Material</strong>s- and Geo-<br />
Sciences. He has strongly contributed to the excellent scientific profile of the department<br />
by his outstanding scientific contributions, but also by his visionary ideas and admirable<br />
management qualities. We will have to struggle hard to find qualified successors.<br />
Fortunately Prof. Fuess has agreed to continue to lead his research group for the next<br />
future until a successor has joined the department. Therefore we still profit from his<br />
experience and knowledge. In September 2006 Prof. Jürgen Eckert followed an offer of<br />
the Institute of for Solid State and <strong>Material</strong>s Research in Dresden as head of the<br />
Department of Complex Solids. We would like to thank him for his contributions in<br />
Darmstadt and wish all the best for his new appointment.<br />
Some of the very qualified junior scientist who have obtained their habilitation at TU<br />
Darmstadt have also left the department: Dr. Doru Lupascu moved to TU Dresden where<br />
he was appointed as professor of functional ceramics; Dr. Roland Schmechel was<br />
appointed as a professor in electrical engineering at University of Duisburg-Essen on<br />
nanostructuring techniques (unfortunately we were not successful to keep him at our<br />
institute with a combined effort of TUD and FZK); Dr. Helmut Ehrenberg has moved to the<br />
IFW Dresden together with Prof. Eckert. We want to thank our younger colleagues for their<br />
valuable contributions to the success of the department and hope for similarly qualified<br />
Post-Docs in the future to secure the high level of our scientific and educational efforts.<br />
A large fraction of time was devoted during 2006 to join the national excellence initiative<br />
with the final application of a cluster of excellence MECAD aiming at multi-functional<br />
materials based on composites for advanced devices. During the first months of the year<br />
regular extended discussions on the scientific content and organisational and structural<br />
demands were held together with our colleagues from the departments of chemistry,<br />
physics, biology, electrical engineering and mechanical engineering. Finally, thanks to the<br />
perfect management of Prof. J. Rödel a very promising research proposal was submitted,<br />
which unfortunately did not receive f<strong>und</strong>ing at the end. However, as we have obtained<br />
encouraging referee reports on the scientific content of our research proposal we intend to<br />
follow this interesting topic as one of our maior scientific subjects of the future.<br />
Fortunately, another major research program in <strong>Material</strong>s Science, the collaborative<br />
research centre on “Electric fatigue in functional materials”, was positively evaluated in<br />
Oct. 2006 and will continue in its second f<strong>und</strong>ing period. This activity is also directed by<br />
Prof. Rödel and a special thanks goes also to Dr. Kinski who provided substantial support<br />
in preparing the proposal consisting of more than 750 printed pages. The proposal was<br />
rated close to excellent by the referees and will be continued nearly without any<br />
deductions. In result, a strong support of the <strong>Material</strong>s Science research activities was<br />
successfully realized, which will help to keep us in action for the next four years.<br />
The annual event “<strong>Material</strong>wissenschaftlicher Tag” in 2006 was devoted to the 60 th<br />
anniversary of Prof. Rauh. At this occasion the research activities in Theoretical <strong>Material</strong>s<br />
Science at our department were presented. Since Prof. Rauh is not only interested in<br />
theoretical physics, but also in classical music, well balanced contributions of talks, posters<br />
and musical performances of the Rauh family stimulated inspiring discussions on the<br />
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difference of numerical and analytical theoretical approaches vs. Beethoven’s and<br />
Mozart’s approach to well defined musical masterpieces.<br />
Finally, we also want to announce special honours of members of our department. First of<br />
all Prof. Riedel was honoured as Honorary Doctor (Dr. h. c.) of the Slovak Academy of<br />
Sciences, Bratislava, Slovak Republik. The students’ price of the best MaWi student was<br />
given to Dipl. Ing. Taek Lim followed by E. Mankel, B. Siepchen and A. Gassmann who<br />
presented their Diploma theses during the yearly Summer Party of the <strong>Material</strong> Science<br />
Institute. The MRS Graduate Student Gold Medal was awarded to Dr.-Ing. Paul Erhart for<br />
this PhD-thesis on point defects in zinc oxide at the MRS Fall Meeting 2006 in Boston.<br />
The year 2006 in the <strong>Material</strong>s Science Institute was brought to an end with the traditional<br />
Christmas Party to which very many people contributed in a more or less active way.<br />
Again a number of high level of art, music, and comedy performances has proven that<br />
materials scientists have talents beyond their scientific abilities. The party was finished<br />
again very late this year after the early visit of Father Christmas.<br />
The Institute of Applied Geosciences finally filled all vacant positions and finished its<br />
restructuring process by the appointment of Prof. Dr. Hans-Joachim Kleebe, who is<br />
heading the Geomaterial Science group since January 2006. Moreover, with the retirement<br />
of Prof. Fuess, Prof. Kleebe took over the administration and responsibility of the<br />
transmission electron microscopy facility. Thereby, electron microscopy and x-ray<br />
diffraction techniques are no longer in one hand. It is anticipated to strengthen the TEM<br />
group and create a state-of-the-art electron microscopy facility which is strongly supports<br />
research at the geo- and material science community as well as other faculty on campus.<br />
The research focus Geothermal Energy was established by the Engineering Geology<br />
Group of Prof. I. Sass. Geothermal energy is one of the few regenerative energy systems,<br />
capable of providing a base load with potentially enormous resources. In July 2006, the<br />
first Geothermal Summer School with about 50 participants was held in Darmstadt, in<br />
cooperation with the Institute and Laboratory for Geotechnics. In addition, in cooperation<br />
with the "Hessisches Ministerium für Wirtschaft, Verkehr <strong>und</strong> Landesentwicklung" the first<br />
Forum on Deep Geothermal Reservoirs took place at TUD with about 150 participants.<br />
The Hydrogeology Group together with the Applied Sedimentology Group initiated a<br />
second new research focus on gro<strong>und</strong>water management in arid regions. In cooperation<br />
with the GTZ, a first project was started on gro<strong>und</strong>water resources in Saudi-Arabia. We will<br />
strengthen our efforts to play a significant role in this area as a qualitative and quantitative<br />
approach to manage regional gro<strong>und</strong>water resources based on the principal of<br />
sustainability is one of the crucial topics in the field of applied geosciences in the future.<br />
In 2006 we could celebrate the award of a prestigious price to one of our young scientists.<br />
Dr. Martin Ebert from the Environmental Mineralogy Group of Prof. Weinbruch, who<br />
received the ‘Adolf-Messer-Award’ 2006 of the Messer Fo<strong>und</strong>ation for his gro<strong>und</strong>breaking<br />
research on atmospheric aerosols and their importance for climate and health. The award<br />
was presented to Martin Ebert in a ceremony by Stefan Messer, owner and CEO of the<br />
Messer Group. We congratulate Martin Ebert on his achievement and the attention his<br />
research has attracted.<br />
Our International Master Course TropHEE (Tropical Hydrogeology, Engineering Geology<br />
and Environmental Management) started in October 2006 with the enrollment of the first<br />
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students. TropHEE is internationally accredited and certified, and designed for<br />
geoscientists (geologists, geoecologists, geophysicists, mineralogists, geographers, soil<br />
scientists, civil engineers) who wish to obtain a wide range of knowledge in hydrogeology,<br />
engineering geology and environmental management with a special emphasis on tropical<br />
and subtropical regions. There are 10 scholarships for TropHEE available every year and<br />
we are expecting about 20 students per year.<br />
As it is the tradition in Geosciences to conclude the year with the ‘Barbara Fest’, all faculty,<br />
staff and students got together to discuss the events of the year as well as the future in a<br />
very friendly and positive atmosphere.<br />
The outcome and most remarkable results of research in 2006 are summarized below for<br />
the different divisions and working groups of the Department of <strong>Material</strong>s- and Geo-<br />
Science. These results would not have been possible without the strong engagement and<br />
outstanding efforts of all people in the department ranging from our excellent workshop<br />
headed by J. Korzer, to the technical and administrative staff in the research groups, the<br />
students, Diploma students, Ph.D. students and last but not least to the PostDocs in the<br />
different research groups. We would like to thank all of them for their valuable<br />
contributions and hope that it will be possible to keep the excellent working atmosphere for<br />
the upcoming years.<br />
Wolfram Jaegermann<br />
Dean of the Faculty of <strong>Material</strong>s- and Geo-Sciences<br />
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Institute of <strong>Material</strong>s Science<br />
Physical Metallurgy<br />
The activity of the Physical Metallurgy Division covers a broad range of research on<br />
structural and functional metallic materials, starting from the basic processes and<br />
mechanisms governing metastable phase formation upon quenching from the melt as well<br />
as solid state processing, including detailed microstructure investigations and structure<br />
analysis ending with the description of the performance of components in technical<br />
applications. Special attention is paid to <strong>und</strong>erstand the correlation between phases,<br />
microstructure and physical properties of the material, also when considering the effect of<br />
processing conditions on materials properties during and after rapid quenching, casting,<br />
mechanical alloying / ball milling, powder consolidation, heat treatment, as well as shaping<br />
and forming operations. The ultimate goal is to use this <strong>und</strong>erstanding to tailor new or to<br />
optimize customized materials with improved properties for applications. The research is<br />
thus spanning from basic scientific questions to technological research and development<br />
efforts. Besides experimental work, also model-based property descriptions including<br />
casting processes, coarsening and recrystallization, forging, sheet drawing and chip<br />
formation, as well as microstructure-based modelling of mechanical properties are<br />
performed. This allows to propose guidelines for further property optimization.<br />
The materials <strong>und</strong>er investigation are titanium-, magnesium-, and aluminium-based light<br />
alloys, steels, multicomponent glass-forming alloys, and nanostructured/ ultrafine-grained<br />
alloys. Their microstructure development and deformation behavior <strong>und</strong>er different loading<br />
conditions and the interaction with environmental conditions like corrosive media are<br />
investigated. In 2005 progress in the area of microstructure-based processing for<br />
properties was achieved in the fields of titanium alloys for various functional and structural<br />
applications and novel nanostructure-dendrite or glassy matrix composites, which combine<br />
high strength with large plastic deformability. The <strong>und</strong>erstanding of the basics of<br />
solidification and mechanically driven phase transitions promises to lead to optimization of<br />
alloys for a variety of applications.<br />
The activities focussing on the improvement of the mechanical properties of metallic<br />
materials are complemented by work related to the development of nanostructured<br />
materials for use as functional materials with interesting properties for magnetic<br />
applications, catalysis, hydrogen storage or as electrode materials. Again, this includes<br />
structural investigations that provide the basis for the <strong>und</strong>erstanding of the physical<br />
properties of such materials. For example, high-resolution scanning and transmission<br />
electron microscopy combined with x-ray scattering techniques and magnetic or<br />
electrochemical measurements allows to describe the nanostructure formation, gives<br />
insight into the nature of structural inhomogeneities and helps to <strong>und</strong>erstand the resulting<br />
physical properties of the materials.<br />
The teaching activities cover basics of phase formation and stability (phase diagrams and<br />
phase transitions, solidification behavior of materials), the mechanical properties of<br />
engineering materials and the f<strong>und</strong>amentals of deformation and fracture as well as<br />
quantitative microstructure analysis. Seminars and extensive laboratory exercises<br />
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complement the lectures and help to intensify the <strong>und</strong>erstanding in these topics and to<br />
improve the practical skills for investigating metallic materials.<br />
The Physical Metallurgy Division has a variety of collaborations with the other groups in<br />
the Institute and with other Departments at Darmstadt University of Technology (e.g.,<br />
Mechanical Engineering, Chemistry, Physics). A special feature of the group is its strong<br />
emphasis on national and international collaboration. It cooperates with more than 15<br />
groups in Germany, Europe (e.g. Denmark, France, Italy, Spain, Poland, Romania, Slovak<br />
Republic, Switzerland, UK etc.) and worldwide (USA, Canada, Australia, China, India,<br />
Japan, Korea, Russia, Ukraine and others). Besides, strong interactions with companies<br />
(e.g. Adam Opel AG, Daimler-Chrysler, EADS, Heraeus, Liquidmetal Inc., Umicore etc.)<br />
exist. Participation in conferences, seminars and workshops aids the actuality of teaching<br />
and research, fosters collaborations and promotes the exchange of students and<br />
scientists.<br />
Staff Members<br />
Head Prof. Dr.-Ing. Jürgen Eckert<br />
Research Associates Prof. Dr. Mariana Calin PD Dr. Clemens Müller<br />
Dr. Ki Buem Kim Dr. Mihai Stoica<br />
Technical Personnel Ulrike Kunz Petra Neuhäusel<br />
Heinz Lehmann Claudia Wasm<strong>und</strong><br />
Secretary Christine Hempel<br />
PhD Students M. Tech. Jayanta Das Dipl.-Ing. Simon Pauly<br />
Dr. Cécilie Duhamel Dipl.-Ing. Mira Sakaliyska<br />
Dipl.-Ing. Thorsten Keller Dipl.-Chem. Sergio Scudino<br />
Dipl.-Ing. Arne Kriegsmann M. Tech. Shankar<br />
Venkataraman<br />
Diploma Students Tilman Bohn Flora Paturaud<br />
Udo Depner Simon Pauly<br />
Alexander Elsen René Richter<br />
Frank Ettingshausen Jan-Michael Rudnig<br />
Martin Frommherz Sascha Sager<br />
Falko Langbein Sebastian Sperling<br />
Guest Scientists Dr. Tatiana Chernova<br />
Dr. Wei Xu<br />
Dr. Peng Yu<br />
Dr. Lai-Chang Zhang<br />
Dr. Wen-Yong Zhang<br />
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Research Projects<br />
Bulk Amorphous Al-Alloys by Ball Milling and Spark-Plasma-Sintering (DFG, 2005-2006)<br />
Bulk Zr-Glasses (DFG, 2004-2006)<br />
Complex Metallic Alloys (EU Network of Excellence, 2004-2008)<br />
DAAD Research Stipend for Dr. T. Chernova, University of Samara, Russia<br />
Deformation Behaviour of Zr-based Metallic Glass and Metallic Glass Composites at<br />
Elevated Temperatures (DFG, 2005-2006)<br />
Ductile Bulk Metallic Glass Composites* (EU Research Training Network 2003-2007)<br />
Glass-forming Ability of Ti-base Metallic Glasses (AvH, 2005-2006)<br />
Improvement of wear resistance by roller burnishing (AIF-EFB, jointly with Prof. Groche,<br />
2006-2008)<br />
In-situ Formed Zirconia- and Alumina-toughened Zr-based Bulk Metallic Glasses (AvH,<br />
2005-2006)<br />
Influence of Shot Peening on Fatigue and Corrosion of the Mg-Alloys AZ91 and AZ80<br />
(2002-2006)<br />
Intensive Program for Transfer of Knowledge to Eastern European Reference Pole for<br />
Micro- and Nanotechnologies NANOTEC-EST (EU 2005-2009)<br />
Investigation and Preparation of Amorphous or Nanocrystalline Ribbons for Soft Magnetic<br />
Coils in Accelerators (GSI, jointly with Prof. Hahn, 2004-2006)<br />
Magnetic Hardening Mechanisms of Bulk Fe3B-based Nanocomposite Magnets Produced<br />
by Crystallization of Nd-Dy-Fe-Co-B Metallic Glass (AvH, 2005-2006)<br />
Microstructure and Mechanical <strong>Properties</strong> of Linear Flow Splitted Sheets (DFG-SFB, 2005-<br />
2009)<br />
Microstructure Control of Novel Ti-based Nanocomposites with Potential for Biomedical<br />
Applications (AvH, 2005-2006)<br />
Nd-base Alloys (DFG, 2001-2007)<br />
Radiation-Induced <strong>Material</strong> Changes of NbTi-Superconductors (GSI, jointly with Prof.<br />
Fueß, 2004-2006)<br />
(* managed via the Leibniz-Institute for Solid State and <strong>Material</strong>s Research Dresden)<br />
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Publications<br />
Kumar, G.; Filip, O.; Löser, W.; Schultz, L.; Eckert, J.; Cooling Rate Controlled<br />
Microstructure and Magnetic <strong>Properties</strong> of Fe20Nd80 Alloys, Intermetallics 14 (2006) 47.<br />
Slipenyuk, A.; Kuprin, V.; Milman, Y.; Goncharuk, V.; Eckert, J.; <strong>Properties</strong> of P/M Processed<br />
Particle Reinforced Metal Matrix Composites Specified by Reinforcement Concentration and<br />
Matrix-to-Reinforcement Particle Size Ratio, Acta. Mater. 54 (2006) 157.<br />
Liu, L. F.; Dai, L. H.; Bai, Y. L.; Wei, B. C.; Eckert, J.; Characterization of Rate-Dependent<br />
Shear Behavior of Zr-based Bulk Metallic Glass Using Shear Punch Testing, J. Mater.<br />
Res. 21 (2006) 153.<br />
Kim, K. B.; Das, J.; Baier, F.; Tang, M. B.; Wang, W. H.; Eckert, J.; Heterogeneity of a<br />
Cu47.5Zr47.5Al5 Bulk Metallic Glass, Appl. Phys. Lett. 88 (2006) 051911.<br />
Kim, K. B.; Warren, P. J.; Cantor, B.; Eckert, J.; Structural Evolution of Nano-Scale<br />
Icosahedral Phase in Novel Multicomponent Amorphous Alloys, Phil. Mag. 86 (2006) 281.<br />
Scudino, S.; Eckert, J.; Breitzke, H.; Lüders, K.; Schultz, L.; Influence of Ball Milling on<br />
Quasicrystal Formation in Melt-Spun Zr-Based Glassy Ribbons, Phil. Mag. 86 (2006) 367.<br />
He, G.; Eckert, J.; Hagiwara, M.; Mechanical <strong>Properties</strong> and Fracture Behavior of the<br />
Modified Ti-Base Bulk Metallic Glass-Forming Alloys, Mater. Lett. 60 (2006) 656.<br />
Mudali, U. K.; Kühn, U.; Eckert, J.; Schultz, L.; Gebert, A.; Corrosion Behaviour of<br />
Zirconium-Based Bulk Metallic Glasses, Trans. Indian Institute of Metals 59 (2006) 123.<br />
Venkataraman, S.; Stoica, M.; Scudino, S.; Gemming, T.; Mickel, C.; Schultz, L.; Eckert,<br />
J.; Revisiting the Cu47Ti33Zr11Ni8Si1 Glass-Forming Alloys, Scripta Mater. 54 (2006) 835.<br />
Sun, B. B.; Sui, M. L.; Wang, Y. M.; Li, Y.; He, G.; Eckert, J.; Ma, E.; Bulk Ti-Based In Situ<br />
Nanocomposite with High Strength and Tensile Ductility, Acta Mater. 54 (2006) 1349.<br />
Venkataraman, S.; Scudino, S.; Eckert, J.; Gemming, T.; Mickel, C.; Schultz, L.; Sordelet,<br />
D. J.; Nanocrystallization of Gas Atomized Cu47Ti33Zr11Ni8Si1 Metallic Glass, J. Mater. Res.<br />
21 (2006) 597.<br />
Yu, P.; Kim, K. B.; Das, J.; Baier, F.; Xu, W.; Eckert, J.; Fabrication and Mechanical<br />
<strong>Properties</strong> of Ni-Nb Metallic Glass Particle-Reinforced Al-Based Metal Matrix Composite,<br />
Scripta Mater. 55 (2006) 1445.<br />
Kim, K. B.; Warren, P. J.; Cantor, B.; Eckert, J.; Enhanced Thermal Stability of the<br />
Devitrified Nano-Scale Icosahedral Phase in Novel Multicomponent Amorphous Alloys, J.<br />
Mater. Res. 21 (2006) 823.<br />
Scudino, S.; Stoica, M.; Mattern, N.; Breitzke, H.; Lüders, K.; Yavari, A. R.; Eckert, J.; Is a<br />
Particular Quenched-In Short-Range Order Necessary for Quasicrystal Formation from<br />
Glassy Precursors?, Phys. Stat. Sol. (b) 243 (2006) R34.<br />
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el Dsoki, C.; Landersheim, V. ; Kaufmann, H.; Bruder, T.; Krug, P.; Bohn, T.; Müller, C.;<br />
Zyklisches Werkstoffverhalten sprühkompaktierter Aluminiumwerkstoffe. Kennwerte für die<br />
Bauteilbemessung: Von der probe zum Bauteil, Mat.-wiss. u. Werkstofftech. 37, 2006,<br />
1006-1017<br />
Kumar, G.; Kerschl, P.; Rößler, U. K.; Nenkov, K.; Müller, K.-H.; Schultz, L.; Eckert, J.;<br />
High-Field Magnetization and Coercivity of Hard Magnetic Mold-Cast Nd80Fe20, J. Appl.<br />
Phys. 99 (2006) 083904.<br />
Venkataraman, S.; Löser, W.; Eckert, J.; Gemming, T.; Mickel, C.; Schubert-Bischoff, P.;<br />
Wanderka, N.; Schultz, L.; Sordelet, D. J.; Nanocrystal Development in Cu47Ti33Zr11Ni8Si1<br />
Metallic Glass Powders, J. Alloys & Compo<strong>und</strong>s 414 (2006) 162.<br />
Scudino, S.; Das, J.; Stoica, M.; Kim, K. B.; Kusy, M.; Eckert, J.; High Strength Hexagonal<br />
Structured Dendritic Phase Reinforced Zr-Ti-Ni Bulk Alloy with Enhanced Ductility, Appl.<br />
Phys. Lett. 88 (2006) 201920.<br />
Xu, W.; Kim, K. B.; Das, J.; Calin, M.; Eckert, J.; Phase Stability and its Effect on the<br />
Deformation Behavior of Ti-Nb-Ta-In/Cr β Alloys, Scripta Mater. 54 (2006) 1943.<br />
Kim, K. B.; Yi, S.; Choi-Yim, H.; Das, J.; Xu, W.; Johnson, W. L.; Eckert, J.; Effect of Cu on<br />
Local Amorphization in Bulk Ni-Ti-Zr-Si Alloys During Solidification, Acta Mater. 54 (2006)<br />
3141.<br />
Venkataraman, S.; Biswas, K.; Wei, B. C.; Sordelet, D. J.; Eckert, J.; On the Fragility of<br />
Cu47Ti33Zr11Ni8Si1 Metallic Glass, J. Phys. D: Appl. Phys. 39 (2006) 2600.<br />
Biswas, K.; Ram, S.; Roth, S.; Schultz, L.; Eckert, J.; Fabrication of Bulk Amorphous<br />
Fe67Co9.5Nd3Dy0.5B20 Alloy by Hot Extrusion of Ribbon and Study of the Magnetic<br />
<strong>Properties</strong>, J. Mater. Sci. 41 (2006) 3445.<br />
Castellero, A.; Bossuyt, S.; Stoica, M.; Deledda, S.; Eckert, J.; Chen, G. Z.; Fray, D. J.;<br />
Greer, A. L.; Improvement of the Glass-Forming Ability of Zr55Cu30Al10Ni5 and<br />
Cu47Ti34Zr11Ni8 Alloys by Electro-Deoxydation of the Melts, Scripta Mater. 55 (2006) 87.<br />
Biswas, K.; Venkataraman, S.; Zhang, W. Y.; Ram, S.; Eckert, J.; Glass-Forming Ability<br />
and Fragility Parameter of Amorphous Fe67Co9.5Nd3Dy0.5B20, J. Appl. Phys. 100 (2006)<br />
023501.<br />
Xu, W.; Kim, K. B.; Das, J.; Calin, M.; Rellinghaus, B.; Eckert, J.; Deformation-Induced<br />
Nanostructuring in a Ti-Nb-Ta-In β Alloy, Appl. Phys. Lett. 89 (2006) 031906.<br />
Kühn, U.; Eckert, J.; Schultz, L.; Annealing-Induced Phase Transitions in a Zr-Ti-Nb-Cu-Ni-<br />
Al Bulk Metallic Glass Matrix Composite Containing Quasicrystalline Precipitates, Int. J.<br />
Mater. Res. (formerly Z. Metallkde.) 97 (2006) 996.<br />
Zhang, L. C.; Xu, J.; Eckert, J.; Thermal Stability and Crystallization Kinetics of<br />
Mechanically Alloyed TiC/Ti-Based Metallic Glass Matrix Composite, J. Appl. Phys. 100<br />
(2006) 033514.<br />
- 12 -
Kim, K. B.; Das, J.; Wu, X.; Zhang, Z. F.; Eckert, J.; Microscopic Deformation Mechanism<br />
of a Ti66.1Nb13.9Ni4.8Cu8Sn7.2 Nanostructure-Dendrite Composite, Acta Mater. 54 (2006)<br />
3701.<br />
Kim, K. B.; Das, J.; Venkataraman, S.; Yi, S.; Eckert, J.; Work Hardening Ability of Ductile<br />
Ti45Cu40Ni7.5Zr5Sn2.5 and Cu47.5Zr47.5Al5 Bulk Metallic Glasses, Appl. Phys. Lett. 54 (2006)<br />
071908.<br />
Kim, K. B.; Das, J.; Wang, X. D.; Zhang, X.; Eckert, J.; Yi, S.; Effect of Sn on<br />
Microstructure and Mechanical <strong>Properties</strong> of (Ti-Cu)-Based Bulk Metallic Glasses, Phil.<br />
Mag. Lett. 86 (2006) 479.<br />
Exner, H.E.; Petzow, G; A Critical Assessment of Porosity Coarsening During Solid State<br />
Sintering, Advances in Science and Technology, Vol. 45, 2006, 539 - 548<br />
Concustell, A.; Sort, J.; Woodcock, T. G.; Gimazov, A.; Suriñach, S.; Gebert, A.; Eckert, J.;<br />
Zhilyaev, A. P.; Baró, M. D.; Enhanced Mircohardness in Nanocrystalline<br />
Ti60Cu14Ni12Sn4Ta10 Processed by High Pressure Torsion, Intermetallics 14 (2006) 871.<br />
Eckert, J.; Das, J.; Kim, K. B.; Baier, F.; Tang, M. B.; Wang, W. H.; Zhang, Z. F.; High<br />
Strength Ductile Cu-Base Metallic Glass, Intermetallics 14 (2006) 876.<br />
Kim, K. B.; Yi, S.; Hwang, I. S.; Eckert, J.; Effect of Cooling Rate on Microstructure and Glass-<br />
Forming Ability of a (Ti33Zr33Hf33)70(Ni50Cu50)20Al10 Alloy, Intermetallics 14 (2006) 972.<br />
Kusy, M.; Kühn, U.; Concustell, A.; Gebert, A.; Das, J.; Eckert, J.; Schultz, L.; Baró, M. D.;<br />
Fracture Surface Morphology of Compressed Bulk Metallic Glass-Matrix-Composites and<br />
Bulk Metallic Glass, Intermetallics 14 (2006) 982.<br />
Venkataraman, S.; Eckert, J.; Schultz, L.; Sordelet, D. J.; Effect of Preannealing on Glass<br />
Transition and Crystallization of Gas Atomized Cu47Ti33Zr11Ni8Si1 Metallic Glass Powders,<br />
Intermetallics 14 (2006) 1085.<br />
Roth, S.; Stoica, M.; Degmová, J.; Gaitzsch, U.; Eckert, J.; Schultz, L.; Fe-Based Bulk<br />
Amorphous Soft Magnetic <strong>Material</strong>s, J. Magn. Magn. Mater. 304 (2006) 192.<br />
Lorenz, B.; Perner, O.; Eckert, J.; Chu, C. W.; Superconducting <strong>Properties</strong> of<br />
Nanocrystalline MgB2, Supercond. Sci. Technol. 19 (2006) 912.<br />
Stoica, M.; Eckert, J.; Roth, S.; Schultz, L.; Yavari, A. R.; Casting and Characterization of<br />
Fe-(Cr, Mo, Ga)-(P, C, B) Soft Magnetic Bulk Metallic Glasses, J. Optoelectronics and<br />
Advanced <strong>Material</strong>s 8 (2006) 1685.<br />
Wu, F. F.; Zhang, Z. F.; Peker, A.; Mao, S. X.; Das, J.; Eckert, J.; Strength Asymmetry of<br />
Ducticle Dendrites Reinforced Zr- and Ti-based Composites, J. Mater. Res. 21 (2006)<br />
2331.<br />
Zhang, Z. F.; Zhang, H.; Shen, B. L.; Inoue, A.; Eckert, J.; Shear Fracture and<br />
Fragmentation Mechanisms of Bulk Metallic Glasses, Phil. Mag. Lett. 86 (2006) 643.<br />
- 13 -
Das, J.; Kim, K. B.; Xu, W.; Wei, B. C.; Zhang, Z. F.; Wang, W. H.; Yi, S.; Eckert, J.;<br />
Ductile Metallic Glasses in Supercooled Martensitic Alloys, Mater. Trans. 47 (2006) 2606.<br />
Concustell, A.; Mattern, N.; Wendrock, H.; Kühn, U.; Gebert, A.; Eckert, J.; Greer, A. L.;<br />
Sort, J.; Baró, M. D.; Mechanical <strong>Properties</strong> of a Two-Phase Amorphous Ni-Nb-Y Alloy<br />
Studied by Nanoindentation, Scripta Mater. 56 (2006) 85.<br />
Kühn, U.; Eymann, K.; Mattern, N.; Eckert, J.; Gebert, A.; Bartusch, B.; Schultz, L.; Limited<br />
Quasicrystal Formation in Zr-Ti-Cu-Ni-Al Bulk Metallic Glasses, Acta Mater. 54 (2006)<br />
4685.<br />
Dasgupta, S.; Das, J.; Eckert, J.; Manna, I.; Influence of Environment and Grain Size on<br />
Magnetic <strong>Properties</strong> of Nanocrystalline Mn-Zn Ferrite, J. Magn. Magn. Mater. 306 (2006)<br />
9.<br />
Dasgupta, S.; Kim, K. B.; Ellrich, J.; Manna, I.; Eckert, J.; Mechano-Chemical Synthesis<br />
and Characterization of Microstructure and Magnetic <strong>Properties</strong> of Nanocrystalline Mn1xZnxFe2O4,<br />
J. Alloys & Compo<strong>und</strong>s 424 (2006) 13.<br />
Van Steenberge, N.; Das, J.; Concustell, A.; Sort, J.; Suriñach, S.; Eckert, J.; Baró, M. D.;<br />
Influence of Annealing on the Microstructure and Hardness of Ti67.9Fe28.36Sn3.85<br />
Nanocomposite Rods, Scripta Mater. 55 (2006) 1087.<br />
Zhang, Z. F.; Wu, F. F.; Gao, W.; Tan, J.; Wang, Z. G.; Stoica, M.; Das, J.; Eckert, J.;<br />
Shen, B. L.; Inoue, A.; Wavy Cleavage Fracture of Bulk Metallic Glass, Appl. Phys. Lett. 89<br />
(2006) 251917.<br />
Das, J.; Eckert, J.; Theissmann, R.; Structural Short-Range Order of the β-Ti Phase in<br />
Bulk Ti-Fe-(Sn) Nanoeutectic Alloys, Appl. Phys. Lett. 89 (2006) 261917.<br />
Eckert, J.; Structure Formation and Mechanical Behavior of Two-Phase Nanostructured<br />
<strong>Material</strong>s, in: Nanostructured <strong>Material</strong>s – Processing, <strong>Properties</strong> and Potential<br />
Applications, (Hrsg. C.C. Koch). 2 nd Edition: William Andrew Publishing, Norwich, NY, USA<br />
(2006) 565.<br />
Eckert, J.; Das, J.; Kim, K. B.; Nanostructured Composites: Ti-Base Alloys, in: The Dekker<br />
Encyclopedia of Nanoscience and Nanotechnology, (Hrsg. J.A. Schwarz, C. Contescu, K.<br />
Putyera). Marcel Dekker, Inc., New York, NY, USA (2006) DOI: 10.1081 / E-ENN-<br />
120042102.<br />
Eckert, J.; Scudino, S.; Yu, P.; Duhamel, C.; Powder Metallurgy of Nanostructured High<br />
Strength <strong>Material</strong>s, in: Progress in Powder Metallurgy, (Hrsg. D.Y Yoon, S.-J.L. Kang, K.Y.<br />
Eun, Y.-S. Kim). Mater. Sci. Forum 534-536 (2006) 1405.<br />
- 14 -
Ceramics Group<br />
The emphasis in the ceramics group is on the correlation between microstructure and<br />
mechanical as well as functional properties. A number of processing methods are<br />
available in order to accomplish different microstructure classes, to determine their specific<br />
properties in an experiment and to rationalize these with straightforward modelling efforts.<br />
Thereby a materials optimization is afforded, which allows effective interplay between<br />
processing, testing and modelling. The scientific effort can be grouped as follows:<br />
1. Sintering of oxides<br />
Sintering of ceramics is approached using a continuum mechanical description, which<br />
affords inclusion of laminate stresses as arise in sintering of thin films and cosintering of<br />
several layers. In order to determine the constitutive equations for the sintering bodies,<br />
dilatometry and a new hot forging apparatus are used. This equipment together with a<br />
substantial modelling effort allows measurement of sintering stresses and viscosities and<br />
thereby predictions of shrinkage and curvature in multilayer structures. From an<br />
application points of view, thin optical layers and printed electronics are also investigated.<br />
<strong>Material</strong>s <strong>und</strong>er consideration are ZrO2, Al2O3, TiO2, ZnO as well as LTCC materials.<br />
2. Mechanical properties of ceramics and composites:<br />
Work on mechanical properties is geared towards an improved <strong>und</strong>erstanding of fracture<br />
strength, fracture toughness, R-curve behaviour and subcritical crack growth.<br />
Together with several European research groups we prepare and characterize metalceramic<br />
composites and metal-ceramic functionally graded materials<br />
<strong>Material</strong>s <strong>und</strong>er consideration are ZrO2, Al2O3/Cu and Al2O3/Al as well as various<br />
piezoceramics.<br />
3. Ferroelectric materials:<br />
Two scientific questions are of interest for this group. Reliability of piezoceramics for<br />
applications as actuator materials is <strong>und</strong>er investigation. An increasing number of electrical<br />
cycles leads to a progressive loss of obtainable strain and polarisation in these materials.<br />
Therefore electrical fatigue as influenced by the type of electrical loading, uniaxial stress,<br />
frequency and temperature are investigated. Recently, we developed a new method for<br />
stress-assisted (electromechanical poling), which reduces the required poling field<br />
considerably. Different new piezoceramics are being developed, especially new lead-free<br />
compositions, but also high-temperature piezoceramics.<br />
<strong>Material</strong>s <strong>und</strong>er consideration are PZT, lead-free piezoceramics and high-temperature<br />
piezoceramics.<br />
- 15 -
Staff Members<br />
Head<br />
Prof. Dr. Jürgen Rödel<br />
Research Associates Dr. Torsten Granzow<br />
Dr. Olivier Guillon<br />
Dr. Alain Brice Kounga Njiwa<br />
Technical Personnel<br />
Secretaries<br />
PhD Students<br />
Dr. Ludwig Weiler<br />
Dr. Ruzhong Zuo<br />
Dr. Nina Balke<br />
Emil Aulbach Herbert Hebermehl<br />
Roswita Geier<br />
M. Sc. Ilona Westram<br />
Dipl.-Ing. Julian Mircea<br />
Dipl. Min. Ingo Kerkamm<br />
M. Phys. Klaus Seifert<br />
M. Sc. Jami Winzer<br />
Dipl. Phys. Julia Glaum<br />
Dipl.-Ing. Thorsten Leist<br />
Diploma Students Lotta Gaab<br />
Markus König<br />
Silke Schaab<br />
Martin Molberg<br />
Bernd Meidel<br />
Andrea Engert<br />
Guest Scientists<br />
Research Projects<br />
Martin Frommherz<br />
Gila Völzke<br />
Dipl.-Phys. Thorsten Schlegel<br />
Dipl.-Ing. Johanna Wallot<br />
Dipl.-Ing. Daniel Meyer<br />
Dipl.-Ing. J.-Baptiste Ollagnier<br />
Dipl.-Ing. Silke Schaab<br />
Dipl.-Ing. Jochen Langer<br />
Dipl.-Ing. Markus König<br />
Goran Pavlovic<br />
Jochen Langer<br />
Thorsten Leist<br />
Joel Kamwa<br />
Florian Straub<br />
Prof. Dr. Sang Kezheng (University Xian)<br />
Dr. Shan-Tao Zhang (University Nanjing)<br />
Prof. Dr. David Green (Pennsylvania State University)<br />
Zuzanna Pouiznik (IPPT Warschau)<br />
Simonas Greicius (Universität Vilnius, Litauen)<br />
Andrius Lektutis (Universität Vilnius, Litauen)<br />
Julius Pozingis (Universität Vilnius, Litauen)<br />
Jaemyung Chang (KAIST, Südkorea)<br />
Enzo Chiarullo (Universität Mailand)<br />
Crack growth in ferroelectrics driven by cyclic electric loading (DFG and NSFC, 2002-<br />
2006)<br />
Processing of textured ceramic actuators with high strain (SFB 595, 2003-2006)<br />
Model experiments to describe the interaction between ferroelectric domains and<br />
agglomerates (SFB 595 2003-2006)<br />
- 16 -
Mesoscopic and macroscopic fatigue in doped ferroelectric ceramics (SFB 595), 2003-<br />
2006<br />
Development of anisotropy during sintering of LTCC materials (DFG, 2004-2006)<br />
Sintering of TiO2 with additives (Merck, 2004-2007)<br />
Knowledge-based multicomponent materials (EU, 6 th framework programme, 2004-2008)<br />
Electrooptical properties of PLZT (DFG 2006-08)<br />
High-temperature piezoceramics (DFG 2006-08)<br />
Printed <strong>Electronic</strong>s: Thin film ZnO (Merck 2006-09)<br />
Developing a ceramic roadmap (DFG 2005-07)<br />
Publications<br />
Kounga Njiwa, A. B.; Fett, T.; Lupascu D.C.; Rödel, J.; Effect of Geometry and electrical<br />
bo<strong>und</strong>ary conditions on R-curves for lead zirconate titanate; Eng. Fract. Mech., 73 (2006)<br />
309.<br />
Bordia R. K.; Zuo R.; Guillon O.; Salamone S.M.; Rödel J.; Anisotropic Constitutive Laws<br />
for Sintering Bodies; Acta <strong>Material</strong>ia, 54 (2006) 111.<br />
Lupascu D. C.; Genenko Y. A.; Balke N.; Aging in Ferroelectrics; J. Am. Ceram. Soc., 89<br />
[1] (2006) 224.<br />
Rao B. S.; Hemambar C.; Pathak A. V.; Pathel K. J.; Rödel J.; Jayram V.; Al/SiC Carriers<br />
for Microwave Integrated Circuits by a New Technique of Pressureless Infiltration; IEEE<br />
Transactions on <strong>Electronic</strong> Packaging Manufacturing, 29 [1] (2006) 58.<br />
Kounga Njiwa A. B.; Aulbach E.; Rödel J.; Turner S. L.; Comyn T. P.; Bell A. J.;<br />
Ferroelasticity and R-Curve Behavior in BiFeO3–PbTiO3; J. Am. Ceram. Soc., 89 [5]<br />
(2006) 1761.<br />
Zuo R.; Rödel J.; Chen R.; Li L.; Sintering and Electrical <strong>Properties</strong> of Lead-Free<br />
Na0.5K0.5NbO3 Piezoelectric Ceramics; J. Am. Ceram. Soc., 89 [6] (2006) 2010.<br />
Granzow T.; Kounga A. B.; Aulbach E.; Rödel J.; Electromechanical poling of<br />
piezoelectrics; Appl. Phys. Lett., 88 (2006) 252907.<br />
Kounga Njiwa A. B.; Aulbach E.; Rödel J.; Mechanical <strong>Properties</strong> of Dry-Pressed Powder<br />
Compacts: Case Study on Alumina Nanoparticles; J. Am. Ceram. Soc., 89 [8] (2006) 2641.<br />
Eichler J.; Hoffman M.; Eisele U.; Rödel J.; R-curve behaviour of 2Y-TZP with submicron<br />
grain size; J. Eur. Ceram Soc., 26 (2006) 3575.<br />
- 17 -
Zhou L.; Rixecker G.; Aldinger F.; Zuo R.; Zhao Z.; Electric Fatigue in Ferroelectric Lead<br />
Zirconate Stannate Titanate Ceramics Prepared by Spark Plasma Sintering; J. Am.<br />
Ceram. Soc., 89 [12] (2006) 3868.<br />
Balke N.; Lupascu D. C.; Blair T.; Gruverman A.; Thickness profile through fatigued bulk<br />
ceramic lead zirconate titanate; J. Appl. Phys.,100 (2006) 114117.<br />
Ollagnier J.-B.; Guillon O.; Rödel J.; Viscosity of LTCC Determined by Discontinuous<br />
Sinter-Forging; Int. J. Appl. Ceram. Technol., 3 [6] (2006) 437.<br />
Granzow, T.; Suvaci E.; Kungl H.; Hoffmann J.; Deaging of heat-treated iron-doped lead<br />
zirconate titanate ceramics; Appl. Phys. Lett., 89 (2006) 262908.<br />
- 18 -
<strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong><br />
The department <strong>Electronic</strong> <strong>Material</strong>s introduces the aspect of electric functional materials<br />
and their properties into the Institute of <strong>Material</strong>s Science. The associated research<br />
concentrates on the characterization of various classes of materials suited for<br />
implementation in information storage and organic electronics. Three major research<br />
topics are presently addressed:<br />
� <strong>Electronic</strong> and optoelectronic properties of organic semiconductors.<br />
� Charge transport and polarization in organic dielectrics.<br />
� Photo- and photostimulated luminescence in inorganic phosphors.<br />
A worldwide interest exists in the use of organic semiconductors in electronic and<br />
optoelectronic components, such as transistors and organic light emitting diodes, for novel<br />
areas of application. So far, multicolor organic displays have been implemented in<br />
commercially available cameras, car-radios, PDAs and mp3-players. Organic devices<br />
reaching further into the future might be simple logic circuits, constituting the core of<br />
communication electronics such as chip cards for radio frequency identification (RFID)<br />
tags and maybe one day flexible electronic newspapers where the information is<br />
continuously renewed via local area networks (LAN). In view of the mandatory<br />
technological development, the activities of the group are concerned with the<br />
characterization of organic material properties regarding the performance of organic<br />
electronic and optoelectronic devices. The major aspect deals with the charge carrier<br />
injection and transport taking place in organic field-effect-transistors and light emitting<br />
diodes. In particular the impact of electronic properties of the insulator / semiconductor<br />
interface on the performance of organic field-effect-transistors was subject of recent<br />
investigations. This research is of great technological importance, since it opens the field<br />
of complementary metal oxide semiconductor (CMOS) technology to organic<br />
semiconductors. A further matter of research activities deals with the stability of organic<br />
light emitting diodes. With the intention to enhance the device stability and performance,<br />
the influence of the device operation on the device life-time in conjunction with material<br />
and device specific properties is in the focus of interest. To conduct these demanding<br />
tasks, various experimental techniques for device fabrication and characterization are<br />
installed. Beside basic electric measurement setups, a laser spectroscopy setup, used for<br />
time-of-flight as well as a life-time measurements, and a Kelvin-probe atomic force<br />
microscope (AFM) to visualize the potential distribution of organic devices with nanometer<br />
resolution are available.<br />
In the field of polymer electrets present research comprises the characterization of surface<br />
charge distribution, charge stability, and charge transport properties of fluoropolymers, as<br />
well as their applications in acoustical transducers. Present investigations of charge<br />
transport and polarization in organic dielectrics are directed towards the basic<br />
<strong>und</strong>erstanding of polarization buildup and stabilization in PVDF and novel microporous<br />
dielectrics, which are scientifically interesting as model ferroelectric polymers. The<br />
available equipment includes poling devices, such as corona and high voltage setups, and<br />
a thermally stimulated current setup to investigate the energetic trap structure in dielectrics<br />
as well as the thermal charging and discharging <strong>und</strong>er high electric fields.<br />
The field of photo- and photostimulated luminescent (PSL) materials (phosphors) is<br />
- 19 -
concerned with the synthesis and characterization of suited inorganic compo<strong>und</strong>s. Such<br />
materials are used as wavelength converters in fluorescent lamps and in scintillating and<br />
information storing crystals. Present work is focused on x-ray detection materials, which<br />
exhibit needle-like growth, needed for improved resolution in medical imaging. In particular<br />
cesium halides-based storage phosphors and scintillators are <strong>und</strong>er investigation. Further<br />
research is concentrated on the low radiation hardness of CsBr:Eu 2+ . Radiation-induced<br />
defects like color centers and precipitations are studied by means of spectroscopic<br />
methods, electron microscopy and structural analysis.<br />
In the field of storage phosphors also BaFBr:Eu 2+ used in commercial image plates is<br />
investigated. On the one hand the mechanism of PSL-sensitization should be clarified. On<br />
the other hand the production of foils and glass ceramics including BaFBr:Eu 2+ is in the<br />
focus of the work.<br />
Another topic is radiation scintillators, which convert x-ray energy immediately into visible<br />
light, then detected by a CCD-array. For dynamical imaging in computer tomography (CT)<br />
a fast decay of the emitted light is required. Therefore investigations are focused on the<br />
mechanisms which influence the lifetime of the light emitting activator transitions.<br />
Furthermore general challenges are the sensitization of such phosphors in respect to the<br />
radiation energy, which can range from ultraviolet over hard γ-rays to thermal neutrons.<br />
Staff Members<br />
Head<br />
Prof. Dr. Heinz von Seggern<br />
Research Associate Dr. Kinga Horvath<br />
Dr. Christian Melzer<br />
Dr. Sergey V. Yampolskii<br />
Technical Personnel<br />
Secretary<br />
PhD Students<br />
Diploma Students<br />
Gabriele Andreß<br />
Sabine Hesse<br />
Gerlinde Dietrich<br />
Dipl.-Ing. Niels Benson<br />
Dipl.-Ing. Arne Fleissner<br />
Dipl.-Ing. Andrea Gassmann<br />
Dipl.-Phys. Oliver Karg<br />
Dipl.-Phys. Frederik Neumann<br />
Dennis Braun<br />
Andrea Gassmann<br />
Urs Krämer<br />
Tobias Lang<br />
Humboldt-fellow Dr. Graham Appleby<br />
Guest Scientist Prof. Dr. Sergei Fedosov<br />
Prof. Dr. Robert Fleming<br />
Dipl.-Phys. Xianguo Meng<br />
- 20 -<br />
Dr. Sergej Zhukov<br />
Dr. Jörg Zimmermann<br />
Bernd Stoll<br />
Dipl.-Phys. Ulrich Niedermeier<br />
Dipl.-Phys. Oliver Ottinger<br />
Dipl.-Ing. Martin Schidleja<br />
Dipl.-Ing. Christopher Siol<br />
Dipl.-Ing. Oliver Weiß<br />
Martin Schidleja<br />
Hanna R. Schmid<br />
Hans Schmidt
Research Projects<br />
Fatigue of organic semiconductor components. (SFB (DFG), 2003-2006)<br />
Phenomenological modelling of bipolar carrier transport in organic semiconducting devices<br />
<strong>und</strong>er special consideration of injection, transport and recombination phenomena. (SFB<br />
(DFG), 2003-2006)<br />
Investigation of fast scintillators with high efficiency for medical applications. (Siemens AG,<br />
prolonged 2004-2006)<br />
Piezoelectric sensor materials based on porous polymers. (BMWA-AiF 2005 – 2007)<br />
Investigation of poled fluoropolymer membranes by means of surface corona treatment.<br />
(Gore & Associates, 2003 – 2006)<br />
Polymer <strong>Electronic</strong>s: Investigation of functional instabilities of polymers and small molecule<br />
based field effect transistors. (BMBF-DLR 2005 – 2008)<br />
Investigation of the operation principle and optimisation of organic light emitting field effect<br />
transistors. (DFG 2005 – 2007)<br />
Self-organisation, orientation and electronic properties of organic thin films based on low<br />
molecular weight, oligomeric and polymeric materials at the interface in field effect<br />
transistors. (SPP (DFG) prolonged 2005 – 2007)<br />
Charge carrier injection and transport in doped organic light emitting diodes. (BMBF-<br />
OSRAM OS 2006 - 2009)<br />
- 21 -
Publications<br />
Fleissner, A.; Schmid, H.; Melzer, C.; Schmechel, R.; von Seggern, H.; Transition from<br />
Non-Dispersive to Dispersive Hole Transport in a Small Molecule Organic Semiconductor<br />
Controlled by Molecular Doping, MRS Proceedings 965E (2006) S14<br />
Hesse, S.; Zimmermann, J.; von Seggern, H.; Ehrenberg, H.; Fuess, H.; Fasel, C.; Riedel,<br />
R.; CsEuBr3: Crystal structure and its role in the photostimulation of CsBr : Eu 2+ , J. Appl.<br />
Phys. 100 (2006) 083506<br />
Neumann, F.; Genenko, Y. A.; Melzer, C.; von Seggern, H.; Self-consistent theory of<br />
unipolar charge-carrier injection in metal/insulator/metal systems, J. Appl. Phys. 100<br />
(2006) 084511<br />
Benson, N.; Schidleja, M.; Melzer, C.; Schmechel, R.; von Seggern, H.; Complementary<br />
organic field effect transistors by ultraviolet dielectric interface modification, Appl. Phys.<br />
Lett. 89 (2006) 182105<br />
Benson, N.; Ahles, M.; Schidleja, M.; Gassmann, A.; Mankel, E.; Mayer, T.; Melzer, C.;<br />
Schmechel, R.; von Seggern, H.; Organic CMOS technology by interface treatment, Proc.<br />
SPIE 6336 (2006) 63360S<br />
Olivati, C. A.; Carvalho, A. J. F.; Balogh, D. T.; von Seggern, H.; Faria, R. M.; Effect of ion<br />
concentration of ionomer in electron injection layer of polymer light-emitting devices, J.<br />
Non-Cryst. Solids 352 (2006) 1686<br />
Zhou, Y.; Yan, X.; Kroke, E.; Riedel, R.; Probst, D.; Thissen, A.; Hauser, R.; Ahles, M.; von<br />
Seggern, H.; Deposition temperature effect on the structure and optical property of RF-<br />
PACVD-derived hydrogenated SiCNO film, Mat.-wiss. u. Werkstofftech. 37 (2006) 173<br />
Hu, Z.; von Seggern, H.; Breakdown-induced polarization buildup in porous fluoropolymer<br />
sandwiches: a thermally stable piezoelectret, J. Appl. Phys. 99 (2006) 024102<br />
Neumann, F.; Genenko, Y. A.; von Seggern, H.; The Einstein relation in systems with trapcontrolled<br />
transport, J. Appl. Phys. 99 (2006) 013704<br />
- 22 -
Surface Science<br />
The surface science division of the institute of materials science uses advanced surface<br />
science techniques to investigate surfaces and interfaces of materials and materials<br />
combinations of technological use. For this purpose integrated UHV-systems have been<br />
built up which combine different surface analytical tools (photoemission, electron<br />
diffraction, ion scattering, scanning probe techniques) with the preparation of thin films<br />
(thermal evaporation, close-spaced sublimation, magnetron sputtering, MOCVD) and<br />
interfaces. The main research interest is directed to devices using polycrystalline<br />
compo<strong>und</strong> semiconductors and interfaces between dissimilar materials. The perspectives<br />
of energy conversion (e.g. solar cells) or storage (intercalation batteries) devices are of<br />
special interest. In addition, the f<strong>und</strong>amental processes involved in chemical and<br />
electrochemical device engineering and oxide thin films for electronic applications are<br />
investigated.<br />
The main research areas are:<br />
• Electrochemical Interfaces<br />
The aim of this research activity is the better <strong>und</strong>erstanding of electrochemical<br />
interfaces and contact formation. In addition, empirically derived (electro-) chemical<br />
processing steps as the controlled modification and structuring of materials is<br />
investigated and further optimized. In the center of our interest are<br />
semiconductor/electrolyte contacts<br />
• Intercalation Batteries<br />
The aim of this research activity is the better <strong>und</strong>erstanding of electronic properties of<br />
Li-intercalation batteries and of their degradation phenomena. Typically all solid state<br />
batteries are prepared and investigated using sputtering and CVD techniques for<br />
cathodes and solid electrolytes. In addition, the solid-electrolyte interface and<br />
synthetic surface layers are investigated as well as composite systems for increasing<br />
the capacity.<br />
• Thin film solar cells<br />
The aim of this research activity is the testing and development of novel materials<br />
and materials combinations for photovoltaic applications. In addition, the interfaces in<br />
microcrystalline thin film solar cells are to be characterized on a microscopic level to<br />
<strong>und</strong>erstand and to further improve the empirically based optimisation of solar cells.<br />
• Organic-inorganic interfaces and composites<br />
In this research area we are aiming at the development of composites marterials for<br />
(opto-)electronic applications. The decisive factors, which govern the electronic<br />
properties of interfaces between organic and inorganic materials are studied.<br />
• Oxide thin films for electronic applications<br />
The aim of this research area is to <strong>und</strong>erstand electronic surface and interfaces<br />
properties of oxides. We are mainly interested in transparent conducting oxide<br />
electrodes for solar cells and organic LEDs but also in dielectric and ferroelectric<br />
perovskites.<br />
- 23 -
• Surface analysis<br />
The UHV-surface science equipment and techniques using different and versatile<br />
integrated preparation chambers is used for cooperative service investigations.<br />
For the experiments we use integrated UHV-preparation and analysis-systems (UPS,<br />
(M)XPS, LEISS, LEED), spectromicroscopy (PEEM) coupled with UHV-STM/AFM. We<br />
further apply synchrotron radiation (SXPS, spectromicroscopy), scanning probe methods<br />
(STM, AFM), and electrochemical measuring techniques. UHV-preparation chambers<br />
dedicated for MBE, CVD, PVD and (electro)chemical treatment are available.<br />
The member of the group are involved in basic courses of the department’s curriculum and<br />
offer special courses on the physics, chemistry and engineering of semiconductor devices<br />
and solar cells, on surface and interface science, and on thin film and surface technology.<br />
Staff Members<br />
Head<br />
Prof. Dr. W. Jaegermann<br />
Research Associates Dr. David Ensling<br />
Dr. Ralf Hunger<br />
Dr. Alexander Issanin<br />
Technical Personnel<br />
Secretary<br />
PhD Students<br />
Diploma Students<br />
Dipl.-Ing. Erich Golusda<br />
Dipl.-Ing. Gabi Haindl<br />
Marga Lang<br />
Dipl.-Ing. Yvonne Gassenbauer<br />
Dipl.-Ing. Christoph Körber<br />
Dipl.-Ing. Johannes Luschitz<br />
Dipl.-Ing. Erik Mankel<br />
Dipl.-Ing. Frank Säuberlich<br />
Mario Böhme<br />
Maxime Monnoyer<br />
Bastian Siepchen<br />
Guest Scientist Alireza Barati<br />
Dr. Sivakumar Bhuvaneswari<br />
Dr. Massimiliano Liberatore<br />
Dr. Venkata Rao Gutlapalli<br />
Krishnakumar Velappan<br />
- 24 -<br />
Dr. Andreas Klein<br />
Dr. Thomas Mayer<br />
Dr. Andreas Thißen<br />
Kerstin Lakus-Wollny<br />
Christina Spanheimer<br />
Dipl.-Ing. Bastian Siepchen<br />
Dipl.-Ing. Robert Schafranek<br />
Dipl.-Ing. Konrad Schwanitz<br />
Dipl.-Ing. Bettina Späth<br />
Dipl.-Ing. Ulrich Weiler<br />
Mark Trummlitz<br />
André Wachau
Research Projects<br />
Dedicated preparation-, transfer and spectrometer system for the analysis of materials<br />
modifications and –synthesis at solid-liquid-interfaces with synchrotron radiation (BMBF,<br />
2001-2007)<br />
High performance CdTe thin film solar cells<br />
(2003 – 2007)<br />
Intercalnet<br />
(EU, 2003 – 2006)<br />
Bo<strong>und</strong>ary layers and thin films of ionic conductors: <strong>Electronic</strong> structure, electrochemical<br />
potentials, defect formation and degradation mechanisms<br />
(DFG – SFB, 2003 – 2006)<br />
Function and fatigue of conducting electrodes in organic LEDs and piezoceramic actuators<br />
(DFG – SFB, 2003 – 2006)<br />
Tunable Integrated Components for Microwaves and Optics<br />
Graduiertenkolleg 1037 (07/2004 – 12/2008)<br />
<strong>Material</strong>s World Network: Interdisciplinary bulk/surface studies of transparent conducting<br />
oxides<br />
(2006 – 2009)<br />
Hybrid structures of TsLiMPO4 phospho-olivines with C-nanofilaments for Li-ion-batteries:<br />
preparation, properties and potential applications<br />
(DFG – SPP1181, 2006 – 2008)<br />
Chemical vapor deposition (PE-MOCVD) of cation-substituted transition metal oxide thin<br />
films (Li(Co1-xNix)1-yMy02 (M=Mg, Al) for intercalation cathodes: structure, electronic<br />
structure and electrochemical parameters<br />
(DFG, 2005 – 2007)<br />
Publications<br />
U. Weiler, K. Schwanitz, C. Kelting, D. Schlettwein, D. Wöhrle, T. Mayer and W.<br />
Jaegermann, Phthalocyanines Incorporated into Hot Wire-CVD Grown Silicon, Thin Solid<br />
Films 511-512, 172 (2006)<br />
T. Mayer, M. Lebedev, R. Hunger, W. Jaegermann, Synchrotron Photoemission Analysis<br />
of Semiconductor/Electrolyte Interfaces by the Frozen-Electrolyte Approach: Interaction of<br />
HCl in 2-Propanol with GaAs(100), J. Phys. Chem. B; 110, 2293-2301 (2006)<br />
C. Kelting, U.Weiler, T.Mayer, W. Jaegermann, S. Makarov, D. Wöhrle, O. Abdallah, M.<br />
Kunst, and D. Schlettwein, Sensitization of thin-film-silicon by a phthalocyanine as strong<br />
organic absorber, Organic <strong>Electronic</strong>s 7, 363–368, (2006)<br />
- 25 -
T. Mayer, U. Weiler, E. Mankel and W. Jaegermann, Bulk sensitization of inorganic<br />
semiconductors with organic guest molecules: zink-phthalozyanine embedded into µc-Si<br />
and ZnSe host matrices , Proc. 4th World Conference on Photovoltaic Energy Conversion<br />
T. Deniozou, N. Esser, T. Schulmeyer, R. Hunger, A (4x2) surface reconstruction of<br />
CuInSe2(001) studied by low-energy electron diffraction and soft x-ray photoemission<br />
spectroscopy, Applied Physics Letters 88(5) (2006), p. 052102-3.<br />
R. Hunger, W. Jaegermann, A. Merson, Y. Shapira, C. Pettenkofer, J. Rappich, <strong>Electronic</strong><br />
structure of methoxy-, bromo-, and nitrobenzene grafted onto Si(111), Journal of Physical<br />
Chemistry B 110(31); 15432-15441.<br />
Y. Gassenbauer, R. Schafranek, A. Klein, S. Zafeiratos, M. Hävecker, A. Knop-Gericke, R.<br />
Schlögl, Surface potential changes of semiconducting oxides monitored by high-pressure<br />
photoelectron spectroscopy: Importance of electron concentration at the surface, Solid<br />
State Ionics 177, 3123-3127 (2006).<br />
S.P. Harvey, T.O. Mason, Y. Gassenbauer, R. Schafranek, A. Klein, Surface vs. Bulk<br />
<strong>Electronic</strong>/Defect Structures of Transparent Conducting Oxides. Part I. Indium Oxide and<br />
ITO, Journal of Physics D: Applied Physics 39, 3959-3968 (2006).<br />
Y. Gassenbauer, R. Schafranek, A. Klein, S. Zafeiratos, M. Hävecker, A. Knop-Gericke, R.<br />
Schlögl, Surface states, surface potentials and segregation at surfaces of tin-doped In2O3,<br />
Physical Review B 73, 245312 (2006).<br />
P. Erhart, K. Albe, A. Klein, First-principles study of intrinsic point defects in ZnO: Role of<br />
band structure, volume relaxation, and finite-size effects, Physical Review B 73, 205203<br />
(2006).<br />
R. Schafranek, A. Klein, In-situ photoemission study of the contact formation of<br />
(Ba,Sr)TiO3 with Cu and Au , Solid State Ionics 177, 1659-1664 (2006).<br />
Y. Gassenbauer, A. Klein, <strong>Electronic</strong> and chemical properties of ITO surfaces and<br />
ITO/ZnPc interfaces studied in-situ by photoelectron spectroscopy, Journal of Physical<br />
Chemistry B 110, 4793-4801 (2006).<br />
A. Sivasankar Reddy, P. Sreedhara Reddy, S. Uthanna, G. Venkata Rao, A. Klein, Effect<br />
of substrate temperature on the physical properties of dc magnetron sputtered Cu2O films,<br />
Physica Status Solidi (a) 203, 844-853 (2006).<br />
A. Klein, T. Schulmeyer, Interfaces of Cu-chalcopyrites, in Wide gap chalcopyrites edited<br />
by S. Siebentritt and U. Rau (Springer-Verlag, Heidelberg, 2006).<br />
F. Rüggeberg, A. Klein, The In2O3/CdTe interface: A possible contact for thin film solar<br />
cells?, Applied Physics A 82, 281-285 (2006).<br />
Q.-H.Wu, A. Thissen, W. Jaegermann, M. Schuez, P.C. Schmidt, Resonant photoemission<br />
spectroscopy study of electronic structure of V2O5, Chemical Physics Letters 430, 309-313<br />
(2006).<br />
- 26 -
Q.-H. Wu, A. Thissen, W. Jaegermann, Photoemission spectroscopy and electronic<br />
structures of LiMn2O4, Chinese Physics Letters 23, 2202-2205 (2006).<br />
F. Donsanti, K. Kostourou, F. Decker, N. Ibris, A.M. Salvi, M. Liberatore, A. Thissen, W.<br />
Jaegermann, D. Lincot, Alkali ion intercalation in V2O5: preparation and laboratory<br />
characterization of thin films produced by ALD, Surface and Interface Analysis 38, 815-818<br />
(2006).<br />
Y.P. Zhou, D. Probst, A. Thissen, E. Kroke, R. Riedel, R. Hauser, H. Hoche, E. Broszeit,<br />
P. Kroll, H. Stafast, Hard silicon carbonitride films obtained by RF-plasma-enhanced<br />
chemical vapour deposition using the single-source precursor<br />
bis(trimethylsilyl)carbodiimide, Journal of the European Ceramic Society 26, 1325-1335<br />
(2006).<br />
Y. Zhou, X. Yan, E. Kroke, R. Riedel, D. Probst, A. Thissen, R. Hauser, M. Ahles, H. von<br />
Seggern, Deposition temperature effect on the structure and optical property of RF-<br />
PACVD-derived hydrogenated SiCNO film, <strong>Material</strong>wissenschaft <strong>und</strong> Werkstofftechnik 37,<br />
173-177 (2006).<br />
- 27 -
Thin films<br />
The Thin Film division works on advanced thin film deposition techniques of novel<br />
materials. In the year 2006 we have introduced a new laser assisted deposition method at<br />
TU Darmstadt, pulsed laser deposition (PLD). In collaboration with the Max-Planck-<br />
Institute for Solid State Physics in Stuttgart, another frontier thin film deposition system has<br />
been designed: a dedicated oxide Molecular Beam Epitaxy (MBE) system (oxide-MBE).<br />
This system is to be one of a few systems worldwide offering comparable functionalities.<br />
We expect that the introduction of two state-of-the-art thin film deposition techniques at TU<br />
Darmstadt will advance the search for novel and enhanced oxide thin films.<br />
The class of oxide ceramics, in particular with perovskite and derived structures,<br />
comprises a stunning variety of new functional materials. Examples are high-temperature<br />
superconductors, magnetic oxides for spintronics, high-k dielectrics, ferroelectrics,<br />
and materials for thin film batteries. As a vision for future, new solid state matter can be<br />
created by building hetero- and composite structures combining different oxide materials.<br />
While present day electronic devices heavily rely on semiconducting materials, a future<br />
way to create novel functional devices could be based on oxide electronics. Oxide<br />
electronics and spintronics are part of the research and graduate education program<br />
“Matronics” that has been applied for within the Excellence Initiative by the the German<br />
federal and state governments to promote science and research at German universities.<br />
Matronics is coordinated by Lambert Alff (Thin Film division) and Heinz von Seggern<br />
(<strong>Electronic</strong> <strong>Material</strong>s division) and has been positively evaluated in the first ro<strong>und</strong> of the<br />
Excellency Initiative.<br />
The characterization tools located in the Thin Film division include x-ray diffraction (XRD),<br />
x-ray photoemission spectroscopy (XPS), high-resolution scanning electron microscopy<br />
(HREM) with light element sensitive EDX, and SQUID magnetometry. A new 16 Tesla<br />
magnet cryostat allowing measurements down to liquid helium temperature has been<br />
installed. Another magnet cryostat lowering the available temperature range to below 300<br />
mK is currently being installed. The group is also using external large scale facilities as<br />
synchrotron radiation (ESRF, Grenoble) and neutron reactors (ILL, Grenoble / HMI, Berlin /<br />
FRM II, Garching) for advanced sample characterization. There is an ongoing cooperation<br />
with GSI (Darmstadt) and with the Institute for Nuclear Physics at the Goethe-University<br />
(Frankfurt) in the field of ion beam techniques (e.g. RBS, NRA, IBM) and nuclear probe<br />
methods (positron annihilation and Mössbauer spectroscopy), in particular with the<br />
direction of defect and interface structure investigations.<br />
Close cooperation exists in particular with the Max-Planck-Institute for Solid State<br />
Research in Stuttgart and with the Japanese company NTT in Atsugi near Tokio. As a new<br />
group member, Dr. Komissinskiy can be welcomed, who has spent several successful<br />
years at the renowned Chalmers University of Technology in Göteborg, Sweden.<br />
In teaching the group is offering courses and lab exercises in basic materials science as<br />
part of the department’s main curriculum. New special courses for advanced students on<br />
Magnetism and Magnetic <strong>Material</strong>s, Spintronics as well as Advanced <strong>Material</strong>s have been<br />
introduced. The group is also giving a practical introduction in high-resolution scanning<br />
electron microscopy and ion beam techniques for students and researchers in the field.<br />
In 2006 Lambert Alff has accepted the position of Dean of Studies for <strong>Material</strong>s Science.<br />
- 28 -
Staff Members<br />
Head / Secretary Prof. Dr. Lambert Alff Marion Bracke<br />
Research Dr. Adam G. Balogh Dr. Philipp Komissinskiy<br />
Associates Dr. Jose Kurian<br />
Technical Personnel Jürgen Schreeck<br />
PhD Students Matthias Hawraneck Yoshiharu Krockenberger<br />
Andreas Winkler<br />
Diploma Students Ceena Joseph Narendirakumar Narayanan<br />
Guest Scientists Dr. Sergej Duvanov, Institute for Applied Physics, Academy of<br />
Sciences, Ukraine<br />
Research Projects<br />
Symmetry of the order parameter and pseudogap behavior in electron doped hightemperature<br />
superconductors, within Research Unit 538 (DFG, 2004-2006)<br />
Superconductivity in water intercalated NaxCoO2 thin films (TU Darmstadt, TU<br />
Braunschweig, and Max-Planck-Institute for Solid State Research, Stuttgart (DFG, 2006-<br />
2010)<br />
Fabrication of electron-doped high-temperature superconductors (TUD & NTT, Japan,<br />
since 1999)<br />
Investigation of defect structure and diffusion in ferroelectric materials, Project B2 within a<br />
Collaborative Research Center (SFB 595, 2003-2010)<br />
Atomic transport and transient processes at nanostructured metal/ceramic and<br />
ceramic/ceramic systems, BMBF, UKR 05/003 (2006-2008)<br />
Study of defect structure of semiconductors and intermetallic phases (TU Darmstadt & TU<br />
Graz, since 1996)<br />
Publications<br />
Alff, L.; Die spinnen, die Oxide: Neue <strong>Material</strong>ien für die Spintronik; in: Thema Forschung:<br />
Intelligente <strong>Material</strong>ien, TU Darmstadt 2/2006.<br />
Bejarano, G.; Caicedo, J.M.; Baca, E.; Prieto, P.; Balogh, A.G.; Enders, S.; Deposition of<br />
B4C/BCN/c-BN multilayered thin films by r.f. magnetron sputtering; Thin Solid Films 494<br />
(2006) 53-57.<br />
- 29 -
Berky, W.; Gottschalk, S.; Elliman, R.G.; Balogh, A.G.; Orientation dependent ion beam<br />
mixing of Ta/Si interfaces; Nucl. Instr. and Meth. B 249 (2006) 200-203.<br />
Geprägs, S.; Majewski, P.; Gross, R.; Ritter, C.; Alff, L.; Electron doping in the double<br />
perovskite LaxA2-xCrWO6 with A = Sr, Ca, and Ba; J. Appl. Phys. 99 (2006) 08J102.<br />
Karim, S.; Toimil-Molares, M.E.; Balogh, A.G.; Ensinger, W.; Cornelius, T.W.; Khan, E.U.;<br />
Neumann, R.; Morphological evolution of Au nanowires controlled by Rayleigh instability;<br />
Nanotechnology 17 (2006) 5954-5959<br />
Kornev, V.K.; Karminskaya, T.Y.; Kislinskii, Yu.V.; Komissinki, P.V.; Constantinian, K.Y.;<br />
Ovsyannikov, G.A.; Dynamics of <strong>und</strong>erdamped Josephson junctions with nonsinusoidal<br />
current-phase relation; Physica C 435 (2006) 27–30.<br />
Krockenberger, Y.; Fritsch, I.; Cristiani, G.; Habermeier, H.-U.; Yu, L.; Bernhard, C.;<br />
Keimer, B.; Alff, L.; Superconductivity in epitaxial thin films of NaxCoO2* yD2O; Appl. Phys.<br />
Lett. 88 (2006) 162501.<br />
Ovsyannikov, G.A.; Borisenko, I.V.; Komissinskii, P.V.; Kislinskii, Yu.V.; Zaitsev, A.V.;<br />
Anomalous proximity effect in superconducting oxide structures with an antiferromagnetic<br />
layer, JETP Lett. 84 (2006) 262-266.<br />
Ovsyannikov, G.A.; Constantinian, K.Y.; Kislinskii, Yu.V.; Komissinskii, P.V.; Borisenko,<br />
I.V.; Karminskaya, T.Yu.; Kornev, V.K.; Microwave dynamics of Josephson structures with<br />
nontrivial current-phase relation; J. Comm. Technology and <strong>Electronic</strong>s 51 (2006) 1078-<br />
1086.<br />
- 30 -
Dispersive Solids<br />
The research of the Dispersive Solids group is based on the development of strategies for<br />
producing novel inorganic, oxidic, and non-oxidic materials. The main focus is the<br />
synthesis of ceramics with properties which exceed the present state of the art.<br />
Synthesis methods like the sol-gel-technology, polymer pyrolysis and chemical vapour<br />
deposition (CVD) as well as high pressure/high temperature synthesis in diamond and<br />
multi anvil cells are used and continuously further developed. Moreover molecular,<br />
oligomeric, and polymeric ceramic precursors as well as inorganic materials derived<br />
therefrom are synthesized and characterized. Further emphasis is put on the<br />
transformation of the precursors into ceramic components (for example layers, fibers, bulk<br />
materials, composites, membranes) and the characterization of their chemical and<br />
physical materials properties. The aim of our research activities is to correlate those<br />
properties with the composition and structure of the molecular precursors.<br />
The present projects include the following four main topics: materials synthesis, properties,<br />
modeling, and processing & applications.<br />
Staff Members<br />
Head<br />
Prof. Dr. Dr. h. c. Ralf Riedel<br />
Research Associates Dr. Hans-Gerhard Bremes<br />
Dr. Aleksander Gurlo<br />
Dr. Ralf Hauser<br />
Dr.-Ing. Elisabeta Horvath-<br />
Bordon<br />
Technical Personnel<br />
Secretaries<br />
PhD Students<br />
Dipl.-Ing. Claudia Fasel<br />
Su-Chen Chang Karen Böhling<br />
Dipl.-Ing. Ricardo Chavez<br />
Dipl.-Ing. Susanne Deuchert<br />
M.Tech. Dmytro Dzivenko<br />
Dipl.-Min. Michael Eberhardt<br />
Dipl.-Ing. Alexander<br />
Klonczynski<br />
- 31 -<br />
Dr. Emanuel Ionescu<br />
Dr. Isabel Kinski<br />
Dr. Sandra Martinez-Crespiera<br />
Dr. Gabriela Mera<br />
Dr. Liviu Toma<br />
Dipl.-Chem. Verena Liebau-<br />
Kunzmann<br />
Dipl.-Ing. Ilaria Menapace<br />
Dipl.-Ing. Bernard Rodrigue<br />
Ngoumeni Yappi<br />
Dipl.-Ing. Vassilios Siozios
Guest Scientists<br />
Research Projects<br />
Prof. Dr. Corneliu Balan, Politehnica, Univ. of Bucharest,<br />
Romania<br />
Dr. Matilda Zemanova, Faculty of Chem. Technology, Slovak<br />
University of Technology, Slovakia<br />
Sepideh Kamrani, Sharif University of Technology, Teheran,<br />
Iran<br />
Lisa Biasetto, Università di Padova, Italy<br />
Prof. Dr. Yali Li, Tianjin University, China<br />
Novel functional ceramics with substitution of anions in oxide systems, (DFG, SFB 595,<br />
project A4, since Jan. 2003)<br />
High pressure synthesis of novel nitrides of model M3-xAxN4 (M, A = V, Nb, Ta, Ti, Zr, Hf,<br />
Pb; 0
Publications<br />
Zhou, Y.; Probst, D.; Thissen, A.; Kroke, E.; Riedel, R.; Hauser, R.; Hoche, H.; Broszeit,<br />
E.; Kroll, P.; Stafast, H.; Hard Silicon Carbonitride Films Obtained by RF-Plasma<br />
Enhanced Chemical Vapour Deposition Using the Single Source Precursor<br />
Bis(trimethylsilyl)-carbodiimide, J. Europ. Ceram. Soc. 26 (2006) 1325-1335.<br />
Liebau-Kunzmann, V.; Fasel, C.; Kolb, R.; Riedel, R.; Lithium Containing Silazanes as<br />
Precursors for SiCN:Li Ceramics – A Potential <strong>Material</strong> for Electrochemical Applications, J.<br />
Europ. Ceram. Soc. 26 (2006) 3897-3901.<br />
Kolb, R.; Fasel, C.; Liebau-Kunzmann, V.; Riedel, R.; SiCN/C-Ceramic Composite as<br />
Anode <strong>Material</strong> for Lithium Ion Batteries, J. Europ. Ceram. Soc. 26 (2006) 3903-3908.<br />
Zhou, Y.; Yan, X.; Kroke, E.; Riedel, R.; Probst, D.; Thissen, A.; Hauser, R.; Ahles, M.; von<br />
Seggern, H.; Deposition Temperature Effect on the Structure and Optical Property of RF-<br />
PACVD-Derived Hydrogenated SiCNO Film, <strong>Material</strong>wissenschaft <strong>und</strong> Werkstofftechnik<br />
37 (2006) 173-177.<br />
Zerr, A.; Riedel, R.; Sekine, T.; Lowther, J.E.; Ching, W.-Y.; Tanaka, I.; Recent Advances<br />
in New Hard High-Pressure Nitrides, Adv. Mat. 18 (2006) 2933.<br />
Hauser, R.; Nahar-Borchard, S.; Riedel, R.; Ikuhara, Y.H.; Iwamoto, Y.; Polymer-Derived<br />
SiBCN Ceramic and their Potential Application for High Temperature Membranes”, J.<br />
Ceram. Soc. Jpn. 114 (2006) 567-570.<br />
Völger, K.W.; Hauser, R.; Kroke, E.; Riedel, R.; Ikuhara, Y.H.; Iwamoto, Y.; Synthesis and<br />
Characterization of Novel Non-Oxide Sol-Gel Derived Mesoporous Amorphous Si-C-N<br />
Membranes, J. Ceram. Soc. Jpn. 114 (2006) 524-528.<br />
Balan, C.; Riedel, R.; Rheological Investigations of a Polymeric Precursor for Ceramic<br />
<strong>Material</strong>s: Experiments and Theoretical Modelling, J. Optoelec. Adv. Mat. 8 (2006) 561-<br />
567.<br />
Riedel, R.; Mera, G.; Hauser, R.; Klonczynski, A.; Silicon-Based Polymer-Derived<br />
Ceramics: Synthesis, <strong>Properties</strong> and Applications --- A Review, J. Ceram. Soc. Jpn. 114<br />
(2006) 425-444.<br />
Ischenko, V.; Harshe, R.; Riedel, R.; Woltersdorf, J.; Cross-Linking of Functionalised<br />
Siloxanes with Alumatrane: Reaction Mechanisms and Kinetics, J. Organomet. Chem. 691<br />
(2006) 4086-4091.<br />
Dzivenko, D.A.; Zerr, A.; Boehler, R.; Riedel, R.; Equation of State of Cubic Hafnium(IV)<br />
Nitride Having Th3P4-Type Structure, Solid State Comm. 139 (2006) 255-258.<br />
Horvath-Bordon, E.; Riedel, R.; Zerr, A.; McMillan, P.F.; Auffermann, G.; Prots, Y.;<br />
Bronger, W.; Kniep, R.; Kroll, P.; High-Pressure Chemistry of Nitride-Based <strong>Material</strong>s,<br />
Chem. Soc. Rev. 35 (2006) 987-1014.<br />
- 33 -
Hesse, S.; Zimmermann, J.; von Seggern, H.; Ehrenberg, H.; Fueß, H.; Fasel, C.; Riedel,<br />
R.; CsEuBr3: Crystal Structure and Its Role in the Photostimulation of CsBr:Eu 2+ , J. Appl.<br />
Phys. 100 (2006) 083506.<br />
Enz, T.; Winterer, M.; Stahl, B.; Bhattacharya, S.; Miehe, G.; Foster, K.; Fasel, C.; Hahn,<br />
H., Structure and magnetic properties of iron nanoparticles stabilized in carbon, J. Appl.<br />
Phys. 99 (2006) 044306.<br />
Riedel, R.; Wakai, F.; Special Issue dedicated to Professor Günter Petzow on the<br />
Occasion of his 80th Birthday: Modern Trends in Advanced Ceramics, J. Ceram. Soc. Jpn.<br />
114 (2006) 1335.<br />
Graf, M.; Gurlo, A.; Barsan, N.; Weimar, U.; Hierlemann, A.; Microfabricated gas sensor<br />
systems with nanocrystalline metal-oxide sensitive films, J. Nanoparticle Research 8<br />
(2006) 823.<br />
Gurlo, A.; Barsan, N.; Weimar, U.; Gas sensors based on semiconducting metal oxides, in<br />
Metal Oxides: Chemistry and Applications, Ed. J.L.G.Fierro, CRC Press, Boca Raton,<br />
2006, pp. 683-738.<br />
Gurlo, A.; Interplay between O2 and SnO2: oxygen ionosorption and spectroscopic<br />
evidence of adsorbed oxygen (Minireview), ChemPhysChem 7 (2006) 2041.<br />
Sahm, T.; Gurlo, A.; Barsan, N.; Weimar, U.; <strong>Properties</strong> of indium oxide semiconducting<br />
sensors deposited by different techniques, Particulate Science and Technology 24 (2006)<br />
441.<br />
Mädler, L.; Sahm, T.; Gurlo, A.; Grunwaldt, J.D.; Barsan, N.; Weimar, U.; Pratsinis, S.E.;<br />
Sensing low concentrations of CO using flame-spray-made Pt/SnO2 nanoparticles, J.<br />
Nanoparticle Research, 8 (2006) 783.<br />
Sahm, T.; Gurlo, A.; Barsan, N.; Weimar, U.; Basics of oxygen and SnO2 interaction: work<br />
function change and conductivity measurements, Sens. Actuators B 118 (2006) 78.<br />
Mädler, L.; Roessler, A.; Pratsinis, S.E.; Sahm, T.; Gurlo, A.; Barsan, N.; Weimar, U.;<br />
Direct formation of highly porous gas-sensing films by in-situ thermophoretic deposition of<br />
flame-made Pt/SnO2 nanoparticles, Sens. Actuators B 114 (2006) 283.<br />
Polleux, J., Gurlo, A.; Barsan, N.; Weimar, U.; Antonietti, M.; Niederberger, M.; Templatefree<br />
synthesis and assembly of single-crystalline tungsten oxide nanowires and their gassensing<br />
properties, Angew. Chem. Int. Ed., 45 (2006) 261.<br />
- 34 -
Patents<br />
Heinrich, J.G.; Günster, J.; Rastätter, S.; Riedel, R.; Verfahren <strong>und</strong> Vorrichtung zur<br />
Herstellung von dreidimensionalen keramischen Strukturen, German Patent, Patent-No.<br />
102 00 313, 27.04.2006.<br />
Awards<br />
Dr. Horvath-Bordon, Elisabeta; Honorary Research Fellow of the Department of<br />
Chemistry, University College London, 1 Dec. 2006 – 1 Dec. 2009.<br />
Prof. Dr. Riedel, Ralf; Honorary Doctorate (Dr. h. c.),12. Sep. 2006, Slovak Academy of<br />
Sciences, Bratislava, Slovakia.<br />
- 35 -
Structure Research<br />
The research in the fields of heterogeneous catalysis, battery materials and magnetic<br />
properties of oxides and alloys continued sucessfully during the last year. The division was<br />
also very actively involved in the Center of Excellence on Fatigue.<br />
The neutron powder diffractometer SPODI had its first year of full operation and fulfilled all<br />
expectations as the instrument which attracted most proposals at FRM II. The beam-line<br />
responsibles are Markus Hölzel and Anatoliy Senyshyn. The synchrotron powder beamline<br />
B2 at HASYLAB is functioning in the frame-work of a Virtual Institute of the Helmholtz<br />
society. The scientists at DORIS in Hamburg were Carsten Bähtz and Dmytro Trots.<br />
Carsten Bähtz discontinued his contract with the Virtual Institute at the end of 2006 to take<br />
a position at FZ Rossendorf. Hermann Pauly who continuously worked in the laboratory<br />
after his retirement more or less stopped his successful research on Zintl-phases. Special<br />
thanks are due to Helmut Ehrenberg who accepted an offer from Institut für Festkörper-<br />
and Werkstoffforschung Dresden and left the institute on Sept. 30 after many years of<br />
successful work in the group of structure research. Prof. Fuess officially retired at the end<br />
of the summer semester but will continue in the frame of a contract with TU Darmstadt for<br />
the next 3 years. He has been appointed as a rapporteur for the cooperative evolution of<br />
five Max-Plack-Institutes and as chairman of the Comission for Joint Research at Large<br />
Scale Facilities (Verb<strong>und</strong>forschung Erforschung kondensierter Materie an Großgeräten) of<br />
the BMBF. He is a member of the Fachkollegium Kristallographie of DFG and numerous<br />
evaluation commitees of DFG, CNRS, CSIC, ESF or of the European Union. He was<br />
awarded a Humboldt-Research-Prize of the Fo<strong>und</strong>ation for Polish Science.<br />
Staff Members<br />
Head<br />
Prof. Dr.-Ing. Dr. h.c. Hartmut Fueß<br />
Research Associates Dr. Natalia Bramnik<br />
Dr. Joachim Brötz<br />
Dr. Helmut Ehrenberg<br />
Dr. Achim Hohl<br />
Dr. Markus Hölzel<br />
Technical Personnel<br />
Secretary<br />
PhD Students<br />
Dipl.-Ing. Heinz Mohren<br />
Jean-Christophe Jaud<br />
Maria Holzmann<br />
Dipl.-Phys. Mouner Abdalslam<br />
Dipl.-Phys. Jens Engel<br />
Dipl.-Chem. Rachid Essehli<br />
Dipl.-Chem. Lars Giebeler<br />
Dipl.-Ing. Toni André Groß<br />
Dipl.-Phys. Aleksandra Gruzdeva<br />
Dipl.-Ing. Hanna Hahn<br />
- 36 -<br />
Dr. Daria Mikhailova<br />
Dr. Isabel Kinski<br />
Dr. Daria Mikhailova<br />
Dr. Anatoliy Senyshyn<br />
Dr. Hans Weitzel<br />
Ingrid Svoboda<br />
Dipl.-Ing. Kristian Nikolowski<br />
Dipl.-Ing. Navid Qureshi<br />
Dipl.-Ing. Frieder Scheiba<br />
Dipl.-Ing Roland Schierholz<br />
Dipl.-Ing Christian Schmitt<br />
Dipl.-Ing. Ljubomira Schmitt<br />
Dipl.-Min. Kristin Schönau
Diploma Student<br />
Dipl.-Phys. Nyam-Ochir Lkhanaajav<br />
Dipl.-Ing Thomas Locherer<br />
Dipl.-Ing. Florian Maurer<br />
Dipl.-Ing. Marian Mazurek<br />
Manuel Hinterstein<br />
Dipl. Ing. Dominic Stürmer<br />
Dipl.-Ing. Björn Schwarz<br />
Dipl.-Ing. Dmytro Trots<br />
Dipl.-Ing. Emanuel Vollmar<br />
Jens Kling<br />
Guest Scientists Dr. Larisa Balsanova, Ulan Ude, Russia<br />
Dr. Miroslav Boča, Academy of Sciences, Bratislava, Slovakia<br />
Prof. Dr. Roman Boča, Technical University Bratislava, Slovakia<br />
Prof. Dr. Abdelwahab Cheikhrouhou, University of Sfax, Tunisia<br />
Dr. Rim Yong Chol, Academy of Sciences, Pyongyang,<br />
Peoples Republic of Korea<br />
Dr. Lubor Dlháň, Technical University Bratislava, Slovakia<br />
Dr. Grygoriy Dmytriv, Ivan-Franko-University Lviv, Ukraina<br />
Dr. Eno Ebenso, University of Calabar, Nigeria<br />
Prof. Dr. Thimme Gowda, University of Mangalore, India<br />
Dipl.-Ing. Radoslava Ivanikova, Technical University Bratislava, Slovakia<br />
Dr. Radovan Herchel, Technical University Bratislava, Slovakia<br />
Dr. Jozef Kožišek, Technical University Bratislava, Slovakia<br />
Dr. Mohamed Loukil, University of Sfax, Tunisia<br />
Dr. Anna Mašlejová, Technical University Bratislava, Slovakia<br />
Dr. Anouar Njeh, University of Sfax, Tunisia<br />
Dr. Blažena Papánková, Technical University Bratislava, Slovakia<br />
Prof. Dr. Volodymyr Pavlyuk, Ivan-Franko-University Lviv, Ukraina<br />
Dipl.-Ing. Jurij Pelikan, Technical University Bratislava, Slovakia<br />
Dipl.-Ing. Lucia Perasinová, Technical University Bratislava, Slovakia<br />
Dr. Nizar Rammeh, University of Sfax, Tunisia<br />
Prof. Ismail Saadoune, University of Marakesh, Marocco<br />
Prof. Dr. Deleg Sangaa, Nat. University, Ulaan Bator, Mongolia<br />
Dr. Andre Skomorokhov, Institute for Physics, Obninsk, Russia<br />
Dr. Jang Jong Su, Academy of Sciences, Pyongyang,<br />
Peoples Republic of Korea<br />
- 37 -
Research Projects<br />
Functional Advanced <strong>Material</strong>s and Engineering. Hybrides and Ceramics (FAME Network<br />
of Excellence, 6 th Framework Programm EU, 2005-2008).<br />
Development of in situ characterization techniques for polycrystalline materials using highenergy<br />
synchrotron radiation (Virtual Institute, Impuls- <strong>und</strong> Vernetzungsfond of the<br />
Helmholtz-Society, 2004-2007).<br />
Design, realisation and operation of the new neutron structure powder diffractometer<br />
(SPODI at the FRM-II, TU München in Garching, BMBF, 1998-2007).<br />
Investigation of superionic conducting properties in the copper silver selenium system<br />
(BMBF, 2004-2007).<br />
Investigation on radiation induced modifications in NbTi superconducting materials<br />
(cooperation with GSI, Darmstadt, 2004-2007).<br />
Controlled deposition and structural investigations of metallic nanowires for field emission<br />
applications (cooperation with GSI, Darmstadt, 2004-2006).<br />
Synthesis and properties of new (oxid)nitrid-ceramics: spinell nitride and sialone (DFG,<br />
2003-2007).<br />
Structural phase transitions and physical properties of Zintl-phases with NaTl-type<br />
structure (B32) at ambient condition (DFG, 2003-2006).<br />
Magnetic phase diagram and correlations between structural and magnetic properties in<br />
Cu(MoxW1-x)O4 (DFG, 2003-2006).<br />
Preparation of new orthomolybdates of alkaline and 3d-transition metals and<br />
characterization of magnetic, ion conducting and catalytic properties (DFG, 2004-2007).<br />
Characterization of the three-phase bo<strong>und</strong>ary in differently synthesized membraneelectrode<br />
assemblies (DFG, 2004-2007).<br />
High pressure synthesis and magnetism of orthorhenates (DFG, 2005-2007).<br />
Electron and magnetization density in the transition metal oxide Co3V2O8 (DFG, 2005-<br />
2007).<br />
The electron structure of TiO2 and VO2: A Joined Electron-Density Study of two <strong>Material</strong>s<br />
in Position, Momentum and Phase Space (DFG, 2005-2007).<br />
Ionic Fluids (Humboldt cooperation with Prof. Dr. V. Balevicius, Vilnius University,<br />
Lithuania, 2003-2006).<br />
- 38 -
Ternary phase diagrams containing Zintl-phases of the NaTl-type structure (B32)<br />
(Scientific and technological cooperation (WTZ) with Prof. Dr. V. Pavlyuk, Ivan-Franko-<br />
University Lviv, Ukraina, 2004-2006).<br />
The magnetic interactions and magnetostructural correlations in R’xR1-xMn2Ge2,<br />
RMn2-xTxGe2 and R’xR1-xMn6Ge6 (R’, R = La, Ce, Pr, Nd, Nd, Cd, Tb, Dy, Gd, Ho, Er, Y<br />
and T = Fe, Cr, Co, Cu) intermetallic compo<strong>und</strong>s (Scientific and technological cooperation<br />
(WTZ) with Prof. Dr. A. Elmali, University of Ankara, Turkey, 2004-2006).<br />
DAAD exchange program with Slovakia (2006-2007).<br />
Structural investigations into the electric fatigue in PZT (DFG-SFB, 2003-2006)<br />
In-situ investigations of the degradation of intercalation batteries <strong>und</strong> their modelling (DFG-<br />
SFB, 2003-2006)<br />
Struktur <strong>und</strong> Wirkungsmechanismus der katalytisch aktiven Phasen (m) in V/W <strong>und</strong> Mo/W-<br />
Mischoxid-Katalysatoren bei der Partialoxidation von einfachen Aldehyden (Acrolein zu<br />
Acrylsäure)<br />
(DFG 2006-2008)<br />
Publications<br />
Atakol, O.; Boča, R.; Ercan, I.; Ercan, F.; Fuess, H.; Haase, W.; Herchel, R.; Magnetic<br />
properties of trinuclear Ni-M-Ni complexes, M = Mn, Co and Ni; Chem. Phys. Lett. 423,<br />
(2006) 192-196<br />
Benker, N.; Roth, C.; Mazurek, M.; Fuess, H.; Synthesis and characterization of ternary<br />
Pt/Ru/Mo catalysts for the anode of the PEM fuel cell; J. New Mat. Electrochem. Syst. 9,<br />
(2006) 121-126<br />
Buhrmester, C.; Miehe, G.; Ehrenberg, H., Fuess, H.; 1-chloro-2,2-dimethylpropane:<br />
Thermal analysis, powder diffraction and spectroscopic investigation of the solid phases;<br />
Cryst. Res. Techn., 41, (2006) 48-54<br />
Buhrmester, C.; Miehe, G.; Ehrenberg, H., Fuess, H., Thermal analysis, powder diffraction<br />
and spectroscopic investigation of the solid phases of 1-chloro-2,2-dimethylpropane, Cryst.<br />
Res. Technol. 41 (2006) 48-54.<br />
Cakir, O.; Dincer, I.; Elmali, A.; Elerman, Y.; Ehrenberg, H., Fuess, H., Magnetic phase<br />
transitions in the Gd1-xTmxMn6Sn6 compo<strong>und</strong>s, J. Alloys Compd. 416(2006) 31-34.<br />
Cao, L.; Scheiba, F.; Roth, C.; Schweiger, F.; Cremers, C.; Stimming, U.; Fuess, H., Chen,<br />
L.; Zhu, W.; Qui, X.; Novel nanocomposite Pt/RuO2 . xH2O/carbon nanotube catalysts for<br />
direct methanol fuel cells; Angew. Chem. Int. Ed. 45, (2006) 5315-5319<br />
Dincer, I. ;Elerman, Y.; Elmali, A.;Ehrenberg, H.; Fuess, H., Baehtz, C.; Magneto-structural<br />
correlations in Pr0.15Gd0.85Mn2Ge2; Sol. State Comm., 140, (2006) 245-247<br />
- 39 -
Dincer, I.; Elerman, Y.; Elmali, A; Ehrenberg, H.; Fuess, H.; Baehtz, C.; Magneto-structural<br />
correlations in Pr0.15Gd0.85Mn2Ge2, Solid State Communications 140(2006) 245-247.<br />
Dincer, I. ; Elmali, A.; Elerman, Y.; H Ehrenberg, H.; Fuess, H., G. André; Neutron<br />
diffraction study on PrMn2-xFexGe2 and general magnetic phase diagram for<br />
RMn2-xFexGe2 (R=La-Sm); J. All. Comp., 416, (2006) 22-30<br />
Ehrenberg, H., Laubach, S.; Schmidt, P. C.; McSweeney, R. ; Knapp, M.; Mishra, K. C.;<br />
Investigation of crystal structure and associated electronic structure ofSr6BP5O20,J.Solid<br />
State Chem. 179 (2006) 968-973.<br />
Ehrenberg, H., Muessig, E.; Bramnik, K. G.; Kampe, P.; Hansen, T.; Preparation and<br />
properties of sodium iron orthooxomolybdates, NaxFey (MoO4)z , Solid State Sciences 8<br />
(2006) 813-820.<br />
Ehrenberg, H.; Schwarz, B.; Weitzel, H.; Magneticphasediagrams of MnMoO4,J.Magn.<br />
Magn. Mater. 305 (2006) 57-62.<br />
Essehli, R.; El Bali, B.; Lachkar, M.; Svoboda, I.; Fuess, H.;<br />
Bis(ethylenediammonium)diaquabis[hydrogendiphosphato(3-)]nickelate(II):structure and<br />
vibrational spectroscoy; Acta Cryst E 62, (2006) m538-m541<br />
Giebeler, L.; Kampe, P.; Wirth, A.; Adams, A.H.; Kunert, J.; Fuess, H., Vogel, H.; Structural<br />
changes of vanadium-molybdenum-tungsten mixed oxide catalysts during the selective<br />
oxidation of acrolein to acrylic acid; J. Mol. Catal. A: Chemical 259, (2006) 309-318<br />
Gowda, B.T.; Kožišek, J.; Fuess, H.; Structural Studies on N-(2,4,6-Trimethylphenyl)methyl/chloro-acetamides,<br />
2,4,6-(CH3)3C6H2NH-CO-CH3-yXy (X= CH3 or Cl and y = 0, 1, 2);<br />
Z. Naturforsch. 61a, (2006) 588-594<br />
Gowda, B.T.; Paulus, H.; Kožišek, J.; Tokarcik, M.; Fuess, H.; Effect of substitution on the<br />
molecular geometry of N-(2/L3/4-substituted-phenyl)-2,2-dichloroacetamides, 2/3/4-<br />
XC6H4NHCO.CHCl2 (X-CH3 or Cl); Z. Naturforsch., 61a, (2006) 675-682<br />
Hartung, J.; Bergsträßer, U.; Greb, M.; Svoboda, I.; H. Fuess; cis-5-Bromo-2,2,6-trimethyltrans-6-phenyltetrahydropyran-3-carboxylic<br />
acid; Acta Cryst E 62, (2006) o1920-o1922<br />
Hartung, J.; Schwarz, M.; Paulus, E.F.; Svoboda, I.; Fuess, H.; 4-(4-Chlorophenyl)-3-(4phenylpent-4-enyloxy)-1,3,-thiazole-2(3H)-thione;<br />
Acta Cryst. C62, (2006) o386-o388<br />
Hartung, J.; Greb, M.; Svoboda, I.; Fuess, H.; (C)-(2,4-Di-tert-butyl-6-{[2S)-3,3-dimethyl-1oxido-2-butyl]iminomethyl}phenolato)ethanol-cis-dioxomolybdenum(VI)<br />
at 100K; Acta<br />
Cryst E 62, (2006) m275-m277<br />
Hartung, J.; Greb, M.; Svoboda, I.; Fuess, H.; Methyl 5-cis-bromo-2,2,6-trimethyl-6-transphenyltetrahydropyran-3-carboxylate;<br />
Acta Cryst, E62, (2006) o4975-o4976<br />
Hartung, J.; Greb, M.; Svoboda, I.; Fuess, H.; 5-cis-Bromo-2,2,6,6tetramethyltetrahydropyran-3-carboxylic<br />
acid; Acta Cryst E 62, (2006) o1918-o1919<br />
- 40 -
Hartung, J.; Kopf, T.; Svoboda, I.; Fuess, H.; Trimethylammonium bromide at 100K; Acta<br />
Cryst E62, (2006) o570-o572<br />
Hartung, J.; Svoboda, I.; Fuess, H.; 1-(1-Adamantyloxy)pyridin-2(1H)-one; Acta Cryst E62,<br />
(2006) o579-o581<br />
Hesse, S.; Zimmermann, J.; von Seggern, H.; Ehrenberg, H.; Fuess, H.; Fasel, C.; Riedel,<br />
R.; CsEuBr3: Crystal structure and its role in the photostimulation process of CsBr:Eu2+;<br />
J. Appl. Phys. 100 (2006) 083506.<br />
Ishihara, H. ; Horiuchi, K.;Svoboda, I.; Fuess, H.; Gesing, T.M.; Buhl, J.-Ch.; Terao, H.;<br />
Crystal Structures of Piperazinium Tetrahalogenometallates (II) [C4H12N2]MX4(M=Zn, Hg;<br />
X=Br,I); Z. Naturforsch. 61b, (2006) 69-72<br />
Ivanda, M.; Hohl, A.; Montagna, M.; Mariotto, G.; Ferrari, M.; Crnjak Orel, Z.; Turković, A.;<br />
Furić, K.; Raman scattering of acoustical modes of silicon nanoparticles embedded in<br />
silica matrix; J. Raman Spectrosc. 37, (2006) 161-165<br />
Ivaniková, R.; Boča, R.; Dlhán, L.; Fuess, H., Mašlejová, A.; Mrázová, V.; Svoboda, I.;<br />
Titiš, J.; Heteroleptic nickel(II) complexes formed from N-donor bases, carboxylic acids<br />
and water: Magnetostructural correlations; Polyhedron 25, (2006) 3261-3268<br />
Ivaniková, R.; Svoboda, I; Fuess, H.; Mašlejová, A.; Trans-dichloro(1,4,8,11tetraazacyclotetradecane)cobalt(III)<br />
chloride; Acta Cryst E62, (2006) m1553-m1554<br />
Ivaniková, R.; Svoboda, I.; Mašlejová, A.; Papánková, B.; Fuess, H.; Bis(2,2’-bipyridineκ<br />
2 N,N’)(nitrato- κ 2 O,O’)cobalt(II) iodide tetraydrate; Acta Cryst, E62, (2006) m3024-m3025<br />
Karim, S.; Toimil-Molares, M.E.; Maurer, F.; Miehe, G.; Ensinger, W.; Liu, J.; Cornelius,<br />
T.W.; Neumann, R.; Synthesis of gold nanowires with controlled crystallographic<br />
characteristics; Appl. Phys. A., 84, (2006) 403-407<br />
Maurer, F.; Dangwal, A.; Lysenkov, D.; Müller, G.; Toimil-Molares, M. E.; Trautmann, C.;<br />
Brötz, J.; Fuess, H.; Field emission of copper nanowires grown in polymer ion-track<br />
membranes; Nucl. Instr. Meth. Phys. Res. B245, (2006) 337-341<br />
Mazurek, M.; Benker, N.; Roth, C.; Buhrmester, T.; Fuess, H.; Electrochemical impedance<br />
and X-ray absorption spectroscopy (EXAFS) as in-situ methods to study the PEMFC<br />
Anode; Fuell Cells 06, (2006) 16-20<br />
Mazurek, M.; Benker, N.; Roth, C.; Fuess, H.; Binary Mixtures of Carbon Supported Pt and<br />
Ru Catalysts for PEM Fuel Cells; Fuel Cells 06, (2006) 208-213<br />
Meštric, H.; Eichel, R.-A.; Dinse, K.-P.; Ozarowski, A.; van Tol, J.; Brunel, L.C.; Kungl, H.;<br />
Hoffmann, M.J.; Schönau, K.A.; Knapp, M.; Fuess, H.; Iron-oxygen vacancy defect<br />
association in polycrystalline iron-modified PbZrO3 antiferroelectrics: Multifrequency<br />
electron paramagnetic resonance and Newman superposition model analysis; Phys. Rev.<br />
B 73, (2006) 184105<br />
Mašlejová, A.; Ivaniková, R.; Svoboda, I.; Papánková, B.; Dlhán, L.; Mikloš, D.; Fuess, H.,<br />
Boča, R.; Structural characterization and magnetic properties of<br />
- 41 -
hexakis(imidazole)nickel(II)bis(formate), bis(chloroacetate), bis(2-chloropropionate) and<br />
hexakis(1-methyl-imidazole)nickel(II)chloride dihydrate; Polyhedron 25, (2006) 1823-1830<br />
Mikhailik, V. B. ; Kraus, H.; Wahl, D.; Ehrenberg, H., Mykhaylyk, M. S.; Optical and<br />
luminescence studies of ZnMoO4 using vaccum ultraviolet synchrotron readiation,<br />
Nucl.Instrum. Meth. A 562 (2006) 513-516.<br />
Mikhailova, D.; Ehrenberg, H., Fuess, H., Synthesis, crystal structure and magnetic prop<br />
erties of new indium rhenium and scandium rhenium oxides, In6ReO12 and Sc6ReO12; J.<br />
Solid State Chem. 179 (2006) 3672-3680.<br />
Mikhailova, D.; Ehrenberg, H.; Fuess, H.; Synthesis and structure determination of copper<br />
perrhenate, CuReO4; Sol. State Chem. 179 (2006) 2004-2011<br />
Mikhailova, D.; Ehrenberg, H.; Fuess, H.; Synthesis, crystal structure and magnetic<br />
properties of new indium rhenium and scandium rhenium oxides, In6ReO12 and Sc6ReO12;<br />
Sol. State Chem. 179, (2006) 3667-3675<br />
Mikhailova, D.; Ehrenberg, H.; Fuess, H., Synthesis and structuredeterminationof copper<br />
perrhenate, CuReO4, J. Solid State Chem. 179 (2006) 2004-2011.<br />
Nikolowski, K. M.; Bramnik, N.; Baehtz, C.; Ehrenberg, H., Fuess, H.; In situ-XRD of Highly<br />
Charged and Discharged LixNi0.8Co0.2O2 (x close to 0); ECS Transactions, vol. 1, issue<br />
26, Rechargeable Lithium and Lithium-Ion Batteries (edt. J. Weidner) (2006) 17-26.<br />
Öksüzoglu, R. M.; Yalcin, N.; Aktas, B.; Fuess, H.; FMR study of ultrahigh vacuum e-beam<br />
evaporated Co23Cu77 nanogranular films: Magnetotransport properties; phys. stat. sol. (a)<br />
203, (2006) 1573-1579<br />
Papánkova, B.; Svoboda, I.; Fuess, H.; Bis(acetato-κO)diaquabis(1-methylimidazoleκN<br />
3 )cobalt(II); Acta Cryst, E62, (2006) m1916-m1918<br />
Qureshi, N.; Fuess, H.; Ehrenberg, H.; Hansen, T.C.; Ritter; C.; Prokes,K.; Podlesnyak, A.;<br />
Schwabe, D.; Magnetic properties of the Kagome mixed compo<strong>und</strong>s (CoxNi1-x)3V2O8,<br />
Phys. Rev. B 74 (2006) 212407.<br />
Rammeh, N.; Ehrenberg, H.; Fuess, H.; Cheikh-Rouhou, A.; Structure and magnetic<br />
properties of the double-perovskites Ba2(B,Re)2O6 (B=Fe, Mn, Co and Ni); phys. stat. sol.<br />
(c) 9, (2006) 3225-3228<br />
Roth, C.; Benker, N.; Mazurek, M.; Scheiba, F.; Fuess, H.; Pt-Ru fuel cell catalysts<br />
subjected to H2CO N2 and air atmosphere: an X-ray absorption study; Appl. Catalysis A,<br />
(2006)<br />
Toupance, T.; El Hamzaoui, H.; Jousseaume, B.; Riague, H.; Saadeddin, I; Campet, G.;<br />
Brötz, J.; Polystannoxane; B; A New Route toward Nanoporous Tin Dioxide; Chem. Mater.<br />
2006, 18, (2006) 6364-6372<br />
- 42 -
Trots, D.M.; Skomorokhov, A.N.; Knapp, M.; Fuess, H.; High-temperature behaviour of<br />
average structure and vibrational density of states in the ternary superionic compo<strong>und</strong><br />
AgCuSe; Eur. Phys. J.B. 51, (2006) 507-512<br />
Yonkeu, A.L.; Miehe, G.; Fuess, H., Goossens, A.M.; Martens, I.A.; A new overgrowth of<br />
mazzite on faujasite zeolite crystal. Investigated by X-ray diffraction and electronic<br />
microscopy; Microp. Mesop. Mater., 96, (2006) 396-404<br />
Umbreen, S.; Brockhaus, M.; Ehrenberg, H.; Schmidt, B.; Norstatines from aldehydes by<br />
sequential organocatalytic-amination and Passerini reaction, Eur.J.Org.Chem.(2006)<br />
4585-4595.<br />
Walha, I.; Cheikh-Rouhou, A.;Ehrenberg, H., Fuess, H.; Effect of calcium-deficiency upon<br />
physical properties of La0.6Ca0.4MnO3, phys. stat. sol. (c)3 (2006) 3260-3265.<br />
- 43 -
Chemical Analytics<br />
The chemical analytics division deals with all kinds of topics concerned with qualitative,<br />
semiquantitative and quantitative analytics of elemental composition and characterisation<br />
of chemical binding in solid and liquid samples.<br />
For solids, measurements with high spatial resolution are carried out by Electron Probe<br />
Micro Analysis (EPMA) and Secondary Ion Mass Spectrometry (SIMS). The latter is also<br />
used for thin film analysis with high depth resolution.<br />
Average compositions of solids are analyzed by X-ray Fluorescence Analysis (XRF),<br />
solutions of materials are measured by Atomic Absorption Spectrometry (AAS), ICP<br />
Optical Emission Spectrometry (ICP-OES) and Gas Chromatography, coupled with high<br />
resolution Mass Spectrometry (GC-MS).<br />
Present research topics are:<br />
Thin film speciation<br />
In thin film technology, the identification of chemical compo<strong>und</strong>s, phases and binding<br />
conditions is of basic importance. In a collaboration with Physikalisch-Technische<br />
B<strong>und</strong>esanstalt in Berlin and institutes in Novosibirsk/Russia, thin films of boron<br />
carbonitride and silicon carbonitride are prepared and characterized. The preparation<br />
techniques are plasma enhanced chemical vapour deposition and sputtering (physical<br />
vapour deposition). The chemical composition of the films is measured by SIMS. The<br />
atomic binding states are investigated by Near Edge X-ray Absorption Fine Structure<br />
(NEXAFS) measurements, partially in Total reflection and Glancing Incidence X-ray<br />
Fluorescence (TXRF, GIXRF) geometry, by X-ray Photoelectron Spectrometry (XPS –<br />
collaboration with Dr. A. Klein, Surface Science), and by Transmission Electron<br />
Microscopy with Electron Energy Loss Spectrometry (TEM-EELS). The TXRF-NEXAFS<br />
experiments are carried out at BESSY II.<br />
In another project, thin films (nanofilms) of carbides of boron, silicon, titanium, and<br />
tantalum are formed by hydrocarbon plasma immersion ion implantation, in collaboration<br />
with Industrial Technology Center of Nagasaki. The chemical film composition is analyzed<br />
by SIMS, the phase composition by X-ray diffraction. Film morphology and microstructure<br />
are investigated by scanning electron microscopy and by atomic force microscopy.<br />
- 44 -
Corrosion<br />
Phenomena of aqueous corrosion of metals, depending on their chemical composition,<br />
phase and structure, are investigated by electrochemical and trace analytical methods.<br />
The methods include potential-time and current-potential (polarization, cyclic voltammetry)<br />
measurements, Electrochemical Noise Analysis (ENA) and Electrochemical Impedance<br />
Spectroscopy (EIS). Immersion tests with chemical analysis of the dissolved material are<br />
carried out by e.g. Atomic Absorption Spectrometry and ICP Optical Emission<br />
Spectrometry. The materials investigated are the metals aluminium, magnesium, and iron,<br />
and alloys.<br />
A special topic is the corrosion of thin films, formed by plasma and ion beam methods,<br />
such as diamond-like amorphous carbon, or by sol-gel synthesis in combination with spin<br />
coating, such as zirconium oxide. These films (on the nanometer scale, i.e. nanofilms)<br />
suffer from microporosity which greatly influences the film/substrate corrosion<br />
performance. The <strong>und</strong>erlying corrosion mechanisms and the correlation between film<br />
deposition parameters and corrosion protection ability are investigated.<br />
Nanopores and nanowires<br />
In collaboration with Gesellschaft für Schwerionenforschung (GSI), membranes or<br />
microfilters are formed by irradiation of polymer foils (polycarbonate, polyimide) and<br />
chemical etching the latent ion tracks to pores. These ion track filters (ITNF: ion track<br />
nanofilters, when the pores have diameters < 100 nm) can be used for filtering liquids from<br />
particles, collecting aerosols, for gas separation, and for analyzing small molecules and<br />
molecular fragments by translocation.<br />
In a further process step, the nanopores are galvanically filled with metals, such as copper<br />
or gold, forming nanowires. The nanowires can be gained by dissolution of the polymer<br />
template. Dimensions, surface topography, microstructure, and crystallinity are<br />
investigated. Further, properties such as electrical conductivity and thermal stability are<br />
studied. The wires decay upon heating to a chain of spheres (Rayleigh instability). This<br />
effect is investigated.<br />
<strong>Material</strong>s in Radiation Fields<br />
In a number of applications, such as in nuclear facilities, particle accelerators and in<br />
space, materials are exposed to energetic ionizing radiation. The irradiation may lead to a<br />
degradation of the materials properties. Polymers are particularly sensitive towards<br />
ionizing radiation. In a collaboration with GSI, polyimide and polyepoxide, which are<br />
components of superconducting beam guiding magnets, were irradiated with relativistic<br />
heavy ions and characterized for their properties, such as network degradation and<br />
electrical conductivity. Another material is polycrystalline graphite, which is being used as<br />
the target wheel and as the beam dump.<br />
- 45 -
Collaborations<br />
The above mentioned and a number of further topics, e.g., from semiconductor research<br />
and from nuclear research, are investigated in collaboration with national institutes and<br />
with research centers and institutes abroad, such as<br />
� Physikalisch-Technische B<strong>und</strong>esanstalt, Berlin;<br />
� Gesellschaft für Schwerionenforschung, Darmstadt;<br />
� Deutsches Kunststoff-Institut, Darmstadt;<br />
� National Inst. of Advanced Industrial Science and Technology, Osaka, Japan;<br />
� Industrial Technology Center of Nagasaki, Japan<br />
� Rutherford Appleton Laboratory, Didcot, England<br />
� Centre Interdisciplinaire de Recherche Ions Lasers, Caen, France<br />
� Joint Institute for Nuclear Research, Dubna, Russia;<br />
� Institute of Inorganic Chemistry, Novosibirsk, Russia;<br />
� Institute for Water and Environmental Problems, Barnaul, Russia;<br />
� Institute of Earth Crust, Irkutsk, Russia;<br />
Staff Members<br />
Head Prof. Dr. Wolfgang Ensinger<br />
Research Associates Dr. Christiane Brockmann Dr. Stefan Flege<br />
Dr. Peter Hoffmann Dr. Gunther Kraft<br />
Dr. Falk Sittner<br />
Technical Personnel Brunhilde Thybusch Dorothea Berres<br />
Renate Benz<br />
Secretary Antje Pappenhagen<br />
PhD Students Mubarak Ali Olaf Baake<br />
Thomas Herrmann Shafqat Karim<br />
Jens von Ringleben Daniel Severin<br />
Ruperto Ugas Tim Vogel<br />
Mehdi Yekehtaz<br />
Diploma Students Tim Seidl Christoph Ochs<br />
Research Projects<br />
Chemical and physical characterization of nanofilm systems (nanofilm speciation) (jointly<br />
with PTB, Berlin; DFG 2005-2007)<br />
Deposition and implantation of carbon from hydrocarbons by plasma immersion ion<br />
implantation (DFG, 2005-2007)<br />
- 46 -
Internal target experiments with highly energetic stored and cooled secondary beams at<br />
the International Acceleration Facility, Darmstadt Ion Research and Antiproton Center (EU,<br />
2005-2007)<br />
Radiation resistance of insulating materials in superconducting magnets (GSI, 2004-2007)<br />
Fabrication and characterization of gold nanowires (GSI, 2004-2007)<br />
Contamination of dacha areas near of industrial complexes in Siberia (NATO, 2004-2006)<br />
Separation of lithium and caesium isotopes from the primary coolant system of a<br />
pressurized water reactor (EnBW AG Kernkraftwerk Philippsburg, 2005-2007)<br />
Publications<br />
Baake, O.; Öksüzoglu, R.M.; Flege, S.; Hoffmann, P.S.; Gottschalk, S.; Fuess, H.; Ortner,<br />
H.M.; Determination of thickness, density and roughness of Co–Ni–Al single and multiple<br />
layer films deposited by high-vacuum e-beam evaporation on different substrates,<br />
<strong>Material</strong>s Characterization 57, 12 ( 2006 )<br />
Brandt, R.; Ditlov, V.A.; Dwiwedi, K.K.; Ensinger, W.; Ganssauge, E.; Guo, S.-L.;<br />
Haiduc, M.; Hashemi-Nezhad, S.R.; Khan, H.A.; Krivopustov, M.I.; Odoj, R.;<br />
Pozharova, E.A.; Smirnitzki, V.A.; Sosnin, A.N.; Westmeier, W.; Zamani-Valasiadou, M.;<br />
Interactions of relativstic heavy ions in thick heavy element targets and some unresolved<br />
problems, E1-2005-167, Joint Institute for Nuclear Research, Dubna, (2006), 1<br />
Cornelius, T. W.; Toimil-Molares, M. E.; Neumann, R.; Karim, S.; Finite-size effects in the<br />
electrical transport properties of single bismuth nanowires, Journal of Applied Physics 100<br />
(11) (2006 ) 114307<br />
Cornelius, T.W.; Toimil-Molares, M.E.; Neumann, R.; Fahsold, G.; Lovrincic, R.; Pucci, A.;<br />
Karim, S.; Quantum size effects manifest in infrared spectra of single bismuth nanowires,<br />
Applied Physics Letters 88 (10) (2006) 103114<br />
Ensinger, W. Corrosion and wear resistant coatings formed by ion beam techniques,<br />
Chapter 18 in: Y. Peauleau (Ed.) <strong>Material</strong>s Surface Processing by Directed Energy<br />
Techniques, Elsevier Science Publishing Company (2006)<br />
Ensinger, W.; Formation of Diamond-Like Carbon Films by Plasma-Based Ion Implantation<br />
and Their Characterization, Diamond and Frontier Carbon Technology 16 (2006) 1<br />
F. Neubrech, T. Kolb, R. Lovrincic, G. Fahsold, A. Pucci, J. Aizpurua, T. W. Cornelius, M.<br />
E. Toimil-Molares, R. Neumann, S. Karim, Resonances of individual metal nanowires in<br />
the infrared, Applied Physics Letters 89 (25) (2006 ) 253104<br />
Hanefeld, P.; Sittner, F.; Ensinger, W.; Greiner, A.; Investigation of the ion permeability of<br />
poly(p-xylylene) films, e-Polymers 26 (2006) 1<br />
Höchbauer, T.; Misra, A.; Nastasi, M.; Mayer, J.W.; Ensinger, W.; Formation of hydrogen<br />
complexes in proton implanted silicon and their influence on the crystal damage, Nucl.<br />
Instr. Meth. Phys. Res. B242 (2006) 623<br />
- 47 -
Hoffmann, P.; Non-Invasive Identification of Chemical Compo<strong>und</strong>s by EDXRS, in: Practical<br />
X-Ray Fluorescence Analysis (Eds.: B. Beckhoff, B. Kanngießer, N. Langhoff, R. Wedell,<br />
H. Wolff) Springer, Berlin – Heidelberg (2006) 769<br />
Karim, S.; Toimil Molares, M.E.; Maurer, F.; Miehe, G.; Ensinger, W.; Liu, J.;<br />
Cornelius, T.W.; Neumann, R.; Synthesis of gold nanowires with controlled<br />
crystallographic characteristics, Appl. Phys. A 84 (2006) 403<br />
Karim, S.; Toimil-Molares, M. E.; Balogh, A.G.; Ensinger, W.; Cornelius, T.W.; Khan, E.U.;<br />
Neumann, R.; Morphological evolution of Au nanowires controlled by Rayleigh instability,<br />
Nanotechnology 17 (2006) 5954<br />
Kraft, G.; Flege, S.; Reiff, F.; Ortner, H.M.; Ensinger, W.; Analysis of the notches of ancient<br />
serrated denars, Archaeometry 48, 4 (2006) 605<br />
Kraft, G.; Flege, S.; Reiff, F.; Ortner, H.M.; Ensinger, W.; Electron-probe microanalysis<br />
investigations of Roman coin silvering techniques, Microchimica Acta 155 (2006) 179<br />
Liu, J.; Duan, J.L. ; Toimil-Molares, M. E.; Karim, S.; Cornelius, T.W.; Dobrev, D.;<br />
Yao, H. J.; Sun, Y. M.; Hou, M. D.; Mo, D.; Wang, Z. G.; Neumann, R.; Electrochemical<br />
fabrication of single-crystalline and polycrystalline Au nanowires: the influence of<br />
deposition parameters, Nanotechnology 17 (8) (2006) 1922<br />
Ortner, H.M.; Kraft, G.;Topochemische Untersuchungen antiker versilberter Münzen, GIT<br />
Labor-Fachzeitschrift 05/2006, 436<br />
Zimmermann, T.; Ensinger, W.; Schmidt, T.C.; Depletion solid-phase microextraction for<br />
the evaluation of fiber-samples partition coefficients of pesticides, J. Chromatography A<br />
1102 (2006) 51<br />
- 48 -
Theoretical <strong>Material</strong>s Science<br />
Teaching by this division addresses the atomistic fo<strong>und</strong>ations of materials science,<br />
including the concepts <strong>und</strong>erlying their representation, from the theoretical physics point of<br />
view. Research focuses on materials modelling, being a powerful tool for materials<br />
development. Experimental results will be <strong>und</strong>erstood, and predictions of further<br />
observations given, in the light of theoretical evidence, both to aid the optimization of the<br />
properties or the performance of materials already in use and to guide the design of novel<br />
materials with properties, or behaviour, required in future engineering applications.<br />
Current investigations centre on the following classes of materials:<br />
Transition metals and related alloys<br />
For this class of materials, represented by Ta and Fe or, respectively, steels, the goal is<br />
examining their suitability for structural components of high-power spallation neutron<br />
sources that are exposed to intense proton beams. Irradiation-induced hydrogen<br />
production <strong>und</strong>er the operating conditions of the envisaged European spallation source is<br />
predicted to generate high internal concentrations of atomic hydrogen which, further<br />
enhanced by stress-driven hydrogen accumulation near microstructural cracks, may lead<br />
to a severe degradation of the mechanical properties of steel, whereas no noticeable<br />
deterioration is to be expected in the case of tantalum.<br />
High-temperature superconductors<br />
For this class of materials, typified by YBa2Cu3O7 and Bi2Sr2Ca2Cu3O10 in thin-film or bulk<br />
form, great interest is directed towards investigating extended defects (e.g. low-angle grain<br />
and twin bo<strong>und</strong>aries) which are considered as weak-links between superconducting grains.<br />
There are two principal aims: (i) exploring the connection between the electromagnetic<br />
response (e.g. the current-voltage relation) and the characteristic defect morphology so as<br />
to obtain insight into constitutive parameters of superconducting films; (ii) searching for<br />
possibilities to improve the current-carrying capability of superconducting materials, which<br />
is limited by the above-mentioned types of defect. Preliminary studies of novel<br />
heterostructures involving superconductor strips with a single grain bo<strong>und</strong>ary defect,<br />
placed in open magnetic cavities, show that magnetic shielding here is a promising way<br />
forward. Another field of research addresses the interaction between electromagnetic<br />
radiation and multilayered heterostructures made up of superconductors as well as a range<br />
of different classes of materials with a view to examining their suitability for novel photonic<br />
crystals. Of special interest are materials whose properties can be controlled by external<br />
parameters and fields.<br />
Organic semiconductors<br />
For this class of materials, represented by Alq3, emphasis is placed on real-time modelling<br />
of the charge transfer by injected carriers and on a theoretical analysis of thermally<br />
stimulated luminescence phenomena with the aim of extracting, in conjunction with<br />
experiments, information about the electronic structure of inherent traps so as to assist<br />
technological exploitation and further materials development. Some of the most important<br />
features to be taken into account hereby are the field-dependence of the mobilities of the<br />
charge carriers addressed as well as the field- and temperature dependences of the<br />
injection barriers present, apart from allowing for the variation of the distribution of traps in<br />
space and depth.<br />
- 49 -
Ferroelectrics<br />
For this class of materials, typified by BaTiO3 , attention is focussed on the process of<br />
ageing, i.e. the gradual change of materials properties with time, isothermal conditions and<br />
absence of external mechanical loads implied. This process manifests itself in alterations<br />
of static and, respectively, kinetic characteristics such as the clamping pressure exerted on<br />
the walls of ferroelectric domains and the asymmetry of the electrical conductivity<br />
regarding current flow parallel or antiparallel to the direction of the spontaneous<br />
polarization; phenomena, which may be explained in terms of migration of charged point<br />
defects <strong>und</strong>er the influence of internal or external electric fields. Preliminary results<br />
obtained with a drift-diffusion approach suggest that the experimentally observed drastic<br />
rise of the clamping pressure with time is indeed controlled by a mechanism of this kind.<br />
The theories <strong>und</strong>erlying these investigations range from microscopic to macroscopic; their<br />
realizations employ analytical as well as computational techniques.<br />
Staff Members<br />
Head H.E. The Hon. Prof. Dr. Dr.habil. Hermann Rauh,<br />
M.A., C.Phys., F.Inst.P., F.I.M., O.I.A.<br />
Research Associates Dr. Yuri A. Genenko, D.Sc.<br />
Dr. Sergey V. Yampolskii<br />
Postgraduate Dipl.-Phys. Frederik Neumann<br />
Secretary N.N.<br />
Visiting Scientists Dr. Alexei V. Golovchan<br />
Prof. Dr. Igor L. Lyubchanskii<br />
Dr. Galina I. Yampolskaya<br />
Research Projects<br />
Electrodynamics of Macroscopic Magnet/Superconductor Heterosystems (German<br />
Research Fo<strong>und</strong>ation (DFG), 2003-2006)<br />
Kinetic Modelling of the Charge Transfer in Organic Semiconductors and Ionic Conductors<br />
(Collaborative Research Centre (SFB) ”Electric Fatigue in Functional <strong>Material</strong>s”, 2003-<br />
2006, with Prof. Dr. H. v. Seggern, Darmstadt University of Technology)<br />
Publications<br />
Genenko, Y.A.; Rauh, H.; Novel superconductor/magnet resonant configurations:<br />
Exact analytic representations of the Meissner state and the critical state, J. Phys.: Conf.<br />
Ser. 43 (2006) 568.<br />
- 50 -
Lupascu, D.C.; Genenko, Y.A.; Balke, N.; Aging in ferroelectrics, J. Amer. Ceramic Soc. 89<br />
(2006) 224.<br />
Neumann, F.; Genenko, Y.A.; v. Seggern, H.; The Einstein relation in systems with trapcontrolled<br />
transport, J. Appl. Phys. 99 (2006) 013704.<br />
Neumann, F.; Genenko, Y.A.; Melzer, C.; v. Seggern, H.; Self-consistent theory of unipolar<br />
charge-carrier injection in metal/insulator/metal systems, J. Appl. Phys. 100 (2006) 084511.<br />
Nikolaenko, Y.M.; Medvedev, Y.V.; Genenko, Y.A.; Ghafari, M.; Hahn, H.; Interface thermal<br />
resistance of a nanostructured FeCoCu film and a Si substrate, phys. stat. sol. (c) 3 (2006)<br />
1343.<br />
Yampolskii, S.V.; Genenko, Y.A.; Rauh, H.; Snezhko, A.V.; The Bean model of the critical<br />
state in a magnetically shielded superconductor filament, J. Phys.: Conf. Ser. 43 (2006)<br />
576.<br />
Yampolskii, S.V.; Yampolskaya, G.I.; Rauh, H.; Magnetic dipole-vortex interaction in a<br />
bilayered superconductor/soft-magnet heterostructure, Europhys. Lett. 74 (2006) 334.<br />
- 51 -
<strong>Material</strong>s Modelling<br />
The research activities of the <strong>Material</strong>s Modelling Division are directed towards the<br />
investigation of materials properties and processing by atomic scale computer simulations.<br />
<strong>Material</strong>s of interest include functional nanoparticles, ferroelectrics, transparent and<br />
organic semiconductors as well as nanostructured metals. We are combining a variety of<br />
methods depending on time and length scales involved in the corresponding problem.<br />
Quantum mechanical calculations based on density functional theory are used for<br />
electronic structure calculations. Large-scale molecular dynamics with analytical<br />
interatomic potentials are the method of choice for studying kinetic processes and plastic<br />
deformation. Kinetic lattice Monte-Carlo simulations are extensively used for simulations of<br />
diffusional and transport processes on long time scales. The group is operating two<br />
parallel PC-clusters and has access to the Hessian High Performance Computers in<br />
Frankfurt and Darmstadt.<br />
The current research areas are:<br />
• Structure and mobility of point defects in transparent conducting oxides and<br />
ferroelectrics<br />
• Thermodynamic and kinetic properties of functional nanoparticles<br />
• Charge carrier transport in organic light-emitting devices<br />
• Mechanical properties of nanocrystalline materials<br />
• Development of reactive interatomic potentials for compo<strong>und</strong> systems<br />
Besides the mandatory teaching of an <strong>und</strong>ergraduate course the <strong>Material</strong>s Modelling<br />
Division is currently offering a 2-semester course on atomic scale methods for materials<br />
simulations and is contributing to the practical course. In 2006 Paul Erhart graduated as<br />
first PhD-student of the <strong>Material</strong>s Modelling division. He was awarded with the Graduate<br />
Student Award Gold Medal at the MRS 2006 Fall Meeting in Boston and now has joined<br />
Lawrence Livermore Lab as a postdoctoral fellow.<br />
Staff Members<br />
Head<br />
Dr. Karsten Albe, Assistant Professor<br />
PhD Students Dipl.-.Ing. Michael Müller<br />
Dipl.-.Ing. Paul Erhart<br />
Diploma Students Johan Pohl<br />
Peter Agoston<br />
Technical Personnel Andreas Hönl (Trainee) Dennis Ratley (apprentice)<br />
Kathleen Feustel (apprentice)<br />
Secretary<br />
Renate Hernichel<br />
- 52 -
Guest Scientist<br />
Research Projects<br />
Prof. Kai Nordl<strong>und</strong>, PhD; University of Helsinki, Finland<br />
Niklas Juslin, MSc; University of Helsinki, Finland<br />
Tommi Järvi, MSc; University of Helsinki, Finland<br />
Petra Träskelin, MSc; University of Helsinki, Finland<br />
Eero Kesälä; University of Helsinki, Finland<br />
Atomistic computer simulations of defects and their mobility in metal-oxides (DFG-SFB<br />
595, Project C2, 2003-2006 )<br />
Atomistic modelling of metal oxide and -carbide nanoscale systems (DAAD, PPP Finland,<br />
2003-2006)<br />
Polymeric nitrogen (DFG, Al 578-3, 2005-2007)<br />
Plasticity of nanocrystalline metals and alloys, (DFG FOR 714, 2006 – 2009)<br />
Metallic nanoglasses (DFG Al 578-6, 2006 – 2007)<br />
Publications<br />
Zhao, S.J.; Albe, K.; Hahn, H.; Grain size dependence of the bulk modulus of<br />
nanocrystalline nickel, Scripta Mat. 55 (2006) 473-476)<br />
Erhart, P.; Juslin, N.; Goy, K.; Nordl<strong>und</strong>, R.; Müller, M.; Albe, K.; Analytic bond-order<br />
potential for atomistic simulations of zinc oxide, J. Phys. Cond. Matter 18 (2006) 8565-<br />
6605<br />
Erhart, P.; Albe, K.; Diffusion of zinc vacancies and interstitials in zinc oxide, Appl. Phys.<br />
Lett. 88 (2006) 201918<br />
Erhart, P.; Albe, K.; Klein, A.: First-principles study of intrinsic point defects in Zn0: Role of<br />
band structure, volume relaxation and finite size effects, Phys. Rev. B 73 (2006) 205203<br />
Erhart, P.; Albe, K.; First-principles study of migration mechanisms and diffusion of oxygen<br />
in zinc oxide, Phys.Rev.B 73 (2006) 115207<br />
Jin, Z.-H.; Gumbsch, P.; Ma, E.; Albe, K.; Lu, K.; Hahn, H.; Gleiter, The interaction<br />
mechanism of screw dislocations with coherent twin bo<strong>und</strong>aries in different face-centred<br />
cubic metals, Scripta Mat., 54 (6) (2006) 1163-1168<br />
- 53 -
<strong>Material</strong>s for Renewable Energies<br />
In December 2004, the new group Renewable Energies formed at the Institute for<br />
<strong>Material</strong>s Science. At present, research focuses on low-temperature fuel cells and related<br />
electrocatalysis using advanced ex-situ, and in particular, operando techniques for the<br />
detailed structural and electrochemical characterization of nanoscale catalysts.<br />
Techniques applied on the structural side include X-ray diffraction (XRD), X-ray absorption<br />
spectroscopy (XAS), and transmission electron microscopy (TEM), whereas<br />
electrocatalytic activities are measured using cyclic voltammetry (CV), electrochemical<br />
impedance spectroscopy (EIS), and single cell fuel cell tests.<br />
Recent projects concern the systematic investigation of the membrane-electrode assembly<br />
in polymer electrolyte fuel cells (PEMFC) before and after use, and its optimization<br />
according to the requirements for efficient operation. In this project, a new methodology for<br />
TEM characterization has been developed, which provides fascinating insights into the<br />
MEA structure. In another approach, a special in-situ fuel cell has been developed and<br />
successfully applied at beamlines X1, Hasylab, Hamburg, and at BM29 and ID24 at ESRF,<br />
Grenoble. First time-resolved operando experiments have been performed shedding light<br />
on f<strong>und</strong>amental mechanisms taking place during real fuel cell operation.<br />
The group has established various national and international cooperations in the fuel cell<br />
community. In a joint project with Tsinghua University, Beijing, and TUM, Munich, the<br />
application of carbon nanotube materials in PEMFC and its effect on the three-phase<br />
bo<strong>und</strong>ary is investigated. In cooperation with David Ramaker and his group at George<br />
Washington University, a novel data analysis technique has been developed, which<br />
allowes us to monitor changes in catalyst structure and adsorbate coverage during real<br />
cell operation. Collaborative agreements exist between the group and several companies,<br />
large scale facilities as well as national and international universities. These are largely<br />
covered by f<strong>und</strong>s from the German Science fo<strong>und</strong>ation (DFG) and the BMBF.<br />
Teaching activities in 2006 included the regular curricula lecture “Methods in <strong>Material</strong>s<br />
Science” and the linked practical course. The group`s research interests are covered by a<br />
lecture on “Fuel Cells – from f<strong>und</strong>amentals to application” and a practical course “X-ray<br />
absorption spectroscopy – f<strong>und</strong>amentals and data analysis” (joint workshop with Prof.<br />
David Ramaker). Furthermore, a workshop on “Scientific work and presentation skills”<br />
(with Dr. I. Kinski) is offered on request.<br />
Staff Members<br />
Head<br />
Secretary<br />
Dr. Christina Roth<br />
Maria Holzmann (joint with Prof. Fuess)<br />
PHD students Dipl.-Ing. Virginie Croze<br />
Dipl.-Ing. Susanne Zils<br />
Students Guillaume Savoye<br />
Guest Scientists<br />
Dipl.-Ing. Frieder Scheiba<br />
(joint with Prof. Fuess)<br />
Dipl.-Ing. Julia Melke (extern, ISE)<br />
Dipl.-Ing. Marcelo da Carmo, IPEN, Sao Paulo (with Prof. Fuess)<br />
- 54 -
Research Projects<br />
Characterization of the three-phase bo<strong>und</strong>ary in differently-synthesized membraneelectrode<br />
assemblies (DFG Sino-German project 2004-2006)<br />
In-situ X-ray diffraction and X-ray absorption spectroscopy for investigation of the cathode<br />
catalyst in a working fuel cell (DFG project 2005-2008)<br />
Structural investigation of membrane-electrode assemblies in fuel cells using ESEM (DFG<br />
project 2006-2009)<br />
Chemical and morphological characterization of nanostructured electrocatalyst systems<br />
supported on modified carbon black and produced by different methods (DAAD-CAPES<br />
Brazil 2006-2007)<br />
Publications<br />
Mazurek, M.; Benker, N.; Roth, C., Buhrmester, Th.; Fuess, H.; Electrochemical<br />
impedance and X-ray absorption spectroscopy (EXAFS) as in-situ methods to study the<br />
PEMFC anode, Fuel Cells 6 (1) (2006) 16-20.<br />
Benker, N.; Roth, C.; Mazurek, M.; Fuess, H.; Synthesis and characterisation of ternary<br />
Pt/Ru/Mo catalysts for the anode of the PEM fuel cell, J. New Mat. Electrochem. Sys. 9<br />
(2006) 121-126.<br />
Mazurek, M.; Benker, N.; Roth, C.; Fuess, H.; Structural and electrochemical investigation<br />
of binary mixtures of carbon-supported Pt and Ru catalysts for PEM fuel cells, Fuel Cells 6<br />
(2006) 208-213.<br />
Scheiba, F.; Scholz, M.; Lin, C.; Roth, C.; Cremers, C.; Qiu, X.; Stimming, U.; Fuess, H.;<br />
On the suitability of hydrous ruthenium oxide supports to enhance intrinisic proton<br />
conductivity in direct methanol anodes, Fuel Cells 6 (2006) 439-446.<br />
Cao, L.; Scheiba, F.; Roth, C.; Schweiger, F.; Cremers, C.; Stimming, U.; Fuess, H.; Chen,<br />
L.; Zhu, W.; Qiu, X.; Novel nano-composite Pt/RuO2·xH2O/CNT catalysts for DMFC,<br />
Angew. Chem. Int. Ed. 45 (2006) 5315-5319.<br />
Roth, C.; Mazurek, M.; Benker, N.; Katalysatoren im Baukastensystem, Thema Forschung<br />
2/2006, 58-63.<br />
- 55 -
Joint Research Laboratory<br />
Nanomaterials<br />
The Joint Research Laboratory Nanomaterials was established in 2004 to enhance the<br />
cooperation between the Institute for Nanotechnology at the Forschungszentrum Karlsruhe<br />
and the Institute of <strong>Material</strong>s Science at the Technische Universität Darmstadt. The startup<br />
to establish the laboratory was provided by both institutions. Scientific personell is<br />
financed by the Forschunszentrum Karlsruhe and by external grants of f<strong>und</strong>ing agencies in<br />
Germany and of the EU as well as by industrial cooperations. The laboratory interacts in<br />
several areas with research groups in <strong>Material</strong>s Science and Chemistry. The research<br />
activities are concentrated in the area of nanoparticulate systems, their synthesis and<br />
processing, microstructural characterization and their properties. The focus is currently on<br />
developing nanoporous structures as bulk materials and thin films on a variety of<br />
substrates for developing catalyst support materials and catalysts, gas sensors and<br />
templates for the growth of light-harvesting molecular structures (porphyrines) and the<br />
development of alternative solar cells for low light conditions. An additional engineering<br />
focus of the research is on the stability of nanostructured materials <strong>und</strong>er operation<br />
conditions, such as high temperatures and gas environments, as well as the study of<br />
mechanical performance of nanoporous structures. The nanomaterials are prepared using<br />
Chemical Vapor Synthesis and Nebulized Spray Pyrolysis starting from metal-organic<br />
precursors and metal salts. Using these methods a wide range of nanostructures can be<br />
synthesized. In addition to several synthesis systems, characterization equipment is<br />
available including X-ray diffraction, nitrogen adsorption, light scattering and Zeta potential<br />
and gas chromatography.<br />
Staff Members<br />
Head<br />
Research Associates Dr. Hermann Sieger<br />
Secretary<br />
Prof. Dr.-Ing. Horst Hahn (Director Institute for Nanotechnology)<br />
Renate Hernichel<br />
PhD Students Dipl.-Ing. Thorsten Enz<br />
Dipl.-Ing. Sebastian Gottschalk<br />
Dipl.-Ing. Peter Marek<br />
Dipl.-Ing. Simon Bubel<br />
Diploma Students Johannes Kostka<br />
Guest Scientists<br />
Jens Suffner<br />
Prof. Ali Beitollahi<br />
Dr. V. Mahender<br />
Dr. M. Karajai<br />
- 56 -<br />
Dr. Jens Ellrich<br />
Dr. Holger Schmitt<br />
Dipl.-Ing. Jens Suffner<br />
Dipl.-Ing. Azad Jaberidarbandi<br />
Dipl. Phys. Anna Castrup<br />
Ravi Mohan Prasad
Research Projects<br />
Defect structure and diffusion in ferroelectric materials (SFB 595 2003 – 2006)<br />
Processing of Nanostructured <strong>Material</strong>s through Metastable Transformations Namamet<br />
(EU 2004 – 2009)<br />
DIRAC secondary-Beams (EU/GSI 2005 – 2008)<br />
Plastizität in Nanokristallinen Metallen <strong>und</strong> Legierungen, Teilprojekt 5, Aufklärung von<br />
Verformungsmechanismen mittels Synchrotron-Röntgenstrahlung (DFG 2006 – 2009)<br />
Metallische Nanogläser (DFG 2006 – 2008)<br />
Publications<br />
Enz, T.; Winterer, M.; Stahl, B.; Bhatacharya, S.; Miehe, G.; Foster, K.; Fasel, C.; Hahn,<br />
H.; Structure and magnetic properties of iron nanoparticles stabilized in carbon, Journal of<br />
Applied Physics, 99 (4) (2006) 044306<br />
Sieger, H.; Suffner, J.; Raju, A.R.; Miehe, G.; Hahn, H.; Thermal Stability of<br />
Nanocrystalline Sm2 O3 and Sm2 O3 –MgO, Journal Amer. Ceram. Soc. 89 (2006) 979-984<br />
Marek, P.; Balaban, S.; Nachrichten aus der Chemie, 54, (2006) 1072-1077<br />
Jin, Z. H.; Gumbsch, E.; Albe, K.; Hahn, H.; Gleiter, H.; The Interaction mechanism of<br />
screw dislocations with coherent twin bo<strong>und</strong>aries in different face-centred cubic metals,<br />
Scripta <strong>Material</strong>ia, 54 ( 2006) 1163-1168<br />
Kruk, R.; Ghafari, M.; Hahn, H.; Birringer, R.; Michels, D.; Kmiec, R.; Marszalek, M., Grainsize-dependent<br />
magnetic properties of nanocrystalline Gd., Physical Review B, 2006, 73<br />
(2006) 054420<br />
Schmitt, H.; Ghafari, M; Kruk, R.; Schmitt, L.A.; Ellrich, J.; Hütten, A.; Hahn, H.; Interfacial<br />
microstructure of Fe/AlOx/Fe-magnetic tunnel junctions in high resolution, Applied Physics<br />
Letters 88 (2006) 122505<br />
Akurati, K.K.; Bhattacharya S.S.; Winterer, M.; Hahn, H.: Synthesis, characterization and<br />
sintering of nanocrystalline titania powders produced by chemical vapour synthesis, J.<br />
Phys. 39 (2006) 2248-2254<br />
Yin, S.; Xu, M.X.; Yang, L.; Liu, F.J.; Rösner, H.; Hahn, H.; Gleiter, H.;Schild, D.; Doyle,S.;<br />
Liu, T.; Hu T.D.; Takayama-Muromachi, E.; Jiang J.Z.; Absence of ferromagnetism in bulk<br />
polycrystalline Zn0.9Coo.1O. Phys.Rev. B73 (2006) 224408<br />
Zhao, Shi-Jin.; Albe, K.; Hahn, H.; Grain size dependence of the bulk modulus of<br />
nanocrystalline nickel, Scripta <strong>Material</strong>ia 55 (2006) 473-476<br />
Brehm, J.; Winterer, M.; Hahn, H.; Synthesis and Structure of Nanocrystalline Transparent<br />
Conducting Zinc Oxides, J. Appl. Phys. 100 (2006) 064311<br />
Bansal, C.; Sarkar, A.K.; Mishra, A:K.; Abraham, T.; Lemier, Ch.; Hahn, H.; <strong>Electronic</strong>ally<br />
tunable conductivity of a nanoporous Au-Fe alloy, Scripta <strong>Material</strong>ia 56 (2006) 705-708<br />
Padmanabhan, K.A.; Dinda, G.P.; Hahn, H.; Gleiter, H.; Inverse Hall-Petch effect and grain<br />
bo<strong>und</strong>ary sliding controlled flow in nanocrystalline materials, Accepted in <strong>Material</strong>s<br />
Science and Engineering A (2006)<br />
- 57 -
Collaborative Research Center (SFB)<br />
„Electric Fatigue in Functional <strong>Material</strong>s“<br />
Phase II: Jan. 2007 – Dec. 2010<br />
www.sfb595.tu-darmstadt.de<br />
The center for collaborative studies (Sonderforschungsbereich) has been awarded by the<br />
Deutsche Forschungsgemeinschaft in 2002 to TU Darmstadt and is centered in the<br />
Department of <strong>Material</strong>s and Earth Sciences with important contributions from the<br />
Department of Chemistry and the Departments of Civil Engineering, Mechanical<br />
Engineering as well as the Mechanical Engineering Department of the University of<br />
Karlsruhe. The center was renewed in 2006 and has recently started its second four-year<br />
f<strong>und</strong>ing period.<br />
It is comprised of a total of 19 projects and financial resources for four years of about 8<br />
Mio. €. The center has an active guest program with guests visiting from 2 days to 3<br />
months. For specific information, please contact either the secretary of the center, Mrs.<br />
Gila Voelzke, or the director of the center, Prof. Jürgen Rödel.<br />
Contact:<br />
Office: SFB 595: Electrical Fatigue in Functional <strong>Material</strong>s,<br />
Institute of <strong>Material</strong>s Science<br />
Petersenstr. 23<br />
64287 Darmstadt<br />
Tel.: +49-6151-16-6362, 6315<br />
Fax: +49-6151-16-6363, 6314<br />
Building/Room: L201 / 55<br />
E-mail: roedel@ceramics.tu-darmstadt.de<br />
Voelzke@ceramics.tu-darmstadt.de<br />
Electrical fatigue in functional materials encompasses a set of phenomena, which lead to<br />
the degradation of materials with an increasing number of electrical cycles. Electrical<br />
cycling leads to both reversible and irreversible currents and polarisations. Ionic and<br />
electronic charge carriers interact with each other and with microstructural elements in the<br />
bulk as well as at interfaces (grain bo<strong>und</strong>aries and domain walls) and interphases<br />
(electrode/electrolyte). This in turn causes local changes in the distribution of electric<br />
currents and electric potentials. As a consequence local overloads and material<br />
degradation ensues and leads to irreversible loss of material properties. This material<br />
degradation can lead finally to mechanical damage as well as to dissociation reactions.<br />
The basic phenomena of electrical fatigue are not yet <strong>und</strong>erstood on a microscopic level.<br />
The goal of this center of excellence in the second phase is the <strong>und</strong>erstanding of the<br />
mechanisms leading to electrical fatigue. An <strong>und</strong>erstanding of the experimental results is<br />
supported by concurrent materials modelling which is geared to encompass different time<br />
and length scales from the material to the component.<br />
A key feature of the center is therefore the steady comparison between theory and<br />
experiment. This is utilized to find the physico-chemical origins of electrical fatigue as well<br />
as to develop strategies for new materials and improved material combinations. The<br />
- 58 -
materials of interest are ferroelectrics, electrical conductors (cathode materials for lithium<br />
batteries and transparent conducting oxides) and semiconducting polymers.<br />
Projects:<br />
Division A: Synthesis<br />
A1<br />
P.I. : Prof. J. Rödel<br />
Topic: Manufacturing of textured ceramics actuators with high strain<br />
A2<br />
P.I. : Prof. M. J. Hoffmann,<br />
Topic: Manufacturing and characterization of PZT-ceramics <strong>und</strong>er dc loading<br />
A3<br />
P.I. : Prof. W. Jaegermann<br />
Topic: Bo<strong>und</strong>ary layers and thin films of ionic conductors: <strong>Electronic</strong> structure,<br />
electrochemical potentials, defect formation and degradation mechanisms<br />
A4<br />
P.I. : Prof. R. Riedel<br />
Topic: Novel functional ceramics using anionic substitution in oxidic systems<br />
A5<br />
P.I.: Prof. M. Rehahn<br />
Topic: Synthesis of semiconducting model polymers and their characterization before and<br />
after cyclic electric fatigue<br />
Division B: Characterization<br />
B1<br />
P.I.: Dr. R.-A. Eichel / Prof. K.-P. Dinse<br />
Topic: EPR-Investigations of defects in ferroelectric ceramic material<br />
B2<br />
P.I.: Dr. Dr. A. G. Balogh<br />
Topic: Investigations of the defect structure and diffusion in ferroelectric materials<br />
B3<br />
P.I.: Prof. H.-J. Kleebe / Prof. H. Fueß<br />
Topic: Structural investigations into the electrical fatigue in PZT<br />
B4<br />
P.I.: Dr. H. Ehrenberg<br />
Topic: In-situ investigations of the degradation of intercalation batteries <strong>und</strong> their modelling<br />
- 59 -
B7<br />
P.I.: Prof. H. v. Seggern / Dr. A. Klein<br />
Topic: Dynamics of electrical properties in fatigued PZT<br />
Division C: Modelling<br />
C1<br />
P.I.: Prof. K. Albe<br />
Topic: Quantum mechanical computer simulations for electron and defect structure of<br />
oxides<br />
C2<br />
P.I.: Prof. K. Albe<br />
Topic: Atomistic computer simulations of defects and their mobility in metal oxides<br />
C3<br />
P.I.: Prof. R. Müller / Prof. W. Becker<br />
Topic: Microscopic investigations into defect agglomeration and its effect on the mobility of<br />
domain walls<br />
C5<br />
P.I.: Dr. Y. Genenko / Prof. H. v. Seggern<br />
Topic: Phenomenological modelling of bipolar carrier transport in organic semiconducting<br />
devices <strong>und</strong>er special consideration of injection, transport and recombination phenomena<br />
Division D: Component properties<br />
D1<br />
P.I.: Professor J. Rödel / Dr. T. Granzow<br />
Topic: Mesoscopic and macroscopic fatigue in doped ferroelectric ceramics<br />
D3<br />
P.I.: Dr. A. Klein<br />
Topic: Function and fatigue of conducting electrodes in organic LEDs and piezoceramic<br />
actuators<br />
D4<br />
P.I.: Dr. Ch. Melzer / Professor H. v. Seggern<br />
Topic: Fatigue of organic semiconductor components<br />
D5<br />
P.I.: Professor W. Jaegermann<br />
Topic: Processing and characterization of Li-ion thin film batteries<br />
- 60 -
Reports of Research Activities<br />
High strength metastable materials with enhanced ductility<br />
J. Das, S. Pauly, F. Ettingshausen, K. B. Kim, J. Eckert<br />
The recent developments in the area of metastable metallic materials like bulk metallic<br />
glasses and nanostructured alloys have revealed the large potential of Cu-, Ti- and Zrbased<br />
glassy and nanostructured (nano-eutectic) composites for a variety of applications<br />
as high specific strength structural materials. Previous investigations on the room<br />
temperature deformation behavior have shown that the respective volume fractions of<br />
dendrites and nano-/ultrafine eutectic matrix govern the overall strength and ductility of the<br />
material. The development of new alloys derived from glass-forming alloy compositions<br />
with homogeneous nano-/ultrafine eutectic microstructure and bulk metallic glasses with<br />
high strength and enhanced room temperature plastic deformability was the major aim of<br />
the work in 2005. Ultimately, this should open up the possibility to develop tailor-made<br />
microstructures in order to improve the mechanical properties of such novel materials.<br />
As an example for ductile bulk metallic glasses, Cu50Zr50 and Cu47.5Zr47.5Al5 2 mm diameter<br />
(∅) rods were investigated in detail using x-ray diffraction (XRD), differential scanning<br />
calorimetry (DSC), scanning electron microscopy (SEM) and transmission electron<br />
microscopy (TEM). Even though the structure of Cu50Zr50 was fo<strong>und</strong> to be amorphous<br />
through XRD and DSC studies, traces of very tiny crystallites were fo<strong>und</strong> to be randomly<br />
present in the glassy matrix. The size of these crystallites is about 2 – 5 nm as measured<br />
from the lattice fringes observed in high resolution images. Cu47.5Zr47.5Al5 gives no hint for<br />
the presence of any distinguishable crystallites like Cu50Zr50. However, the selected area<br />
diffraction pattern from the overall structure shows a weak contrast overlapping on the<br />
amorphous ring (Fig. 1, inset). The high resolution image of this alloy reveals no lattice<br />
fringes of crystals. Maximum 3 – 4 atomic layers are observed to have a regular<br />
arrangement without any long-range order.<br />
Fig. 1: High resolution TEM image of a<br />
Cu47.5Zr47.5Al5 glass. Inset: selected area<br />
diffraction pattern from such a microstructure.<br />
Cu50Zr5<br />
Cu47.5Zr47.5Al5<br />
Cu47.5Zr47.5Al5<br />
Fig. 2: Compressive stress-strain curves of Cu50Zr50 and<br />
Cu47.5Zr47.5Al5 glassy rods. Inset: true stress-true strain<br />
curve of Cu47.5Zr47.5Al5 showing “work-hardening”-like<br />
behavior.<br />
- 61 -
The glass transition temperature (Tg) of Cu50Zr50 and Cu47.5Zr47.5Al5 2 mm∅ rods are<br />
estimated to be 671 K and 698 K, respectively. The supercooled liquid region (∆Tx) for<br />
Cu50Zr50 and Cu47.5Zr47.5Al5 is 46 K and 74 K, respectively. This proves that addition of Al<br />
increases the glass-forming ability of binary Cu50Zr50. The resulting Cu47.5Zr47.5Al5 glass<br />
exhibits high strength (2265 MPa) together with a large room temperature ductility of up to<br />
18%, as depicted in Fig. 2. After yielding a strong increase in the flow stress is observed<br />
during deformation indicating a “work-hardening” like behavior.<br />
In recent years, a large number of high strength and ductile Ti-base nanocomposites with<br />
bimodal distribution of micrometer-sized primary bcc β-Ti dendrites / primary FeTi(Co)<br />
phase distributed in a nano-/ultrafine eutectic matrix has been reported. Similar properties<br />
have been achieved by tailoring the eutectic structure without any micrometer-sized<br />
toughening phase. For example, (Ti0.705Fe0.295)100-x Snx (x = 0 and 3.85) ultrafine eutectics<br />
were prepared by slow cooling from the melt through cold crucible casting into 6 mm<br />
diameter rods. The microstructure of both alloys exhibits an eutectic consisting of A2 (β-Ti)<br />
and B2 (FeTi) phases. Ti67.78Fe28.36Sn3.85 shows pronounced colony bo<strong>und</strong>aries and<br />
equiaxed colonies with a cell size of 50 – 10 µm (Fig. 3). The growth of the FeTi phase is<br />
rather parallel at the center of the colony with an interlamellar spacing (λ) of 300 nm, which<br />
is more refined than the binary Ti70.5Fe29.5 eutectic (λ = 500 nm). At the colony bo<strong>und</strong>ary<br />
the growth of the FeTi phase becomes restricted in the longitudinal direction and becomes<br />
coarser. TEM investigations suggest that both alloys exhibit the same orientation<br />
relationship ([110]β-Ti || [110]FeTi) and [200]β-Ti || [200]FeTi) between the A2 and B2 structures<br />
(inset to Fig. 3). XRD analysis revealed that there is an increase in the difference between<br />
the lattice parameter values (δ) of the A2 and B2 structures from 0.017 nm (Ti70.5Fe29.5) to<br />
0.028 nm (Ti67.78Fe28.36Sn3.85).<br />
Ti67.78Fe28.36Sn3.85 exhibits a significantly improved ductility reaching a fracture strain of εf =<br />
9.6 % compared with εf = 2.6% for Ti70.5Fe29.5. The fracture strength is σ max = 1935 MPa<br />
for Ti70.5Fe29.5 and σ max = 2260 MPa for Ti67.78Fe28.36Sn3.85 (Fig. 4). Possibly a higher lattice<br />
mismatch in the ternary alloy (δ = 0.028 nm) between the A2 and B2 structures introduces<br />
coherency strains at the interface, which may be a favorable condition to absorb the<br />
dislocations emitted from the β-Ti(Fe,Sn) phase during deformation. This, in turn, allows to<br />
emit dislocations or activates slip in the FeTi phase providing better slip transfer across the<br />
interface.<br />
Fig. 3: SEM (secondary electron) image of the<br />
Ti67.79Fe28.36Sn3.85 nano-/ultrafine eutectic. Inset:<br />
SAED pattern showing diffractions from A2 (β-Ti)<br />
and B2 (FeTi) structures.<br />
Fig. 4: Compressive engineering stress-strain<br />
curves of Ti70.5Fe29.5 and Ti67.79Fe28.36Sn3.85<br />
nano-/ultrafine eutectics.<br />
- 62 -
Transition of crack closure mechanism in Ti-6Al-4V<br />
Arne Kriegsmann and Clemens Müller<br />
During cyclic loading, fatigue crack closure occurs when crack faces are in contact before<br />
minimum load. It is assumed that no crack-tip damage occurs while crack faces are in<br />
contact, so this portion of the load cycle is ineffective for fatigue crack growth. Therefore,<br />
the effective stress intensity range ∆Keff at the crack tip and thereby the crack propagation<br />
rate decreases.<br />
Fatigue crack closure can result from residual plastic deformations remaining in the wake<br />
of an advancing crack, fracture surface roughness or corrosion deposits in the crack wake.<br />
These three closure mechanisms are called plasticity induced closure, roughness induced<br />
closure and oxide induced closure, respectively.<br />
500 µm<br />
25 µm<br />
Fig. 1a: Lamellar microstructure Fig. 1b: Equiaxed microstructure<br />
Fig. 1c: Transition from coarse lamellar (left) to equiaxed (right) microstructure<br />
At higher values of ∆K, material at the crack tip experiences large tensile plastic strains<br />
which are not reversed upon unloading. Tensile residual displacements left in the crack<br />
wake cause plasticity induced crack closure. At low stress intensity levels crack growth<br />
proceeds locally in one slip system, leading to a kinked crack and finally to roughness<br />
induced crack closure. Thus, when determining the crack propagation threshold a change<br />
from plasticity induced to roughness induced crack closure takes place for most<br />
microstructures. This transition and its consequences on crack closure level is still not fully<br />
<strong>und</strong>erstood.<br />
Ti-6Al-4V lamellar microstructures (Fig. 1a) cause roughness induced crack closure even<br />
at high ∆K values. At the same ∆K, equiaxed microstructures (Fig. 1b) lead to plasticity<br />
induced crack closure resulting in lower Kop values. In this investigation a heat treatment<br />
using a temperature gradient was used to produce specimens showing a sharp transition<br />
(Fig. 1c) from lamellar to equiaxed microstructure. During fatigue crack growth this<br />
- 63 -
transition allows to investigate at constant loading ∆K, the change in crack closure due to<br />
microstructural change.<br />
The results of crack closure measurements are expressed by the development of Kop over<br />
the crack distance from the transition (Fig. 2). It is obvious that the slope of the linear<br />
approximation is different for the two crack propagation directions (equiaxed to lamellar<br />
and lamellar to equiaxed). The difference in the slope for the two crack propagation<br />
directions indicates that there is a “microstructual history effect”, which affects crack<br />
closure and therefore crack growth rate too, leading to direction depending crack<br />
propagation rates.<br />
K op [MPam 1/2 ]<br />
8<br />
7<br />
6<br />
5<br />
4<br />
3<br />
2<br />
m=-0,29<br />
m=0,46<br />
equiaxed to lamellar<br />
lamellar to equiaxed<br />
-6 -4 -2 0 2 4 6 8 10 12<br />
distance from transition [mm]<br />
Fig. 2: Variation of Kop with the change in microstructure<br />
Derived from dislocation theory, equation 1 is valid to calculate Kop in the case of<br />
roughness induced crack closure.<br />
2<br />
1/<br />
2 3/<br />
2 Sθ<br />
K op = C ⋅σ<br />
ys ⋅ K max ⋅ SH<br />
⋅ sin Sθ<br />
⋅ cos<br />
(eq. 1)<br />
2<br />
SH, Sθ: standard deviation of height- and angle-distribution C: fitting parameter<br />
Calculation of Kop is in good agreement with experimental values in lamellar<br />
microstructures showing roughness induced crack closure. In the range of microstructural<br />
transition the calculated Kop values do not fit the experimental ones. This indicates that<br />
small volume fractions of equiaxed grains reduce the roughness induced crack closure<br />
significantly by reducing the shear displacement of the crack tip.<br />
- 64 -
Constrained Sintering of Ceramic Films<br />
Olivier Guillon, Jürgen Rödel<br />
Ceramic coatings are deposited on substrates because of their mechanical properties<br />
(resistance against wear, hardness…), chemical inertness (acting as a protection against<br />
corrosion), low thermal conductivity (thermal barriers coatings for metallic parts in<br />
turbines), electrical, piezoelectrical properties... (functional layers used in multilayer<br />
electronic circuits, sensors, actuators applications). Typical coating thicknesses range from<br />
less than 1 µm to several h<strong>und</strong>reds of µm. A common way to process such layers is to<br />
disperse ceramic powder in a liquid media. This suspension is then deposited for instance<br />
by dip coating or tape casting. To achieve optimal final properties and adhesion onto the<br />
substrate, ceramic films have to be densified through a heating process (sintering step).<br />
Due to the geometrical constraining conditions imposed by the <strong>und</strong>erlying stiff substrate,<br />
film densification is significantly limited when compared to the free sintering case. As<br />
shrinkage is not allowed in the plane, densification can only take place along film thickness<br />
direction and biaxial tensile stresses arise in plane. These stresses are concentrated by<br />
defects (microcracks which appeared during drying, heterogeneous regions, inclusions...)<br />
and can lead through creep crack growth to consequent damage (cracking, delamination)<br />
in the film.<br />
Sintering behaviour of alumina films has been recently investigated in the Ceramics<br />
Group. A fine and pure α-alumina powder was chosen as a model material for the solid<br />
state sintering. Thanks to a high resolution laser dilatometer and an amplifying mechanical<br />
system, both developed in Darmstadt, it was possible to measure in-situ film shrinkage as<br />
a function of time for different temperatures (from 1150 to 1350°C). Even if shrinkage is<br />
enhanced in the thickness direction, global film densification is reduced. An isotropic<br />
model developed in the framework of continuum mechanics can be used with parameters<br />
(densification rate and viscous Poisson’s ratio) determined on bulk specimens freely<br />
sintered. Predictions systematically overestimate the experimental results (Fig. 1), showing<br />
that the assumption that microstructures of constrained film and free sintering body are the<br />
same may not hold.<br />
A cautious investigation of film microstructure reveals a continuous development of<br />
anisotropy in constrained films during sintering. Pores become more anisometric and<br />
orientate along the thickness direction with increasing density. Thanks to image analysis, it<br />
is even possible to quantify this anisotropy. Similar effects, though much more limited, can<br />
be observed for grains (longer normal to the thickness). These new results may explain<br />
the discrepancies between model and experiments.<br />
- 65 -
Relative density<br />
1.00<br />
0.95<br />
0.90<br />
0.85<br />
0.80<br />
0.75<br />
0.70<br />
1300°C<br />
1150°C<br />
Film exp. Film model<br />
Bulk<br />
0.65<br />
0 2000 4000 6000 8000 10000<br />
Isothermal time [s]<br />
Fig 1. Experiment and modelled densification curves for 2 sintering temperatures<br />
The effect of film thickness was also investigated. Thinner layers seem to be more<br />
constrained, as they densify more slowly than thicker ones. Particle rearrangement may be<br />
hindered close to the substrate, which leads to a lower local density than elsewhere in the<br />
film (Fig 2).<br />
Fig. 2 Polished cross-section of a sintered film<br />
Finally, an extension of the sintering model to anisotropic bodies has been proposed. In<br />
the case of transverse isotropy, 2 free sintering strain rates, 2 uniaxial viscosity as well as<br />
3 viscous Poisson’s ratios are introduced. In specific cases, such as constrained sintering,<br />
only 2 Poisson’s ratios are required. The experimental determination of these parameters<br />
is still challenging, as anisotropic specimens have to be obtained before being loaded in<br />
different directions and their strains measured.<br />
- 66 -
Breakdown-induced light emission and poling dynamics of<br />
porous fluoropolymers<br />
S. Zhukov and H. von Seggern<br />
Recently, a new class of plastics with a very strong piezoelectricity has been discussed in<br />
literature: foams. It has been demonstrated that inner pores, when properly charged in an<br />
external electric field, are responsible for a high piezoelectric response of cellular<br />
polypropylene (PP) [1-3] and expanded polytetrafluoroethylene (ePTFE) [3-5] films.<br />
Surprisingly, a strong difference in the obtainable polarization and the related piezoelectric<br />
d33 coefficients has been recognized between samples with closed-pore (PP) and openpore<br />
(ePTFE) geometry. Most research groups report quasi-static or low-frequency<br />
dynamic coefficients up to 200 pC/N on standard grades of porous PP films, whereas the<br />
open-porous ePTFE films reveal rather small values of 10 to 20 pC/N.<br />
Up to date the charging mechanism of open-porous electrets materials is not completely<br />
<strong>und</strong>erstood. To clarify this issue, we investigated the emission of light during the corona<br />
poling of single ePTFE films and the same film sandwiched between two solid FEP films.<br />
Generally, the charging mechanism is supposed to arise from electrical breakdown within<br />
the voids during the poling process [4,5]. The separation of charges due to the electrical<br />
breakdown leads to the aspired polarization buildup. However, each breakdown event is<br />
accompanied by light emission. Thus the emission of light can be considered as a direct<br />
proof of the occurrence of breakdown events and indicates an ongoing poling process<br />
within the sample.<br />
Experiments were carried<br />
12.5 µm FEP<br />
ePTFE<br />
5µm 12.5 µm FEP<br />
out on porous ePTFE films<br />
from GoodFellow<br />
Cambridge Limited,<br />
England. The samples are<br />
63 µm thick with a nominal<br />
porosity of 91% and a pore<br />
size of 1 µm. In order to<br />
handle the films they are<br />
mounted in a circular<br />
aluminum holder with an<br />
inner diameter of 42 mm. A<br />
gold electrode was<br />
deposited onto the bottom<br />
side of the film by thermal<br />
evaporation. The utilized sandwiches are fabricated from the same ePTFE film placed<br />
between an unmetallized FEP film (top) and a one-side-metallized FEP film (bottom) as<br />
displayed in Fig. 1. The employed FEP films have a thickness of 12.5 µm and are<br />
purchased from Sheldahl Company, USA.<br />
63µm<br />
Figure 1. Artist view of the threelayer<br />
sandwich sample.<br />
Negative charging is conducted in air with a corona triode consisting of a point-to-plane<br />
corona discharge and a grid between needle and sample. The charging experiments were<br />
carried out with the unmetallized surface of the samples facing the corona needle. The grid<br />
can be vibrated sinusoidally to measure the surface potential VS of the sample by means<br />
of the Kelvin technique. The dc needle voltage (VC) was kept at VC = −8.0 kV, whereas dc<br />
grid voltage (VG) is varied between 0 and −2500 V to achieve different surface potentials.<br />
In order to measure the light emission during sample poling a photomultiplier (Hamamatsu<br />
R6094) was incorporated into the charging chamber.<br />
- 67 -
Fig. 2 shows the time dependencies for the charging currents IC (a), surface potentials VS<br />
(b) and the light intensities ∆Ilight (c) for a single ePTFE film at grid voltages ranging from<br />
−500 to −1500 V. As soon as the applied electric field exceeds a threshold value of -700 V<br />
the film starts to emit light. The light emission is accompanied by a charging current IC and<br />
a buildup of surface potential VS. After 5 s the current IC, the surface potential VS and the<br />
light emission ∆Ilight saturate to non-zero values. The constant current can be explained by<br />
an equivalent circuit model consisting of the sample capacitor and a leakage resistor in<br />
parallel. The leakage current (saturated current IC) is caused by charge transport initiated<br />
by ongoing local breakdowns. Hence, the charge carriers generated in the material voids<br />
must permanently vanish during the poling process, most likely due to ejection at the metal<br />
electrode and neutralization of corona induced charges at the ePTFE top surface. As a<br />
consequence, the surface charge potential does not change for grid voltages VG < −700 V<br />
[4].<br />
I C , [µA]<br />
V S , [ V ]<br />
∆I light , [a.u.]<br />
0,00<br />
-0,05<br />
-0,10<br />
-0,15<br />
-0,20<br />
-800<br />
-600<br />
-400<br />
-200<br />
0<br />
2,0<br />
1,5<br />
1,0<br />
0,5<br />
0,0<br />
a)<br />
0 5 10 15 20<br />
b) -700... -1500V<br />
0 5 10 15 20<br />
c)<br />
0 5 10 15 20<br />
t 1<br />
-500V<br />
-700V<br />
-800V<br />
-900V<br />
-1000V<br />
-1250V<br />
-1500V<br />
-500V<br />
-1500V<br />
-1250V<br />
-1000V<br />
-900V<br />
-800V<br />
-700V<br />
-500V<br />
time, [sec]<br />
Figure 2. Time dependencies of charging currents (a),<br />
surface potentials (b) and light intensities (c)<br />
during negative poling of an individual ePTFE film<br />
at different grid voltages as indicated.<br />
I C , [µΑ]<br />
V S , [ V ]<br />
∆I light , [a.u.]<br />
0,00<br />
-0,05<br />
-0,10<br />
-0,15<br />
-2000<br />
-1000<br />
0<br />
3<br />
2<br />
1<br />
0<br />
a)<br />
0 25 50 75<br />
b)<br />
0 25 50 75<br />
t 1<br />
c)<br />
0 25 50 75<br />
time, [sec]<br />
Figure 3. Time dependencies of charging currents (a),<br />
surface potentials (b) and light intensities (c)<br />
during negative poling of three-layer sandwich at<br />
grid voltage of -2500 V.<br />
In the contrary to the results obtained from single ePFTE films, the light intensity ∆Ilight and<br />
the charging current IC detected during the poling of the sandwich structure exhibit initially<br />
maxima and decay with time to zero. This is depicted in Fig. 3. Time t1 indicates the onset<br />
of light emission. Concomitantly, the saturated surface potential coincides for all applied<br />
grid voltage with VG. Due to the blocking character of the FEP films, on can anticipate that<br />
the positive and negative charges generated during breakdown are trapped at opposite<br />
- 68 -
ePFTE/FEP film interfaces and cannot leave the ePFTE film. The buildup of oppositely<br />
charged surfaces results in a polarization field compensating for the electric field induced<br />
by the corona charging. Once the internal electric field falls below the threshold field for<br />
electrical breakdown, further electrical breakdown is inhibited and the light intensity as well<br />
as the charging current diminished to zero. The macroscopic dipole formation accounts<br />
also for the drastic difference in piezoactivity between the single porous films and<br />
sandwiched structures. Opposite to the low piezoactivity of the single ePTFE film<br />
(20 pC/N), the three-layer sandwich reveals a large quasi-static piezoelectric d33 coefficient<br />
up to 800 pC/N [5].<br />
In summary, it has been shown that the monitoring of light emission during poling of<br />
porous electrets give an important additional information on the charging mechanism. The<br />
emitted light itself is a direct proof of breakdown in the porous material, which was indeed<br />
observed for the single as well as the sandwiched porous structures. The good agreement<br />
of the poling current and the light intensity progression in time disclose basic features of<br />
the charge separation process in ePTFE layers.<br />
The authors acknowledge the financial support of Arbeitsgemeinschaft industrieller<br />
Forschungsvereinigungen (AiF) “Otto von Guericke” e.V. (ref. Nr.: 09518/03)<br />
References<br />
[1] G. M. Sessler and J. Hillenbrand, Appl. Phys. Lett. 75 (1999) 3405.<br />
[2] J. Peltonen, M. Paajanen, and J. Lekkala, J. Appl. Phys. 88 (2000) 4787.<br />
[3] R. Gerhard-Multhaupt, IEEE Trans. Dielectr. Electr. Insul. 9 (2002) 850.<br />
[4] Z. Hu and H. von Seggern, J. Appl. Phys. 98 (2005) 014108.<br />
[5] Z. Hu and H. von Seggern, J. Appl. Phys. 99 (2006) 024102.<br />
- 69 -
Dielectric interface trap engineering by UV irradiation: A novel<br />
method to control OFET charge carrier transport properties<br />
N. Benson, M. Schidleja, C. Melzer, H. von Seggern<br />
For modern day electronics the integration of field effect transistors with complementary<br />
polarity on a single substrate is essential, in order to enhance the logic capability of the<br />
respective circuits. When considering organic electronics, however, this has proven<br />
difficult since most organic semiconductors exhibit either suitable hole (p) or electron (n)<br />
conduction [1]. The development of organic circuitry therefore requires the deposition of<br />
spatially separated p- and n-type organic semiconductors. However, recent publications<br />
[2,3] revealed the importance of the dielectric/semiconductor interface for charge carrier<br />
Drain<br />
Ca<br />
V DS<br />
Pentacene<br />
PMMA<br />
SiO2 ++ p - Si<br />
Gate<br />
Fig. 1: OFET configuration of both p- and n-type<br />
devices.<br />
Ca<br />
Source<br />
transport in the OFET channel, and<br />
demonstrated the feasibility to<br />
determine the OFET charge carrier<br />
transport properties by controlling the<br />
interfacial electrical trap density.<br />
In the current article we demonstrate<br />
that unipolar p- and n-type OFETs can<br />
be realized by employing pentacene<br />
as the organic semiconductor and a<br />
Ca source/drain metallization. The<br />
OFETs simply differ by UV exposure of<br />
the utilized PMMA dielectric layer in<br />
ambient atmosphere prior to the<br />
pentacene deposition. The OFET<br />
substrate is a highly p-doped<br />
1.7x1.7 cm 2 silicon waver, functioning as the gate contact, with a 200 nm thick SiO2 dry<br />
oxide. In the following, an 120 nm thick PMMA dielectric layer was spin coated from a<br />
2% wt THF solution. Subsequently, the PMMA layer of selected substrates was exposed<br />
to UV light for 10 minutes in air, using<br />
wavelengths of 254 and 185 nm with a<br />
respective intensity of 15 mW/cm 2 and<br />
1.5 mW/cm 2 . A 50 nm thick pentacene<br />
layer and 100 nm thick Ca<br />
Drain/Source contacts were then<br />
precipitated by physical vapour<br />
deposition, using a rate of 2 Å/s at a<br />
chamber base pressure
I D [10 -5 A]<br />
14<br />
12<br />
10<br />
8<br />
6<br />
4<br />
2<br />
0<br />
-2<br />
-4<br />
-6<br />
-8<br />
-10<br />
-12<br />
Before Cycle 1<br />
After Cycle 8<br />
V GS = -80V<br />
0 20 40<br />
VDS [V]<br />
60 80<br />
-80 -60 -40 -20 0 20 40 60 80<br />
with a low current hysteresis<br />
and a steep increase in the<br />
linear region of the transistor,<br />
indicating ohmic contacts for<br />
electron injection. In contrast, an<br />
OFET built on a UV modified<br />
PMMA dielectric exhibits initially<br />
negligible hole and no electron<br />
currents, as illustrated by the<br />
output characteristic shown in<br />
Fig. 3. However, once the OFET<br />
is further operated in electron<br />
accumulation, as shown by the<br />
first quadrant of Fig. 3 at<br />
VGS = 0 V, a significant increase<br />
in ID between the initial and the<br />
8 th operating cycle is visible.<br />
This increase in ID, is due to a<br />
quasi ambipolar hole current [6]<br />
for │VDS│≥│VGS -Vth,p│. The<br />
unipolar p-type characteristic of<br />
this transistor can be confirmed when considering the third quadrant of Fig. 3, showing the<br />
output characteristic measured at VGS = -80 V after the 8 th cycle in hole accumulation.<br />
Surprisingly, the increase in ID occurs despite an energy difference of 2.2eV between the<br />
work function of Ca (2.87eV) and the highest occupied molecular orbital of pentacene<br />
(5.07eV). The pronounced S-shaped output characteristic in the linear region of the OFET<br />
(Fig. 3) indicates the expected large contact resistance.<br />
1/2 [10 -3 A 1/2 ]<br />
I D<br />
12<br />
10<br />
V DS [V]<br />
8<br />
6<br />
4<br />
2<br />
0<br />
V GS = 0V<br />
Individual<br />
Cycles<br />
Linear<br />
regression<br />
Fig. 3: OFET ID characteristic for a UV-modified device. The<br />
first quadrant illustrates ID at VGS = 0 V and the third<br />
quadrant at VGS = 80 V. The arrows indicate the increase in<br />
ID. Inset: ∆Vth during operation in el. accumulation.<br />
The inset of Fig. 3 reveals the origin of the hole current enhancement during subsequent<br />
electron accumulation cycles. Let us first consider the ambipolar drain current equation as<br />
derived by Schmechel et. al. [6] for µn = 0 cm 2 V -1 s -1 and VGS = 0 V:<br />
∆V th<br />
wCeff<br />
µ p<br />
= (VDS<br />
+ Vth,<br />
p − ∆V<br />
) for:│VDS│≥│VGS -Vth,p│. (1)<br />
2l<br />
ID th<br />
Ceff = 10.4 nFcm -2 represents the resulting area capacitance of the SiO2 / PMMA dielectric<br />
layer. With Eq.1 it becomes apparent that the output characteristics in the inset of Fig. 3<br />
are subject to a positive threshold voltage shift (∆Vth), while the hole mobility remains<br />
approximately constant. After the 8 th cycle ∆Vth saturates and reaches approximately 60 V.<br />
This value has been derived from the output characteristic in hole accumulation. We<br />
propose that ∆Vth is a result of trapped negative charge (nt), since it has been<br />
demonstrated that the exposure of PMMA to UV light in air results in the formation of -<br />
COH as well as -COOH functional end groups [4] in the near surface layer of the polymer.<br />
In accordance with the work of Chua et. al. [5], who have recently identified -OH groups as<br />
electron traps, the UV treatment of the PMMA dielectric therefore generates electron traps<br />
at the semiconductor / polymer dielectric interface. Once driven in electron accumulation,<br />
the electron current is inhibited, since the accumulated electrons are trapped. However, as<br />
long as the trapped negative charges are residual, even <strong>und</strong>er hole accumulation, they will<br />
be compensated by positive charges (p) leading to a positive ∆Vth. To obtain a threshold<br />
shift of ∆Vth = 60 V, p can be estimated to be:<br />
- 71 -
∆V<br />
C<br />
q<br />
th eff<br />
12 −2<br />
p ( VGS<br />
= 0V)<br />
= = 3.<br />
9 * 10 cm , (2)<br />
where q is the elementary charge. This figure is equal to nt, as long as the negative<br />
charges are trapped directly at the dielectric/semiconductor interface. The lack in<br />
hysteresis, however, observed for the p-type OFET drain current characteristic, indicates<br />
(1) the absence of hole traps and (2) the absence of recombination of the mobile holes<br />
with the trapped electrons. This leads to the conclusion, that the negative charges are not<br />
localized directly at the semiconductor dielectric interface, but in a near surface layer of the<br />
PMMA dielectric, isolated from mobile holes in the transistor channel.<br />
We have demonstrated the feasibility to convert unipolar n-type pentacene OFETs into ptype<br />
OFETs by a modification of the polymer dielectric through a UV treatment in air. The<br />
change in OFET polarity is due to a large positive threshold voltage shift of about 60 V,<br />
resulting from trapped negative charge carriers within the UV-treated PMMA layer. The<br />
proposed modification of the dielectric / semiconductor interface allows for the<br />
development of organic complementary circuits, since the introduced p- and n-channel<br />
transistors exhibit comparable current characteristics in terms of mobilities (≈ 0,1 cm 2 /Vs),<br />
on / off ratios (≈ 10 4 -10 5 ) and current maxima, as derived from the respective transfer<br />
characteristics.<br />
References<br />
[1] C. D. Dimitrakopoulos and P. R. L. Malenfant, Adv. Mater.14 (2002) 99.<br />
[2] M. Ahles, R. Schmechel, and H. v. Seggern, Appl. Phys. Lett. 85 (2004) 4499.<br />
[3] T. Yasuda, T. Goto, K.Fujita, and T. Tsutui, Appl. Phys. Lett. 85 (2004) 2098.<br />
[4] A. Torikai, M. Ohno, and K. Fueki, J. Appl. Polym. Sci. 41 (1990) 1023.<br />
[5] L.-L. Chua, J. Zaumseil, J.-F. Chang, E. C.-W. Ou, P. K.-H. Ho, H. Sirringhaus, and R.<br />
H. Friend, Nature 434 (2005) 194.<br />
[6] R. Schmechel, M. Ahles, and H. v. Seggern, J. Appl. Phys. 98 (2005) 084511.<br />
- 72 -
Synchrotron Induced Photoelectron Spectroscopy at the Solid-<br />
Liquid Interface of Dye Sensitized Solar Cells<br />
Konrad Schwanitz, Eric Mankel, Ralf Hunger, Thomas Mayer,<br />
and Wolfram Jaegermann<br />
At BESSY we run the experimental station SoLiAS, dedicated to solid-liquid interface<br />
analysis. SoLiAS allows for the transfer of wet chemically prepared surfaces to the ultra<br />
high vacuum without contact to ambient air. In addition in situ (co)adsorption of volatile<br />
solvent species onto liquid nitrogen cooled samples is possible. SoLiAS proves to be very<br />
useful in analyzing the chemical and electronic structure of solid-liquid interfaces e.g. of<br />
dye sensitized solar cells. A monolayer of Ru(N3)-dye was adsorbed from ethanol solution<br />
<strong>und</strong>er clean N2 atmosphere in an UHV-integrated electrochemical cell (EC). Acetonitrile or<br />
benzene were adsorbed from the liquid in the EC or in situ from the gas phase. Ex situ<br />
sintered nanocrystalline anatase substrates as well as in situ deposited polycrystalline<br />
TiO2 samples were used. Distinct reversible changes occur in synchrotron induced<br />
photoelectron valence band and core level spectra when the solvent is adsorbed to<br />
pristine and dye covered TiO2 substrates. Based on the experimental results the alignment<br />
of electronic states and a model on the dye-solvent interaction have been deduced.<br />
The valence band maximum of nc-TiO2 is fo<strong>und</strong> at EB = 3.6 eV binding energy while the<br />
f<strong>und</strong>amental gap is 3.2 eV only. Surface gap states related to Ti 3+ 3d 1 orbitals are fo<strong>und</strong><br />
with a maximum at EB = 1.3 eV and in addition just below the Fermi level. In the rigid band<br />
model these states are assigned to occupied conduction band states but may be due to<br />
substochiometric TiO2-x. Adsorption of acetonitrile is accompanied by quenching of the<br />
surface gap states (Fig. 1). This finding is confirmed in Ti2p core orbital spectra by the<br />
quenching of the Ti 3+ low binding energy shoulder of the Ti 4+ bulk emission. Coadsorption<br />
of acetonitrile (Fig. 2) shifts the dye HOMO by 150 meV from 2.0 eV binding energy to<br />
2.15 eV.<br />
Fig. 1: Intensity normalized (O2p valence<br />
band) SXPS spectra of the gap states of<br />
nanocrystalline anatase TiO2 in the course of<br />
acetonitrile adsorption and desorption.<br />
Fig. 2: SXPS spectra of the gap states of<br />
nanocrystalline anatase TiO2 in the course of<br />
Ru(N3)-dye adsorption and acetonitrile<br />
coadsorption and desorption.<br />
- 73 -
Fig. 3: Schematic of the photovoltaic-relevant<br />
valence states in the rigid band model a) as<br />
prepared nanocrystalline TiO2 anatase film, b) after<br />
dye adsorption from ethanol solution with HOMO<br />
position, c) after coadsorption of the solvent<br />
acetonitrile with the HOMO shifted by 150meV to<br />
higher EB. Using the optical absorption maximum<br />
the LUMO is fo<strong>und</strong> 0.17 eV above the Fermi level.<br />
A schematic representation of the<br />
photovoltaic-relevant valence states<br />
as deduced in the simple rigid band<br />
model is displayed in Fig.3. The<br />
measured HOMO corresponds to the<br />
position of the lowest energy holestate<br />
created by the photoemission of<br />
an electron i.e. the HOMO of the<br />
molecular cation. Except for a Franck<br />
Condon shift of approximately 0.1 eV<br />
away from the Fermi level due to<br />
vibrational excitation in the<br />
photoemission process, this is the<br />
relevant energy position for<br />
rereduction by the redox system. For<br />
the electron injection process the<br />
alignment of the LUMO to the<br />
conduction band edge is crucial.<br />
Using the energy of the optical<br />
absorption maximum (535nm =<br />
2.32eV), the LUMO is fo<strong>und</strong> 0.17 eV<br />
above the Fermi level.<br />
While the shape of the S2p line of the dye NCS group does not change when benzene is<br />
coadsorbed (Fig 4a right), the S2p emission counterintuitively sharpens upon CH3CN<br />
coadsorption (Fig 4a left). In a simple model (Fig. 4b left) the polar solvent acetonitrile<br />
penetrates the dye layer and the interaction of the dye NCS groups with the TiO2 surface<br />
and with neighbouring dye molecules is suppressed due to a solvation shell. The S2p<br />
intensity development in the course of CH3CN adsorption suggests reorientation of the dye<br />
molecules pointing the NCS groups away from the surface towards the electrolyte. On the<br />
other hand nonpolar benzene just covers the dye layer (Fig. 4b right). The solvation and<br />
orientation of the dye by acetonitrile may be important for obtaining vectorial photovoltaic<br />
charge transfer of the electron from the dye LUMO to the TiO2 conduction band and the<br />
hole from the dye HOMO to the electrolyte.<br />
Fig. 4a: Ru(N3)-dye S2p level in the course of<br />
acetonitrile (left) and benzene (right) coadsorption<br />
and desorption.<br />
- 74 -<br />
Fig. 4b: Cartoon of the Ru(N3)-dye/solvent<br />
interaction in the course of acetonitrile (left)<br />
and benzene (right) coadsorption.
Alkyl- and aryl-modified Si(111) for silicon/organic hybrid devices<br />
Ralf Hunger, Wolfram Jaegermann<br />
Silicon/Organic junctions attract interest in several application perspectives: for<br />
silicon/organic hybrid devices such as biosensors, storage devices, or solar cells, as well<br />
as in the perspective of molecular electronics. It combines the advantages of modularity<br />
and tailoring capabilities of organic chemistry with the established, industrial-scale proven<br />
silicon technology.<br />
An example silicon/organic hybrid device is shown in Figure 1. It is a “wet” field-effect<br />
transistor (w-FET) acting as a biochemical sensor. The central idea of this device is that<br />
biochemical sensor molecules with highly specific binding properties are attached on the<br />
gate electrode of a w-FET. This is the active region of the electrochemical sensor, which<br />
is contacted by an electrolyte. Realizing this device in silicon technology requires two<br />
technological preconditions: a) The gate electrode surface needs to be stable against the<br />
electrolyte (corrosion resistance). b) sensor molecules need to be fixed to the gate<br />
electrode in a defined way, and (lateral) spatial pattern, thus “chemical lithography” is<br />
required.<br />
Fig. 1:<br />
Schematics of an<br />
electrochemical,<br />
“wet” field effect<br />
transistor, w-FET,<br />
for biosensing<br />
applications.<br />
Alkyl-modified silicon surfaces are one interesting class of materials considered for surface<br />
passivation and structuring. Various surface terminations such as methyl-, ethyl, or butylfunctionalized<br />
Si(111) were realized by our collaborator groups at CalTech, Pasadena<br />
(N.S. Lewis), the Waseda University Tokyo (T. Osaka) or at the HMI Berlin (J. Rappich),<br />
employing wet chemical as well as electrochemical processing. A schematic<br />
representation of these surfaces is shown in Figure 3. The methyl-terminated surface is<br />
particular in comparison to the other, longer-chain alkyl-terminations in two aspects: (1)<br />
The methyl (-CH3) termination is the only alkyl species the van-der-Waals radius of which<br />
is small enough such that the passivation of every silicon surface atom by a methyl group<br />
is possible. Our measurements showed that already for the next largest alkyl, i.e. ethyl<br />
(C2H5), only a fractional coverage of about 2/3 of a monolayer are achieved. (2) Methylmodified<br />
n-Si(111) surfaces in the presence of water affect a p-conductive surface<br />
channel, which makes them particularly promising for the implementation as passivation<br />
layers in w-FET devices. The mechanism leading to p-type surface channels is not yet<br />
<strong>und</strong>erstood and is a focal point of our studies.<br />
The chemical, electronic, and structural properties of alkylated Si(111) surfaces are<br />
analysed in our “Solid/Liquid Analysis System” (SoLiAS) at the 3 rd generation synchrotron<br />
facility BESSY II in Berlin. SoLiAS is equipped with the analytical methods of highresolution<br />
photoelectron spectroscopy and low energy electron diffraction (LEED). Figure<br />
2 shows the LEED pattern of ethylated Si(111) which proofs an exceptionally high degree<br />
of lateral ordering of the wet chemically processed surfaces. These surfaces are<br />
subjected to further processing steps within the SoLiAS station such as vacuum thin film<br />
deposition, electrodeposition or gas phase adsorption, etc. which allow for an in-situ<br />
- 75 -
synthesis and analysis of interfaces with different contact phases.<br />
The <strong>und</strong>ulator beamline U49/2-PGM2 operated by<br />
our “Collaborating Research Group” BTU Cottbus-<br />
HMI-TU Darmstadt, supplies photon energies in<br />
the range from 90 eV to 1400 eV, and thus core<br />
level emissions as well as valence electronic<br />
structures can be studied in high resolution as<br />
illustrated in Figure 3. Photoelectron spectra of<br />
differently modified silicon surfaces in the valence<br />
band and the C 1s core level regions are shown.<br />
The direct bonding of the terminator group to<br />
surface Si atoms is evidenced by the characteristic emission from the Si-C bond orbital (or<br />
analogously the Si-H bond) at aro<strong>und</strong> 5 eV. Another characteristic feature of direct Si-C<br />
linkage (in contrast to carboxylic bonding Si-O-C) is the low binding energy component CSi<br />
at aro<strong>und</strong> 284.3 eV (silicon-bo<strong>und</strong> carbon) in the C 1s emission. The second component<br />
CCH2 at 285.0 eV is related to C-C or C-H bonded, aliphatic species. With increasing alkyl<br />
chain length the intensity of the aliphatic component increases. For ethylated Si(111), the<br />
ratio CCH2 / CSi is about 1:1, for butylated Si 1:3 in accordance with expectations. As<br />
mentioned above, based on a careful intensity study, the CH3 termination appears as the<br />
only one to achieve 100 % surface termination.<br />
Fig. 2: LEED pattern of Si(111)-C2H5<br />
In addition to alkylated surfaces, aryl-functionalizations of Si(111) by for example<br />
nitrobenzene or bromobenzene were studied. These systems are interesting for surface<br />
engineering because it could be shown that the molecular dipoles grafted onto the Si(111)<br />
surface affect a surface dipole layer which modifies the silicon surface potential. In our<br />
ongoing research project, the interface engineering possibilities of such alkyl-or arylmodified<br />
surfaces in contact with electrolytes and organic or inorganic semiconductors will<br />
be further investigated.<br />
C1s<br />
hn = 650 eV<br />
C x H y<br />
C CH2<br />
C Si<br />
288 287 286 285 284 283<br />
binding energy (eV)<br />
Butyl-Si<br />
Ethyl-Si<br />
Methyl-Si<br />
H-Si<br />
hn = 150 eV<br />
C 2s<br />
σ Si-C<br />
σ Si-H<br />
20 15 10 5 0<br />
binding energy (eV)<br />
Figure 3: Photoelectron spectra of various alkylated Si(111) surfaces. The direct Si-C linkage is<br />
evidenced by the the surface state emission from the Si-C bond orbital and the low BE component<br />
in the C 1s emission (“CSi”), which is associated with silicon-bo<strong>und</strong> aliphatic carbon. “CCH2”<br />
corresponds to aliphatic, only C-C and C-H coordinated carbon.<br />
- 76 -
New unconventional superconductors:<br />
Water intercalated NaxCoO2<br />
Yoshiharu Krockenberger, Jose Kurian, Philipp Komissinskiy, Lambert Alff<br />
The observation of superconductivity in the layered transition metal oxide NaxCoO2 · y H2O<br />
(K. Takada et al., Nature (London) 422, 53 (2003)) has caused a tremendous upsurge of<br />
scientific interest due to its similarities and its differences to the copper based hightemperature<br />
superconductors. Two years after the discovery, we report the fabrication of<br />
single-phase superconducting epitaxial thin films of Na0.3CoO2 ·1.3 D2O grown by pulsed<br />
laser deposition technique. This opens additional roads for experimental research<br />
exploring the superconducting state and the phase diagram of this unconventional<br />
material.<br />
Superconductivity in NaxCoO2 · y H2O is a property of the cobalt oxide planes. Like in the<br />
case of the cuprates, the phase diagram of sodium cobaltate encompasses several<br />
competing electronic phases, and there are many indications that the superconducting<br />
state is unconventional. While in high-temperature superconductors the twodimensional<br />
character of the corresponding copper oxide planes is stabilized by the intrinsically<br />
strongly anisotropic crystal structure, in NaxCoO2 a complicated water intercalation<br />
process is needed to amplify this anisotropy and induce superconductivity. The main<br />
difficulties in fabricating highquality bulk material of NaxCoO2 · y H2O are the following:<br />
First, sodium can be inhomogeneously distributed in the entire bulk sample, resulting in an<br />
ill-defined doping level. Second, impurity Co oxides such as CoO and Co3O4 are likely to<br />
grow due to the high volatility of sodium. Third, it is difficult to avoid the formation of<br />
Na2CO3 in conventional bulk sample fabrication. As a result, high-quality single crystals or<br />
bulk samples of NaxCoO2 · y H2O are rare, and it is even more difficult to obtain clean<br />
surfaces for optical spectroscopy and tunneling experiments in this material. While highquality<br />
thin films of high-temperature superconductors have allowed a large variety of<br />
phase-sensitive experiments to explore the symmetry of the superconducting order<br />
parameter, corresponding studies have thus far not proven possible for water-intercalated<br />
sodium cobaltate, due to the lack of superconducting thin films. Thin-film deposition<br />
techniques offer major advantages in the synthesis of highquality samples, such as a welldefined<br />
vacuum and oxidizing environment. Recently, epitaxial growth of high-quality, “dry”<br />
NaxCoO2 films by pulsed laser deposition on SrTiO3 substrates has been reported. In<br />
these thin films, phase purity was established within the detection limits of x-ray diffraction<br />
in four-circle geometry, and flat surfaces are obtained. As a further milestone, we now<br />
report the fabrication of superconducting thin films of NaxCoO2 · y D2O.<br />
- 77 -<br />
Fig. 1: White light interferometric scan image<br />
of the surface of a Na0.3CoO2 ·1.3 D2O thin<br />
film on SrTiO3 (001). Within the blue regions<br />
the surface roughness is below 10 nm. The<br />
rare spikes arise from sodium carbonate. [1].
Fig. 2: Resistivity vs temperature for an<br />
epitaxial Na0.3CoO2 ·1.3 D2O thin film on<br />
SrTiO3 (001). In the inset superconducting<br />
quantum interference device (SQUID)<br />
magnetization measurement shows<br />
unambiguously the flux expulsion effect at the<br />
critical temperature of about 4.2 K [1].<br />
For obtaining a film at the desired composition x = 0.3, it is vital to provide a strong<br />
oxidizing agent to deintercalate Na + ions. In principle, this can be accomplished by the<br />
standard Br2–CH3CN-solution method, which is also used for bulk synthesis. However, we<br />
have fo<strong>und</strong> that NO2–BF4 is superior to the conventional method, as Br is avoided and the<br />
deintercalation time scale is considerably accelerated. The decisive step is the<br />
intercalation of water into the thin films. In contrast to bulk materials, single-phase thin<br />
films cannot be simply immersed into water, because the thin films tend to peel off the<br />
substrate. Only a much milder method allows the successful fabrication of<br />
superconducting thin films. Oxygen flow with 100% humidity supplied by a D2O bath at a<br />
well-defined temperature (19 °C) is provided to the sample over several days (196 h). In<br />
contrast to alternative preparation routes, this method also yields a clean and smooth<br />
surface (see Fig. 1), which is a necessary prerequisite for meaningful surface-sensitive<br />
measurements. The water-intercalated NaxCoO2 ·y D2O thin films indeed show<br />
superconductivity for x = 0.3 and y = 1.3 with TC,zero about 4.2 K (see Fig. 2). The relatively<br />
sharp superconducting transition with a width of 1.5 K in the resistivity vs temperature<br />
curve confirms the high quality of the thin films. Above the critical temperature, the thin<br />
films show metallic behavior up to room temperature with almost linear slope, similar to the<br />
high-temperature superconductors.<br />
The achievement of superconducting thin films of NaxCoO2 · y D2O paves the way for<br />
additional experiments with this unconventional superconductor. Thin-film-based<br />
Josephson and tunneling experiments, which are expected to yield important clues to the<br />
unconventional nature of superconductivity in this material, can now readily be performed.<br />
Further, superconducting quantum interference device (SQUID) experiments now come<br />
within reach. Such experiments could confirm that, following the discovery of p-wave<br />
superconductivity in Sr2RuO4, the compo<strong>und</strong> NaxCoO2 · y H2O is another metallic solidstate<br />
analog to liquid 3 He with an even higher transition temperature. Following the<br />
successful example of high-temperature superconductors, high quality superconducting<br />
thin film samples of waterintercalated sodium cobaltate thus promise to enhance our<br />
knowledge about this complex material.<br />
In collaboration with MPI Stuttgart (B. Keimer, H.-U. Habermeier, G. Cristiani) and TU<br />
Braunschweig (P. Lemmens)<br />
[1] Y. Krockenberger, I. Fritsch, G. Cristiani, H.-U. Habermeier, Li Yu, C. Bernhard, B.<br />
Keimer, and L. Alff Appl. Phys. Lett. 88, 162501 (2006).<br />
- 78 -
Designed materials for spin electronics<br />
Lambert Alff, Yoshiharu Krockenberger, Andreas Winkler<br />
In the search for new spintronic materials with high spin polarization at room temperature,<br />
we have synthesized an osmium-based double perovskite with a Curie temperature of 725<br />
K. Our combined experimental results confirm the existence of a sizable induced magnetic<br />
moment at the Os site, supported by band-structure calculations, in agreement with a<br />
proposed kinetic-energy-driven mechanism of ferrimagnetism in these compo<strong>und</strong>s. The<br />
intriguing property of Sr2CrOsO6 is that it is at the end point of a metal-insulator transition<br />
due to 5d band filling and at the same time ferrimagnetism and high-spin polarization are<br />
preserved.<br />
A so-called half-metal is a highly desired material for spintronics, as only charge carriers<br />
having one of the two possible polarization states contribute to conduction. In the class of<br />
ferrimagnetic double perovskites such half-metals are well known, e.g., Sr2FeMoO6. The<br />
compo<strong>und</strong> Sr2CrOsO6 described here is special, as it has a completely filled 5d t2g<br />
minority-spin orbital, while the majority-spin channel is still gapped. It is thus at the end<br />
point of an ideally fully spin-polarized metal-insulator transition. At the metallic side of this<br />
transition we have the half-metallic materials Sr2CrWO6 and Sr2CrReO6. Within the unique<br />
materials class of double perovskites, therefore, one can find high-Curie-temperature<br />
ferrimagnets with spinpolarized conductivity ranging over several orders of magnitude from<br />
ferrimagnetic metallic to ferrimagnetic insulating tunable by electron doping. Note that<br />
Sr2CrOsO6, where a regular spin-polarized 5d band is shifted below the Fermi level, is<br />
f<strong>und</strong>amentally different from a diluted magnetic semiconductor, where spin-polarized<br />
charge carriers derive from impurity states.<br />
While for simple perovskites such as the half-metallic ferromagnetic manganites the Curie<br />
temperature TC is in the highest case still close to room temperature, half-metallic<br />
ferrimagnetic double perovskites can have a considerably higher TC. It has been<br />
suggested that ferrimagnetism in the double perovskites is kinetic energy driven. In short,<br />
due to the hybridization of the exchange-split 3d orbitals of Fe 3+ (3d 5 , majority-spin orbitals<br />
fully occupied) or Cr 3+ (3d 3 , only t2g are fully occupied) and the nonmagnetic 4d/5d orbitals<br />
of Mo, W, Re, or Os (N sites), a kinetic energy gain is only possible for the minority-spin<br />
carriers. This will lead to a corresponding shift of the bare energy levels at the<br />
nonmagnetic site and a strong tendency to half-metallic behavior. This mechanism is<br />
operative for the Fe 3+ and Cr 3+ (M sites) compo<strong>und</strong>s, where all 3d majority-spin states and<br />
all t2g majority-spin states, respectively, are fully occupied and represent localized spins. In<br />
agreement with band-structure calculations this mechanism is naturally associated with<br />
half-metallic behavior, as the spin-polarized conduction electrons mediate<br />
antiferromagnetic order between M and N ions and, thus, ferromagnetic order between the<br />
M sites. In addition, this mechanism will lead to an induced magnetic moment at the<br />
nonmagnetic sites as Mo, W, Re, or Os, in convincing quantitative agreement with recent<br />
band-structure calculations. It has been suggested and verified by observation of the<br />
corresponding x-ray magnetic circular dichroism (XMCD) that the induced magnetic<br />
moment at the nonmagnetic site scales with TC of the compo<strong>und</strong> or, in other words, the<br />
bandwidth in the conducting minority-spin channel scales with the magnetic transition<br />
temperature. This behaviour has also been confirmed qualitatively by nuclear magnetic<br />
resonance (NMR) experiments for FeRe-based double perovskites. Quantitatively,<br />
however, Re shows an unusually enhanced induced magnetic moment in the double<br />
perovskite structure, as compared to Mo, W, and Os.<br />
- 79 -
Fig. 2: X-ray appearance near-edge<br />
structure (XANES) (left axis) and XMCD<br />
signal (right axis) at the Os L2 and L3<br />
edges in Sr2CrOsO6. The inset shows<br />
the element-resolved magnetic<br />
moments of Cr (µCr) and Os (µOs), the<br />
total magnetic moment (µtot), and the<br />
lattice distortion as determined from<br />
neutron scattering data refinement [1].<br />
Fig. 1: Rietveld refinements of the<br />
neutron powder data of Sr2CrOsO6<br />
taken at 553 K. The observed and<br />
calculated diffraction intensities as<br />
well as the difference pattern are<br />
shown. The upper left inset shows a<br />
view along the [111) direction<br />
revealing the rhombohedral structure<br />
of the double perovskite. The upper<br />
right inset shows the temperature<br />
dependence of the Sr2CrOsO6 (444)<br />
diffraction peak (cubic) splitting into a<br />
(404) and (0 0 12) peak (hexagonal).<br />
The XMCD measurements on the<br />
Os L2,3 edges were performed at<br />
the European Synchrotron Radiation<br />
Facility (ESRF) at beamline ID12. As<br />
shown in Fig. 2 a very clear XMCD<br />
signal is observed, signaling a<br />
strong local magnetic moment at the<br />
Os site opposite to the net magnetization. The experimentally determined value is in good<br />
agreement with the neutron scattering result.<br />
We have unambiguously demonstrated that an increase of the number of 5d electrons<br />
leads to an increase of the transition temperature in ferrimagnetic double perovskites<br />
irrespective of the changes in conductivity. Fully spin-polarized conductivity, as indicated<br />
by the large induced magnetic moments and supported further by band-structure<br />
calculations, can be changed from half-metallic behaviour (known in Sr2CrWO6 and<br />
Sr2CrReO6) to insulating behaviour in the high-Curie-temperature ferrimagnetic insulator<br />
Sr2CrOsO6.<br />
In collaboration with MPI Stuttgart (K. Mogare, M. Jansen, M. Reehuis), KTH Stockholm<br />
(A. Delin, G. Vaitheeswaran), and ESRF Grenoble (F. Wilhelm, A. Rogalev). Support by<br />
DFG (AL 560/4).<br />
[1] Y. Krockenberger, K. Mogare, M. Reehuis, M. Tovar, M. Jansen, G. Vaitheeswaran, V.<br />
Kanchana, F. Bultmark, A. Delin, F. Wilhelm, A. Rogalev, A. Winkler, and L. Alff, Phys.<br />
Rev B 75, 020404(R) (2007).<br />
- 80 -
SiCN/C-Ceramic Composite as Anode <strong>Material</strong> for<br />
Lithium Ion Batteries<br />
Robert Kolb, Claudia Fasel, Verena Liebau-Kunzmann, Ralf Riedel<br />
The choice of electrode and electrolyte materials to design lithium batteries is limited due<br />
to the chemical reactivity of the used materials during the intercalation/deintercalation<br />
process. Amorphous silicon carbonitride ceramics (SiCN) are known to be chemically<br />
stable in corrosive environments and exhibit disordered carbonaceous regions making it<br />
potentially suitable to protect graphite from exfoliation. The material studied in this work<br />
was synthesized by mixing commercial graphite powder with the crosslinked polysilazane<br />
VL20 ® . Pyrolysis of the polymer/graphite compo<strong>und</strong> at appropriate temperatures in inert<br />
argon atmosphere resulted in the formation of an amorphous SiCN/graphite composite<br />
material. First electrochemical investigations of pure SiCN and of the SiCN/C composite<br />
are presented here. A reversible capacity of 474 mAhg -1 was achieved with a sample<br />
containing 25 wt% VL20® and 75 wt% graphite. The measured capacity exceeds that of<br />
the used graphite powder by a factor of 1.3 without any fading over 50 cycles.<br />
Potential [V] vs. Li/Li +<br />
3,5<br />
3,0<br />
2,5<br />
2,0<br />
1,5<br />
1,0<br />
0,5<br />
0,0<br />
450°C<br />
650°C<br />
850°C<br />
1050°C<br />
1250°C<br />
Graphite<br />
0 100 200 300 400 500 600 700<br />
Capacity [mAhg -1 ]<br />
Fig. 1: First charge- and discharge of 25VL20-75C samples pyrolysed at different temperatures<br />
compared to pure graphite vs. Li/Li + .<br />
- 81 -
Capacity [mAhg -1 ]<br />
700<br />
600<br />
500<br />
400<br />
25VL20-75C charge<br />
25VL20-75C discharge<br />
pure Graphite charge<br />
pure Graphite discharge<br />
300<br />
0 10 20 30 40 50<br />
Cycle number<br />
Fig. 2: Change of capacity after the first 50 cycles of 25VL20-75C powder sample pyrolysed at<br />
1050 °C compared to pure graphite powder vs. Li/Li + .<br />
Conclusion and Outlook<br />
This finding indicates that the SiCN phase is an active phase in terms of lithium<br />
intercalation/deintercalation and that it is a promising candidate as protective layer on<br />
graphite, due to its chemical stability. Still unfavourable is the low coulombic efficiency due<br />
to the large specific surface area of the formed SiCN phase. Therefore future work will be<br />
focused on reducing the surface area to improve the electrochemical properties.<br />
Furthermore the influence of the amorphous SiCN layer on the capacity and chemical<br />
stability of other electrode materials like silicon and optimized carbon materials as well as<br />
on different electrolytes is of particular interest.<br />
- 82 -
Recent Advances in New Hard High-Pressure Nitrides<br />
Andreas Zerr 1 , Ralf Riedel 1 , Toshimori Sekine 2 , J. E. Lowther 3 , Wai-Yim<br />
Ching 4 , Isao Tanaka 5<br />
1 Institut für <strong>Material</strong>wissenschaft, TU Darmstadt, Petersenstr. 23, 64287 Darmstadt, Germany<br />
2 Advanced <strong>Material</strong>s Laboratory, National Institute for <strong>Material</strong>s Science, Tsukuba 305-0044, Japan<br />
3 DST-NRF Center of Excellence in Strong <strong>Material</strong>s and School of Physics, University of the Witwatersrand,<br />
P. O. Wits, 2050, Johannesburg, South Africa.<br />
4 Department of Physics, University of Missouri-Kansas City, Kansas City, Missouri, 64110, USA<br />
5 Department of <strong>Material</strong>s Science and Engineering, Kyoto University, Yoshida, Sakyo, Kyoto 606-8501<br />
Japan.<br />
Since the discovery of spinel nitrides in 1999, there is presently much effort in basic<br />
science to further develop advanced nitrides and electronic nitrides. Aim and scope of the<br />
research in this field is to synthesize novel nitrides for structural and functional<br />
applications. Silicon-based spinel nitrides combine ultra-high hardness with high thermal<br />
stability in terms of decomposition in different environments and are expected to show<br />
interesting optoelectronic properties. These features make spinel nitrides suitable for<br />
applications as cutting tools and light emitting diodes, respectively. The ultra-high pressure<br />
and temperature synthesis of spinel silicon nitride and germanium nitride on the one hand<br />
as well as the successful synthesis of tin nitride at ambient pressure on the other hand<br />
have caused an enormous impact on both basic science and technological development of<br />
advanced nitrides. Moreover, the novel phases of transition metal nitrides like Zr3N4 and<br />
Hf3N4 with Th3P4 structure as well as the recently published mono nitrides of Pt or Mo<br />
demonstrate the scientific potential of high pressure synthesis techniques in the field of<br />
materials science. Here, the state of the art and the progress in the field of novel hard<br />
materials based on nitrides and produced <strong>und</strong>er high pressure are reviewed.<br />
Fig. 1: Spinel-type structure of γ-Si3N4 (left) with calculated electronic band structure (right).<br />
- 83 -
Texture investigations and field emission properties<br />
of metallic nanowires<br />
Florian Maurer, Joachim Brötz, and Hartmut Fueß<br />
Due to their quasi one-dimensional geometry metallic nanowires possess high aspect<br />
ratios, i.e. high ratio of length over diameter. High nanowire aspect ratios, as well as small<br />
radii of curvature of the nanowire tips lead to an amplification of an externally applied<br />
electric field [1] and thus increases the probability of a field emission current by tunnelling.<br />
For field emission applications of vertically-aligned metallic nanowire ensembles it is<br />
desirable to control the aspect ratio, as well as the radius of curvature. A suitable method<br />
to fabricate high aspect nanowire ensembles (diameter a few ten nm, length a few ten µm)<br />
with controllable geometric and structural properties is the polymer template technique [2]:<br />
Nanoporous templates are produced by irradiating polymeric foils with accelerated heavy<br />
ions. After chemical etching of the ion-induced damage tracks, the cylindrical pores of the<br />
template are filled with metal by electrodeposition. The nanowire diameter is adjusted by<br />
the time of etching the ion-induced tracks and its height is controlled during<br />
electrodeposition by coulometry. The radius of curvature, i.e. the degree of single<br />
crystallinity can be controlled by different electrodeposition parameters, e.g. temperature<br />
or overvoltage. Different preferred growth orientations, i.e. textures, of the nanowires might<br />
influence the field emission properties of metallic nanowires in terms of work function. Fig.<br />
1 shows a scanning electron microscopy (SEM) image of a copper nanowire ensemble.<br />
Fig. 1: SEM image of an ensemble with free-standing and vertically-aligned copper nanowires.<br />
Strong textures in direction have been observed for numerous metallic fcc<br />
nanowires <strong>und</strong>er direct current (dc) deposition conditions [2, 3]. On the other hand, a<br />
preferred growth direction of fcc nanowires in has been observed <strong>und</strong>er alternating<br />
current (ac) deposition conditions [3]. X-ray diffractograms of Au nanowire ensembles of<br />
different textures are shown in Fig. 2.<br />
- 84 -
intensity I [a.u.]<br />
intensity I [a.u.]<br />
a)<br />
111<br />
200<br />
200<br />
220<br />
220<br />
311<br />
30 40 50 60 70 80 90 100 110 120<br />
b)<br />
111<br />
texture<br />
311<br />
texture<br />
30 40 50 60 70 80 90 100 110 120<br />
222<br />
222<br />
diffraction angle 2θ [°]<br />
400<br />
400<br />
331 420<br />
331 420<br />
Fig. 2: X-ray diffractograms of Au nanowire ensembles of a) texture <strong>und</strong>er ac deposition;<br />
b) texture <strong>und</strong>er dc deposition conditions; the dashed vertical lines with triangles atop<br />
represent the intensity distribution of a polycrystalline and untextured sample.<br />
To explain these experimental results, the broken bond model [4] is applied to the<br />
anisotropy of single-crystalline or textured wires in combination with surface-energy<br />
minimization growth tendencies: The energy of an atomic surface is considered to be<br />
proportional to its broken-bond density. The constitution of the circular top and base<br />
planes, as well as the cylindrical mantle surfaces depend on of the wire and can be<br />
determined from crystallographic projections [5]. The evolution of the surface energy E<br />
of textured fcc nanowires with increasing aspect ratio h/d, is shown in Fig. 3.<br />
Up to an aspect ratio of 1 a texture represents the configuration of lowest energy.<br />
At higher aspect ratios the orientation becomes the most favourable growth<br />
direction. In TEM investigations for such oriented Au nanowires with strong textured large<br />
elongated grains were observed. Under ac conditions, lattice sites of high reactivity, i.e.,<br />
lattice defects or surfaces with high number of broken bonds are preferentially dissolved<br />
during the anodic cycles of the alternating polarity. As {110} surfaces exhibit a high<br />
number of broken bonds these lattice sites, and thus the texture, successively<br />
disappear <strong>und</strong>er ac conditions. In absence of {110} surfaces, a texture represents<br />
the orientation of lowest energy for aspect ratios larger than~5 (see Fig. 3). In TEM<br />
investigations a distinct texture in direction was only observed at the upper part of<br />
the nanowires, i.e. the texture starts to develop at an advanced state of the<br />
electrodeposition. X-Ray line profile analysis can be used to show that surface defects are<br />
preferably dissolved compared to line defects (dislocations) <strong>und</strong> ac conditions. The <br />
texture <strong>und</strong>er dc and the texture <strong>und</strong>er ac deposition conditions become stronger at<br />
smaller diameters, as the transition aspect ratios are reached earlier.<br />
Field emission properties of nanowire ensembles can be investigated in terms of field<br />
emission scanning microscopy. Emitter densities of 4.4×10 4 cm -2 and 2.4×10 4 cm -2 were<br />
determined for bare and Au-coated Cu nanowire ensembles of 10 6 cm -2 , respectively.<br />
Emission of only a few percent of the nanowires was ascribed to mutual electrostatic<br />
- 85 -
screening effects. Gold coating of copper nanowires influences field emission in terms of<br />
higher radii of curvature and work function. The mean emitted currents were about 50 nA<br />
for bare and µA for Au coated single nanowires. A mean field amplification factor of<br />
245 was deduced from the slope of a Fowler-Nordheim plot of bare Cu nanowires [6]. In<br />
general, Au coating improves stability of field emission. Furthermore, Cu nanowire<br />
ensembles were successfully tested as cryogenic electron sources in Penning traps for<br />
high sensitive measurements of the g-factor of charged particles. Requirements in the<br />
electron source is a stable field emission current of a few ten nA at low temperatures (5 K),<br />
high magnetic fields and <strong>und</strong>er high vacuum (up to 10 -16 mbar). The field emission<br />
properties of nickel nanowire ensembles were improved by Au coating, where a lower field<br />
amplification factor of 302 was observed for Au coated compared to 331 for uncoated Ni<br />
nanowires [7].<br />
total surface energy E <br />
(normalized to γ {111} )<br />
<br />
0.36<br />
1.00<br />
aspect ratio (h/d)<br />
5.00<br />
<br />
<br />
Fig. 3: Evolution of surface energy E of textured fcc nanowires with aspect ratio h/d.<br />
[1] T. Utsumi; IEEE Transactions on Electron Devices 38 (1991) 2276<br />
[2] M.E. Toimil-Molares, J. Brötz, V. Buschmann, D. Dobrev, R. Neumann, R. Scholz,<br />
I.U. Schuchert, C. Trautmann, J. Vetter; Nucl. Instr. Meth. Phys. Res. B 185 (2001)<br />
192.<br />
[3] S. Karim, M.E. Toimil-Molares, F. Maurer, G. Miehe, W. Ensinger, J.<br />
Liu, T.W. Cornelius, R. Neumann; Appl. Phys. A 84 (2006) 403.<br />
[4] J.K. Mackenzie, A.J.W. Moore, J.F. Nicholas; J. Phys. Chem. Solids 23, (1962) 185.<br />
[5] F. Maurer, J. Brötz, S. Karim, M.E. Toimil-Molares, C. Trautmann, H. Fuess;<br />
Nanotechnolgy (2007), 135709.<br />
[6] F. Maurer, A. Dangwal, D. Lysenkov, G. Müller, M.E. Toimil-Molares, C. Trautmann,<br />
J. Brötz, H. Fuess; Nucl. Instr. Meth. Phys. Res. B 245 (2006) 337.<br />
[7] A. Dangwal, G. Müller, F. Maurer, J. Brötz, H. Fuess; J. Vac. Sci. Tech. B (2007) in<br />
press.<br />
- 86 -
<strong>Material</strong> modifications induced by swift heavy ions in NbTi<br />
Aleksandra Newirkowez 1 , Joachim Brötz 1 , Hartmut Fuess 1 , Reinhard<br />
Neumann 2 , Christina Trautmann 2 , Kay-Obbe Voss 2<br />
1 University of Technology, Darmstadt, Germany; 2 GSI, Darmstadt, Germany<br />
The Facility for Antiproton and Ion Research (FAIR) to be built at GSI will be equipped with<br />
superconducting magnets. Due to the high beam intensities and related beam losses,<br />
radiation damage of the Cu/NbTi superconducting wires used in the magnet coils has to be<br />
considered [1]. Radiation-induced degradation of the superconducting properties of NbTi<br />
alloy was studied in the 1970s and ‘80s. Using projectiles such as protons, neutrons,<br />
deuterons, and O ions, was shown to result in increased electrical resistivity and<br />
decreased critical current, superconducting transition temperature, and upper critical<br />
magnetic field [2]. These irradiations with light and/or low-energy ion beams involve small<br />
electronic energy losses.<br />
Here we are interested in radiation effects in particular in structural changes produced with<br />
swift heavy ions (2.6-GeV U) of much higher electronic energy deposition.<br />
A superconducting wire has typically a diameter of ~1 mm and consists of several<br />
thousand thin NbTi-filaments arranged in b<strong>und</strong>les embedded in a copper matrix for thermal<br />
stabilization (Fig. 1). The filaments are a few µm thick and are composed of β-NbTi (bcc)<br />
and α-Ti precipitate (hcp) which improve the critical current by flux-pinning. During the<br />
cold-drawing process of the filaments, the β-NbTi matrix develops a <br />
crystallographic texture.<br />
Fig. 1: Optical micrograph of cross-section of multifilamentary wire (dark: NbTi filaments, light: Cu<br />
matrix).<br />
The irradiation of NbTi filaments was performed at the UNILAC (GSI) applying fluences<br />
between 3×10 11 and 5×10 12 ions/cm 2 at a flux of 1 - 2×10 8 ions/cm 2 ·s. Before irradiation,<br />
the copper matrix was dissolved in aq. FeCl3. The filaments were clamped on an Al holder<br />
and exposed to a beam of 2.6-GeV U ions at room temperature. The electronic energy<br />
loss (dE/dx)e for U in NbTi is 53 keV/nm.<br />
Radiation-induced effects were examined using transmission electron microscopy (TEM)<br />
(Philips CM20, 200 keV), x-ray powder diffraction (λMo–Kα1 = 0.70926 Å) in flat-sample<br />
transmission geometry and with four-circle diffractometry (λCo–Kα = 1.78897 Å).<br />
- 87 -
Figure 2 shows a selected region of the diffraction pattern of filaments irradiated with<br />
different fluences. The position of the dominant reflection of β-NbTi remains unchanged,<br />
i.e., there is no obvious change of the lattice parameters. The weak reflection of the<br />
equilibrium hcp α-Ti phase decreases already at a low fluence of 3×10 11 ions/cm 2 . By<br />
TEM, we find evidence for the hexagonal ω-Ti phase probably resulting from a transition of<br />
α- into ω-Ti [3]. Neither track formation nor any other phase transition or amorphization of<br />
the β-NbTi phase was detected.<br />
Fig. 2: X-ray diffraction pattern of filaments as function of applied fluence.<br />
Irradiated filaments showed changes of the β-NbTi texture, but quantitative analysis is<br />
problematic due to the small diameter of the filaments. We therefore measured larger foil<br />
samples with a ( 100)[<br />
110]<br />
texture before and after irradiation at a four-circle<br />
diffractometer. Comparing their pole figures gives evidence of irradiation-induced<br />
degradation and rotation of the azimuthal distribution of the (100) planes (Fig. 3).<br />
Fig. 3: (100) pole figures of NbTi-foil (left: virgin, right: irradiated with 10 12 cm -2 U ions).<br />
References<br />
[1] L. Latysheva, N. Sobolevskiy, G. Moritz, E. Mustafin, G. Walter, GSI Scientific Report<br />
2003 (May 2004) p. 252.<br />
[2] S.T. Sekula, J. Nucl. Mat. 72 (1978) 91.<br />
[3] H. Dammak, A. Dunlop, D. Lesueur, Nucl. Instr. Meth. B 107 (1996) 204.<br />
- 88 -
SIMS Analysis of Carbide Nanofilms of Titanium and Tantalum<br />
Formed by Methane Plasma Immersion Ion Implantation<br />
S. Flege, G. Kraft, W. Ensinger<br />
It is well-known that ion implantation of carbon into reactive carbide-forming metals such<br />
as titanium leads to thin films of hard carbides which improve the tribological resistance of<br />
the metal. Apart from conventional beam-line ion implantation, plasma immersion ion<br />
implantation (PIII) can be used.<br />
Titanium and tantalum samples were treated by high voltage pulses at -20 kV in an<br />
atmosphere of methane. The high voltage created a plasma, from which ions of methane<br />
and its fragments were accelerated towards the sample and were implanted. Process<br />
times between 0.5 and 2 hours at a pulse repetition rate of 1 kHz were used.<br />
The samples were analyzed for phase composition by glancing incidence X-ray diffraction<br />
(GIXRD). The element composition was analyzed by X-ray photoelectron spectrometry<br />
(XPS) and by secondary ion mass spectrometry (SIMS) with 8 kV O2+ sputtering.<br />
Fig. 1 shows the SIMS depth profile, given as mass signal intensities over the sputtering<br />
time, of a Ti sample, treated for 1h. 6 masses have been recorded: H-1, C-12, O-16, Ti-46,<br />
Ti-48, and Ti-48 C-12 (mass 60).<br />
Fig. 1: SIMS element profile of Ti, treated by<br />
pulse biasing for 1 h<br />
- 89 -<br />
Fig. 2: SIMS carbon profiles of Ti samples,<br />
treated for 0.5, 1, or 2 h, extracted from the<br />
C-12 signals
The spectrum shows that apart from C, hydrogen has been implanted. In the plasma,<br />
different hydrogen-containing ionic species are present, such as CH4 + , CH3 + , and<br />
CH2 + . The H profile starts at a certain level at the surface, and drops almost an order<br />
of magnitude in depth. The carbon profiles of samples, treated with different process<br />
times, are compared in Fig. 2. They were extracted from the C-12 signal. A strict<br />
quantitative comparison is not possible, as the secondary ion yield might slightly<br />
differ, however, one can state that the amount of incorporated carbon increases with<br />
process time. Also, the shape of the depth profiles change. At the lowest process<br />
time, the profile drops monotonely with depth.<br />
A process time of 1 h leads to a typical PIII implantation profile: a slight drop below<br />
the surface, followed by an increase, and a slope down to the backgro<strong>und</strong> level.<br />
When the process time is doubled, the profile changes further. A plateau seems to be<br />
formed, indicating a possible saturation effect. The situation with tantalum is similar.<br />
Fig. 3 shows the depth profile of five masses, apart from the above mentioned H, C,<br />
and O, it is Ta-181, and Ta-181 C-12. Again, a typical PIII implantation profile is<br />
observed.<br />
Fig. 3: SIMS element<br />
profile of Ta, treated<br />
by pulse biasing for 2<br />
h<br />
The carbon profiles are compared in Fig. 4. An increase in process time leads to an<br />
increase in the amount of implanted C. It can be assumed that the carbide film is<br />
shallower in comparison to Ti. The thickness of the carbide zone is dependent on<br />
mass and density of the sample element, because the projected range of the carbon<br />
ions is a direct function of substrate mass and density. For a full acceleration voltage<br />
of 20 kV and CH4 + ions, the energy of the C atom is 15 keV, while it is 1.25 for each<br />
H atom, as the molecule breaks up upon impact and the single atoms take a part of<br />
the kinetic energy of the molecule, according to their mass. Following SRIM<br />
calculations, the projected range of 15 keV carbon ions in Ti is 32.5 nm, while it is<br />
only 14.6 nm in Ta. Other species, such as CH2 + show accordingly a slightly higher<br />
energy. However, a part of the ions have a lower kinetic energy, as they do not<br />
experience the full acceleration voltage or they collide with molecules from the gas<br />
atmosphere. The sum of all energies, as well as sputtering effects, lead to the<br />
observed depth profiles.<br />
- 90 -
In the XRD spectra, apart from the peaks of Ti and Ta, small peaks of the respective<br />
carbide phases MeC can be identified. Carbon implantation led to formation of the<br />
carbide phase. The peaks are rather weak and broad, which is assumed to be a<br />
consequence of small grain sizes and the shallowness of the implanted zone. XPS<br />
combined with Ar sputtering showed the development of the binding conditions with<br />
depth. In the C1s spectrum, on top of the sample, a thin film of elemental carbon was<br />
fo<strong>und</strong>. After 1 min sputtering, a chemical shift to carbide was detected. With<br />
increasing sputtering time, i.e. depth, the C signal became smaller and vanished,<br />
when the thickness of the implant region was exceeded. The Ti2p signal appeared at<br />
the position of the carbide and shifted to the position of elemental Ti upon sputtering.<br />
This showed that the TiC phase had been formed, in accordance with XRD.<br />
Basically, the same result was fo<strong>und</strong> for Ta in the C1s and Ta4f spectra.<br />
Fig. 4: SIMS<br />
carbon profiles of<br />
Ti samples,<br />
treated for 0.5, 1,<br />
or 2 h, extracted<br />
from the Ta-181<br />
C-12 signals<br />
It can be<br />
concluded that pulse biasing titanium and tantalum in an atmosphere of methane in<br />
an appropriate pressure range leads to formation of a methane plasma from which<br />
ions are accelerated towards the metal targets. Thus, thin gradient films of implanted<br />
carbon are formed. Carbide phase formation has been shown by X-ray diffraction,<br />
indicating the presence of small carbide crystallites, and by the shifted photoelectron<br />
energy states of metal and carbon. Depth profiling by sputter etching in combination<br />
with photoelectron spectroscopy and by secondary ion mass spectrometry showed<br />
thin carbon films on top and gradient carbide films below.<br />
Acknowledgments<br />
The authors would like to thank Deutsche Forschungsgemeinschaft (DFG) for<br />
financial support with the project EN207/19-1.<br />
The fruitful collaboration with Drs. K. Baba and R. Hatada from Industrial Technology<br />
Center of Nagasaki is gratefully acknowledged.<br />
- 91 -
The effect of crystallinity on the thermal instability<br />
of gold nanowires<br />
S. Karim, W. Ensinger<br />
Metallic nanowires are an important component of future nanoscale devices. Among<br />
other important factors, the thermal stability of nanowires is crucial for a reliable<br />
performance of nanowire based devices. Recent experimental and theoretical results<br />
demonstrate that the so-called Rayleigh instability causes the decay of a cylindrical<br />
nanowire into nanospheres in particular at elevated temperatures where atomic<br />
movement by diffusion becomes significant. This pose a serious obstacle to the<br />
sustained reliability of nanowire based devices. For this reason, the Rayleigh<br />
instability of gold nanowires was investigated. The emphasis was on their<br />
crystallographic properties.<br />
Cylindrical gold nanowires with diameters D = 87 nm were prepared by<br />
electrochemical deposition in Polycarbonate templates. The polymer foils of<br />
thickness 30 µm were irradiated normal to the surface at the UNILAC linear<br />
accelerator of GSI, Darmstadt, with uranium ions of energy 2 GeV at a fluence 10 8<br />
ions/cm 2 . Nanoporous templates were then produced by chemically etching the latent<br />
ion tracks. After deposition of a conductive Cu back-electrode, wires were grown<br />
electrochemically in the templates. By systematically varying the deposition<br />
conditions, polycrystalline (PC) and single-crystalline (SC) gold nanowires with wellcontrolled<br />
crystallographic characteristics were obtained. Characterization of wires by<br />
X-ray diffraction (XRD), and transmission electron microscopy (TEM) confirmed that<br />
the SC gold wires contained no grain bo<strong>und</strong>aries and possess a strong 〈110〉<br />
preferred orientation. The PC wires exhibit a bamboo-like structure with the grain<br />
sizes varying between several h<strong>und</strong>red nanometers and few micrometers . Figure 1<br />
shows representative XRD diffractograms of both types of samples.<br />
Intensity (a.u.)<br />
111<br />
Cu<br />
200<br />
Cu<br />
220<br />
311<br />
222<br />
40 60 80 100<br />
2 Theta (deg)<br />
Fig. 1: XRD patterns of (a) single-crystalline and (b) poly-crystalline wires of diameter 87 nm.<br />
Cu reflections are ascribed to the Cu back-electrode.<br />
For the annealing experiments, the Polycarbonate matrix was dissolved. The<br />
samples were introduced in a vacuum furnace (~5×10 -4 Pa), heated up to a<br />
temperature<br />
- 92 -<br />
Cu<br />
(a)<br />
(b)
Ta = 600 o C, held at Ta for a certain annealing time ta, and then cooled down to room<br />
temperature. The samples were examined using a high-resolution scanning electron<br />
microscope (HRSEM). The micrographs in Figure 2 illustrate two sequences of the<br />
morphological transformation of (left) poly- and (right) single-crystalline cylindrical<br />
gold wires caused by the Rayleigh instability. For both type of wires thickness<br />
<strong>und</strong>ulations are first developed along the wire axis leading to fragmentation.<br />
Eventually, the fragments change to spheres. Figures 2a and 2e display the<br />
morphology of the as-prepared poly- and single-crystalline wires prior to annealing.<br />
The polycrystalline wires developed axial perturbations after one hour annealing (Fig.<br />
2b), and the wires fragmented, and decayed partially into nanospheres after ta = 2 h<br />
(Fig. 2c). Finally after ta = 2.5 h, the wires had been transformed completely into<br />
chains of nanospheres (Fig. 2d). The decay of the single-crystalline wires is depicted<br />
in Figures 2e-2h. The single-crystalline wires proved to be significantly more resistant<br />
to Rayleigh instability compared to the polycrystalline ones. First radial perturbations<br />
appeared after ta = 2.5 h, fragmentation was observed after ta = 3 h, and complete<br />
decay into spheres occurred only after an annealing time of ta = 5 h.<br />
200nm RT<br />
(a)<br />
(b)<br />
(c)<br />
(d)<br />
2µm<br />
5µm<br />
2µm<br />
500nm<br />
t a =1h<br />
t a =2h<br />
t a =2.5h<br />
200nm<br />
(e)<br />
200nm<br />
(f)<br />
RT<br />
2µm t a =3.5h<br />
(g)<br />
(h)<br />
5µm<br />
t a =2.5h<br />
t a =5h<br />
Fig. 2: The HRSEM images show the stages of the decay of poly- (left), and single-crystalline<br />
(right) gold nanowires of diameter 87 nm into nanospheres upon annealing for different times<br />
ta at 600 o C.<br />
In summary, the results that the nanowire crystallinity influences the Rayleigh<br />
instability considerably. The single crystalline wires are fo<strong>und</strong> to be more resistant<br />
against the Rayleigh instability than polycrystalline ones of the same thickness.<br />
Acknowledgment:<br />
The authors would like to thank Drs. T.W. Cornelius, R. Neumann (GSI), and A.G.<br />
Balogh (Thin Films) for the fruitful collaboration.<br />
- 93 -
Electrochemical investigation and characterisation<br />
of thin-film porosity<br />
F. Sittner, W. Ensinger<br />
Especially thin film technology has to meet the high demands of the trend of<br />
miniaturization in technical applications. In spite of shrinking dimensions of technical<br />
devices their performance must keep up and even improve. The coatings have to be<br />
homogenous and free from pores to keep their protective properties against wear and<br />
corrosion. Apart from the difficulties of the deposition process itself even the<br />
characterization of the film-porosity is nontrivial, since high resolution imaging<br />
methods like atomic force microscopy or scanning electron microscopy can only<br />
reproduce a small piece of the whole sample’s area. And it is hardly possible to<br />
distinguish between defective spots only located on the surface of the film and pores<br />
that go through the whole coating material giving rise to a corrosive attack on the<br />
substrate. With electrochemical methods small defects in thin insulating films can be<br />
easily detected.<br />
Three different carbon-based coatings were deposited onto polished iron substrates.<br />
Thin fullerene films were deposited via evaporation followed by an ion beam<br />
treatment to crush the fullerene molecules and form a dense amorphous carbon<br />
layer. Another set of samples were coated with poly(p-xylylene), which is a very good<br />
insulating polymer, in a vapour phase deposition process.<br />
The porosity of coated metal samples was analyzed using cyclic voltammetry in a<br />
weakly acidic medium. A sample plot is shown in Fig.1 to illustrate the procedure.<br />
The potential range from -1 to<br />
current density I / Acm<br />
-2<br />
1.0E-01<br />
1.0E-02<br />
1.0E-03<br />
1.0E-04<br />
1.0E-05<br />
1.0E-06<br />
EOC<br />
Icrit.<br />
-1000 -500 0 500 1000<br />
potential E / mV<br />
Fig.1: current density vs. potential plot of an uncoated<br />
iron substrate in an acetate buffer with a pH of 6,75<br />
+1 V was scanned with 10<br />
mV/s and the current density<br />
was recorded. The shape of<br />
the curve gives information<br />
about the corrosion<br />
mechanism and two important<br />
measurands can be extracted<br />
from the current density vs.<br />
potential plot: the maximum<br />
“critical” dissolution current Icrit.<br />
and the open circuit potential<br />
EOCP.<br />
When the potential rises<br />
beyond EOCP the anodic<br />
reaction dominates and the<br />
current density increases<br />
rapidly due to the dissolution of<br />
the iron substrate. The current<br />
density reaches a maximum<br />
which is called the “critical<br />
current density” Icrit. after which the current drops several orders of magnitude. The<br />
drop is due to the sedimentation of corrosion reaction products on the metal surface<br />
– first as a thin porous film, finally as a dense oxide layer, protecting the metal from<br />
further corrosive attack. This state is called “passivation”. The height of Icrit. is<br />
proportional to the size of the uncoated area on the sample surface. This uncoated<br />
- 94 -
area represents the porosity of the protective coating, which now can be easily and<br />
directly measured via the critical current density. EOCP is the open circuit potential,<br />
which varies with different coatings. This is a fact which has attracted only little<br />
attention, so far. Plotting Icrit. against the number of measuring cycles gives an<br />
impression of the long term<br />
current density I crit. / Acm -2<br />
1.0E-01<br />
1.0E-03<br />
1.0E-05<br />
1.0E-07<br />
0 2 4 6 8 10<br />
number of cycles<br />
uncoated iron<br />
fullerene film<br />
plasma-treated<br />
fullerene film<br />
Fig. 2: Icrit. vs. scan cycles for uncoated iron, C60-film<br />
and irradiated C60-film<br />
behaviour of the sample.<br />
This can be seen in Fig. 2<br />
which shows the<br />
development of critical<br />
current densities over a<br />
period of 10 cycles for an<br />
uncoated iron sample, a<br />
fullerene coated sample and<br />
a fullerene coated sample<br />
which has been treated with<br />
an argon ion bombardment.<br />
It can be seen that both<br />
coatings reduce the current<br />
densities significantly about<br />
two orders of magnitude but<br />
the long-term behaviour of<br />
the ion-treated sample is<br />
much better. This is due to<br />
ion bombardment which<br />
formed a thin and dense layer of amorphous carbon in the upper region of the<br />
coating, improving the protection abilities of the film.<br />
current density Icrit. / Acm -2<br />
EOCP / mV<br />
-590<br />
-600<br />
-610<br />
-620<br />
-630<br />
1.5E-04<br />
1.0E-04<br />
5.0E-05<br />
0.0E+00<br />
0 50 100 150 200 250<br />
0 50 100 150 200 250<br />
film thickness / nm<br />
Fig. 3: Development of a) EOCP and b) Icrit. with increasing<br />
film thickness for C60-coated iron samples<br />
- 95 -<br />
a<br />
b<br />
Another set of fullerenecoated<br />
samples with different<br />
film thicknesses was<br />
investigated and the change<br />
of Icrit. and EOCP was<br />
recorded. The results are<br />
shown in Fig. 3. With higher<br />
film thickness, current<br />
densities decrease because<br />
existing pores are closed or<br />
narrowed with increasing film<br />
thickness. The development<br />
of EOCP is quite remarkable<br />
because the potential should<br />
not be affected by the film<br />
thickness since<br />
electrochemical potentials<br />
are not dependent on the<br />
surface area which is<br />
determined by the film<br />
porosity.
This phenomenon can be <strong>und</strong>erstood considering a pore not as a simple cylindrical<br />
hole, characterized by its base area and height. Actually due to the three-dimensional<br />
shape of a small pore it acts as a diffusion barrier for the dissolved ions. Therefore in<br />
a small pore the near surface concentration of dissolved iron will be higher than in a<br />
wider pore through which the dissolved ions can much easier diffuse away from the<br />
surface. But the higher the iron concentration near the surface is, the more is a<br />
further dissolution inhibited and the necessary potential to continue the dissolution is<br />
shifted to higher anodic values. That means if a metal surface is covered with an<br />
insulating coating a high shift of the open circuit potential into anodic direction<br />
indicates very small pores in the coating material.<br />
This correlation is supported by the results from similar measurements of iron<br />
samples that had been coated with different film thicknesses of the insulating polymer<br />
poly(p-xylylene) as can be seen in Fig. 4. Again there is a shift of the open circuit<br />
potential in anodic direction going along with a decrease in porosity at higher film<br />
thicknesses.<br />
current density I / A cm -2<br />
1.0E-02<br />
1.0E-05<br />
1.0E-08<br />
1.0E-11<br />
1.0E-14<br />
-1000 -500 0 500 1000<br />
Fig. 4: Iron samples coated with poly(p-xylylene)<br />
potential E / mV<br />
140 nm<br />
240 nm<br />
560 nm<br />
While the dissolution current density is proportional to the sum of the base areas of<br />
all pores in the coating, the potential shift of the open circuit potential is an indicator<br />
of the average size of the pores. Thus it is possible to distinguish between a few<br />
major flaws in the coating and a widespread micro-porosity which may both show the<br />
same current density.<br />
- 96 -
Self-consistent theory of unipolar charge-carrier injection<br />
in metal/insulator/metal systems<br />
F. Neumann, Y.A. Genenko, C. Melzer, H. von Seggern<br />
Charge carrier injection is an important factor in many electronic devices, especially<br />
in applications with insulators, where virtually all charge carriers have to be injected<br />
from the electrodes. Examples that have been the subject of interest are electronic<br />
devices built with organic semiconductors such as organic light-emitting diodes<br />
(OLEDs). In this work we develop a device model for a metal/insulator/metal system<br />
including the description of charge carrier injection at both metal/insulator interfaces.<br />
This model takes into account the electrostatic potential generated by the charges<br />
injected. The treatment of this issue faces the problem of self consistency, since the<br />
amount of injected charges depends on the height of the energy barriers at the<br />
contacts, while the electrostatic potential generated by this charge modifies the<br />
height of the injection barrier itself. This problem is solved by defining the bo<strong>und</strong>ary<br />
conditions in the electrode materials far away from the contacts, where the influence<br />
of the charge transfer can be ignored. As a result, charge carrier densities and<br />
electric field distributions in the respective media are coupled and depend on the<br />
conditions of the system.<br />
Let us consider an insulator of thickness L sandwiched in between two metal<br />
electrodes. The insulator is supposed to be extended over the space with –L/2 < x <<br />
L/2, whereas the metal electrodes are extended over the semi spaces with x < -L/2<br />
and x > L/2, respectively. The continuity of the electrical displacement and of the<br />
electrochemical potential across the whole system entails, particularly, at the metal/<br />
insulator interface the following bo<strong>und</strong>ary conditions:<br />
± ±<br />
⎡ ∆ eε<br />
l<br />
⎤<br />
TF<br />
( ± L / 2)<br />
= N exp⎢−<br />
± F ( ± L / 2)<br />
⎥<br />
⎣ kT kT ⎦<br />
ns s<br />
where (x)<br />
is the electron density in the insulator,<br />
n s<br />
(1)<br />
N is the effective density of<br />
±<br />
states in the LUMO band (LUMO – lowest unoccupied molecular orbital), ∆ are the<br />
energy barriers between the Fermi-levels of the respective metal electrodes and the<br />
±<br />
bottom of the LUMO-band, T is the temperature, lTF<br />
is the Thomas-Fermi length in<br />
the respective electrodes, ε is the dielectric constant of the insulator, Fs (x)<br />
is the<br />
electric field in the insulator, k and e are the Boltzmann constant and the<br />
elementary charge, respectively. Using the above bo<strong>und</strong>ary conditions the onedimensional<br />
drift-diffusion equation together with the Poisson equation were solved<br />
numerically.<br />
Knowledge about the distribution of the electric field allows for the determination of<br />
the voltage drop V across the whole system for a given current density j and hence<br />
for the calculation of the current-density-voltage (I-V)-characteristics. In Fig. 1 we<br />
present I-V-characteristics of a Ca/organic/Mg system. The I-V-curve calculated for<br />
vanishing injection barriers represents a limitation of the current flow through the<br />
system. The curves at V>1V with ∆ < ∆ ≅ 0.<br />
27 eV coincide with that in the case<br />
−<br />
crit<br />
- 97 -
∆ = 0<br />
−<br />
exhibiting dominance of space charge effects at low barriers. At low voltages<br />
up to 0.1 V all I-V-characteristics show an Ohmic-like j ≈ V dependence. This Ohmic<br />
regime is followed by an exponential increase of the current density with the voltage<br />
up to the built-in voltage VBI = 0.81 eV corresponding to the difference in the workfunctions<br />
of the electrodes. This increase can be attributed to a diffusive charge<br />
carrier transport against the weakened electric field in the organic material. If a high<br />
injection barrier is present, the following current-density increase is also exponential<br />
due to the barrier modification by the electric field at the interface. After all, when the<br />
injection barrier at the injecting electrode falls below ∆ crit the calcium contact can<br />
supply more charge carriers than the bulk of the organic semiconductor can<br />
transport. That is why all the I-V-characteristics end up in the space charge limited<br />
regime.<br />
In the case of high injection barriers the approximate analytic consideration results in<br />
the I-V-characteristic of the system which reads<br />
⎛ eV ⎞<br />
− exp⎜−<br />
⎟ −1<br />
V + V ⎛ ∆ ⎞<br />
BI<br />
eff<br />
exp⎜<br />
⎟ ⎝ kT<br />
j = −eµ<br />
⎠<br />
s N<br />
⎜<br />
−<br />
⎟<br />
, (2)<br />
L ⎝ kT ⎠ ⎛ e(<br />
V + VBI<br />
) ⎞<br />
exp⎜−<br />
⎟ −1<br />
⎝ kT ⎠<br />
where µ s is the mobility of electrons in the insulator and the modified barrier equals<br />
−<br />
−<br />
∆eff<br />
= ∆ + eε lTFFs<br />
( −L<br />
/ 2)<br />
. The agreement of this formula with numerical calculations is<br />
perfect for reverse and forward bias until the space charge effects become dominant.<br />
Fig. 1: I-V-characteristics for an organic layer with thickness L = 100 nm contacted with a<br />
calcium electrode at x = -L/2 and a magnesium electrode at x = L/2. The injection barrier of<br />
the calcium electrode is varied from 0 eV to 0.4 eV with an increment of 0.1 eV.<br />
Finally, the presented model is capable of describing a metal/insulator/metal device<br />
in the injection limited as well as in the space charge limited regime and reveals<br />
conditions of the crossover from one regime to another.<br />
- 98 -
Penetration of an external magnetic field into a multistrip<br />
superconductor/soft-magnet heterostructure<br />
S.V. Yampolskii, Y.A. Genenko, H. Rauh<br />
Heterostructures made up of superconductor (SC) and soft-magnet (SM)<br />
constituents are being studied extensively because of their potential for improving<br />
the performance of SCs. The use of SMs for such structures offers the possibility<br />
to alter the pinning of magnetic vortices in the SC constituents through easy<br />
tuning of the intrinsic magnetic moment of the SM constituents. Furthermore, the<br />
large permeability of SMs allows to improve the critical parameters of SC wires<br />
and strips by shielding the transport current self-induced magnetic field as well as<br />
an externally imposed magnetic field.<br />
As is known from previous work, the critical current of a periodic structure of SC<br />
strips separated by slits is markedly enhanced compared with that of an isolated<br />
SC strip. Here, therefore, we study how filling the slits with SM strips controls the<br />
penetration of magnetic flux into such a heterostructure. To this end, we consider<br />
a periodic array of infinitely extended type-II SC and SM strips of respective<br />
widths wS and M , i.e. period , and thickness d, oriented parallel to<br />
the x-y-plane of a cartesian coordinate system x, y, z and exposed to a transverse<br />
external magnetic field H , as shown in Fig. 1. The SC constituents shall be<br />
devoid of magnetic flux penetrated from their infinitely far ends; the SM<br />
constituents shall be fully described by the relative magnetic permeability<br />
w w=w S+wM<br />
0<br />
µ .<br />
Assuming, in addition, d/w
constituents. The requirement of vanishing of the z-component of the total<br />
magnetic field on the surfaces z= ± d/2 of the SC constituents,<br />
Hz( x ) =H 0 +HS,z( x ) +HM,z( x)<br />
, determines the sheet current distribution in the<br />
Meissner state.<br />
The field of complete penetration of magnetic flux, H p , corresponds to the<br />
transition of the SC constituents into the full critical state; it is fo<strong>und</strong> by setting<br />
H z =0 for x =0 in conjunction with the sheet current distribution<br />
J( x) =-Jcsgn ( x)<br />
which, in turn, is governed by the critical sheet current Jc<br />
.<br />
Fig. 2 displays the calculated dependence of H p on the relative width of the SM<br />
constituents using different values of d and µ .<br />
Fig. 2: Variation of the field of complete penetration of magnetic flux into the SC strips<br />
with the width of the SM constituents, for dw=0.005, µ = 1000 (curve 1), dw=0.01,<br />
µ = 500 (curve 2) and dw=0.01, µ = 1000 (curve 3).<br />
Evidently, due to the presence of even narrow SM strips, H p slightly increases<br />
compared to the respective field p H 0 for the case of a periodic array of isolated SC<br />
strips. A pronounced rise of H p occurs when the width of the SM constituents<br />
grows relative to the width of the SC constituents; behaviour which can be<br />
explained by the fact that, owing to their high permeability, the SM strips attract<br />
part of the external magnetic flux so as to decrease the effective local magnetic<br />
field applied to the SC constituents. This redistribution of the field also occurs in a<br />
periodic array of isolated SM strips, where maximum reduction of the total<br />
magnetic field halfway between the strips, ∆Hz = ( H0d πw) ψ ⎡⎣ ( w -wM) 2 ⎤⎦<br />
with the<br />
digamma function ψ , is attained in the limit µ >> 1.<br />
- 100 -
Structural stability of multiply twinned FePt nanoparticles<br />
Michael Müller and Karsten Albe<br />
The prospect of realizing magnetic nanoparticles that can be applied in high-density<br />
recording or medical applications has driven a large number of research activities in<br />
recent years. Among all candidate materials FePt in the face centered tetragonal L10<br />
phase has attracted much attention. This structure is characterized by alternating Fe<br />
and Pt layers in c-direction and possesses a high uniaxial magneto-crystalline<br />
anisotropy energy (MAE). Because of the high MAE, single crystalline FePt<br />
nanoparticles with a diameter as small as 4 nm can maintain a stable magnetization<br />
direction on a time scale of 10 years. When prepared by gas-phase synthesis<br />
processes, however, no single crystalline FePt particles are obtained. Instead,<br />
multiply twinned shapes in the form of icosahedral or decahedral particles are<br />
predominant. In order to <strong>und</strong>erstand the occurrence of the different structural<br />
motives, a detailed knowledge of the energetics of FePt particles in the various<br />
conformations is necessary. In our work we investigated the structural stability of<br />
FePt nanoparticles by atomic scale and continuum model calculations.<br />
In conjunction with a recently developed interatomic FePt potential, the molecular<br />
statics method has been applied for calculating the fully relaxed energy of FePt<br />
nanoparticles in single crystalline, multiply twinned icosahedral and multiply twinned<br />
decahedral morphologies. The particle energy as a function of size is shown in Fig. 1.<br />
In general, even for the smallest particle sizes studied, the single crystalline shapes<br />
are energetically favored over multiply twinned particles by at least 10 meV/atom.<br />
Also, icosahedral particles exhibit a much higher energy than decahedral ones<br />
because of their higher internal strain and larger twin bo<strong>und</strong>ary areas. The large<br />
energy differences between single crystalline particles on the one hand and<br />
icosahedral and decahedral particles on the other hand, however, can mainly be<br />
attributed to a large twin bo<strong>und</strong>ary energy predicted by the interatomic potential.<br />
Compared to electronic structure calculations, an overestimation of the twin bo<strong>und</strong>ary<br />
energy by a factor of two is possible.<br />
Fig. 1: Average potential energy for FePt nanoparticles in different morphologies. Data points<br />
denote molecular statics calculations, curves are predictions of the continuum model Eq. (1).<br />
- 101 -
In order to assess the influence of the uncertainty of the twin bo<strong>und</strong>ary energy, a<br />
more versatile continuum description of particle energies has been employed. In this<br />
continuum model, the energy of a nanoparticle is approximated by the sum of<br />
volume, surface and twin bo<strong>und</strong>ary energy terms:<br />
E( N)<br />
= N E + W + A ( N)<br />
γ + A ( N)<br />
γ . (1)<br />
( c ) twin twin ∑<br />
hkl hkl<br />
hkl<br />
Here, Ec is the cohesive energy per atom in the bulk phase and W is an average<br />
strain energy per atom, which is zero for single crystalline particles. Atwin and γtwin<br />
denote the twin bo<strong>und</strong>ary area and its energy. Furthermore, Ahkl and γhkl denote the<br />
total area and energies of the hkl facets terminating the particle surface. For<br />
validating the continuum model, its predictions on particle energies when provided<br />
with materials parameters from the interatomic potential are compared with the<br />
atomistic calculations in Fig. 1, where an excellent agreement is fo<strong>und</strong>.<br />
By varying the surface and twin bo<strong>und</strong>ary energies, Eq. (1) has now been used for<br />
evaluating the bo<strong>und</strong>aries between stability domains of decahedral, icosahedral and<br />
single crystalline particles as is shown in Fig. 2.<br />
Fig. 2:.Stability of FePt particles in multiply twinned and single crystalline morphologies as<br />
obtained from Eq. (1) by varying surface and twin bo<strong>und</strong>ary energies. The vertical lines<br />
indicate surface and twin bo<strong>und</strong>ary energies predicted by the interatomic potential used in<br />
Fig. 1 and values estimated on the basis of first principles calculations.<br />
For estimating which set of surface and twin bo<strong>und</strong>ary energies best describes<br />
reality, reference values from first principles calculations have been considered,<br />
which amount to 100 meV/Å 2 and 6.5 meV/Å 2 , respectively. For this set of energies,<br />
Fig. 2 reveals that icosahedral particles are stable up to a diameter of 2.6 nm.<br />
The calculations on particle energies provide a reasonable explanation for the<br />
predominance of icosahedral FePt nanoparticles prepared by inert gas condensation.<br />
Since icosahedral particles are energetically most stable for small sizes below 2.6<br />
nm, it is likely that icosahedral seeds evolve during the nucleation stage of inert gas<br />
condensation. When growing further, kinetic trapping of the particles in the<br />
metastable morphology can then lead to the presence of icosahedral particles even<br />
at larger sizes.<br />
- 102 -
Phase diagram of the Pt-Rh alloy studied with a refined<br />
BOS mixing model<br />
Johan Pohl and Karsten Albe<br />
The Pt-Rh alloy is used in automotive exhaust gas converters as a three-way<br />
catalyst. It has attracted much attention from the scientific community due to its<br />
catalytic applications. But although many studies have been performed on the bulk,<br />
surface and nanoparticulate properties of this alloy, some features still remain<br />
puzzling. An answer to the question whether Pt-Rh phase separates or not could only<br />
recently be given. The widely accepted phase diagram, which shows a miscibility gap<br />
and predicts a critical temperature of 1033K, has been constructed by E. Raub [1] in<br />
1959. He inferred from the experimentally confirmed phase separation in Ir-Pt, Ir-Pd<br />
and Pd-Rh, that Pt-Rh would behave similarly. The critical temperature was<br />
estimated from the difference in the melting points of the two constituents. Although<br />
the phase diagram was reprinted many times since, a miscibility gap has never been<br />
observed in experiment. Recent ab-inito density functional theory (DFT) studies [2], in<br />
contrast, provide strong hints that Pt-Rh does not phase separate, but that various<br />
ordered compo<strong>und</strong>s exist at temperatures below 300K. These studies have been<br />
corroborated by experimental results using diffuse X-ray scattering in order to<br />
measure the amount of short-range order present in the alloy at a temperature as<br />
high as 923K [3]. A corrected phase diagram for Pt-Rh, however, that incorporates<br />
the findings of the last 10 years has not been available so far.<br />
Fig. 1: The phase diagram of Pt-Rh based on our calculations, the 40 and D022 structures are the<br />
stable compo<strong>und</strong>s that are fo<strong>und</strong> at low temperatures, above 240K there are no stable ordered<br />
structures.<br />
- 103 -
In this study, we have therefore determined the Pt-Rh phase diagram by calculating<br />
the grand canonical potential. We applied the thermodynamic integration method<br />
using lattice-based Monte Carlo simulations in the semi-grand canonical ensemble,<br />
where the total number of atoms is fixed, while the difference between the number of<br />
A and B type atoms is allowed to fluctuate for a fixed chemical potential. A<br />
numerically efficient lattice based Hamiltonian was developed by fitting an improved<br />
version of DePristo’s bond-order simulation (BOS) mixing model [4] to a set of input<br />
data obtained from DFT calculations. The calculated the phase diagram of Pt-Rh is<br />
shown in Fig. 1. The phase bo<strong>und</strong>aries are obtained by looking for discontinuities in<br />
the order parameter when integrating down over temperature at constant chemical<br />
potential, and for discontinuities in concentration when integrating over the chemical<br />
Fig. 2: The first eight Warren-Cowley short range order parameters in the vicinity of the<br />
order-disorder transition for Pt-50 at.% Rh. The ordered structure below the transition<br />
temperature is “40”.<br />
potential at constant temperature.<br />
The order-disorder transition of both ordered phases were furthermore analyzed by<br />
calculating the Warren-Cowley short range order parameters (see Fig. 2).<br />
The jump in the order parameters occurs at 239 K if we start with an ordered<br />
configuration and is slightly higher if a random distribution is cooled from high<br />
temperatures. The order-disorder transition was also examined for the stable D022<br />
structure at a concentration of 75 % rhodium. In that case we find a transition<br />
temperature of 210K. Just as for the case of the “40” structure the phase transition is<br />
of first order.<br />
[1] E. Raub, J. Less-Common Met 1, 3 (1959)<br />
[2] Z. Lu, B. Klein and A. Zunger, J. Phase Equilib. 16, 36 (1995)<br />
[3] C. Steiner et al., Phys. Rev. B 71, 104204 (2005)<br />
[4] L.Zhu and A. DePristo, J. Chem. Phys. 102, 5342 (1995)<br />
[5] A. Kohan, P. Tepesch, G. Ceder and C. Wolverton, Comp. Mat. Sci. 9, 389 (1998)<br />
- 104 -
Pt-Ru fuel cell catalysts subjected to H2, CO, N2 and air<br />
atmosphere: An X-ray absorption study<br />
C. Roth, V. Croze, J. Melke 1 , M. Mazurek, F. Scheiba<br />
1 Fraunhofer Institut für Solare Energiesysteme (ISE), Freiburg<br />
Nanoscale metal particles continue to attract interest because of their unique<br />
properties and their importance as catalytically active materials in heterogeneous<br />
catalysis. In particular, binary and multinary systems have been in the focus of recent<br />
research, as the combination of different metals results in fascinating synergistic<br />
effects. A prominent example for bimetallic systems applied in fuel cells is Pt-Ru,<br />
where Ru is added to Pt to enhance its CO tolerance, when used with COcontaminated<br />
fuels [1]. Essentially, two mechanisms have been proposed for the<br />
improved CO tolerance: 1) a bifunctional mechanism [2], where oxygen-containing<br />
species are produced at the Ru sites, which oxidize strongly-adsorbed CO from<br />
neighboured Pt sites, and 2) in a so-called ligand effect with ruthenium modifying the<br />
electronic structure of the Pt by donating electron density, thus either weakening the<br />
Pt-CO bond and thereby allowing CO to be more easily oxidized by OH adsorbed at<br />
the Pt surface, or by enhancing Pt-H2O activation and thereby allowing the reaction<br />
of OH and CO directly on the Pt [3]. Which mechanism dominates in operation, is<br />
largely determined by the samples morphology and the Pt/Ru site distribution, as<br />
revealed in recent literature [4, and references therein].<br />
The structure of different Pt-Ru electrocatalysts has been investigated in dependence<br />
of the prevailing atmosphere using a new reactor/furnace set-up, which enables Xray<br />
absorption spectroscopy (EXAFS) measurements in transmission geometry,<br />
whilst the catalysts are heated up to 100 °C in 5% H2/N2, 5% CO/N2, N2, and air<br />
atmosphere. EXAFS is especially suited for the characterization of nanoscale<br />
supported catalysts, as no long-range order is required and there is no need for ultrahigh<br />
vacuum conditions. In contrast to recent literature describing in-situ experiments<br />
at commercial catalysts in operating fuel cells and reporting mostly metallic Pt and Ru<br />
during operation [3], we specifically decided to exclude the influence of<br />
electrochemical potential. By this, it should be possible to distinguish between effects<br />
brought about by potential and those induced by atmosphere and temperature,<br />
although it has to be borne in mind that the electrolyte and the potential have a huge<br />
effect on the chemistry. It is assumed, that catalyst changes will be exaggerated in<br />
the gas phase, as both the electrolyte and water double layer are supposed to<br />
reduce these effects significantly.<br />
Two different monometallic (Pt/C, Ru/C) and two different bimetallic (Pt-Ru/C alloy,<br />
Pt/Ru/C mixture) electrocatalysts were investigated in different atmospheres at a<br />
temperature of 100 °C in the in-situ XAS reactor. Figure 1 shows the proposed<br />
structural models calculated by conventional EXAFS analysis.<br />
- 105 -
Fig. 1: Proposed models for a) Pt, b) Pt-Ru alloy, and c) Pt/Ru mix samples. Black atoms<br />
indicate Ru(O)x, green atoms indicate Ru, yellow atoms indicate Pt.<br />
The model for the Pt-Ru alloy sample is composed of 80 atoms, 40 Pt and 40 Ru,<br />
with approximately 1/3 of the Ru atoms present as Ru(O)x islands. The sample is not<br />
pictured as well-alloyed, but almost as a fusion of Pt and Ru nanoparticles with a<br />
relatively small Pt-Ru interface. The Pt/Ru mixture, however, is calculated to be an<br />
amalgam of Pt nanoparticles (50 atoms) with a small (3 atoms) surface Ru<br />
substituent, coincident with similar Ru nanoparticles (40 atoms) with a parallel Pt<br />
surface constituency (8 atoms). Obviously, as the coordination numbers predicted by<br />
the EXAFS fit are an average per metal atom, and as the mechanical mixing method<br />
is unlikely to produce identical individual nanoparticles, it is not suggested that this<br />
model indicates the absolute configuration of the sample.<br />
norm. absorption [a.u.]<br />
1.5<br />
1.0<br />
0.5<br />
0.0<br />
11.54 11.56 11.58 11.6 11.62<br />
photon energy [keV]<br />
FT kχ(k)<br />
0,15<br />
0,10<br />
0,05<br />
0,00<br />
-0,05<br />
-0,10<br />
0 1 2 3<br />
R [Å]<br />
Fig. 2: XANES spectra recorded at the Pt L3 edge in air, H2/N2, and CO/N2 for Pt-Ru (left) and<br />
corresponding Fourier transforms in hydrogen (black, solid line), in CO (gray, solid line) and<br />
in air atmosphere (black, dashed line).<br />
In Figure 2, the XANES region of the spectra recorded for Pt-Ru at the Pt L3 edge in<br />
air, 5 % H2/N2, and 5 % CO/N2 is shown. In air as well as in nitrogen atmosphere, all<br />
three catalysts appear significantly oxidized, as indicated by their pronounced whiteline<br />
intensities. This, of course, means that they were already oxidized in their pristine<br />
- 106 -<br />
4
state, and neither air, nor nitrogen atmosphere change this situation. Upon exposure<br />
to either CO or hydrogen, however, the white-line decreases significantly. In the case<br />
of the hydrogen, this decrease indicates reduction of the oxides present in the<br />
pristine sample. In CO atmosphere, the modified white-line is assumed to result from<br />
both a reduction of surface oxides present as well as a strong interaction between<br />
the CO and the catalyst surface (CO poisoning). In contrast to both bimetallic<br />
samples, in the monometallic Pt catalyst the decrease in white-line intensity appears<br />
to be less pronounced due to a stronger degree of CO poisoning.<br />
The oscillatory part of the XAFS data changes significantly as a function of the<br />
atmosphere, which can be seen best in the corresponding Fourier transforms (FT’s)<br />
(Fig. 2, right). The FT’s in CO and hydrogen look very similar and metal-like, whereas<br />
the FT in air displays distinctly different features indicative of an oxide. Fitting of the<br />
data has been performed using the XDAP code, and the respective R and N values<br />
are reported elsewhere [5]. The XANES and EXAFS results support each other nicely<br />
indicating the reduction of platinum oxides by hydrogen, whereas CO adsorbs<br />
strongly at Pt surfaces in all three catalyst systems. Ruthenium oxides become<br />
reduced easily in hydrogen, while the reduction of ruthenium oxides in CO<br />
atmosphere seems to depend on the Pt and Ru surface site distribution.<br />
In summary, alloy formation seems to be advantageous, as it decreases particle<br />
growth and oxidation in the catalysts. Evidence of CO poisoning has been observed<br />
on all Pt surfaces, but most pronouncedly for the pure Pt catalyst. Moreover,<br />
significant differences between Pt-Ru alloy and Pt/Ru mixture have been revealed,<br />
and are due to the different Pt/Ru site distribution. A clear effect of Ru island<br />
morphology on O and CO adsorption, as described in the literature [4], has been<br />
observed: the larger Pt-decorated Ru nanoparticles of the mixture are significantly<br />
more oxidized than the Ru surfaces in the alloy. A significant amount of Pt/Ru<br />
neighbour sites is required, as Pt “catalyzes” the reduction of nearby ruthenium<br />
oxides. Furthermore, Ru-CO bonds are strengthened via the ligand effect also<br />
depending on the Pt/Ru site distribution. The observed differences should also lead<br />
to mechanistic differences in real fuel cell operation.<br />
Financial support of the DFG has been gratefully acknowledged. The authors thank<br />
F. Haass, M. Bron, H. Fuess and P. Claus for providing the in-situ furnace set-up and<br />
E. Welter and the staff at beamline X1, Hasylab, Hamburg, for their kind support.<br />
Literature<br />
1. H. A. Gasteiger, N. M. Markovic, P. N. Ross, Jr., E. J. Cairns, J. Phys. Chem.<br />
98, 1994, 617.<br />
2. T. Yajima, H. Uchida, M. Watanabe, J. Phys. Chem. B 108, 2004, 2654.<br />
3. C. Roth, N. Benker, T. Buhrmester, M. Mazurek, M. Loster, H. Fuess, D. C.<br />
Koningsberger, D. E. Ramaker, J. Am. Chem. Soc. 127, 2005, 14607.<br />
4. F. J. Scott, S. Mukerjee, D. E. Ramaker, submitted to J. Electrochem. Soc.<br />
5. C. Roth, N. Benker, M. Mazurek, F. Scheiba, H. Fuess, Appl. Catalysis A 319<br />
(2007) 81-90.<br />
- 107 -
Synthesis of oxide-polymer nanocomposites via plasma<br />
polymerization<br />
Jens Suffner (1) , Gallus Schechner (2) , Hermann Sieger (1) , Horst Hahn (1),(3)<br />
(1) Joint Research Laboratory Nanomaterials<br />
(2) SusTech GmbH<br />
(3) Institute for Nanotechnology (FZ Karlsruhe)<br />
In the last years, nanoscale materials have gained tremendous interest in science<br />
due to their unique properties, like superparamagnetism, superplasticity, and<br />
quantum confinement.<br />
Nanoscale powders are characterized by a large surface-to-volume ratio leading to<br />
specific surface areas in the range of several h<strong>und</strong>reds of square meters per gram.<br />
Therefore it is obvious, that the particle-matrix interface has a large impact on the<br />
properties of the particles. In this work [1] , the oxide nanoparticles silica and zirconia<br />
have been produced by thermal decomposition in a hot wall reactor followed by a<br />
subsequent coating with a polymer (see figure 1).<br />
Fig. 1: Setup for the in-situ production of polymer coated oxide nanoparticles.<br />
Plasma polymerization is a feasible technique for the production of dense coatings<br />
on particles. Schallehn et al. [2] have been able to produce plasma polymerized<br />
ethylene (ppE) by this technique. Here, we describe the formation of various<br />
polymers on silica and zirconia and study the influence of the monomer on the<br />
resulting surface properties. A large variety of substances can be used as starting<br />
material for the organic coating, what allows tailoring of the interface properties and<br />
adopting the surface properties to the matrix medium by the right choice of monomer,<br />
e.g. siloxanes for silicone matrices. The following monomers could be successfully<br />
coated on the oxide core:<br />
• Hexafluoro-m-xylene (C8H4F6) and hexafluoropropene (C3F6), leading to highly<br />
fluorinated surfaces<br />
• Octamethylcyclotetrasiloxane (C8H24S4O4), leading to a siloxane surface<br />
• Methylmethacrylate (MMA, C5H8O2) and ethyl-2-cyanoacrylate (ECA,<br />
C6H7O2N), leading to an acrylate surface<br />
- 108 -
Figure 2 shows the successful coating of plasma polymerized hexafluoro-m-xylene<br />
on ZrO2. Polymerization through plasma agitation always leads to an amorphous<br />
coating that can be clearly distinguished from the dark and crystalline oxide core. In<br />
all cases, oxide particles can be produced with diameters smaller than 10 nm and<br />
varying coating thickness of 2 - 10 nm.<br />
Fig. 2: Transmission electron micrograph of<br />
an amorphous polymer coating on the zirconia<br />
core (Image by R. Schierholz, Structural<br />
research division).<br />
Transmittance T [a.u.]<br />
3180<br />
ν (N-H)<br />
ν (C-H)<br />
ppECA/<br />
SiO (p)<br />
2<br />
CO<br />
2<br />
ppMMA/<br />
SiO 2<br />
SiO 2<br />
1600<br />
ν<br />
1710<br />
(C=C)<br />
ν (-C=O)<br />
δ (C-H)<br />
880<br />
δ (Si(CH 3 ) 2 )<br />
3000 2000 1000<br />
Wavenumber [cm -1 ]<br />
*<br />
*<br />
*<br />
* SiO 2<br />
*<br />
*<br />
*<br />
664<br />
δ (N-H 2 )<br />
Fig. 3: FT-IR spectra of uncoated silica, silica<br />
coated with plasma polymerized MMA<br />
(ppMMA/SiO2) and silica coated with plasma<br />
polymerized ECA (ppECA/SiO2).<br />
The influence of the coating material on the dispersability was studied in the case of<br />
the acrylate-based coatings ppMMA and ppECA on silica [3] . Powders derived from<br />
methylmethacrylate are characterised by a hydrophobic surface, making it impossible<br />
to disperse them in water. The powders are not wettable. The exchange of a methyl<br />
group to a cyano group (-CN) in the monomer leads to enhanced dispersability in<br />
water. In the plasma, the C≡N bond is split and reassembled with hydrogen in the<br />
coating to form –NH2 groups, as determined by FT-IR spectroscopy (Fig. 3). The<br />
hydrocarbon bands of the coating can be fo<strong>und</strong> in the range of 2875 – 2960 cm -1 .<br />
Vibrations of the methacrylate can be identified aro<strong>und</strong> 1710 cm -1 for the C=O bond<br />
and aro<strong>und</strong> 1600 cm -1 for the double bonded carbon. The vibrations responsible for<br />
δ(N-H2) aro<strong>und</strong> 664 cm -1 and for ν(N-H) aro<strong>und</strong> 3180 cm -1 appear only in the<br />
spectrum measured on particles coated with ECA-derived coatings.<br />
Literatur:<br />
[1] J. Suffner, Diploma thesis, Faculty of <strong>Material</strong>s- and Geo-Sciences (TU<br />
Darmstadt), 2006<br />
[2] M. Schallehn, M. Winterer, T.E. Weidrich, U. Keiderling, H. Hahn, Chem. Vap.<br />
Deposition 2001, 9, 40.<br />
[3] J. Suffner, G. Schechner, H. Sieger, H. Hahn, Chem. Vap. Deposition<br />
(accepted for publication)<br />
- 109 -<br />
*<br />
*<br />
*
Diploma Theses<br />
Böhme, Mario; Herstellung <strong>und</strong> Charakterisierung von β-FeSi2/Si<br />
Kompositwerkstoffen zur photovoltaischen Applikationen; Surface Science;<br />
December 06<br />
Bohn, Tilman; Vergleich zweier Methoden zur Bestimmung lokaler Umformgrade<br />
verzweigter Blechstrukturen; Physical Metallurgy ; February 06<br />
Braun, Dennis; Injektion von Ladungsträgern in organische Halbleiter; <strong>Electronic</strong><br />
<strong>Material</strong> <strong>Properties</strong>; September 06<br />
Depner, Udo; Werkstoffeigenschaften von ultrahochfesten Stählen für den Einsatz in<br />
Strukturbauteilen; Physical Metallurgy ; April 06<br />
Elsen, Alexander; Untersuchungen des Einflusses von Versuchsparametern auf die<br />
ermittelten Werkstoffkennwerte aus dem uniaxialen, quasistatischen Zugversuch;<br />
Physical Metallurgy; October 06<br />
Engert, Andrea; Metal to Ceramic Sealant Joints for Planar Solid Oxide Fuel Cells;<br />
Ceramics Group; December 06<br />
Ettinghausen, Frank; Hochfeste duktile eutektische Ti-Legierungen; Physical<br />
Metallurgy ; March 06<br />
Frommherz, Martin; Charakterisierung von hochtemperaturbeständigen Cu/Al2O3<br />
Verb<strong>und</strong>werkstoffen mit Durchdringungsgefüge; Ceramics Group; October 06<br />
Gaab, Lotta; Bruchzähigkeit von Perlmutt der Abalone; Ceramics Group; April 06<br />
Gassmann, Andrea; Ursache <strong>und</strong> Einfluss der Grenzflächenpassivierung auf die<br />
elektrischen Eigenschaften von organischen Feldtransistoren; <strong>Electronic</strong> <strong>Material</strong><br />
<strong>Properties</strong> ; February 06<br />
Hinterstein, Manuel; The Solution of the (6x5) surface superstructure3D Structural<br />
Determination of C60on Au(110); Structure Research; May 06<br />
Kling, Jens; In-situ elektronenmikroskopische Untersuchung der Domänenstruktur<br />
von Pb(Ti,Zr)O3 unter Polung; Structure Researchructure Research; November 06<br />
König, Markus; Herstellung <strong>und</strong> Charakterisierung eines Kupfer-Aluminiumoxid-<br />
Verb<strong>und</strong>werkstoffs mit Durchdringungsgefüge; Ceramics Group; May 06<br />
Körber, Christoph; Charakterisierung der Halbleiter-Heterogrenzfläche ZnO/GaAs<br />
mittels Photoelektronenspektroskopie; Surface Science; August 06<br />
Kostka, Johannes; Variation der Boranentwicklung in boranatbasierten<br />
Nanokompositen für die Wasserstoffspeicherung; Joint Research Laboratory<br />
Nanomaterialsmaterials ; October 06<br />
Krämer, Urs; Einfluss der Sauerstoff- <strong>und</strong> Schwefelkonzentration auf die optischen<br />
Eigenschaften von europium-dotierten Cäsiumbromid; <strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong>;<br />
March 06<br />
Langbein, Falko; Fließverhalten <strong>und</strong> dessen Berechnung dualer Gefüge der (α + β)-<br />
Titanlegierung Ti-6Al-4V; Physical Metallurgy ; May 06<br />
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Lange, Tobias; Organische CMOS-Technik durch Grenzflächenmodifikation;<br />
<strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong>; October 06<br />
Langer, Jochen; Elektrostatische Dispergierung von Zinkoxid-Pulvern <strong>und</strong><br />
Herstellung von Schichten; Ceramics Group; October 06<br />
Leist, Thorsten ; Spannungsunterstütztes Polen von PZT; Ceramics Group;<br />
October 06<br />
Meidel, Bernd; Herstellung wismut- <strong>und</strong> zinkhaltiger Perowskite; Ceramics Group;<br />
November 06<br />
Molberg, Martin; Lichtinduzierte Streuung in Blei-Lanthan-Zirkonat-Titanat; Ceramics<br />
Group; October 06<br />
Monnoyer, Maxime; Silizium-Farbstoff-Hybridsystemen für die Photovoltaik:<br />
Abscheidung auf p+ dotierten Siliziumfilmen; <strong>Material</strong>s for Renewable Energies;<br />
October 06<br />
Paturaud, Flora; Mikrostruktur <strong>und</strong> mechanische Eigenschaften von Kobalt-Eisen-<br />
Legierungen; Physical Metallurgy ; October 06<br />
Pauly, Simon; Charakterisierung eines duktilen Glas-Matrix-Komposits auf Kupfer-<br />
Zirkonium-Basis; Physical Metallurgy ; May 06<br />
Pavlovic, Goran; Abscheidung piezoelektrischer Na0,5K0,5NbO3-Schichten aus<br />
Schlickern auf Ringelektroden, deren Sinterung <strong>und</strong> Charakterisierung; Ceramics<br />
Group ; March 06<br />
Richter, René; Untersuchungen zum Erstarrungsverhalten von Weichlotlegierungen;<br />
Physical Metallurgy ; May 06<br />
Rudnig, Jan; Untersuchungen <strong>und</strong> Charakterisierung von Al/Al2O3 <strong>und</strong> TiMgN PVD-<br />
Beschichtungen auf der Magnesium-Druckgusslegierung AZ91D im Hinblick auf die<br />
Erhöhung der Verschleißbeständigkeit <strong>und</strong> unter Berücksichtigung des<br />
Korrosionsverhaltens; Physical Metallurgy ; May 06<br />
Sager, Sascha; Herstellung <strong>und</strong> Charakterisierung metallischer Gläser <strong>und</strong><br />
Komposite in den Systemen FeZr <strong>und</strong> AlYNiCo; Physical Metallurgy ; November 06<br />
Schaab, Silke; Nanostrukturierte Beschichtungen aus Kohlestoff-Nanoröhren/TiO2<br />
Kompositen für funktionelle <strong>und</strong> bio-medizinische Anwendungen; Ceramics Group;<br />
July 06<br />
Schidleja, Martin; Der Einfluss von Dielektrika auf die Ambipolarität von Transistoren;<br />
<strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong>; February 06<br />
Schmid, Hanna; Untersuchung des Ladungstransports in organischen Halbleitern<br />
mittels Flugzeitmessungen; <strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong> ; February 06<br />
Schmidt, Hans; Struktur-Eigenschaftsbeziehungen von weißelektroluminesziereden<br />
Polymeren; <strong>Electronic</strong> <strong>Material</strong> <strong>Properties</strong> ; February 06<br />
Siepchen, Bastian; Modelluntersuchungen an der CdS/CdTe Heterogrenzfläche;<br />
Surface Science; March 06<br />
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Sperling, Sebastian; Untersuchungen zur Phasenbildung <strong>und</strong> Stabilität von Al3Mg2;<br />
Physical Metallurgy ; June 06<br />
Straub, Florian; Pulsed Laser Desposition of Self-Assembled Multiferroic BiFeO3-<br />
CoFe2O4 Thin Film Nanostructures; Ceramics Group; October 06<br />
Suffner, Jens; Funktionalisierung von oxidischen Nanopartikeln durch<br />
Plasmapolymerisation; Joint Research Laboratory Nanomaterialsmaterials ; May 06<br />
Zils, Susanne; Entwicklung eines neuen Verfahrens zur Herstellung von Membran-<br />
Elektroden-Einheiten (MEA) über ionomer-gecoatete Katalysatoren; <strong>Material</strong>s for<br />
Renewable Energies; September 06<br />
PhD Theses<br />
Balke, Nina; Ermüdung von Pb(Zr,Ti)O3 für unterschiedliche elektrische<br />
Belastungsformen; Ceramics Group; July 06<br />
Dindorf, Christian; Ermüdung <strong>und</strong> Korrosion nach mechanischer<br />
Oberflächenbehandlung von Leichtmetallen; Physical Metallurgy; April 06<br />
Ensling, David; Photoelektronenspektroskopische Untersuchungen der<br />
elektronischen Struktur dünner Lithiumkobaltoxidschichten; Surface Science;<br />
September 06<br />
Erhart, Paul Harro; Intrinsic Point Defects in Zinc Oxide: Modeling of Structural,<br />
<strong>Electronic</strong>, Thermodynamic and Kinetic <strong>Properties</strong>; <strong>Material</strong>s Modeling; July 06<br />
Klonczynski, Alexander; Herstellung <strong>und</strong> Charakterisierung hochtemperaturstabiler<br />
Si(B)OC Keramiken auf Basis kommerzieller Polysiloxane; Dispersive Solids;<br />
December 06<br />
Knoth, Markus; Zur Realstruktur von Perlglanzpigmenten; Structure Research;<br />
May 06<br />
Krockenberger, Joshiharu; Epitaxial thin film growth and properties of unconventional<br />
oxide superconductors cuprates and cobaltates; Thin Films; December 06<br />
Mazurek, Marian; Impedanzspektroskopie an Anodenkatalysatoren für<br />
Membranbrennstoffzellen; Structure Research; February 06<br />
Säuberlich, Frank; Oberflächen <strong>und</strong> Grenzflächen polykristalliner<br />
kathodenzerstäubter Zinkoxid Dünnschichten; Surface Science; July 06<br />
Vollmar, Emanuel; Strukturelle Phasenübergänge <strong>und</strong> physikalische Eigenschaften<br />
von Zintl-Phasen des NaTl-Strukturtyps; Structure Research; April 06<br />
Weiler, Ulrich; Silizium-Farbstoff-Hybridsysteme für die Photovoltaik - Präparation<br />
<strong>und</strong> Eigenschaften; Surface Science; February 06<br />
Westram, Ilona; Crack Propagation in Pb(Zr, Ti)O3 <strong>und</strong>er Cyclic Electric Loading;<br />
Ceramics Group; July 06<br />
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Mechanical Workshop<br />
The mechanical workshop of the Institute of <strong>Material</strong>s Science is designing,<br />
manufacturing and modifying academic equipment for a broad range of projects. In<br />
the year 2006 the workshop was involved in the following major projects:<br />
• Design and realisation of a new neutron structure powder diffractometer<br />
(SPODI) at the FRM-II, TU Munich, Garching<br />
• UHV-preparation chambers dedicated for MBE, CVD, PVD and<br />
(electro)chemical treatment<br />
• Design and manufacturing of a protection chamber for x-rays with up to<br />
150keV photons<br />
Staff Members<br />
Head<br />
Jochen Korzer<br />
Technical Personnel Frank Bockhard<br />
Ulrich Füllhardt<br />
Volker Klügl<br />
Herry Wedel<br />
<strong>Electronic</strong> Personnel<br />
Michael Weber<br />
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Institute of Applied<br />
Geosiences<br />
Physical Geology and Global<br />
Cycles<br />
In the solar system, Earth is an unique rocky planet with an ocean and an<br />
atmosphere. It is inhabited by bacteria since about 4 billion years and by higher life -<br />
plants and animals - since ca. 600 million years. Organisms, air, water, and rocks are<br />
interconnected in an unending cycle of matter and energy: The Earth System.<br />
The crustal plates of Earth are driven by radioactive heat. This causes creation of<br />
new crust at mid-ocean ridges at rates of several centimetres per year. On the other<br />
side, plate margins collide, become subducted into the mantle again, or fold up vast<br />
mountain ranges like the Alps and the Himalayas, combining rocks of very different<br />
origin. During subduction the basaltic crust is partially melted generating more felsic<br />
magmas which rise to form continental-type plutons and to cause lines of andesitic<br />
volcanoes such as occurring aro<strong>und</strong> the entire Pacific rim. This is called the<br />
endogenic cycle of rocks.<br />
At the same time Earth receives solar radiation which moves air and water in gigantic<br />
cycles aro<strong>und</strong> the planet. Specifically the water cycle causes the denudation of<br />
mountains by mechanical erosion and the leveling of plains by chemical weathering,<br />
the latter aided tremendously by vegetation and their CO2-input to soils. This is called<br />
the exogenic cycle of rocks.<br />
This exogenic cycle is increasingly impacted by mankind. The radiation balance of<br />
the atmosphere has been upset by the emission of carbon dioxide, methane and<br />
other tracegases, Earth is warming. Industrially produced chlorinated hydrocarbons<br />
have risen to the stratosphere, threatening the protective ozone layer. Dust from<br />
traffic, industry and agriculture produce reagents which alter the air chemistry,<br />
causing unprecedented interactions with the marine realm, with vegetation and even<br />
with rocks through acidification, excessive deposition of nutrients and salts. Dry and<br />
wet deposition of anthropogenic (i.e. produced by humans) particles can be<br />
measured world-wide. The population explosion caused the intensification of<br />
agriculture and the alarming loss of topsoil and cuts down on the extent of natural<br />
ecosystems at the same time. The artificial fertilization of soils causes wide-spread<br />
nitrate pollution of shallow gro<strong>und</strong> waters and urbanization alters the water cycle<br />
above and below gro<strong>und</strong>. Local leakage and accidents with chemicals impact soil,<br />
rivers and gro<strong>und</strong> water. Civil engineering, discharges and denudation cause<br />
alterations in almost all rivers world-wide and even coastal seas show increasing<br />
eutrophication, siltation and ecosystem changes in the water column and in the<br />
shallow sediments. The scars left by the mining of minerals and fossil energy are<br />
visible everywhere and cause increasingly problems. Everywhere man has changed<br />
the rate of natural processes. He spreads ever further into the landscape, utilizing<br />
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egions and building in areas which should not be used considering their natural<br />
risks. Therefore damages through natural catastrophes rise traumatically<br />
endangering the world insurance system.<br />
All these processes and changes and their consequences are topics of<br />
Environmental Geology. Understanding global change and accepting the<br />
responsibility of mankind for this planet and its resources for future generations are<br />
prerequisites for the planning of a sustainable development.<br />
The division of Physical Geology and Geological Cycles at the Institute for Applied<br />
Geo-sciences addresses several questions important to environmental geology both<br />
in the present and in the geological past. These can be summarized as follows:<br />
• Paleoclimatology (through the study of varved sediments in the Dead Sea Basin/<br />
Jordan and in Lake Van/Turkey and through the study of speleothems)<br />
• Carbonate geochemistry through time (through the study of alkaline crater lakes,<br />
stromatolites and through modeling of early ocean conditions also for other<br />
planets and moons of the solar system)<br />
• Karst and cave development (through the studies of cave development in<br />
limestone, gypsum and lava and through the study of cave deposits and their<br />
paleontological content and geochemical composition)<br />
• Biogeochemistry of rivers (through the study of the biogeochemistry of rivers such<br />
as the Ebro and Rhine or in Patagonia).<br />
Currently two German research f<strong>und</strong>ed projects are pursued, the reports of which<br />
follow below.<br />
Staff Members<br />
Head<br />
Research<br />
Associates<br />
Technical Personnel<br />
Secretaries (Partial)<br />
Diploma Students<br />
Doctoral Students<br />
Guest Scientists<br />
Prof. Dr. Stephan Kempe<br />
Dr. Jens Hartmann<br />
Dr. Doris Döppes<br />
Ingrid Hirsmüller<br />
Jürgen Krumm<br />
Kirsten Herrmann Monika Schweikhard<br />
Clemens Schmidt<br />
Hanna Wicke<br />
Shahrazad Abu-Ghazleh Nils Jansen<br />
Hans-Peter Hubrich<br />
Prof. Dr. Ahmad Al-Malabeh, Hashemite University, Jordan<br />
Prof. Dr. Kenji Okubo, Okayama University, Japan<br />
Prof. Dr. Josef Kazmierczak, Polnische Akademie der<br />
Wissenschaften<br />
Dr. Hans H. Dürr, Utrecht University, Niederlande<br />
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Research Projects<br />
Geomorphology and Paleoclimatology of Lake Lisan Terraces, Dead Sea, Jordan<br />
(DFG, DAAD)<br />
Publications<br />
Hartmann, J.; Long-term seismotectonic influence on the hydrochemical composition<br />
of a spring located at Koryaksky-Volcano, Kamchatka, deduced from aggregated<br />
earthquake information, International Journal of Earth Sciences 95/4 (2006) 649.<br />
Hartmann, J., Levy, J.; Seismotectonic influence on precursory changes in gro<strong>und</strong><br />
water: Kobe earthquake, Japan, Hydrogeology Journal 14/7 (2006) 1307.<br />
Hartmann, J., Levy, J., Okada, N.; Managing Surface Water Contamination in<br />
Nagoya, Japan: An Integrated Water Basin Management Decision Framework, Water<br />
Resources Management 20/3 (2006) 411.<br />
Kazmierczak, J. & Kempe, S.; Modern analogues of Precambrian stromatolites from<br />
caldera lakes of Niuafo'ou Island, Tonga, Naturwissenschaften 93 (2006) 119.<br />
Kempe, S., Al-Malabeh, A., Al-Shreideh, A., Henschel, H.-V.; Al-Daher Cave<br />
(Bergish), Jordan, the first extensive Jordanian Limestone Cave: A convective<br />
Carlsbad-type cave?, J. Cave and Karst Studies 68/3 (2006) 107.<br />
Jansen, N., Rüde, T.; Faziesabhängigkeit geogener Arsengehalte in Sedimenten der<br />
Niederrheinischen Bucht, Schriftenreihe der Deutschen Gesellschaft für<br />
<strong>Geowissenschaften</strong> SDGG, 43 (2006)<br />
Kempe, S., Kempe, E. & Ketz-Kempe, C.; Die ersten Beschreibungen von Höhlen<br />
durch Frauen: Lady Cravens Besuch der Höhle von Antiparos <strong>und</strong> Johanna<br />
Schopenhauers Schilderung der Peaks Cavern, Natur <strong>und</strong> Mensch, Jahresmitteilung<br />
2005 der Naturhistorischen Gesellschaft Nürnberg e.V. (2006) 19.<br />
Kempe, S. Hubrich, H.-P. & Suckstorff, K.; The story of the 1833 Fercher Survey,<br />
Postojnska jama, continues: An additional document and newly discovered<br />
inscriptions, Acta Carsologica, 35/1 (2006) 131.<br />
Kempe, S., Hubrich, H.-P., Suckstorff, K.; The history of Postojnska jama: The 1748<br />
Joseph Anton Nagel inscriptions in jama near Predjama and Postojnska jama, Acta<br />
Carsologica 35/2 (2006) 7.<br />
Rosendahl, W.; Döppes, D.; Wollnashorn <strong>und</strong> Höhlenhyäne – eiszeitliches Treiben<br />
im Odenwald, hessenArchäölogie 2005 (2006) 23.<br />
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Hydrogeology<br />
Main research interests of the Hydrogeology Group are the fate of organic<br />
contaminants in the subsurface and the development of novel methods to remediate<br />
soil and gro<strong>und</strong>water contaminations. These areas are closely connected as the<br />
application of effective clean-up technologies relies on a detailed <strong>und</strong>erstanding of<br />
the chemical and physical processes in the subsurface.<br />
Group Members<br />
Head: Prof. Dr. Christoph Schüth<br />
Research Associate: Dr. Matthias Piepenbrink<br />
PD Dr. Peter Harres (- 31.05.06)<br />
Technical Personnel: Rainer Brannolte<br />
Secretaries: Angela Brezel<br />
PhD Students: Dipl.-Geol. Meike Beier<br />
Dipl.-Geol. Katy Unger Shayesteh<br />
M.Sc. Flor Toledo Rodriguez<br />
M.Sc. Shamsul Abedin Tarafder<br />
M.Sc. Marina Nazarova<br />
Dipl.-Geol. Guido Vero<br />
Diploma Students: Timo Luchs Nils Michelsen<br />
Research projects<br />
Reversibility of sorption processes in natural and synthetic sorbents (2005-2007)<br />
Diffusion, sorption and reactions in micro- and mesopores (2005-2007)<br />
Implementation of a catalytic treatment system for gro<strong>und</strong>water contaminated with<br />
chlorinated solvents (2005-2006)<br />
Innovative technologies for gro<strong>und</strong>water remediation (2006 -)<br />
Contaminated Datcha Areas in Sibira. Joint project with <strong>Material</strong> Sciences and WAR<br />
(2006).<br />
Management of regional water resources in arid areas – The Wajid aquifer in Saudi<br />
Arabia (2006-2008).<br />
Publications<br />
Russold, S.; Schirmer, M.; Piepenbrink, M.; Schirmer, K. (2006): Modeling the Impact of a<br />
Benzene Source Zone on the Transport Behavior of PAHs in Gro<strong>und</strong>water. Environ. Sci.<br />
Technol. 40 (11), 3565-3571.<br />
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Engineering Geology<br />
Engineering Geology is an applied earth science and a branch of the applied geology<br />
which requires not only multidisciplinary knowledge within the natural sciences<br />
(geology, chemistry, physics, mathematics), but still the engineering sciences. The<br />
common aims of all special subjects contributing to engineering geology are the<br />
investigation, the use, the protection and the remediation of the upper parts of the<br />
earth's crust.<br />
Regarding the worldwide rising importance of renewable energy resources,<br />
Engineering Geology as the sciences which deals direct with the use of geothermal<br />
energy is one of the future's most important applied geosciences. A highly qualified<br />
geothermal lab and experimental hall is planned and will be realized starting in 2007<br />
with first equipment.<br />
Engineering Geology seizes the behaviour of rocks and rock masses according to the<br />
genetic material properties and their earth-history development. It quantifies the<br />
mechanical, physical and hydro mechanical characteristics and the behaviour of soils<br />
and rocks in detail and in the assembly.<br />
Important corresponding special subjects are the soil and rock mechanics, civil<br />
services, fo<strong>und</strong>ation engineering, tunnel and cavity construction, drilling technology,<br />
measurement engineering and applied subjects of hydrology and hydrogeology,<br />
petrology and geochemistry. Engineering geology has thus strong relations with the<br />
geotechnical engineering. It translates the results and knowledge of the geosciences<br />
into the engineering requirements.<br />
Thus, Engineering Geology contributes to the fact that buildings of all kinds can be<br />
build and heated surely and economically. For this purpose the building gro<strong>und</strong> and<br />
other <strong>und</strong>ergro<strong>und</strong> conditions for engineering structures, such as geothermal power<br />
plants, traffic routes e.g. roads, bridges, tunnels as well as other infrastructure such<br />
as caverns, dams, pipelines as well as buildings such as high rise buildings, halls,<br />
wind power stations as well as water-structural plants such as water gates, dams,<br />
dykes, are investigated.<br />
Staff Members<br />
Head<br />
Research Associates<br />
Ph.-D. Students<br />
Technical Personnel<br />
Prof. Dr. Ingo Sass<br />
Dipl.-Ing. Ulrich Burbaum<br />
Dr.-Ing. Thomas Nix<br />
Dipl.-Ing. Marek Naser<br />
Dipl.-Geol. Ulf Gwildis<br />
Gabriela Schubert<br />
Jürgen Krumm<br />
Dipl.-Ing. Arne Buß<br />
Rainer Seehaus<br />
Secretary Kirsten Herrmann Monika Schweikhardt<br />
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Diploma Students<br />
Guest Scientists<br />
and Lecturers<br />
Research Projects<br />
Dipl.-Ing. Anne Minhans<br />
Sebastian Homuth<br />
Claudia Mack<br />
Dipl.-Ing. Matthias Keil<br />
Dr. Burkhard Sanner, European Geothermal Energy Council<br />
Dr. Sven Rumohr, Hessian Agency for Environment and Geology<br />
Interaction of Adhesive Soils, e.g. Clays and Steel Construction for Drilling<br />
Tools e.g. Tunnel Boring Machines.<br />
The adhesive behaviour of cohesive soils e.g. clays may cause an immense<br />
decrease of the advance rate of tunnel boring machines or of a drilling process. The<br />
chemical and physical properties of soils which causes adhesion are in research to<br />
<strong>und</strong>erstand the processes of the jamming of boring tools. An adhesion measuring<br />
device was developed:<br />
Environmental and Geotechnical Behaviour of Polymeric Organic Additives for<br />
Drilling Fluids for Tunnel Boring Machines<br />
To reduce or to eliminate the jamming effects of adhesive soils, a polymeric organic<br />
additive must be applicated to boring fluids. The additive has to be chosen according<br />
to geotechnical criteria, which is affected by geological, hydrogeological and boring<br />
aspects. After use, this boring fluid, mixed with soil, has to be deposited. This is<br />
actually an environmental challenge due to the additive, so that the research in this<br />
filed should bring up a clear <strong>und</strong>erstanding of the elution process.<br />
Investigation on in situ Degradation of Urban Organic Lake Deposits using<br />
Biodegradable Polymers<br />
Organic lake deposits reduce the capacity of water storage reservoirs. To decrease<br />
the capacity reducing volume of organic lake deposits, a polymer can be added to<br />
the lake water. The biochemical effects are not well known yet. Therefore a research<br />
project is in process using a lake in the city of Darmstadt. The research content a<br />
broad field and laboratory test program on the lake deposits as well as the monitoring<br />
of the volume of the lake deposits.<br />
Investigation of River Dikes with Gro<strong>und</strong> Penetrating Radar (GPR)<br />
Flood waters cause financial, material and personal damages. Dikes are the most<br />
important instruments of the flood protection. In Hesse, the first dikes were<br />
constructed in the 15 th century. Since these times the dikes were extended, elevated,<br />
repaired and renovated. Therefore, the dikes are not composed of a homogeneous<br />
material but of various areas with different substantial and geotechnical properties.<br />
To guarantee the stability of the dikes and to design the reconstruction measures,<br />
complete information about the condition and the configuration of the dikes are<br />
necessary. Common practices in dike investigations are so<strong>und</strong>ings and small<br />
drillings. These methods are only providing punctual information on the dike structure<br />
and are invasive. A single gap in the information on the dike structure already means<br />
to take a risk of a dike failure. Geophysical Investigations such as GPR, geoelectric<br />
and seismic measures are providing two-dimensional continuous data. Among these<br />
methods GPR affords the highest resolution and a fast investigation.<br />
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Investigation of a Doline in NE-Hesse with GPR (Cooperation with HLUG).<br />
The HLUG investigated a depression area in Bad Soden Allendorf. The geophysical<br />
investigation concentrated on the expansion of a depression caused by carstification<br />
of Permian (Zechstein) evaporite formation. The area is overbuilt with roads and<br />
single housings. The depression is situated right beneath a street. Different<br />
measures for stabilization and rehabilitation were <strong>und</strong>er discussion. The investigation<br />
with GPR helped to determine the expansion of the endangered area. With this<br />
information, the covering was realized by a reinforced concrete plate.<br />
Determination of the Thermal <strong>Properties</strong> of Soils using Geophysical Methods<br />
especially Gro<strong>und</strong> Penetrating Radar and Geoelectrical Methods<br />
(RELGeotherm)<br />
As the spatial distribution of thermal properties is important for the designing and<br />
monitoring of geothermal installations, a non-invasive, high-resolution geophysical<br />
investigation of the thermal properties is eligible.<br />
The basis for a development of a geophysical investigation of geothermal properties<br />
is the knowledge of the interrelation between geothermal and geophysical properties.<br />
Preliminary investigation started to determine quantitatively the dependence of<br />
geothermal properties on relative dielectric permittivity and electrical conductivity.<br />
Improvement of Infiltration Potential Maps using Gro<strong>und</strong> Penetrating Radar<br />
(GPR)<br />
To generate infiltration potential maps, infiltration tests are performed punctually.<br />
Additionally, the geology and the land use are used to interpolate between these<br />
tests. This information can be extracted from maps and other available geotechnical,<br />
geological and other data and reports. The results of the infiltration tests are often<br />
varying even though the geology and the land use are looking similar. These<br />
variations are generated by small scaled discontinuities of the soils structure and the<br />
composition in the shallow subsurface. To achieve a high resolution spatial<br />
extrapolation of the results from infiltration tests, the structure and composition of the<br />
shallow subsurface must be investigated with a high resolution. Especially the<br />
hydrological properties are important. Therefore, the Infiltration process was<br />
monitored in a natural soil on two test sites, in Darmstadt, TU-Lichtwiese and<br />
Dieburg. The infiltration test was accomplished with a double ring Infiltrometer made<br />
of plastic to minimize the influence on the measurements with GPR.<br />
Determination of Hydraulic <strong>Properties</strong> of sintered HD-PE well Screens<br />
Sintered High Density Polyethylene well screens are hydrophobic. The sintering<br />
process allows control the pore sizes and tortuosity of pores. Additionally HD-PE<br />
filters offer a large open entrance area for the filtrandum (gro<strong>und</strong>water). Preliminary<br />
investigations have been accomplished to start an industry financed project in 2007.<br />
In this project the hydraulic properties will be investigated in laboratory scale and in<br />
the field.<br />
Determination of Geothermal <strong>Properties</strong> of Soils and Rocks<br />
For the dimensioning of Borehole Heat exchangers knowledge of thermal properties<br />
of soil is needed. Presently only few data about these properties are existing.<br />
Therefore, laboratory determination for the soils in the area of Calw (Germany) is<br />
performed and a potential map will be developed.<br />
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Publications<br />
Burbaum, U. (2006): „Tragwerksplanung im konventionellen Tunnelbau“, Lecture in<br />
Frankfurt, Symposium of Fa. Wayss & Freytag Ingenieurbau AG<br />
Buss, A., Jahnke, C. (2006): Hydraulische Modellierung der hydrothermalen<br />
Prozesse im Geothermiefeld Kizildere/Tekkehamam (Türkei) - In: Voigt, H.-J.,<br />
Kaufmann-Knoke, R., Jahnke, C & Herd. R.: Indikatoren im Gr<strong>und</strong>wasser -<br />
Kurzfassung der Vorträge <strong>und</strong> Poster - Tagung der Fachsektion Hydrogeologie in der<br />
DGG - 24.-28. Mai 2006, Cottbus. - Schriftenreihe der Deutschen Gesellschaft für<br />
<strong>Geowissenschaften</strong>, 43: 116; Hannover.<br />
Katzenbach, R. & Sass, I. (2006): Geothermal Summer School 2006.- lecture notes<br />
of the advanced training programme, 380 p. TUD.<br />
Katzenbach, R.; Sass, I.; Clauß, F. & Waberseck, T. (2006): Optimierung von<br />
Erdwärmesonden in Bezug auf Boden- <strong>und</strong> Gr<strong>und</strong>wasserverhältnisse sowie<br />
Verpressmaterial - Qualitätssicherung - Tagungsband des 4. Forum Wärmepumpe,<br />
Solarpraxis AG, Berlin, 26.-27. Oktober 2006<br />
Katzenbach, R.; Sass I.; Clauß F.; Waberseck T. (2006): Geothermische Erk<strong>und</strong>ung<br />
zur Optimierung des Einsatzes erdgekoppelter Wärmepumpen, poster presentation<br />
9. Geothermische Fachtagung, Karlsruhe, 15.-17. November 2006<br />
Naser, M., Sass, I., Hornung, J., Hinderer, M. (2006): Geotechnische Untersuchung<br />
von Deichen mit Georadar, Mitteilungen des Institutes <strong>und</strong> der Versuchsanstalt für<br />
Geotechnik der Technischen Universität Darmstadt, Vorträge zum 13. Darmstädter<br />
Geotechnik-Kolloquium, Hrsg.: Prof- Dr.-Ing. Rolf Katzenbach, Heft 73, 151-160<br />
Sass, I.; Hoppe, A.; Burbaum, U.; Lerch, C., Wawrzyniak, C.: "Bauen im<br />
Thermalwasserdistrikt - Geothermische Erk<strong>und</strong>ung", poster presentation at the 9th<br />
geothermal congress, 15. - 17.11.2006 in Karlsruhe<br />
Sass, I. (2006): Bau <strong>und</strong> Ausbau von Erdwärmesonden, Qualitätssicherung, Vortrag<br />
im Rahmen der Fortbildungsveranstaltung Geothermie der Fachsektion<br />
Hydrogeologie in der Deutschen Gesellschaft für <strong>Geowissenschaften</strong>, am 11.Oktober<br />
2006, Freiburg<br />
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Applied Sedimentology<br />
Sedimentary rocks cover about 75% of the earth’s surface and host the most<br />
important oil and water resources in the world. Sedimentological research and<br />
teaching at the Darmstadt University of Technology focus on applied aspects with<br />
specific emphasis on hydrogeological, engineering and environmental issues.<br />
However, also research related to oil exploration is carried out with a speciality in<br />
palynology and reservoir characterization. To predict gro<strong>und</strong>water movement,<br />
pollutant transport or fo<strong>und</strong>ations of buildings in sedimentary rocks a detailed<br />
knowledge about the hydraulic, geochemical or geotechnical properties is needed<br />
which often vary about several magnitudes. This kind of subsurface heterogeneity<br />
can be related to distinct sedimentological patterns of various depositional systems.<br />
In addition, changes of depositional systems with time can be explained by specific<br />
controlling parameters e.g. changes in sea level, climate, sediment supply and are<br />
nowadays described by the concept of sequence stratigraphy. The research in<br />
applied sedimentology also includes modelling of erosion and sediment transport and<br />
its implication for the management of rivers and reservoirs with the help of GIS.<br />
In 2002, a georadar equipment has been established as a specific method for nearsurface<br />
investigations. First results in the exploration of soils, rocks, and river dikes<br />
could be achieved on various test sites in SW Germany. In the meantime, a centre of<br />
near surface investigation methods has been fo<strong>und</strong>ed by the Universities of Frankfurt<br />
(Applied geophysics), Tuebingen (Applied sedimentology), Gießen (soil sciences),<br />
industrial partners and the TU Darmstadt. Within this Center an instrumental pool is<br />
shared, regular meetings are organised and research projects are initiated. In 2005,<br />
self-constructed facilities for permeability measurements of soil and rock materials in<br />
the laboratory went into operation. In 2006, two new DFG projects have been started<br />
in the sedimentological research group. One is part of a DFG-Forschergruppe<br />
together with the Universities of Frankfurt, Mainz and others. This joint research<br />
group investigates the origin and evolution of extreme rift-flank uplift in East Africa<br />
and its impact on climate, environment and the human evolution (see special<br />
contribution). The other concerns the reconstruction of Miocene plate reorganisation<br />
in western Mexico by interpretation of syntectonic volcaniclastic successions of the<br />
Transmexican Volcanic belt.<br />
Staff Members<br />
Head Prof. Dr. Matthias Hinderer<br />
Research Associates Dr.Jens Hornung Dr. Ulrich Bieg Dr. Sybille Roller<br />
Technical Personnel Erich Wettengl<br />
Secretaries Angela Bretzel<br />
PhD Students Dipl.-Geol.<br />
Inge Neeb<br />
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MSc.<br />
Crisanto Silva<br />
Dipl.-Geol.<br />
Nils Lenhardt
Diploma Students<br />
Research Projects<br />
Dipl.-Geol.<br />
Frank Owenier<br />
Dipl.-Geol.<br />
Katrin Ruckwied<br />
Kristian Bär Matthias Greb<br />
Gunther Stapp<br />
Dipl.-Geol.<br />
Martin Kastowski<br />
Sedimentary geology in general and reservoircharacterisation:<br />
• Linking source and sink in the Ruwenzori Mountains and adjacent rift basins,<br />
Uganda: landscape evolution and the sedimentary record of extreme uplift:<br />
Subproject B3 of DFG Research Group RIFT-LINK “Rift Dynamics, Uplift and<br />
Climate Change: Interdisciplinary Research Linking Asthenosphere,<br />
Lithosphere, Biosphere and Atmosphere” (DFG HI 643/7-1)<br />
• Volcaniclastic successions at the southern margin of the Transmexican<br />
Volcanic Belt as witness of the Miocene plate reorganisation of the western<br />
Mexican coast (DFG HI 643/5-1)<br />
• The geology of raw materials, sequence stratigraphy and palynology in the<br />
“Muschelkalk” of south Germany and Hungary. (Cooperation with University<br />
Halle PhD thesis, DFG GO 761/1-1).<br />
• Reservoir characterisation through outcrop analogue studies in a terminal<br />
alluvial plain of the south German Keuper formation. (Studienarbeit)<br />
• Comparison of Pangaean land locked successions (Upper Triassic;<br />
Germany,Hungary, China): lithofacies make up, reservoir architecture and<br />
depositional controls.<br />
Quarternary sedimentary geology and surface processes:<br />
• Sediment budget and sequence stratigraphy of Pliocene and Quaternary<br />
unconsolidated deposits of the Rheingletscher area, Swiss midlands and the<br />
Upper Rhein Graben (SPP International Continental Drilling Project; DFG HI<br />
643/2-3; 2002-2005)<br />
• Carbon burial in and CO2 evasion from Europe`s lakes and reservoirs (DFG<br />
since August 2004 cooperation with University of Leipzig) – Hi 643/4-1.<br />
• Genesis of alluvial fans and bajadas according to tectonical uplift and climate<br />
change in the central Andes, Peru.<br />
• Architecture, 3-dimensional sediment-mass partitioning and georisk<br />
assessment of a debris flow fan in Switzerland (Diploma thesis).<br />
Hydrogeology, engineering-geology:<br />
• Characterisation of periglacial debris layers with gro<strong>und</strong> penetrating radar in<br />
terms of sedimentology, hydrogeology and soil-science (PhD thesis).<br />
• Reconstruction of Holocene, Roman and modern sediment yield from valley<br />
and reservoir fillings in the Huerva catchment, Ebro basin, Spain (PhD thesis<br />
financed by DAAD).<br />
• Geotechnical characterisation of radar facies patterns in river dykes as a<br />
diagnostic tool for monitoring, quality management and<br />
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econstruction.(Diploma thesis in cooperation with the Regierungspräsidium<br />
Darmstadt).<br />
• Water-rock interaction in the geothermal field Los Humeros, Central Mexico<br />
(Cooperation with Centro de Investigaciones en Energia, Temixco, Mexiko)<br />
(Diploma thesis and PhD thesis).<br />
Publications<br />
Hinderer, M. (2006): Stoffbilanzen in kleinen Einzugsgebieten Baden-Württembergs.<br />
Gr<strong>und</strong>wasser 11: 164-178. Springer-Verlag, Heidelberg.<br />
Voigt, S., Haubold, H., Meng, S., Krause, D., Buchantschenko, J., Ruckwied, K. &<br />
Götz, A.E. (2006): Die Fossil-Lagerstätte Madygen: Ein Beitrag zur Geologie <strong>und</strong><br />
Paläontologie der Madygen-Formation (Mittel- bis Ober-Trias, SW-Kirgisistan,<br />
Zentralasien). - Hallesches Jahrb. Geowiss., Beiheft 22: 85-119, 4 Abb., 1 Tab., 6<br />
Taf.; Halle (Saale).<br />
Pleuger, J., Roller, S., Walter, J.M., Jansen, E. & Froitzheim, N. (2006): Structural<br />
evolution of the contact between two Penninic nappes (Zermatt-Saas zone and<br />
Combin zone, Western Alps) and implications for the exhumation mechanism and<br />
palaeogeography. International Journal of Earth Sciences (Geologische R<strong>und</strong>schau).<br />
http://springerlink.com/content/e2610760582xj262/fulltext.pdf<br />
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Geo-Resources and Geo-Hazards<br />
Land use conflicts intensify in areas aro<strong>und</strong> growing cities where space becomes<br />
increasingly valuable. To favour a sustainable land-use decision making, the<br />
significance of geo-resources (e.g. gro<strong>und</strong>water, sand and gravel, soils) or geohazards<br />
(sinkholes due to subrosion, heavy metals in rocks and soils) must be duly<br />
considered, since geo-resources and geo-hazards are related to geological<br />
structures and are therefore immovable. However, geological structures are usually<br />
very complex in shape which makes them hard to <strong>und</strong>erstand for non-experts. A key<br />
to their integration to decision processes is a comprehensible and transparent 3D<br />
visualisation of the subsurface serving as a base for further two-dimensional thematic<br />
maps which can be integrated in a GIS-based evaluation framework. Within this<br />
framework, other information from economy, ecology or sociology can also be<br />
integrated and evaluated together with geological data using a spatial decision<br />
support system with multi-criteria techniques.<br />
Staff Members<br />
Head Prof. Dr. Andreas Hoppe<br />
Research Associates Dr. Oswald Marinoni<br />
Dipl.-Geoökol. Monika Hofmann<br />
Dipl.-Geol. Stefan Lang<br />
Technical Personnel Dipl.-Kartogr. (FH) Ulrike Simons<br />
Holger Scheibner<br />
Secretaries Kirsten Herrmann<br />
Monika Schweikhard<br />
PhD Students Lic. geogr. Teresa Lamelas Gracia<br />
Students Andreas Deckelmann<br />
Christian Tigler<br />
Research Projects<br />
A focus was set on evaluating and developing methods to support the sustainable<br />
use of geo-resources in and aro<strong>und</strong> metropolitan areas. Our methods include the<br />
enhanced implementation of outranking methods which still face computational limits<br />
and have been refined by Oswald Marinoni (who left in autumn for CSIRO in<br />
Brisbane, Australia), as well as existing methods which have been evaluated in<br />
different case studies and presented during international meetings in Barcelona,<br />
Bruges, Freiberg and Vienna (EGU and Karst Congress). The discussion within the<br />
interdisciplinary “Forschungsschwerpunkt Stadtforschung” (Urban Sciences) at<br />
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Darmstadt University of Technology (TUD) has been continued. Research<br />
concentrated especially on the peripheries of three metropolitan areas:<br />
(i) The Cenozoic terrestrial Hanau-Seligenstadt Basin between the Odenwald and<br />
Spessart Mts with its important geo-potentials for the Rhine-Main Area has been<br />
analysed with respect to its sedimentological and tectonic history and reported in a<br />
dissertation by Stefan Lang. He also presented the results at international meetings<br />
in Freudenstadt and Fukuoka/Japan. A first approach to evaluate the economic<br />
potential of its raw materials supported by GIS-techniques has been performed in<br />
cooperation with the TUD Institute of Economics (diploma thesis of Florian Schmidt,<br />
orientated by Carsten Helm).<br />
(ii) The evaluation of geo-resources and geo-hazards in the Ebro Basin in the<br />
surro<strong>und</strong>ings of Zaragoza, the fast growing capital of the Province of Aragón, Spain,<br />
has been concluded by Teresa Lamelas Gracia. This project has been supported by<br />
the DFG and performed in cooperation with Juan de la Riva from the Universidad de<br />
Zaragoza. The dissertation report provides 68 thematic maps covering a broad<br />
spectrum of regionalized information from geology, geomorphology, soils, water and<br />
raw materials to natural protection areas,gro<strong>und</strong>water vulnerability and subrosionhazard.<br />
The students Andreas Deckelmann and Christian Tigler have mapped an<br />
area southeast of Zaragoza in great detail and proved the close correlation between<br />
human irrigation activities and sudden sinkholes caused by dissolution of <strong>und</strong>erlying<br />
Miocene sulfates.<br />
(iii) The investigations in the northern outskirts of Belo Horizonte (Minas Gerais,<br />
Brazil), a fast growing metropolitan area supporting by now more than 4.5 million<br />
inhabitants has been continued with field work by Monika Hofmann (supported by the<br />
DAAD) in cooperation with Joachim Karfunkel from the Universidade Federal de<br />
Minas Gerais. The study concentrated on erosion phenomena and landscape<br />
changes due to extraction of raw materials. First results were presented at the<br />
national meeting of Brazilian geologists in Aracajú.<br />
A small project investigating the geothermal anomaly in the unsaturated zone within<br />
the spa district of Wiesbaden (supported by the city of Wiesbaden) has been finished<br />
by modelling the possible heat transfer in cooperation with the TUD Institute of<br />
Energy and Powerplant Technology (Johannes Janicka) The investigations on the<br />
eastern master fault of the Upper Rhein Graben <strong>und</strong>er the future Science and<br />
Congress Centre in Darmstadt (supported by Bauverein Darmstadt GmbH) have<br />
continued.<br />
Publications<br />
Hoppe, A. (2006): Wasser im Nahen Osten – ein Kriegsgr<strong>und</strong>? Israel <strong>und</strong> die<br />
Besetzten Gebiete im Kontext geologischer Entwicklung. – Naturwiss. R<strong>und</strong>schau 59<br />
(5): 241-247, Stuttgart.<br />
Hoppe, A., Hofmann, M., Lamelas T.G., Lang, S., Lerch, C. & Marinoni, O. (2006):<br />
Geo-Informationssysteme zur Bewertung von Geo-Potenzialen in der Peripherie von<br />
Ballungsräumen.- Wiss. Mitt. Inst. Geol. TUB Freiberg (Kolloquium „GIS – Geowissenschaftliche<br />
Anwendungen <strong>und</strong> Entwicklungen“), 31: 273-276, Freiberg.<br />
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Hoppe, A., Lang, S., Lerch, C. & Marinoni, O. (2006): Geology and a spatial decision<br />
support system for the surro<strong>und</strong>ings of urban areas: An example from southern<br />
Hesse (Germany). - Z. dt. Ges. Geowiss. 157: 135-146, Stuttgart.<br />
Hoppe, A., Lerch, C. & Lang, S. (2006): Detailed estimates of gro<strong>und</strong>water<br />
vulnerability using three dimensional geological models.- Proc. 5. Europ. Congr. Reg.<br />
Geoscient. Cartogr. Inform. Syst. vol. 1: 35-37, Barcelona (13.-16.6.2006).<br />
Lamelas, T., Marinoni, O., Hoppe, A. & de la Riva, J. (2006): The use of spatial<br />
decision support systems for sand and gravel extraction suitability in the context of a<br />
sustainable development in the surro<strong>und</strong>ings of Zaragoza (Spain).- Proc. 5. Europ.<br />
Congr. Reg. Geoscient. Cartogr. Inform. Syst. vol. 2: 180-183, Barcelona (13.-<br />
16.6.2006).<br />
Lamelas, T., Marinoni, O., Hoppe, A. & de la Riva, J. (2006): Sustainable land-use<br />
management with the help of spatial decision support systems: An example of a<br />
covered karst area in the surro<strong>und</strong>ings of Zaragoza (Spain).- Proc. Int. Conf. “All<br />
about Karst & Water – Decision Making in a Sensitive Environment”, 58-67, Vienna.<br />
Lang, A., Bartholomä, A., Hoppe, A. & Lerch, C. (2006): Einblicke in den Untergr<strong>und</strong><br />
– Flachwasser-Seismik auf dem Main. – Natur <strong>und</strong> Museum 136: 15-19, Frankfurt<br />
a.M.<br />
Marinoni, O. (2006): A discussion of the computational limitations of outranking<br />
methods for land-use suitability assessment. – Int. J. Geogr. Inform. Sci. 20 (1): 69-<br />
87.<br />
Marinoni, O. & Hoppe, A. (2006): Using the Anaylitical Hierarchy Process to support<br />
the sustainable use of geo-resources in metropolitan areas. – J. Syst. Sci. Syst.<br />
Engin. 15 (2): 154-164, Tsinhua.<br />
Nix, T. & Marinoni, O. (2006): Quantitative landslide risk analysis and risk evaluation<br />
for publicly accessible geosites.- Int. Assoc. Engin. Geol. Conf., 12 pp., Nottingham<br />
(6.-10.9.2006).<br />
Striegler, K., Fettel, M. & Hoppe, A. (2006): Bergbauspuren im Odenwald. – Z.<br />
Gesch. Berg- u. Hüttenwesen 12 (2): 4-95, Idar-Oberstein.<br />
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Geomaterials Science<br />
Geomaterial Science (Applied Mineralogy) explores formation/processing conditions,<br />
composition, microstructure and properties of minerals, rocks and synthesized compo<strong>und</strong>s,<br />
where the latter reveal a wide variety of industrial applications. The research focuses on a<br />
comprehensive characterization of the relevant natural and synthetic phases, their<br />
performance <strong>und</strong>er pressure, temperature, deformation and local chemical environment as<br />
well as tailored synthesis experiments for high-tech materials.<br />
The experimental studies focus on the crystal chemistry of minerals and synthetic<br />
compo<strong>und</strong>s, in particular, their crystal structure, phase assemblage, deformation behaviour<br />
and microstructure evolution. The microstructure variation (e.g., during exposure to high<br />
temperature) has an essential effect on thermo-mechanical and electrical properties of<br />
synthetic materials as well as natural minerals, which in turn can be used to reconstruct the<br />
mechanical and thermal history of rock during sub- or obduction processes.<br />
An important facet of the Fachgebiet Geomaterial Science (and Environmental Mineralogy of<br />
Prof. Weinbruch) at the Institute of Applied Geosciences is the application of electron<br />
microscopy techniques for the detailed micro/nano-structural characterization of solids. Here,<br />
transmission electron microscopy (TEM) in combination with spectroscopic analytical<br />
methods such as energy-dispersive X-Ray spectroscopy (EDS), electron energy-loss<br />
spectroscopy (EELS) and energy filtered imaging (GIF) are the main tools employed for<br />
detailed microstructure and defect characterization. High-resolution imaging of local defects<br />
on the atomic scale in addition to chemical analysis with high lateral resolution (down to a<br />
few nanometers) is similarly applied to high-performance ceramics, natural minerals,<br />
meteorites and corrosion phenomena.<br />
Recent research projects involve topics such as fatigue of ferroelectrics, re-calibration of the<br />
clinopyroxene-garnet geothermometer with respect to small variations in the Fe 2+ /Fe 3+ -ratio,<br />
formation temperature of meteorites, defect structure in Bixbyite single crystals and<br />
transparent ceramics based on the spinel structure.<br />
Future research activities will include investigations on interface structures in polycrystals,<br />
high-temperature microstructures and the study of biomaterials based on hydroxylapatite.<br />
Staff Members<br />
Head Prof. Dr. Hans-Joachim Kleebe<br />
Research Associate Dr. Stefan lauterbach<br />
Technical Personnel Bernd Dreieicher<br />
Secretary Betina Schubotz<br />
PhD Students N.N.; Fe-Mg Geothermometer<br />
Jens Kling; SFB-595 (co-supervision with Prof. H. Fueß)<br />
Guest Scientists Prof. Dr. Wolfgang Müller<br />
Dr. Avanish Srivastava, New Delhi, India<br />
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Research Projects<br />
Transmission electron microscopy of ultrahigh pressure metamorphic eclogite from<br />
the Chinese Continental Scientific Drilling project at Donghai (DFG 2006-2008, Prof.<br />
Wolfgang Müller in collaboration with Z. Xu, Institute of Geology, Chinese Academy<br />
of Geological Sciences).<br />
Rapid Exhumation of the Eclogite Zone in the Tauern Window: Deformation Effects in<br />
Eclogite Minerals Close to the Interface Eclogite Zone/Lower Schist Cover (scientific<br />
interaction 2005-2009), Prof. Wolfgang Müller in collaboration with G. Franz, TU<br />
Berlin).<br />
Thermal History of Chromite Layers and Iron-Rich Rims in Chondrules of the Allende<br />
Meteorite (scientific cooperation 2006-2007 with Prof. Stefan Weinbruch and PD Dr.<br />
Peter van Aken).<br />
Planar Defects in Bixbyite, (Mn,Fe)2O3; A Prominent Diffusion Path (scientific<br />
cooperation 2005-2008 with Dr. Alexander Rečnic, Jožef Stefan Institute, Ljubljana,<br />
Slovenia).<br />
The Effect of LiF Addition on the Sintering Mechanism of Spinel, MgAl2O4 (scientific<br />
collaboration 2005-2008 with Prof. Ivar E. Reimanis, Colorado School of Mines,<br />
Golden, CO, USA).<br />
Microstructure Characterization of Boron Suboxide, B6O (scientific interaction 2006-<br />
2008 with Prof. Jack Sigalas, School of Chemical and Metallurgical Engineering,<br />
University of the Witwatersrand, Johannesburg, Gauteng, South Africa).<br />
Temperature and Pressure Dependence of the Fe 2+ /Fe 3+ -Ratio in Omphacite for Re-<br />
Calibration of the Fe-Mg Geothermometer (DFG 2006-2008).<br />
Deformation Experiments on Omphacite at Pressure and Temperature Conditions of<br />
High Pressure Metamorphism (Prof. Wolfgang Müller, 2005-2008, in collaboration<br />
with N. Walte, N. Miyajima, D. Frost, Bavarian Geoinstitute, Bayreuth).<br />
Microstructures of Eclogite Minerals from the Ultrahigh Pressure Metamorphic Unit at<br />
Lago di Cignana, Western Alps, Italy (Prof. Wolfgang Müller, 2005-2008, in<br />
collaboration with R. Compagnoni, Torino, Italy).<br />
Publications<br />
Ayers, R.; Nielsen-Preiss, S.; Ferguson, V.; Gotolli, G.; Moore, J.J.; Kleebe, H.-J.;<br />
Osteoblast-like cell mineralization induced by multiphasic calcium phosphate<br />
ceramic, Mater. Sci. Eng., C 26 (2006) 1333.<br />
Gregori, G.; Kleebe, H.-J.; Mayr, H.; Ziegler, G.; EELS characterization of β-tricalcium<br />
phosphate and hyrdroxyapatite, J. Eur. Ceram. Soc., [8] (2006) 26, 1473.<br />
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Gregori, G.; Kleebe H.-J.; Sorarù, G.D.; Energy-filtered tem study of Ostwald ripening<br />
of Si nanocrystals in SiCO glasses, J. Am. Ceram. Soc., 89 [5] (2006) 1699.<br />
Gregori, G.; Kleebe, H.-J.; Blum, Y.D.; Babonneau, F.; Evolution of C-rich SiOC<br />
ceramics, part-II. Characterization by high lateral resolution techniques: electron<br />
energy-loss spectroscopy, high-resolution TEM and energy-filtered TEM, Int. J. Mat.<br />
Res., 97 [6] (2006), 710.<br />
Guo, L.; Singh, R.N.; Kleebe, H.-J.; Growth of boron-rich nanowires by chemical<br />
vapor deposition (CVD), J. Nanomat., 1 [58237] (2006) 1.<br />
Kleebe, H.-J.; Gregori, G.; Babonneau, F.; Blum, Y.D.; MacQueen, D.B.; Masse, S.;<br />
Evolution of C-rich SiOC ceramics, part-I. Characterization by integral spectroscopic<br />
techniques: solid-state NMR and Raman spectroscopy, Int. J. Mat. Res., 97 [6]<br />
(2006), 699.<br />
Lehner, W.; Kleebe, H.-J.; Ziegler, G.; Variation of sintering parameters at an early<br />
stage of densification affecting β-Si3N4 microstructure, J. Eur. Ceram. Soc., 26 [2]<br />
(2006) 201.<br />
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Technical Petrology<br />
with emphasis in Low Temperature Petrology<br />
The scientific and educational field of this 35 years young branch within the applied<br />
geosciences is based on indispensable knowledge in magmatic, metamorphic<br />
(greenschist facies to ultra-metamorphism) low-temperature (studies in diagenesis<br />
and sub-greenschist facies metamorphism) and hydrothermal petrology but also in<br />
geothermal geology and sediment petrography. On these f<strong>und</strong>amentals it is possible<br />
to evaluate the mechanical, chemical and physical properties of rocks and the<br />
determination for their technical use in engineering geology, in environmental<br />
sciences, in geo-material and thermal-energy sciences. The determination of the<br />
genetic history and evolution of rocks through time and space gives, e.g., basic<br />
information on the study of rock and ore deposits for prospection and exploitation<br />
interests. To <strong>und</strong>erstand mineralization, re-crystallisation and petrogenesis of rocks<br />
an important effort is focussed on tectono-thermal research, tectonophysics and<br />
structural geology (from the kilometre to nanometre scale). Furthermore, many<br />
natural processes are catalytically controlled by deformation. A better <strong>und</strong>erstanding<br />
of these processes can be recorded from deformation versus crystallisation and<br />
deformation versus metamorphism/ heating studies in the field and by experimental<br />
simulations. Therefore technical petrology is strongly field-oriented and linked to<br />
mineralogy, structural geology and also to geochemistry. Technical petrology in our<br />
department will be centred on low-temperature petrology with strong relations to<br />
applied mineralogy (geomaterial science), applied sedimentology and geothermal<br />
science, three other fields of principal interest at the TU Darmstadt.<br />
Low Temperature Petrology covers a broad field of studies: - on diagenesis with<br />
application in hydrocarbon, hydrothermal and geothermal exploration, - on clay and<br />
carbonaceous materials related with applied organic and clay petrology studies, - on<br />
maceral analysis of coals, - on sorption properties of carbonaceous and clay<br />
materials, - on the determination of graphitisation nano- and microstructures<br />
(refractory quality), - on the improvement of forward numerical geothermal, and<br />
maturity, and basin-analysis models (studies on hydrocarbon and fluid migration) - or<br />
on the synthesis of graphite structures and organic matter maturity related to<br />
technical aspects, - on recognizing of soot and carbon black in filtering installations or<br />
the thermal resistance of organic particles among other applications. It is important to<br />
<strong>und</strong>erstand the chemical and physical parameters of natural systems to be able to<br />
recognize the differences caused by anthropogenic changes.<br />
In the low-temperature range, neoformation of mesoscopic and macroscopic phases<br />
is very rare and the minerals to be studied have a very small grain-size. Also stable<br />
thermodynamic conditions are scarce and metastable phases and chemical<br />
disequilibria conditions are very common. Therefore a broad analytical spectrum<br />
must be applied. In the FG Technical Petrology, general microscopy (MPV coal<br />
reflection microscopy, fluorescence microscopy, transmitted light microscopy in the<br />
Joint Research Microscopy Laboratory, installed in 2004 and supported by the<br />
Mineralogisch Petrographisches Institut Basel, CH) and basically XRD powder and<br />
texture studies (Clay and XRD Laboratory, installed in 2005) can be combined with<br />
ICP-AES, TOC, AAS, AOX and gas chromatography (GC-ECD, GC-MS) in the<br />
Organic Geo-chemical Laboratory (recently installed with thankful help by the<br />
- 131 -
Hessische Industriemüll GmbH). Due to the small size, also fluid inclusion studies,<br />
DTA, TGA, AEM, TEM, HRTEM, Raman spectroscopy, EELS and XAS give<br />
important hints to low temperature petrologic researches (in collaboration with<br />
research groups of the GEO-initiative Rhein-Main – Darmstadt, Mainz, Frankfurt).<br />
The main research interests of the study group of R. Ferreiro Mählmann (head of the<br />
group since August 2002) are concentrated in the petrological and petrographical<br />
study of tectono-metamorphic orogenic terrains (Alps, Vosges, Carpathians, Andes,<br />
New Caledonia). The major aim is to discriminate specifically between pre-, syn- and<br />
post-kinematic metamorphic events to get a better <strong>und</strong>erstanding of the orogenic<br />
processes that were active during subduction, collision, stacking and exhumation in<br />
several parts of mountain belts. More specifically research is concentrated on<br />
diagenesis and low-temperature metamorphism, dealing primarily with pelites and<br />
rocks rich in organic matter. Here the principal interest is focussed on the study of<br />
vitrinite, bituminite and secondary macerals, important constituents of coals and the<br />
main source for oil and gas formation and economic reservoirs. In low-grade<br />
metamorphic studies reaction-disequilibrium is a frequent factor and is documented<br />
through the irregularity of the alteration processes of mineral and organic matter<br />
reactions. The research is concentrated on the application of field-petrology and<br />
mineralogical laboratory methods to problems related to equilibrium and<br />
disequilibrium conditions.<br />
R. Le Bayon (assistant since December 2004) focuses his research on the<br />
metamorphic petrology concerning silicate bearing-rocks and on organic matter<br />
maturity and graphitization. One of the aims of metamorphic petrology is to determine<br />
the pressure-temperature history of natural rocks, and thus to aid <strong>und</strong>erstanding of<br />
orogenic processes. Magnesian metamorphic rocks with metapelitic mineral<br />
assemblage and composition are of great interest in metamorphic petrology for there<br />
ability to constrain P-T conditions in structural units where metamorphism is not<br />
mesoscopically and macroscopically visible. The principal goal of the study<br />
(associated with C. de Capitani – University of Basel, CH) is to improve<br />
<strong>und</strong>erstanding of the phase relationships in magnesian metapelites with bulk<br />
compositions mostly comprised by the system K2O – FeO – MgO – Al2O3 – SiO2 –<br />
H2O (KFMASH) as a function of pressure, temperature, water activity and bulk-rock<br />
composition, and thus to constrain and interpret large-scale geodynamic evolutions.<br />
Another aim of R. Le Bayon (associated with C.J. Hetherington – University of<br />
Boston, USA) concerning the Si-bearing metamorphic rock was to determine the<br />
pressure-temperature evolution recorded by chemically zoned crystal. Chemical<br />
zoning of prograde metamorphic minerals is commonly attributed to net transfer<br />
reactions, intra-crystalline diffusion or the growth of compositionally differing zones of<br />
the same phase during consecutive geological events. The study is devoted to<br />
<strong>und</strong>erstand complex chemical zonation recorded in garnet grains. For a given bulk<br />
rock chemistry, equilibrium phase diagrams are calculated over a specified P-T range<br />
using thermodynamic software. Metamorphic minerals of a facies critical paragenesis<br />
are identified and their isopleths calculated to model the variation in composition of<br />
each phase in response to variations in pressure and temperature. The modelled<br />
chemical changes are compared with the observed chemical zoning and the Alpine<br />
metamorphic history of the gneiss and its garnet grains is reconstructed. The<br />
modelling of the prograde mineral reactions using a bulk rock composition, combined<br />
- 132 -
with observed chemical zoning in metamorphic minerals, is a valuable method for<br />
constraining the prograde P-T path when standard methods are inapplicable.<br />
To <strong>und</strong>erstand metamorphic mechanisms and to model kinetic evolution of the<br />
maturation of organic matter, R. Le Bayon (associated with G. Brey – University of<br />
Frankfurt am Main, D; L. Nasdala – University of Vienna, A; W.G. Ernst – University<br />
of Stanford, USA) is carrying pressure-temperature-time experiments at the<br />
mineralogical institute of the University of Frankfurt am Main. This modelling will<br />
serve as a tool to better <strong>und</strong>erstand and constrain the pressure-temperature-time<br />
evolution of carbonaceous-bearing metamorphic rocks.<br />
The studies of H. Hofmann (assistant since August 2004) are based in the research<br />
field of applied clay mineralogy, e.g. geochemical processes related to the formation<br />
of bentonites by the low- grade alteration of volcanic ashes and tuffs. Bentonites,<br />
namely the swelling smectites, are most important to a large number of industrial and<br />
technical applications due to their special physico-chemical properties like sorption<br />
capacity for water, cations and organic complexes, as well as high swelling- and<br />
sealing capacity. Possible technical and geotechnical applications related to these<br />
properties are located in the pharmaceutical – and oil industry, and since a couple of<br />
years in the secure disposal of radioactive waste. Each of these applications requires<br />
different material properties. Despite the fact that most of the properties of smectites<br />
are quite well known physically and chemically, it is not yet clear where they originate<br />
from and how fast material properties can change if the environmental conditions<br />
change. To be able to predict if and how the material will change <strong>und</strong>er extreme<br />
conditions like they are present in a nuclear waste disposal site, it is essential to<br />
know how fast the material can adapt to new environmental conditions.<br />
Bentonites are formed by alteration of volcanic ashes and tuffs, partly millions of<br />
years ago. However, it is not well known, when <strong>und</strong>er which conditions the alteration<br />
process initiated, and how much time is required to form the swelling clays. It is<br />
attempted to determine the kinetics of the reaction progress and the controlling<br />
factors of physico-chemical property changes responding to different environmental<br />
conditions.<br />
The main projects of D. Scheuvens, collaborating with M. Hinderer (FG Applied<br />
Sedimentology) and E. Stein in the Odenwald mountains is based on a rock-registry<br />
survey jointly with the IFS (Institut für Gesteinskonservierung) and the UNESCO<br />
Geopark Bergstraße-Odenwald centre. E. Stein also investigates the interplay of<br />
plutonism, deformation and metamorphism in the eastern part of the `zone axiale´ of<br />
the Montagne Noire (southern France), a classical geological region to study the<br />
burial and exhumation of rocks.<br />
Staff Members<br />
Head Prof. Dr. Rafael Ferreiro Mählmann<br />
Research associates Dr. Ronan Le Bayon, PD Dr. Eckardt Stein<br />
Dr. Heiko Hofmann, Dr. Dirk Scheuvens<br />
- 133 -
Technical Personnel Josef Kolb, Dipl.-Ing. Zahra Neumann<br />
Secretary Natali Vakalopoulos<br />
Research Projects<br />
Experimental kinetic study of organic matter maturation: an appraisal of<br />
pressure, temperature and time effects on reflectance properties of vitrinite. -<br />
(DFG, Cooperation with University of Frankfurt a. M., D; University of Vienna, A<br />
and Stanford University, USA).<br />
Geochronology and tectono-thermal history of the Penninic-Austroalpine bo<strong>und</strong>ary<br />
(Arosa Zone) in Eastern Switzerland; a multi-methodical comparison of methods. -<br />
(SNF, Willkomm Fond, cooperation with University of Bern, CH and Departement für<br />
Zivilschutz, Bern, CH).<br />
Deformation, fluid flow and mineral reactions along the Glarus overthrust and along<br />
the extensional Turba Mylonite Zone, eastern Swiss Alps, Switzerland. Effects of<br />
tectonic shear strain on phyllosilicates and organic matter. - (SNF, OTKA Hungary,<br />
August Collin Fond cooperation with University of Basel, CH; University of Genève,<br />
CH; University of Budapest, HU; Johns Hopkins University Baltimore, USA).<br />
Bituminite parameters to determine thermal metamorphism - field data and<br />
experimental studies. - (cooperation with University of Chile, Santiago de Chile, CL;<br />
Institutul Geologic al Romaniei, Bucharest, RO; University Complutense, Madrid, E;<br />
Stanford University, USA; University of Gießen, D; Peking University, China and ETH<br />
Zürich, CH).<br />
Effect of contact metamorphism on very low-grade parameters: a natural laboratory<br />
study in the Vosges (France) - (Cooperation with University of Frankfurt a. M., D).<br />
Publications<br />
Potel, S.; Ferreiro Mählmann, R.; Stern, W.B.; Mullis, J.; Frey, M.; Very low-grade<br />
metamorphic evolution of pelitic rocks <strong>und</strong>er high-pressure/low-temperature<br />
conditions, NW New Caledonia (SW Pacific), Journal of Petrology, 47/5 (2006) 991-<br />
1015.<br />
Le Bayon, R.; De Capitani, C.; Frey, M.; Modelling phase-assemblage diagrams for<br />
magnesian metapelites in the system K2O – FeO – MgO – Al2O3 – SiO2 – H2O:<br />
geodynamic consequences for the Monte Rosa nappe, Western Alps, Contributions<br />
to Mineralogy and Petrology, 151 (2006) 395-412.<br />
- 134 -
Environmental Mineralogy<br />
Environmental mineralogy focuses its research on the characterization of individual<br />
aerosol particles by electron beam techniques (high-resolution scanning electron<br />
micro-scopy, transmission electron microscopy, environmental scanning electron<br />
microscopy).<br />
We study individual aerosol particles in order to derive the physical and chemical<br />
properties (e.g. complex refractive index, deliquescence behavior) of the atmospheric<br />
aerosol. These data are of great importance for modeling the global radiation balance<br />
and its change due to human activities.<br />
We are also interested in studying the particulate matter exposure at working places<br />
and in urban environments. As aerosol particles may have adverse effects on human<br />
health, the knowledge of the particle size distribution and the chemical and<br />
mineralogical composition of the particles is of prime importance in order to derive<br />
the exact mechanisms of the health effects.<br />
Our research is carried out in cooperation with the following national and international<br />
partners: Max Planck Institute for Chemistry (Department of Biogeochemistry) in<br />
Mainz, Institute for Atmospheric Physics (University of Mainz), Forschungszentrum<br />
Karlsruhe (Institut für Meteorologie <strong>und</strong> Klimaforschung), Institute for Tropospheric<br />
Research in Leipzig, Paul Scherrer Institut (Laboratory of Atmospheric Chemistry) in<br />
Villigen (Switzerland), National Institute of Occupational Health in Oslo (Norway), and<br />
McDonnell Center for the Space Sciences in St. Louis (USA).<br />
Other fields of research include kinetics of mineral reactions and cosmochemistry.<br />
Staff Members<br />
Head<br />
Prof. Dr. Stephan Weinbruch<br />
Research Associates Dr. Nathalie Benker<br />
Dr. Martin Ebert<br />
Dr. Konrad Kandler<br />
Dipl.-Met. Dörthe Müller-Ebert<br />
Dr. Annette Worringen<br />
Dr. Frank Zimmermann<br />
Technical Personnel<br />
Secretary<br />
PhD Students<br />
Thomas Dirsch<br />
Astrid Zilz<br />
Dipl.-Min. Marion Inerle-Hof<br />
Guest Scientist Dr. Marie Choël (University of<br />
Wimereux, France<br />
- 135 -
Research Projects<br />
Environmental scanning electron microscopical studies of ice-forming nuclei (SFB<br />
641; “Die troposphärische Eisphase” (2004-2007).<br />
Electron microscopy of Saharan mineral dust (DFG Forschergruppe SAMUM) (2004-<br />
2010).<br />
Source apportionment of rural and urban aerosols.<br />
Characterization of working place aerosols (National Institute of Occupational Health,<br />
Oslo, Norway)<br />
Environmental scanning electron microscopical studies of the hygroscopic behaviour<br />
of individual aerosol particles.<br />
Publications 2006<br />
Ebert, Martin; Der Staub in unserer Atmosphäre, in: Staub, Spiegel der Umwelt, J.<br />
Söntgen <strong>und</strong> K. Völzke, Ed. Oekom Verlag (2006) 83-96.<br />
Mazurek, M.; Benker, N.; Roth, C.; Buhrmester, Th.; Fuess, H.; Electrochemical<br />
Impedance and X-ray absorption spectroscopy (EXAFS) as in-situ methods to study<br />
the PEMFC anode, Fuel Cells 6 (1) (2006) 16-20.<br />
Benker, N.; Roth, C.; Mazurek, M.; Fuess, H.; Synthesis and characterisation of<br />
ternary Pt/Ru/Mo catalysts for the anode of the PEM fuel cell, J. New Mat.<br />
Electrochem. Sys. 9, (2006) 121-126.<br />
Mazurek, M.; Benker, N.; Roth, C.; Fuess, H.; Structural and electrochemical<br />
investigation of binary mixtures of carbon-supported Pt and Ru catalysts for PEM fuel<br />
cells, Fuel Cells 6 (2006) 208-213.<br />
Thomassen Y.; Koch W.; Dunkhorst W.; Ellingsen D.G.; Skaugset N.P.; Jordbekken<br />
L.; Drabløs P.A.; and Weinbruch S.; Ultrafine particles at workplaces of a primary<br />
aluminium smelter, J. of Environmental Monitoring, 8, (2006)127-133.<br />
Weinbruch S.; Styrsa V.; and Dirsch T.; The size distribution of exsolution lamellae in<br />
iron-free clinopyroxene, American Mineralogist, 91, (2006) 551-559.<br />
Zimmermann F.; Matschullat J.; Brüggemann E.; Plessow K.; Wienhaus O.;<br />
Temporal and elevation-related variability in precipitation chemistry from 1993 to<br />
2002, eastern Erzgebirge, Germany, Water, Air, and Soil Pollution 170 (2006), 123-<br />
141.<br />
Zimmermann F.; Plessow K.; Queck R.; Bernhofer C.; Matschullat, J.; Atmospheric<br />
N- and S-fluxes to a spruce forest – Comparison of inferential modelling and the<br />
throughfall method, Atmospheric Environment 40 (2006), 4782-4796.<br />
- 136 -
Reports of Research Activities<br />
The terraces of Lake Lisan: a continuous record of the<br />
climatic changes during the Late Pleistocene.<br />
Shahrazad Abu Ghazleh and Stephan Kempe<br />
Lake Lisan filled the Dead Sea depression between 63-15 Ka B.P. (Kaufmann et al.,<br />
1992; Shramm et al., 2000). The regression of the Lake Lisan to the current Dead<br />
Sea led to a sequence of shore terraces (Fig. 1) that offer excellent possibilities to<br />
reconstruct the lake history and correlate it with climatic changes during the Late<br />
Pleistocene.<br />
Five cross sections of these terraces were examined by differential GPS altimetry.<br />
The terraces were fo<strong>und</strong> to be horizontal, <strong>und</strong>isturbed and characterized by a gentle<br />
foreshore with a slope of 3.5-12 degrees and a steep backshore with slope of 12-27<br />
degrees. The terraces range in elevation between -370 and -117 m (i.e. below sea<br />
level) that represent the levels of the lake in Late Pleistocene and suggest (a) a much<br />
higher stand of Lake Lisan at -117 m (Fig. 2) than the previous known level of -150 m<br />
(Bowmann and Gross, 1992); (b) a sharp but gradual drop of the lake from a very<br />
high level at about -117 m to a very low level at about -370 m; (c) substantial climatic<br />
changes in the Jordan valley during the Late Pleistocene from initially very wet<br />
conditions to extremely dry conditions.<br />
On these terraces - between -370 and -148 m - in-situ precipitated, calcareous<br />
stromatolites are preserved. Some form large, laminated, massive, head-like blocks<br />
others are finely laminated crusts. Since stromatolites are formed on algal mats, they<br />
are indicative of relatively shallow water conditions. Calcareous crusts less clearly<br />
laminated and more clotty in structure appear between -148 and -117 m. This may<br />
indicate (a) that the lake chemistry at high lake stands was less alkaline due to high<br />
fresh water input; or (b) that the wave action was stronger at the steep eastern shore<br />
of Lake Lisan, formed by Cambrian sandstones and dolomites. Dating stromatolites<br />
with 14C and U/Th and of the terraces sediments by OSL is in progress.<br />
- 137 -
Fig. 1: Aerial photo of the Lake Lisan terraces in Numirah area/ Eastern Coast of the Dead Sea.<br />
Fig. 2: The high terraces of Lake Lisan at -117 m in the Eastern Coast of the Dead Sea.<br />
- 138 -
High riverine fluxes of dissolved silica from Japan – the<br />
influence of lithology<br />
J. Hartmann 1 , N. Jansen 1 , H.H. Dürr 2 , S. Kempe 1<br />
1 Institute for Applied Geosciences, Darmstadt University of Technology, Germany,<br />
2 Department of Physical Geography, Utrecht University, Netherlands<br />
Silicate weathering is a significant sink for atmospheric CO2 and thus relevant for<br />
climatic processes. Weathering rates are controlled by climate, vegetation, land use,<br />
relief and particularly lithology. It was hypothesized that volcanic islands and back arc<br />
basins are hyperactive with respect to silicate weathering. This is due to the high<br />
content of easily weatherable Ca + Mg-silicate minerals ab<strong>und</strong>ant in volcanic rocks.<br />
This work analyzes the influence of lithology on specific silica fluxes. Data from 262<br />
river chemistry monitoring locations were used as well as a newly developed<br />
lithological map (Fig. 1). It distinguishes 15 lithologic units. According to this<br />
classification the lithology of Japan is assembled of 13% plutonic rocks, 32% volcanic<br />
rocks, 49% sediments and 5% metamorphites, contrasting with the world average<br />
lithology that consists of 7% plutonic rocks, 7% volcanic rocks, 64% sediments and<br />
16% metamorphites. 65% of the surface area of Japan are documented by the data<br />
set and the average silica flux for this area is 22 t · km -2 · a -1 . This value is 6.7 times<br />
higher than the world average of 3.3 t · km -2 · a -1 (Dürr et al., in prep.). Despite its<br />
small size, Japan discharges 2.1% of worldwide riverine dissolved silica fluxes into<br />
coastal waters. The specific silica flux of the most productive watershed is as much<br />
as 84 t · km -2 · a -1 . The watersheds containing more than 80% volcanic rocks are<br />
characterized by an average specific silica flux of 40 t · km -2 · a -1 . This stretches out<br />
the importance of volcanic rocks for weathering rates and CO2 uptake respectively.<br />
Reference:<br />
Dürr, H., Meybeck, M., Sferratore, A. & Hartmann, J. (in preperation): Estimating<br />
silica fluxes to the coastal zone using a global segmentation, for C.R. Geosciences<br />
- 139 -
Lithological Map of the<br />
Japanese Archipelago<br />
Fig 1: Newly developed lithological map of Japan.<br />
- 140 -
Gro<strong>und</strong>water treatment technologies<br />
Christoph Schüth<br />
Contamination of gro<strong>und</strong>water with organic contaminants, especially chlorinated<br />
hydrocarbon compo<strong>und</strong>s (CHCs) and petroleum hydrocarbons as constituents of<br />
gasoline, is a wide-spread problem in industrialized countries. The treatment of the<br />
contaminated gro<strong>und</strong>water is in<br />
most cases achieved by<br />
pumping it through an<br />
adsorbent on-site, e.g. granular<br />
activated carbon (GAC). The<br />
efficiency of such a system can<br />
be further increased by air<br />
stripping the contaminants, as<br />
the sorption capacities of these<br />
compo<strong>und</strong>s on GAC are<br />
increased out of the gas-phase,<br />
due to the minimization or<br />
absence of competitive effects<br />
of the gro<strong>und</strong>water itself or<br />
other gro<strong>und</strong>water solutes.<br />
Fig. 1: HFM module. The contaminated gro<strong>und</strong>water<br />
enters the module at one side and flows over the<br />
shellside (outside) of the hollow fibers to the outlet.<br />
Nitrogen is used as an inert strip gas and is applied<br />
on the lumenside (inside) of the hollow fibers in<br />
counterflow.<br />
Furthermore, alternative<br />
destructive treatment options for the gas phase exist, e.g. catalytic oxidation, or<br />
reductive catalysis especially for chlorinated compo<strong>und</strong>s.<br />
Packed tower aeration is the<br />
most common stripping<br />
method, although it has<br />
several disadvantages. An<br />
alternative approach is the<br />
use of polypropylene hollow<br />
1<br />
100<br />
fiber membrane modules<br />
(HFM), that are routinely<br />
used for the degassing of<br />
process waters e.g. in the<br />
electronics industry or for<br />
0.1<br />
50<br />
the deaeration of bottled<br />
beverages (Fig. 1). With a<br />
very small footprint, these<br />
units provide a large surface<br />
area for mass transfer and<br />
enable an independent<br />
control of gas and liquid flow<br />
rates without the risk of<br />
flooding. Volume specific<br />
overall mass transfer<br />
coefficients for HFM<br />
0.01<br />
0<br />
0.01 0.1 1<br />
H (-)<br />
Fig. 2: Removal efficiencies for the 12 compo<strong>und</strong>s using<br />
three<br />
different experimental conditions (water flow rate<br />
constant<br />
tant at 0.4 l/min, gas flow and pressure combinations<br />
of 2.0 l/min and 0.25 atm (open circles), 0.8 l/min and 0.1<br />
atm (solid circles), 0.4 l/min and 0.05 atm (solid triangles)<br />
respectively, resembling constant Ra/w ratios of 20, and<br />
co rresponding mass balances (symbols with dotted lines).<br />
stripping have been reported to be an order of magnitude higher compared to packed<br />
C/C0 (-)<br />
NAP<br />
1,1,2,2-TCA<br />
MTBE<br />
- 141 -<br />
1,2-DCA<br />
1,2-DCB<br />
1,4-DCB<br />
CB<br />
cis-1,2-DCE<br />
TOL<br />
TCE<br />
PCE<br />
1,1-DCE<br />
Mass balance (%)
tower stripping, and therefore much lower strip-gas to water flow ratios are needed for<br />
an effective stripping.<br />
The removal of 12 organic contaminants from water using a HFM module was studied<br />
<strong>und</strong>er low strip gas flow to water flow ratios (up to 5:1). Removal efficiencies were fo<strong>und</strong><br />
to be strongly dependent on the Henry’s law constants indicating a substantial mass<br />
transfer resistance on the gas side. Vacuum can be either used to increase removal<br />
efficiencies, or to decrease the amount of strip gas that has to be treated without<br />
sacrificing efficiency (Fig. 2).<br />
The conventional resistance in series model was inapplicable to predict mass transfer<br />
coefficients in our experiments as it assumes, that at least for the operation conditions<br />
used here, the liquid side mass transfer resistance dominates the overall resistance for<br />
all compo<strong>und</strong>s (Fig. 3, left). Therefore, a new hybrid numerical and analytical modeling<br />
approach in the finite element simulator RockFlow/GeoSys for hydraulic flow and mass<br />
transport was developed. This approach enables the prediction of the removal<br />
efficiencies within a few minutes, whereas a pure numerical approach would require<br />
several hours to days due to numerical stability controls. The input parameters for the<br />
model are defined by the geometry of the HFM and the operating conditions, no<br />
empirical formulations are applied.<br />
The model allows the investigation of the main factors controlling the removal<br />
characteristics, e.g. the dependency on Henry’s law coefficient, gas side diffusional<br />
Kcalc (m/s)<br />
3.0e-5<br />
2.0e-5<br />
1.0e-5<br />
0.0<br />
0.0 1.0e-5 2.0e-5 3.0e-5<br />
K exp (m/s)<br />
C/C0 (-) m odel<br />
0.001<br />
0.01<br />
0.1<br />
1<br />
1<br />
0.1<br />
0.01<br />
C/C0 (-) experimental<br />
Fig. 3: Left: Calculated overall mass transfer coefficients K vs. experimental K.<br />
Calculations based on the resistance in series model. Right: Comparison of the<br />
experimental removal efficiencies (C/C0, with C being the outflow aqueous concentration<br />
and C0 being the inflow aqueous concentration) with the removal efficiencies calculated<br />
by the proposed model.<br />
resistance, and aqueous diffusion limitation, and also enables the efficient design of<br />
further organic removal systems based on the HFM technology. The model was able to<br />
predict removal efficiencies for all experimental conditions with reasonable accuracy<br />
(Fig. 3 right).<br />
- 142 -<br />
0.001
As the second step of the treatment method, the catalytic conversion of several organic<br />
contaminants was studied at elevated temperatures (50°C – 400°C) in the gas phase. In<br />
particular, the catalytic hydrodehalogenation of seven aliphatic chlorinated organic<br />
compo<strong>und</strong>s (PCE, TCE, cis-1,2-DCE, 1,1-DCE, 1,1,2,2-TCA, 1,2-DCA), and the<br />
hydrogenation as well as oxidation of ether compo<strong>und</strong>s used as fuel oxygenates<br />
(MTBE, ETBE, TAME, DIPE) was studied over palladium catalysts. In all cases the<br />
compo<strong>und</strong>s were transformed to non toxic or less toxic products. Reaction rates were in<br />
general pseudo first order and half lives were in the range of milliseconds to seconds,<br />
depending on the compo<strong>und</strong> and the temperature. As an example the temperature<br />
dependent first order rates obtained for the reductive conversion of chlorinated aliphatic<br />
compo<strong>und</strong>s are compiled in Table 1. In general, ethane was the sole degradation<br />
product.<br />
Table 1: Gas phase reductive catalytic conversion of chlorinated aliphatic compo<strong>und</strong>s<br />
using a palladium on alumina catalyst. Rates are reported as sec -1 .<br />
T, o C 1,1-DCE c-1,2-DCE TCE PCE 1,1,2,2-<br />
TCA<br />
1,2-DCA Chloroethane<br />
50 9.42±0.09 7.91±0.18 4.23±0.18 3.2±0.04 n.d. n.d. n.d.<br />
75 13.4±0.25 11.8±0.40 7.42±0.12 5.82±0.11 n.d. n.d. n.d.<br />
100 18.9±0.46 18.2±0.25 11.9±0.18 9.83±0.10 4.35±0.09 n.d. n.d.<br />
150 29.4±0.54 28.9±0.63 21.8±0.48 19.4±0.25 12.3±0.12 n.d. n.d.<br />
200 n.d. n.d. 38.2±1.35 36.8±0.69 24.2±0.27 1.50±0.05 n.d.<br />
250 n.d. n.d. n.d. n.d. 39.9±0.25 3.14±0.04 2.55±0.06<br />
300 n.d. n.d. n.d. n.d. n.d. 6.13±0.06 5.26±0.15<br />
350 n.d. n.d. n.d. n.d. n.d. 9.48±0.13 9.05±0.11<br />
400 n.d. n.d. n.d. n.d. n.d. n.d. 15.5±0.26<br />
Currently, a container based pilot scale gro<strong>und</strong>water treatment plant is <strong>und</strong>er<br />
construction in cooperation with the Environmental Research Center Leipzig/Halle<br />
(UFZ) to advance this technology into real use.<br />
- 143 -
Diffusion and reaction in micro- and mesopores<br />
Christoph Schüth<br />
Diffusion in micro- and mesopores is in many cases limiting for mass transfer and<br />
reaction rates in porous natural or synthetic materials. Accessibility and reactivity of<br />
micro- and meso-pore domains should be a function of the pore sizes as well as pore<br />
polarities. In natural po-rous media both parameters can be assumed to show a<br />
distribution, depending on the type of the porous material. Moreover, educts and<br />
products of a reaction may show different po-larities resulting in a distribution of<br />
diffusivities with an impact on overall reaction rates.<br />
The objective of this work is the synthesis and characterization of well-defined porous<br />
mate-rials with different pore sizes and polarities containing catalytically active sites,<br />
and study their accessibility with various methods. The catalytic hydrodehalogenation of<br />
chlorinated hydrocarbons (trichloroethylene (TCE) and chlorobenzene) and the<br />
hydrogenation of ben-zene serve as model reactions resulting in different product<br />
distributions in terms of polarity and molecular size. The use of well-characterized<br />
model solids should allow to relate diffu-sion rates and reactivities of the different<br />
materials to pore sizes and pore polarities.<br />
In the first step, the synthesis and first characterization of metal complexes will be<br />
performed. The selection of the metal complexes is predefined by the model reactions<br />
as described earlier. Pincer complexes (M-1a-c,2a-c) which are accessible by various<br />
procedures will be synthesized. In general a number of organic and organometallic<br />
transformations have to be performed to generate complexes M-1a-c,2a-c. Their special<br />
features are the different donor atoms which coordinate to the metal, the functional<br />
groups at the donor atoms and very important for this project the hydrolysable group at<br />
the end of the spacer. These features allow to adjust the metal complexes for a special<br />
application in catalysis.<br />
(R'O) 3Si<br />
X<br />
[M]<br />
X<br />
M-1a-c, M-2a-c<br />
Scheme 1<br />
X = SR (1), NR 2 (2)<br />
R = Me (a), Ph (b), Cy (c)<br />
[M] = Rh, Pd, Ni, Ru complex fragments<br />
R' = Me, Et<br />
Spacer e.g. C 6-alkane or short PEG chain<br />
It is planned to perform the dehalogenation reactions with the SCS-Pd complexes (Pd-<br />
1). Catalysts of this type are highly stable in air and water and are known to cleave<br />
carbon-chlorine bonds. This will be important for field applications planned at a later<br />
date of this project. To fine tune the active center with respect to electron density and<br />
steric hindrance R will be varied from methyl (Pd-1a), phenyl (Pd-1b) to cyclo-hexyl (Pd-<br />
1a). All complexes will be screened for their catalytic activity in dehalogenation and<br />
hydrogenation reactions.<br />
- 144 -
Those complexes which performed best in the reactivity screening will be incorporated<br />
into porous oxides. The porous oxides will be prepared by sol-gel processing. This<br />
technique allows the creation of oxide networks by progressive hydrolysis and<br />
condensation reactions of molecular precursors (Scheme 2). Therefore it is an ideal and<br />
versatile method to incorporate well defined metal complex catalysts into the network.<br />
The parameters which influence the sol-gel reaction allow to control the morphology and<br />
properties of the materials. As in this project the pore size and the polarity of the matrix<br />
are of interest only those parameters will be varied which have an influence on this<br />
properties.<br />
The following educts and parameters will be considered: (1) The alkoxysilanes<br />
tetramethoxysilane (TMOS), tetraethoxysilane (TEOS), methyltrimethoxysilane<br />
(MTMOS) and phenyltrialkoxysilane (PhTMOS); (2) The metal complex catalysts<br />
developed; (3) the solvents THF, H2O, ethanol, ethylene glycol, glycerine; (4) pH; (5)<br />
templates (tensides, organic polymers etc.).<br />
k H 2O +<br />
l Si(OR') 4 +<br />
m RSi(OR') 3 + n<br />
Scheme 2<br />
(R'O) 3Si<br />
1. pH<br />
X 2. Solvent<br />
3. Templates<br />
[M]<br />
4. Temperature<br />
5. Pressure<br />
X<br />
6. Stirring speed<br />
M-1a-c,2a-c<br />
MOS and TEOS are network builders. Their different alkoxy groups allow to control the<br />
ki-netic of the hydrolysis. If only these are used in the reaction the pore size of the<br />
materials depends on the pH. The amount of alkyltrimethoxysilanes will have an<br />
influence on the pore sizes and on the polarity. It is further assumed that the Alkyl group<br />
will have an additional effect on the diffusion of the organic molecules into the porous<br />
material. For the generation of larger pore sizes template additives might have to be<br />
used. Due to the thermal sensitivity of the metal complexes calcination has to be<br />
excluded. Thus the additives will have to be ex-tracted by extensive solvent processing.<br />
During the mixing of the organic and inorganic reaction partners the organic part of the<br />
metal complex catalyst will be surro<strong>und</strong>ed by the non-polar organic functions R. This will<br />
ensure that in the final material the catalyst will be on the non-polar surface of the<br />
pores.<br />
When the main properties of the solids and the resulting processes limiting or enabling<br />
the access of diffusing compo<strong>und</strong>s into micro- and mesopores are known, this<br />
knowledge could be used to synthesize tailored materials for a specific application. This<br />
could be catalysts with high and sustained reactivities in aqueous systems by<br />
selectively providing access to reactive sites. In gro<strong>und</strong>water remediation, there is<br />
especially a need for destructive methods as can be achieved by catalysis, because no<br />
secondary waste streams are produced. Besides the f<strong>und</strong>amental research, this project<br />
has therefore also a very applied backgro<strong>und</strong>, with the potential for a commercial<br />
utilization of the results.<br />
- 145 -<br />
Si<br />
X<br />
X<br />
[M]<br />
X
Rift dynamics, uplift and climate change in<br />
Equatorial Africa:<br />
Sybille Roller, Matthias Hinderer, Jens Hornung<br />
Situated in the central western branch of the East African Rift system, the Rwenzori<br />
Mountains and adjacent rift flanks are the highest uplifted rift flanks on earth. Their<br />
extreme uplift may have significantly contributed to the aridisation of East Africa since<br />
the Late Miocene.<br />
Within the DFG research Unit (Forschergruppe “RIFTLINK” with University of Frankfurt,<br />
University of Mainz and other institutions) we are running the sedimentological part<br />
which is titled:<br />
Linking source and sink in the Rwenzori Mountains and adjacent rift basins,<br />
Uganda: landscape evolution and the sedimentary record of extreme uplift<br />
The goal of the subproject is to study the erosional denudation of the Rwenzori<br />
Mountains since their extreme uplift in the Late Miocene. This comprises both, analysis<br />
of the erosional features and landscape evolution, as well as the sedimentary record in<br />
the adjacent rift basins. The working programme for the running time of the project is<br />
based on three investigation fields: 1.) “Source region”: Erosion and fluvial transport, 2.)<br />
“Sink region”: Basin analysis, 3.) “Modelling”: Numerical simulations of landscape<br />
evolution including basin fill history.<br />
Prevailing questions concern the close connection between the extreme uplift and the<br />
erosive unloading and the chronological relation of both processes. Therefore, we try to<br />
<strong>und</strong>erstand the role of endogenic processes, the role of climate, and the possibility of a<br />
dynamic balance between uplift and denudation. We intend to develop a timestratigraphic<br />
frame from the Late Miocene to Present. Moreover we will calculate<br />
denudation rates, sediment efflux, and interpret the controlling factors of both<br />
processes.<br />
Dense tropical vegetation and thick pedogenesis to a certain extent hamper continuous<br />
and area-wide sedimentological investigations, but some scarcely available outcrops<br />
provide insights both in the lake and river sediments and into several of the uplift<br />
induced alluvial fan deposits, respectively, and admit some relative age assumptions, as<br />
well as examinations of lithology, structure, and facies-type. Ages of younger alluvial<br />
sediments are determined using Optically Stimulated Luminescence (OSL) dating.<br />
Erosion rates are evaluated by measuring the concentration of in-situ produced<br />
Terrigenic Cosmogenic Nuclides (TCN; e.g. 10 Be) in the quartz grains of river sands.<br />
The results will then be integrated into an evolutionary model of erosion, sediment flux,<br />
and rift basin fill for the central western branch of the East African Rift.<br />
A first field campaign was carried out in August 2006 to get an idea about the quantity<br />
and quality of the loosely distributed outcrops. For a complete data set of erosion rates,<br />
quartz-bearing river sand was sampled in 14 prominent rivers all aro<strong>und</strong> the Rwenzori<br />
Mountains on Ugandan territory. In the meantime the material entered its complex<br />
preparation process for concentration measurement of 10 Be in the accelerator mass<br />
- 146 -
spectrometer (AMS) (method performed in cooperation with University of Hannover and<br />
AMS-Laboratory in Glasgow).<br />
During a second field campaign in January/February 2007 several stratigraphic sections<br />
in the Semliki, B<strong>und</strong>ibugyo, Mobuku, and Kasese areas were mapped in detail to<br />
resolve the temporal and spatial relationship between lake sediments, distal floodplain<br />
sediments, and proximal alluvial fan deposits. Interfingering is complex due to<br />
contemporaneous influence of both fluctuating climatic and tectonic events. At key<br />
localities and if lithology was appropriate, lightproof samples for OSL-dating were<br />
excavated. Comparable to TCN-dating, the OSL-method requires highly sophisticated<br />
preparation and measurement performance that can be provided by the OSL lab at<br />
Liverpool University.<br />
A high-resolution DEM (30m) helps to analyse the landscape morphometry of the rift<br />
flanks. Beside a visual interpretation of the DEM, ArcGIS helps to quantify the<br />
morphometric parameters (catchment size, hydrological properties).<br />
Fig. 1: High resolution DEM of the Rwenzori Mountains situated in the western branch of the<br />
East African Rift system.<br />
- 147 -
Geology, land use change and erosion in the northern<br />
periphery of Belo Horizonte, Brazil<br />
Monika Hofmann 1 , Andreas Hoppe 1 , Allan Buchi², Joachim Karfunkel 2,<br />
Ricardo Pagung 2<br />
1 Institut für Angewandte <strong>Geowissenschaften</strong>, TU-Darmstadt, Germany;<br />
2 Instituto de Geociências, Universidade Federal de Minas Gerais, Belo Horizonte, Brazil<br />
Belo Horizonte, the capital of the state Minas Gerais (Brazil), has been considered by<br />
the UNO as one of the cities of South America that will be a megacity with more than<br />
ten million inhabitants by the middle of this century. As the city already does not support<br />
its growth to the south because of restricted access and accentuated relief, the future<br />
tendency will be to expand towards the north. The newly built highway between the<br />
international airport Confins 40 km north of Belo Horizonte and the city itself is<br />
accelerating the urbanization of the neighbouring municipalities, especially as tax<br />
reductions for industrial plants and easy access are favouring rapid development of the<br />
region. The urbanized area, including the area in process of urbanization (periurban<br />
area / bare soil), increased from 13% in 1987 to 20 % in 2002. In the same time, the<br />
forested area decreased from 45 to 36%. The analysis of geo-resources and geohazards<br />
is essential for the sustainable growth of every city, even more so if the city is<br />
growing very fast into a fragile environment as is the case in Belo Horizonte.<br />
Lagoa Santa, a city of 45000 inhabitants lying at the triangular lake north of Belo<br />
Horizonte, is the biggest city affected by the trend towards urbanisation due to the new<br />
highway. The prices for real estates in its municipal area are rising even before the<br />
highway is finished. Still, Lagoa Santa is situated on highly erodible siltite hills and<br />
severe erosion with has formed many gullies is already threatening the infrastructure.<br />
Also in the neighbouring valley of the Riberão da Mata whose alluvial plain serves both<br />
as sand, clay and gravel resource and as one of the very few plain building sites,<br />
concentrated overland flow resulting from sealed areas increase the risk of in<strong>und</strong>ations.<br />
Fig. 1: Belo Horizonte and the study site in its northern periphery.<br />
In the whole northern periphery of Belo Horizonte which includes the municipality of<br />
Lagoa Santa, a general erosion index has been calculated, regarding the erodibility of<br />
soils as well as topography: The erodibility of soils has been estimated on behalf of the<br />
lithology in the area and whether laterite crusts exist or not. While the Archean<br />
- 148 -
granite/gneiss basement rocks in the south and west are highly erodible due to deep<br />
weathering and low infiltration capacity, the overlying carbonate rocks outcropping in the<br />
north and east are less prone to erosion due to better soil structure and rapid infiltration<br />
in the karst system which prevents excessive overland flow (Fig. 2). Aro<strong>und</strong> the lake of<br />
Lagoa Santa, the Neoproterozoic carbonate rocks are overlain by siltite rocks with a<br />
very low infiltration capacity and weak soil and saprolite cohesion. In these highly<br />
vulnerable hills, many gullies can be observed already, most but not all of them related<br />
to urban areas. On the mountain tops in the middle of the study area, laterite crusts<br />
protect the <strong>und</strong>erlying soils from erosion and thus these areas are assigned low<br />
erodibility values.<br />
Fig. 2: Erosivity of the study area, based on<br />
lithology and the existence of laterite crusts.<br />
Fig. 3: Erosion hazard of the study area<br />
derived by overlay of erosivity and topographic<br />
index.<br />
- 149 -<br />
A map showing the natural erosion<br />
hazard in the area has been created<br />
by overlying the erodibility map with a<br />
map showing a topographic index<br />
based on the length slope factor used<br />
in the universal soil loss equation. The<br />
resulting map (Fig. 3) highlights the<br />
areas of the steep siltite hills aro<strong>und</strong><br />
the city of Lagoa Santa in the east and<br />
the hilly landscape on Archean<br />
gneiss/granite rocks in the south and<br />
west. In an ongoing study existing<br />
gullies in Lagoa Santa are evaluated<br />
with regard to their catchment area,<br />
steepness, flow concentration along<br />
roads and the amount of sealed area<br />
in the catchment in order to estimate<br />
local threshold values for gullying.<br />
Additionally to regional erosion hazard<br />
estimation, a local case study on land<br />
use change due to sand and gravel<br />
extraction and urbanisation in the<br />
alluvium of the Riberão da Mata has<br />
been performed. This area has been<br />
subject to sand, clay and gravel<br />
extraction during the last decades, and<br />
many of the small scale mining sites<br />
have been simply left open after the<br />
extraction had been banned due to the<br />
Brazilian legislation that puts a buffer<br />
zone along rivers <strong>und</strong>er protection or<br />
as sand extraction at low costs above<br />
the gro<strong>und</strong>water level was not viable<br />
anymore. Still, it is one of the few<br />
areas close to the city where sand and<br />
gravel for construction purposes can<br />
be fo<strong>und</strong>. A visual analysis of aerial<br />
photos and satellite images covering
nearly half a century has been performed, concentrating on the impact of sand and<br />
gravel mining and the recuperation of abandoned mining areas as well as on the<br />
proceeding urbanisation. Fig. 4 shows the dynamic of the urbanisation of the alluvial<br />
plains from 1977 until 1990. These analyses were accompanied by field observations<br />
including geological, pedological and environmental aspects such as the state of the<br />
recuperation of abandoned extraction areas as well as sedimentological structures. The<br />
total area of 6,68 km² of the alluvium between the road MG 424 and the road MG 010,<br />
have been subject to many drastic transformations during the last decades. Frequent<br />
changes of the riverbed, erosion at its margins, siltation and the augmentation of<br />
exposed soil in the alluvial plain could be observed.<br />
Fig.4: Proceeding urbanisation of the alluvial plain of the Riberâo da Mata<br />
between 1977 and 1990.<br />
The peak of the sand mining activities was in the decades of 1970 to 1980, when the<br />
city of Belo Horizonte was growing very rapidly and environment legislation was less<br />
strict. Still, even today, active sand and clay mines can be fo<strong>und</strong> in the area, showing<br />
the importance of these resources for the city. During the last decades, approximately<br />
30% of the study area has been subject to mining (1.5 km² during the 1977 and only 0,5<br />
km² in 1990). In some abandoned mining areas, industrial plants breaking carbonate<br />
rocks for gravel substitution have been constructed, as the alluvium offers plain<br />
construction sites. The gravel mining has stopped since, as the natural gravel resources<br />
are scarce and deep seated. The natural recuperation of abandoned mining areas is<br />
slow and exposed soil and active erosion carries away fertile soil and increases the<br />
sediment load of the river. In the 1970s, 0,4 km² of the area could be classified as<br />
exposed soil showing signs of erosion. The multi-temporal analysis of the land use in<br />
this area together with a comparison with other source areas showed that certain georesources<br />
like sand and gravel for construction purposes are heavily needed in close<br />
distance to the growing city, but competing for space with other uses and with<br />
environmental legislation.<br />
- 150 -
Planar Defects in Bixbyite, (Mn,Fe)2O3;<br />
A Prominent Diffusion Path<br />
Hans-Joachim Kleebe, Stefan Lauterbach<br />
Bixbyite is a rather uncommon manganese-iron oxide (Mn,Fe)2O3, crystallizing in the<br />
Ia3 space group [1], forming black cubic crystals with metallic lustre that are commonly<br />
truncated by small icositetrahedral faces at corners. Bixbyite normally occurs in small<br />
crystals reaching some mm in size. However, there is one location at Thomas Range<br />
(Utah), where large crystals up to 4 cm are fo<strong>und</strong>. These crystals occur in cavities of a<br />
rhyolite host rock associated with topaz, pseudobrookite, braunite, hematite,<br />
hausmannite and quartz [2].<br />
In contrast to the small isomorphic crystals, most of the larger bixbyite crystals from<br />
Thomas Range show distinct re-entrant facets at halfway of every edge of the cube,<br />
linked by a band of parallel linear features, crossing at the center of each cube face.<br />
These linear features were first characterized as twin bo<strong>und</strong>aries, but they cannot be a<br />
result of local twinning, since any twinning operation on {100} planes of the<br />
centrosymmetric bixbyite structure would produce an identical single crystal.<br />
High-resolution transmission electron microscopy (HRTEM) was used to study the<br />
structure of those linear features. HRTEM images showed fault planes running along<br />
{100} planes of the bixbyite structure. The interfaces are atomically sharp and planar<br />
over large areas of the crystal. TEM/EDS analyses revealed an enrichment of Si in the<br />
fault regions with a simultaneous increase in Mn. The composition of the planar defects<br />
closely corresponds to the manganese silicate braunite, Mn 2+ Mn 3+ 6SiO12 [3].<br />
Small precipitates observed in close proximity to the planar faults suggest an increased<br />
diffusion rate along those defects. The enhanced grain growth of the larger bixbyite<br />
crystals can be rationalized by fast diffusion along those planar braunite interlayers.<br />
[1] Dachs, H. (1956): Die Kristallstruktur des Bixbyits (Fe, Mn)2O3, Z. für Kristallographie, 107, 370.<br />
[2] Eric H. Christiansen, E. H, James V. Bikun, J. V., Michael F. Sheridan, M. F., Donald M. Burt, D. M.<br />
(1984): Geochemical Evolution of Topaz Rhyolites from the Thomas Range and Spor Mountain, Utah,<br />
American Mineralogist, 69, 223.<br />
[3] De Villiers, J.P.R. & Buseck, P.R. (1989): Stacking Variations and Non-Stoichiometry in the Bixbyite-<br />
Braunite Polysomatic Mineral Group, American Mineralogist, 74, 1325.<br />
- 151 -<br />
Fig. 1: HRTEM image of the intrinsic defect<br />
structure observed in a lager bixbyite single<br />
crystal. Note the presence of small<br />
precipitates adjacent to the planar faults of<br />
braunite, Mn7SiO12.
The Effect of LiF Addition on the Sintering Mechanism of<br />
Spinel, MgAl2O4<br />
Hans-Joachim Kleebe, Mathis Müller, Keith Rozenberg 1 , Ivar E. Reimanis 1<br />
1 Colorado School of Mines, Metallurgical and <strong>Material</strong>s Engineering Dept., Golden, CO 80401, USA<br />
MgAl2O4 is widely regarded as one of the most promising optical ceramics [1,2]. It has<br />
excellent transmissivity in the near infrared frequency range. There is an excellent body<br />
of research on the sintering mechanisms of pure spinel for optical applications.<br />
Unfortunately hot pressing with LiF doped spinel, which is one of the most promising<br />
processes for producing optical quality spinel ceramic, is also one of the least<br />
<strong>und</strong>erstood. Many compo<strong>und</strong>s have been proposed or used as sintering aids for<br />
MgAl2O4 spinel (hereafter called spinel). For example, Na3AlF6, AlCl3, CaCO3, and LiF<br />
have all been shown to promote sintering in spinel, though the detailed mechanisms<br />
have remained elusive. LiF has been used to speed up the sintering kinetics of several<br />
other systems including SrTiO3, and BaTiO3, and MgO. LiF, is the only compo<strong>und</strong><br />
considered for use as a sintering aid in the production of low porosity, transparent spinel<br />
via hot pressing.<br />
The effect of LiF on the sintering of spinel has been only qualitatively studied. An<br />
<strong>und</strong>erstanding of the mechanism for removal of LiF from the system is essential as any<br />
residual LiF or related species could destroy the optical properties of the material. It has<br />
been shown that LiF reduces the sintering temperature of spinel by nearly 200°C, and<br />
decreases reaction temperatures during reactive sintering. More recent studies on<br />
dense spinel were performed to determine the location of LiF subsequent to sintering,<br />
with the objective of better <strong>und</strong>erstanding its role in sintering. LiF was not identified in<br />
any of the studies, suggesting that it may react with spinel during sintering and/or<br />
ultimately was removed from the system. It is known that LiF is active at the interface<br />
between spinel grains at higher temperatures. Furthermore, it has been reported that<br />
spinel sintered in the presence of LiF has a substantially higher Al content. Large<br />
amounts of LiF have also been observed to act corrosively with spinel. All of these<br />
observations indicate that LiF does chemically react with the spinel at elevated<br />
temperatures. A recent study indicates that LiF reacts with Al in spinel, forming LiAlO2,<br />
and leaving Mg-rich regions in the matrix. This, however, leaves the question of what<br />
becomes of the fluoride species. This spinel<br />
project addresses the issue of how LiF can<br />
promote the sintering performance of<br />
magnesium aluminate. In addition to HRTEM<br />
investigations, model experiments with high<br />
volume fraction of LiF addition are performed.<br />
[1] R. J. Bratton, “Translucent Sintered MgAl2O4”,<br />
J. Am. Ceram. Soc., 57 [7] 283-86 (1974).<br />
[2] C.-J. Ting and H.-Y. Lu, “Hot Pressing of<br />
Magnesium Aluminate Spinel; Part-II. Microstructural<br />
Development”, Acta mater. 47 [3] 831-<br />
40 (1999).<br />
Fig. 2: TEM image of the spinel sample, doped<br />
with 5 wt% LiF and pre-sintered at 900 o C. In close<br />
proximity of the intrinsic pores, an amorphous LiFphase<br />
was observed (transient phase).<br />
- 152 -
Microstructure Characterization of Boron Suboxide, B6O<br />
Hans-Joachim Kleebe, Stefan Lauterbach, Mathias Herrmann 1 ,<br />
Jack Sigalas 2<br />
1 Fraunhofer Institut für Keramische Technologien <strong>und</strong> Systeme, Dresden<br />
2 University of the Witwatersrand, Johannesburg, Gauteng, South Africa<br />
Hexaboron monoxide (B6O), commonly termed boron suboxide, is known as a<br />
superhard material, constituted of the light elements boron and oxygen. The<br />
extraordinary hardness of such a low-density material has been attributed to the intrinsic<br />
strong and directional covalent bonds between B and O, leading to a tight, threedimensional<br />
network with an excellent resistance towards external shear.<br />
The average Vickers hardness (Hv) of B6O is about 45 GPa, which is next to diamond<br />
(Hv: 70–100 GPa) and cubic boron nitride, c-BN (Hv: 45–50 GPa). Similarly, the<br />
average fracture toughness of B6O (4.5 MPa m 1/2 ) is higher as compared to c-BN (2.8<br />
MPa m 1/2 ) and comparable to diamond (5.0 MPa m 1/2 ). Due to its strong covalent<br />
bonding, B6O materials demonstrate exceptional physical and chemical performance<br />
such as high hardness, low density, high thermal conductivity, chemical inertness and<br />
good wear resistance. Its thermal stability, even at temperatures above 1000 °C, and<br />
its chemical inertness with ferrous alloys makes it in some instances even more suitable<br />
for industrial applications as for example diamond. In general, B6O materials have<br />
potential applications as abrasives, due to their high hardness, and are also considered<br />
as potential candidates for high-temperature semiconductors (with an estimated band<br />
gap of approximately 2.4 eV) and for<br />
thermo-electrics. Despite various potential<br />
applications, densification and processing<br />
of B6O materials was shown to be rather<br />
cumbersome. Therefore, a detailed<br />
microstructure characterization was<br />
performed in order to gain insight in the<br />
submicron structure that formed upon<br />
sintering.<br />
ACerS – NIST Phase Equilibria Diagrams<br />
Fig. 02339—System Al2O3-B2O3.<br />
P. J. M. Gielisse and W. R. Foster, Nature<br />
(London), 195 [4836] 69-70 (1962).<br />
The main objectives of the TEM study were<br />
(i) to verify as to whether an amorphous<br />
intergranular phase is present at the B6O<br />
grain bo<strong>und</strong>aries (doped versus <strong>und</strong>oped<br />
sintered samples), (ii) what type of<br />
crystalline grain-bo<strong>und</strong>ary phases are<br />
present in the sintered, coated B6O sample:<br />
Al4B2O9 and/or Al18B4O33, and (iii) the<br />
overall defect structure in the materials was<br />
to be characterized (in particular, the<br />
question whether stacking faults in B6O can<br />
be eliminated via long-term annealing was<br />
addressed).<br />
- 153 -
In case of the <strong>und</strong>oped sintered B6O sample, the individual B6O grains are typically well<br />
faceted with sharp edges. The grain-size distribution in this sample is bimodal with<br />
larger grains (1-2 µm) embedded in a fine-grain B6O matrix. All B6O grains typically<br />
reveal numerous stacking faults (similar to B4C particles). In the case of the doped,<br />
sintered B6O sample, the grain size was greatly increased (by a factor of about 5x).<br />
Stacking faults are a common feature of this B6O material even upon long-term anneal.<br />
A secondary phase formation was observed in the Al-containing sample. With respect to<br />
the phase diagram, the two aluminium borate compo<strong>und</strong>s that are most likely to form<br />
upon sintering are Al4B2O9 and/or Al18B4O33.<br />
Conventional TEM (bright field; Figure 3) and HRTEM (Figure 4) were performed on the<br />
crystalline secondary phase in addition to selected area electron diffraction (SAD). The<br />
diffraction pattern given in Figure 4 can be indexed corresponding to a primitive<br />
orthorhombic unit cell (a,b = 0.7617 and c = 0.2827 nm; Pbma) as well as with respect<br />
to an A-centered orthorhombic symmetry (Amam). EDS analysis does not allow the<br />
distinction between both phases, because this technique is rather insensitive to boron<br />
(no quantitative analysis possible). The A-centered phase; however, should follow the<br />
extinction rules (k+l=2n). Under the assumption that the rather weak {010}-type<br />
reflections visible in the SAD-pattern<br />
(Figure 4) are a result from 2 nd -order Laue<br />
reflections, it is concluded that extinction<br />
occurs. Therefore, the secondary crystalline<br />
Al-compo<strong>und</strong> observed in this material is<br />
the Al18B4O33 phase. It should be noted that<br />
the secondary phase shows an identical<br />
orientation within an area of 20-50 microns<br />
within the sample. This observation<br />
indicates that this Al-phase is characterized<br />
by a rather low nucleation rate, which is<br />
uncommon for most secondary phases.<br />
Fig. 3: TEM image of the secondary Al-phase,<br />
Al18B4O33, observed in the doped, sintered B6O<br />
sample.<br />
Fig. 4: HRTEM image of the secondary Alphase<br />
present in B6O. Note the presence of<br />
stacking faults as well the weak reflections in<br />
the SAD pattern (extinction).<br />
- 154 -
Pressure and Temperature Dependence of the Fe 2+ /Fe 3+ -Ratio<br />
in Omphacite for the Re-Calibration of the Fe-Mg<br />
Geothermometer<br />
Stefan Lauterbach, Hans-Joachim Kleebe<br />
Iron is present in omphacite, (Ca,Na)(Mg,,Al,Fe 2+ ,Fe 3+ )Si2O6, a common clinopyroxene<br />
(Figure 5), as di- and trivalent cations. Analyzing the iron content via micoprobe, the<br />
overall iron content can be determined; however, without a distinction between Fe 2+ and<br />
Fe 3+ . The commonly used geothermomenter calibration of high pressure (HP) and ultrahigh<br />
pressure (UHP) eclogites is solely based on the Fe 2+ content as the total iron<br />
content. Thereby, the determined corresponding formation temperatures may differ by<br />
up to 400 degree Celsius, since the Fe 3+ content is not considered.<br />
Mathematical corrections of the Fe 2+ /Fe 3+ -ratio in omphacite are based on stoiciometric<br />
considerations, while analytical techniques to determine the actutal Fe 3+ content are still<br />
lacking. Moreover, experimental calibration of the Fe 2+ /Fe 3+ -ratio are commonly not<br />
satisfying. Therefore, a re-calibration of the Fe 2+ /Fe 3+ -ratio is performed by measuring<br />
both the Fe 2+ and Fe 3+ content in omphacite employing the technique of electron<br />
energy-loss spectroscopy (EELS). Parallel, energy-dispersive X-ray spectroscopy<br />
(EDS) is used, in order to determine the overall Fe-content of the sample. The<br />
experimental EDS and EELS data allow a quantitative determination of the Fe 2+ and<br />
Fe 3+ content. In addition, the high lateral resolution of the transmission electron<br />
microscope (TEM), down to a few nanometer, allows the analysis of model samples that<br />
were synthesized at rather low temperatures (short diffusion profile), which are close to<br />
the formation temperature assumed for natural omphacites.<br />
Due to the high lateral resolution of the electron transmission microscopy techniques<br />
EELS and EDS, exchange equilibria at the sub-micron level are suitable for the<br />
experimental determination of the Fe 2+ /Fe 3+ -ratio, even at synthesis temperatures as<br />
low as 800 o C. Such low-temperature samples omit the normally applies extrapolation of<br />
HT data to low temperatures and add “hard data” to the lower temperature regime.<br />
Apart from synthetic samples, natural omphacites (HP-eclogites) from the Tauern<br />
Window are studied.<br />
Fig. 5: TEM bright field image of Omphacite,<br />
(Ca,Na)(Mg,,Al,Fe 2+ ,Fe 3+ )Si2O6; clinopyroxene)<br />
in an orientation which reveals typical antiphase<br />
bo<strong>und</strong>aries (APB; courtesy W. Müller).<br />
- 155 -
Microstructures in Omphacite and Other Minerals from<br />
Eclogite Near to the Interface Eclogite Zone/Lower Schist<br />
Cover, Tauern Window, Austria<br />
Wolfgang Friedrich Müller and Gerhard Franz 1<br />
1 Institut für Angewandte <strong>Geowissenschaften</strong>, Technische Universität Berlin<br />
Rapid exhumation of eclogitic rocks from depths between 60 and 100 km to an<br />
intermediate crustal level of about 30 km or less, is frequently reported from high- and<br />
ultra-high pressure terrains. It is unclear, however, how the rocks and their mineral<br />
constituents respond to such high strain rates, which are possibly also associated with<br />
large, crustal earthquakes. It is also an open question, which mechanical and<br />
temperature effects are produced by fast exhumation of high-pressure nappes or<br />
intercalated slices in its neighbourhood and in itself.<br />
It was recently established [1] that the high-pressure terrain of the Pennine in the<br />
Eastern Alps, the Eclogite Zone (EZ) in the Tauern Window, shows very high uplift<br />
rates. Radiometric age determinations (Rb/Sr) from eclogite facies rocks of the EZ and<br />
of post-eclogitic greenschist facies vein assemblage revealed minimum uplift rates of ><br />
36 mm/a. The event of the rapid imbrication of the EZ between other tectonic units<br />
caused unusual deformation microstructures in a sample from the lower tectonic unit<br />
which is the Venediger nappe or Lower Schist Cover (LSC) [2]. In an eclogite sample on<br />
the order of 10 m distant from the EZ polygonisation of garnet into subgrains of 0.5 to 3<br />
µm, high dislocation density in titanite, and deformation twin lamellae on (100) in<br />
clinozoisite were observed [2]. In order to see if there are similar effects in rocks from<br />
the EZ, we studied an eclogite as close as possible to the thrust plane by transmission<br />
electron microscopy (TEM). The distance of the sample locality to the thrust fault<br />
between LSC and EZ is about 50 m. This sample (WP 291) served already Glodny et al.<br />
[1] for the age determination. According to thermobarometry, the EZ eclogites have<br />
experienced peak P-T conditions of 2.0 - 2.5 GPa and 600 ± 30 °C (see [1] and<br />
quotations therein).<br />
Omphacite<br />
The omphacite grains impress by their wealth of microstructures: Antiphase domains<br />
(APDs) separated from each other by antiphase domain bo<strong>und</strong>aries (APBs), chain<br />
multiplicity faults (CMFs), twin lamellae on (100), non-crystallographic faults, free<br />
dislocations, small angle grain bo<strong>und</strong>aries, and recrystallised grains. With exception of<br />
the APDs, all microstructures are due to deformation and to recovery and<br />
recrystallisation as consequence of deformation which may be syn- or<br />
postdeformational.<br />
Antiphase domains (APDs) are present in all grains studied. They arise from the phase<br />
transition C2/c→P2/n due to the diffusion-controlled ordering of Mg and Al. The<br />
displacement vector of the antiphase domains is 1/2[110] [3, 4]. From the peak<br />
metamorphic temperature of the EZ of about 600 °C it is clear that our omphacite<br />
crystallised first in the disordered C-lattice but within the phase regime of the P-phase<br />
[3]. The APDs have mostly a size of 0.2 to 0.4 µm. Electron diffraction patterns show<br />
well-ordered omphacite of space group P2/n with sharp reflections.<br />
CMFs (intercalations of layers with a different chain multiplicity; here double chains like<br />
in amphibole) parallel to (010) are frequenty observed. They have been described in<br />
- 156 -
detail by [5]. CMFs are apparently quite typical for omphacites from the EZ and the LSC<br />
from the Tauern Window, and are seldom described from other occurrences.<br />
An astonishing feature observed in several omphacite grains are faults which are not<br />
oriented parallel to a distinct crystallographic plane but have preferential orientations<br />
subparallel to (100); they are terminated by dislocations. These ‘non-crystallographic<br />
faults’ were apparently produced by moving dislocations. Attempts to analyze their<br />
displacement vector failed.<br />
While free dislocations are rare, small-angle grain bo<strong>und</strong>aries formed by one or two sets<br />
of dislocations are relatively frequent. In one case, even a recrystallizing grain was<br />
observed (Fig. 1a) forming a large angle grain bo<strong>und</strong>ary with the matrix grain.<br />
Polysynthetic twin lamellae on (100) (Fig.1b) are interpreted as deformation twins<br />
because growth twins of this type are unknown and the grain is obviously deformed as<br />
evidenced by free dislocations.<br />
Clinozoisite shows deformation twin lamellae on (100) with widths which vary between<br />
about 3 and 150 nm. They have been first observed in the LSC sample close to the<br />
interface to the EZ [2]. Garnet contained rarely dislocations and low angle grain<br />
bo<strong>und</strong>aries. Barroisitic amphibole displayed a small-angle grain bo<strong>und</strong>ary which<br />
consisted of segments parallel to (110), but otherwise no specific deformation effects<br />
were apparent.<br />
In conclusion: The TEM results show strong deformation of omphacite and clinozoisite,<br />
but garnet is almost free of dislocations. Comparison of these results with those by<br />
Barnert [6] on samples farther away from the interface to the LSC shows no significant<br />
differences of the effects of ‘normal’ deformation in the EZ omphacites and the<br />
deformation associated with the rapid exhumation. The only exception are the noncrystallographic<br />
faults in omphacite mentioned above which may indicate locally<br />
elevated temperatures.<br />
Fig.6: TEM electron micrographs of omphacite. (a) Recrystallising grain (bright grain in the left<br />
corner) growing into the omphacite matrix in which APBs are visible; bright-field image. (b)<br />
Omphacite with deformation twin lamellae on (100); dark-field image.<br />
[1] Glodny J. et al. (2005) Contr. Mineral. Petrol. 149, 699-712<br />
[2] Müller W.F., Franz G. (2004) Eur. J. Min. 16, 939-944<br />
[3] Champness P.E. (1973) Am. Mineral. 58, 540-542<br />
[4] Phakey P.P., Ghose S. (1973): Contr. Mineral. Petrol. 39, 239-245<br />
[5] Müller, W.F. et al. (2004) Eur. J. Min., 16: 37-48<br />
[6] Barnert, E.B. (2003) Doctoral thesis, TU Darmstadt, Fb 11<br />
- 157 -
Modelling phase-assemblage diagrams for magnesian<br />
metapelites in the system K2O – FeO – MgO – Al2O3 – SiO2 –<br />
H2O: geodynamic consequences for the Monte Rosa nappe,<br />
Western Alps.<br />
R. Le Bayon 1 , C. de Capitani and M. Frey 2<br />
1 TU Darmstadt and 2 University of Basel, CH<br />
Magnesian metamorphic rocks with metapelitic mineral assemblages and composition<br />
are of great interest in metamorphic petrology for their ability to constrain P-T conditions<br />
in terranes where metamorphism is not easily visible. Phase-assemblages diagrams for<br />
natural and modal magnesian metapelites in the system KFMASH are presented to<br />
document how phase relationships respond to water activity, bulk composition, pressure<br />
and temperature. The phase assemblage displayed on these phase diagrams are<br />
consistent with natural mineral assemblages occurring in magnesian metapelites. It is<br />
shown that the equilibrium assemblages at high pressure conditions are very sensitive<br />
to a(H2O). Specifically, the appearance of the characteristic HP assemblage chloritoidtalc-phengite-quartz<br />
(with excess H2O) in the magnesian metapelites of the Monte Rosa<br />
nappe (Western Alps) is due to reduction of a(H2O). Furthermore, the mineral<br />
assemblages are determined by the whole-rock FeO/(FeO+MgO) ratio and effective Al<br />
content XA as well as P and T.<br />
The predicted mineral association for the low- and high –XA model bulk compositions of<br />
magnesian metapelites at high pressure are not dependent on the XA variations as they<br />
show a similar sequence of mineral assemblages. Above 20 kbar, the prograde<br />
sequence of assemblages associated with phengite (with excess SiO2 and H2O) for low-<br />
and high-XA bulk compositions of magnesian metapelites is: carpholite-chlorite –»<br />
chlorite-chloritoid –» chloritoid-talc –» chloritoid-talc-kyanite –» talc-garnet-kyanite –»<br />
garnet-kyanite ± biotite. At low to medium P-T conditions, a low-XA stabilises the<br />
phengite-bearing assemblages associated with chlorite, chlorite + K-feldspar and<br />
chlorite + biotite while a high-XA results in the chlorite-phengite bearing assemblages<br />
associated with pyrophyllite, andalusite, kyanite and carpholite. At high-XA magnesian<br />
metapelites with nearly iron-free content stabilises the talc-kyanite-phengite assemblage<br />
at moderate to high P-T conditions.<br />
Taking into account the effective bulk composition and a(H2O) involved in the<br />
metamorphic history, the calculated phase-assemblage diagrams may be applied to all<br />
magnesian metapelites that have compositions within the system KFMASH and<br />
therefore may contribute to gaining insights into the metamorphic evolution of deep<br />
buried structural units. As an example, the magnesian metapelites of the Monte Rosa<br />
nappe have been investigated, and an exhumation path (following Alpine continental<br />
collision of the subdued delaminated Monte Rosa nappe) with P-T conditions for the<br />
western roof of the Monte Rosa nappe has been derived for the first time. The<br />
exhumation shows first a near-isothermal decompression from the Alpine eclogite peak<br />
conditions aro<strong>und</strong> 24 kbar and 505°C down to approximately 8 kbar and 475°C followed<br />
by a second decompression with concomitant cooling.<br />
- 158 -
Chemical composition and mineralogical composition of<br />
Saharan mineral dust over south east Morocco<br />
K. Kandler 1 , C. Deutscher 2 , M. Ebert 1 , H. Hofmann 1 , S. Jäckel 1 , A.<br />
Petzold 3 , L. Schütz 2 , S. Weinbruch 1 , B. Weinzierl 3 , S. Zorn 2<br />
1 Institute of Applied Geosciences, Darmstadt University of Technology, Darmstadt<br />
2 Institute for Physics of the Atmosphere, Johannes-Gutenberg-University, Mainz<br />
3 Institute of Atmospheric Physics, German Aerospace Center, Wessling<br />
The Saharan Mineral Dust Experiment (SAMUM) is dedicated to the <strong>und</strong>erstanding of<br />
the radiative effects of mineral dust. A joint field campaign focussed on the source-near<br />
investigation of Saharan dust was carried out in southern Morocco. Gro<strong>und</strong> based<br />
measurements were a performed near Tinfou and at the Ouarzazate airport; airborne<br />
measurements were carried out onboard a Falcon and a Partenvia aircraft. Together<br />
th th<br />
with Satellite observations, these measurements ranged from May 13 to June 7 , 2006.<br />
Airborne as well as gro<strong>und</strong> based samples were collected with a miniature impactor<br />
system on carbon coated substrates and carbon foils; additionally, filter samples were<br />
collected, of which the aerosol mass concentration was determined. The size-resolved<br />
particle aspect ratio and chemical composition is determined by means of electronmicroscopical<br />
single particle analysis. The mineralogical composition of the filter<br />
samples is determined by x-ray diffraction. Additional information on single particles will<br />
be collected by transmission electron microscopy.<br />
The bulk mineralogical composition was fo<strong>und</strong> to be dominated by major compo<strong>und</strong>s<br />
like quartz, calcite, feldspars (plagioclase and K-spars), and clay minerals<br />
(illite/muscovite, kaoline, and chlorite) and minor compo<strong>und</strong>s like hematite.<br />
relative fraction<br />
1.0<br />
0.8<br />
0.6<br />
0.4<br />
0.2<br />
n=50 n=361 n=1276 n=1329 n=209 n=13<br />
0.0<br />
1 10<br />
particle diameter, µm<br />
other<br />
carbonaceous<br />
sulfates<br />
mixtures<br />
silicates<br />
quartz<br />
halite<br />
gypsum<br />
other calcium rich<br />
carbonates<br />
titanium rich<br />
iron rich<br />
Fig. 1: Relative ab<strong>und</strong>ance of particles classes as function of particle diameter for a sample<br />
collected at 100 m altitude above the valley east of Ouarzazate, Morocco<br />
- 159 -
As an example, Fig. 2 shows the chemical composition of particles between 1 and<br />
1.5 µm in diameter as a function of measurement altitude over Tinfou for May 19, 2006,<br />
11:24 to 11:42 h. On this day, the mineral dust layer extended up to approximately 4.5<br />
km. The composition of the layer was quite homogeneous, except the sulfate-silicate<br />
mixtures on the gro<strong>und</strong> and at the top of the layer being more ab<strong>und</strong>ant than within. The<br />
latter indicates anthropogeneous influence in the bo<strong>und</strong>ary layer as well as in the<br />
tropospheric backgro<strong>und</strong>. On the other hand, the layer was not homogeneous in the<br />
horizontal as is shown by Fig. 1. 140 km to the north east, a significantly higher content<br />
of calcium-bearing particles can be detected, appearing as a mode aro<strong>und</strong> 3 µm<br />
diameter.<br />
elevation, m a. s. l.<br />
5,000<br />
4,000<br />
3,000<br />
2,000<br />
1,000<br />
iron rich<br />
titanium rich<br />
carbonates<br />
other calcium rich<br />
gypsum<br />
halite<br />
0.00 0.20 0.40 0.60 0.80 1.00<br />
relative ab<strong>und</strong>ance<br />
quartz<br />
silicates<br />
mixtures<br />
sulfates<br />
carbonaceous<br />
other<br />
Fig. 2: Relative ab<strong>und</strong>ance of particle classes as function of altitude over Tinfou, Morocco<br />
- 160 -
Diploma Theses<br />
Keil, Matthias; Entwicklung eines geologischen Modells zur Entstehung von Erdfällen in<br />
Nordhessen; Engineering Geology; Juli 2006.<br />
Naser, Simon Marek; Erk<strong>und</strong>ung von Deichen mit Georadar-Möglichkeiten <strong>und</strong><br />
Grenzen; Engineering Geology; April 2006.<br />
Schnitzspan, Anne; Risikoevaluation eines Rutschungsgebietes in Graach an der<br />
Mosel; Engineering Geology; April 2006.<br />
Magister Theses<br />
Witt, Bettina; Stadteilentwicklung als Konzept der Stadtförderung. Vergleichende<br />
Untersuchung zu Notwendigkeit <strong>und</strong> Umsetzung von Stadtteilförderungsprogrammen<br />
am Beispiel dreier Stadtteile; Geography; March 06<br />
Hartmann, Simone; Neue Konzeptionen in der Planung von Großsiedlungen <strong>und</strong><br />
Stadtteilen. Erfahrungen aus Fehlplanungen <strong>und</strong> Fehlentwicklungen von<br />
Großsiedlungen der 60er Jahre dargestellt am Beispiel Darmstadt Neu-Kranichstein;<br />
Geography; March 06<br />
PhD Theses<br />
Lindstaedt, Tamara; Regionsmarketing <strong>und</strong> die Bedeutung regionsbezogener Identität -<br />
Der Übergangsbereich der Verdichtungsräume Rhein-Main <strong>und</strong> Rhein-Neckar als<br />
Beispiel; Geography; October 06<br />
Vester, Barbara ; Feinstaubexposition im urbanen Hintergr<strong>und</strong>aerosol des Rhein-Main-<br />
Gebietes: Ergebnisse aus Einzelpartikelanalysen; Environmental Mineralogy; July 06<br />
Zeiß (Blau), Tatjana ; Die Struktur sek<strong>und</strong>ärer Versorgungsstandorte im südlichen<br />
Rhein-Main-Gebiet <strong>und</strong> die modellhafte Entwicklung eines räumlichen<br />
Verteilungsmusters; Geography; October 06<br />
- 161 -
MATERIALS SCIENCE<br />
Physical Metallurgy<br />
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Surface Science<br />
Thin Films<br />
Dispersive Solids<br />
Structure Research<br />
Chemical Analytics<br />
Theoretical <strong>Material</strong>s Science<br />
<strong>Material</strong>s Modelling<br />
<strong>Material</strong>s for Renewable Energies<br />
Joint Research Laboratory Nanomaterials<br />
Collaborative Research Center (SFB)<br />
APPLIED GEOSCIENCES<br />
Physical Geology and Global Cycles<br />
Hydrogeology<br />
Engineering Geology<br />
Applied Sedimentology<br />
Georesources and Geohazards<br />
Geomaterials Science<br />
Technical Petrology<br />
Environmental Mineralogy<br />
- 162 -<br />
www.tu-darmstadt.de/fb/matgeo