Report 2003 - Glass and Ceramics - Friedrich-Alexander-Universität ...

Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg6

1 ERLANGEN – THE UNIVERSITY TOWNErlangen was first referred to in 1002 during the reign of King Henry II. In 1402, it wasdeclared a town and came under the rule of the Earl of Hohenzollern at Nuernberg.Erlangen, being a small town at that time, was almost demolished during the 30 Years War(1618-1648), but was already growing when Earl Christian Ernst of Brandenburg-Bayreuthinvited the French Hugenottes to come to Erlangen, after the Decree of Nantes had beencancelled. In 1686, a new town, Christian-Erlang, was founded next to the old town ofErlangen. The two towns eventually grew together and formed the city which is todayknown as Erlangen. Christian-Erlang became a second residence of the Earl, after a castlehad been built there, and a knights` academy for the education of young nobles was addedin 1701. Later on, under the Earl of Brandenburg-Bayreuth, it became the BayreuthAcademy.Earl Friedrich of Bayreuth originally planned to establish the University in Bayreuth, sincein 1743 the University status had been bestowed on the Bayreuth Academy by EmperorKarl VII. Riots between students and officers of the Bayreuth garrison contributed to theEarl's decision to issue a decree ordering the University to be moved to Erlangen. Theuniversity was formally opened on November 4 th , 1743.The city and university of Erlangen went through various changes of government in the18 th and 19 th centuries. In 1769, Earl Alexander of Brandenburg-Ansbach inherited theprincipality of Brandenburg-Bayreuth after the Bayreuth line died out. He assumedresponsibility for the university, adding his name to that of the founder, so that the officialname of the university became "Friedrich-Alexander-Universität". In 1792, Alexanderceded his jurisdiction of Erlangen to Prussia, and in the following years the city wasadministered by the Prussian minister, von Hardenberg. After the Prussian defeat, the townand the principality of Bayreuth came under French rule until 1810, when Napoleonrelinquished them to the King of Bavaria. Between 1889 and 1916 many new universityinstitutes and hospitals were established.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg7

After World War II, the number of Erlangen residents rose up to 45,000 due to the refugeeinflux. The establishment of Siemens-Schuckert headquarters, today Siemens AG, in 1947formed the character of the city. Until 1927, the University of Erlangen had four faculties:theology, law, medicine, and philosophy. In that year, separation of the natural science andthe philosophy faculty created the natural science faculty. In 1961, the university wasexpanded. Incorporation of the School of Economic and Social Sciences in Nuernberg intothe old „Friedrich-Alexander-Universität“ resulted in the addition of a sixth faculty, thefaculty of Economic and Social Science. As a consequence, the university was renamed"Friedrich-Alexander-Universität Erlangen-Nürnberg". The Faculty of EngineeringSciences was constituted in 1966. The Educational Science Faculty was formed in 1972 byincorporating the Nuernberg College of Education into the university.Today the „Friedrich-Alexander-Universität Erlangen-Nürnberg“ comprises elevenfaculties and 23.615 registered students (WS 2003/2004). The large number of studentsand important research institutes contribute to the lively, intelligent and sophisticatedclimate of the city. However, not only the students think that Erlangen, with its manycultural activities, restaurants, and "pubs", is worthwhile to live in. A very-well-developednetwork of bicycle paths and public transport system, many parks and trees in the citycentre (in 1990 and 1991 Erlangen was nominated to be the "ecological capital" ofGermany) and, finally, a large variety of leisure activities provide a very high standard ofliving in the "capital of cyclists" at the gateway to Franconian Switzerland.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg8

2 THE FACULTY OF ENGINEERING SCIENCESThe idea of a Faculty of Engineering Sciences at the „Friedrich-Alexander-Universität ofErlangen-Nürnberg“ was already born in 1903. However, it was not before 1957 that theissue was presented to the University Senate for discussion. The first institutes wereformed in 1965 and 1966 within the Natural Science Faculty. The Faculty of EngineeringSciences was formally established on November 3 rd , 1966.Between 1964 and 1991, the campus of the Faculty of Engineering Sciences wasestablished at the southern outskirts of the city. It provides modern education and researchfacilities with equipment having a value of more than € 250 million. Almost 620 positionsfor scientific and non-scientific staff were provided by the State of Bavaria. In 2003, thefaculty comprised 46 chairs and 89 professors. The Faculty of Engineering Sciencesconsists of five subject areas: chemical engineering, electrical engineering, mechanicalengineering, computer science, and materials science. Each subject area offers a fullprogram course.Campus of the Faculty of Engineering SciencesReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg9

thesis (“Diplomarbeit”) of 6 months where upon the academic degree “Diplomingenieur”is granted.This reformed program is compatible with the international bachelor and master programs.Thus, beginning with the winter semester 2001/02, a new curriculum leading to theacademic degrees of Bachelor of Materials Science and Engineering (BSc) and Master ofMaterials Science and Engineering (MSc) was introduced. Both programs were approvedby the Bavarian Ministry of Science, Research, and Arts in summer 2001 for a period of 5years. The bachelor course is a 3 years program (6 semesters). The bachelor degreequalifies for the master program (1.5 years). The bachelor program is similar to the first 3years of the diploma program in the field of materials science and engineering, butcontains additional courses on economics and production technology.In summary, the reformed Materials Science and Engineering program of the University ofErlangen-Nürnberg preserves the advantages of the broad basic education in naturalscience and mathematics during the first 2 years but offers an intense, broad and deeplyspecified materials science and engineering education. Specialisation is focused on the last2 semesters, which prepares for professional life as well as for a subsequent doctoratestudy, leading to the academic degree “Dr.-Ing.” The structure of the reformed curriculumreduces redundancies to a minimum in order to a highly efficient progress of the studiestogether with the examinations immediately after each course. The following figure showsthe schematic structure of the diploma, bachelor and master program of the department ofmaterials science and engineering.In the winter semester 2002/03, the new curriculum “Materials in Medicine” wasintroduced in co-operation with the Medical School. An extensive training program ofbiomaterials for biomedical applications is offered. Optional courses include "Pyhsics inMedicine", "Computaional Sciences in Medicine", and "Medical Technology".Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg12

Curriculum Materials Science and Engineering1 st2 ndyear3 rdyear4 thyear5 thyear4 th Semester5 th Semester6 th Semester (Bachelor Thesis)7 th Semester8 th Semester9 th Semester (Final Thesis)DeepeningStudies CourseStudiesStudies ininCore CoreSubjectDiscipline1 st Semesteryear 2 nd Semester BasicVor-Studies3 rd CourseSemesterdiplomHauptdiplomBachelorMasterExams in the end of eachsemsterSchematic structure of the curriculumof Materials Science and EngineeringReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg13

ResearchA special feature of the Department is the broad spectrum of its research activities andknow-how, essentially covering all the material classes and functions, and extending frommaterial processing and characterisation to application in technical devices and systems.Research fields of common interest to all individual institutes include:• Processing of advanced composite materials with metallic, ceramic andpolymer matrices• Structure and properties of high temperature materials• Crystal growth and directional solidification• Interfaces and coatings• Material and processing modelling and simulation• Biomimetic MaterialsThe trend is to strengthen links between the different institutes and to enhance cooperation.A very useful tool in pointing out links between the different institutes of the Departmenthave been the "Erlanger Werkstofftage", which take place bi-annually and are dedicated toa topic of common interest to all institutes. In 1995, this topic was "Modelling of MaterialsPreparation and Properties", in 1997 "From Materials to Components", in 1999 "Materialsfor Medicine" and in 2001 "Awards at the Department of Materials Science".Casting of a glass melt for the "Girls Technology Course"Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg14

3 INSTITUTE III: GLASS AND CERAMICSGeneral IntroductionResearch at the Institute of Glass and Ceramics in 2003 was focused on fundamentalaspects of novel glass and ceramics processing techniques and on the microstructure -property correlation. In the field of ceramics processing, research centred on biotemplatingtechniques based on chemically modified cellulose template structures, polymer-fillerderived ceramic foams and rapid prototyping. Current research projects and activities inthe field of glass were the development of new glasses with special optical and dielectricproperties, modelling the Mie scattering of light on small particles in glasses, andmeasurements and analysis of strength and residual stresses of glasses for transportationapplications. In the field of functional ceramics, research was concentrated on the processdevelopment of ceramic multilayer technology and on LTCC materials (Low TemperatureCofired Ceramics). Glass-ceramic composites of different filler material and glasscomposition for LTCC applications were studied concerning their microstrcuturaldevelopment and their dielectric properties.Acquired new experimental equipment was focused on rapid prototyping, i.e. laminatedobject manufacturing (LOM) and 3D-printing. Starting in 2003, the institute is nowassociated with the new "Zentralinstitut für Neue Materialien und Prozesstechnik, ZMP"(Centre of Advanced Materials and Processing) and the "Zentralinstitut fürBiomedizinische Technik" (Centre of Biomedical Technology).Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg15

Members of the Institute of Glass and CeramicsReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg16

StaffProfessorsProf. Dr. rer. nat. Peter Greil (Head of Institute)Prof. Dr.-Ing. Andreas Roosen (Functional Ceramics)Prof. Dr. rer. nat. Rudolf Weißmann (Glass)Prof. Dr.-Ing. Reiner Gast, adjunct honorary professor (Chairman of LandesgewerbeanstaltBayern, Nürnberg, ret.)Prof. Dr. rer. nat. Helmut A. Schaeffer (Chairman of Hüttentechnische Vereinigung derDeutschen Glasindustrie, Frankfurt)SecretariesCandice AdleffEvelyne Penert-MüllerSenior Research AssociatesDr.-Ing. Henning Dannheim (Acad. Director) Mechanical ReliabilityDr. rer. nat. Heinrich MörtelSilicate CeramicsDr.-Ing. Frank MüllerBiomaterialsDr. rer. nat. Michael SchefflerPolymer Derived CeramicsDr. rer. nat. Heino SieberBiomimetic Materials SynthesisDr.-Ing. Nahum TravitzkyRapid PrototypingDr. rer. silv. Cordt ZollfrankBioengineered CeramicsResearch AssociatesBiomimetic Materials SynthesisDipl.-Ing. Jing CaoDipl.-Ing. Tobias FeyDr. Carlos Rambo (Ph.D.)Dr. rer. nat. Olga RusinaReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg17

BiomaterialsDr. Lenka JonášováDipl.-Ing. Sandro Tomas MartinsDr.-Ing. Uli LohbauerBioengineered CeramicsDipl.-Ing. Peter CrommeFunctional CeramicsDipl.-Ing. (FH) Georg BesendörferDipl.-Ing. Marcel HagymásiDipl.-Min. Stefan KemethmüllerDipl.-Ing Karin SchindlerDipl.-Ing. Alfons StiegelschmittDipl.-Ing. Michael Švec*Dipl.-Ing. Eduard Volz*Dipl.-Ing. Matthias Wagner*GlassDipl.-Ing. Svetlana Emelianova*Dipl.-Ing. René HennauerPolymer Derived CeramicsDipl.-Ing. Jürgen ZeschkyDipl.-Ing. Daniel SchwarzeRapid PrototypingMSc Thomas HöfnerDipl.-Ing. Lars WeisenselSilicate CeramicsThomas Jüttner* now in industryTechnical StaffDipl.-Ing. (FH) Ernst AdlerSabine BrungsFrancoise GröningEvelyn GruberBeate MüllerPeter ReinhardtAlena RybarKurt SandnerReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg18

Dipl.-Ing. (FH) Helmut HädrichMadeleine KerzelUrsula KlarmannGerhard MattauchAngela MeixnerEva SpringerHana StrelecAndreas ThomsenSteffi WaidhasAlfred ZaschkaTobias Fey discussing polymer derived ceramics withThomas Höfner (front) and Daniel Schwarze (right)Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg19

GraduatesInternshipsBernd LercheIn-vitro behaviour of Na 2 O-SiO 2 - and CaO-SiO 2 -gels in SBF and Ringer solutionFrank DebusInfluence of size and fraction of Al 2 O 3 -filler on the structure of and mechanical propertiesof ceramic foamsKristina LeßnauCeramic fibres from preceramic polymersRebecca VoigtIn-situ formation of carbon nanotubes (CNTs) in polymer derived ceramicsYeon-Suk JangSintering behaviour of SiC-glasscompositesDiploma ThesesThomas Höfner (Master Thesis)Manufacturing and characterization of polymer-derived ceramic light-weight sandwichstructuresReinhold MelcherPatterning of ceramics using micro-contact-printing of biotemplatesStefan SchoemakerDielectric properties of glass ceramicsCornelia TreulNovel glass ceramic composites manufactured from highly packed green bodiesReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg20

Ph.D.-ThesesOliver DernovsekLiquid infiltration process for manufacturing of fibre reinforced composite ceramicsSvetlana EmelianovaOptimising of Sm-doped borate glasses for spectral hole burning applicationsUlrich LohbauerFibre reinforced glass ionomer cements for dental applicationsEvelina VogliBiomorphous SiC-ceramics through gas-phase siliconizingEduard VolzCorrelation between electrical properties and microstructure in SiC-ceramicsHonouring Svetlana Emelianova for successful Ph.D. examinationReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg21

Visiting ScientistsProf. Dr. Wilson Acchar (July 2003)Departamento de Física, Universidade Federal do Rio Grande do Norte, Natal, BrazilTarcisio Andrade (since September 2003)Universidade Federal do Rio Grande do Norte, Natal, BrazilBrasilienDr. Mohammed Awaad (Mai-June 2003)Ceramics Department at National Research Center, Dokki, Cairo, EgyptProf. Dr. Ana Helena Bressiani (August 2003)Istituto de Pesquisas Energéticas e Nucleares (IPEN), Sao Paulo, BrazilDr. Magali De Campos (December 2002 – December 2003)Instituto de Pesquisas Energeticas e Nucleares (IPEN), Sao Paulo, BrazilDr. Ohmprakash Chakrabarti (September – November 2003)Central Glass and Ceramic Research Institute, Kalkutta, IndienBrian Chen (October – November 2003)Nat. Taiwan University, Institute of Materials Science and Engineering, Taipeh, TaiwanDr. Andris Cimmers (July-August 2003)Institute of Silicate Materials Technical University Riga, LatviaProf. Dr. Achraf Eminov (September – December 2003)Chemistry-Technology Institute, Taschkent, UsbekistanDr. Ahmed El Magrhraby (October 2003)Ceramics Department at National Research Center, Dokki, Cairo, EgyptReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg22

Prof. Dr. Salma Naga (Mai –June, October 2003)Ceramics Department at National Research Center, Dokki, Cairo, EgyptDr. Carlos Rambo (since September 2002)Istituto de Pesquisas Energéticas e Nucleares (IPEN), Sao Paulo, BrazilBrasilienAssistant Professor Dr. Ruta Švinka (July 2003)Institute of Silicate Materials Technical University Riga, LatviaProf. Dr. Visvaldis Švinka (July, November 2003)Institute of Silicate Materials Technical University Riga, LatviaSheng-Chang Wang (September – October 2003)Nat. Taiwan University, Institute of Materials Science and Engineering, Taipeh, TaiwanDr. Diva Wolff (November 2002 – November 2003)Universidade Federal do Rio Grande do NorteNatal, Brasilien, International Project CAPES/DAAD, BrazilBonnie Yu (September – October 2003)Nat. Taiwan University, Institute of Materials Science and Engineering. Taipeh, TaiwanReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg23

Evelina Vogli directing the "Girls Technology Course"Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg24

Laboratory and OfficesTotal space: 2050 m 2Laboratory: 1600 m 2Part of the processing workshopMain Equipment:Laboratories• Polymer processing laboratory• Bioengineering laboratory• Sol-gel laboratory• Ceramography workshop• Processing workshopAnalysis• Dilatometers (up to 1800 °C)• Thermal analysis (DTA/TGA/DSC/TMA)• 2 X-ray diffractometers (high-temperature)• Microwave (100 GHz) and ultrasonic devices for non-destructive testingReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg25

• 2 servohydraulic, high temperature mechanical testing systems• Gas absorption analyser• Hg high-pressure porosimeter• Electron paramagnetic resonance spectrometer• ICP-OES (Spectro Analytical Instruments) and N/O analyser• High-pressure liquid chromatograph• Geo-pycnometer• Laser granulometer• Micro hardness tester• Viscosimeter (Paar Physica) and high-temperature viscosimeter• Single fibre tensile testing, screw extruder and measurement unitMicrostructure• Environmental scanning electron microscope (ESEM)• Atomic force microscope/ colloidal probing facilities• Scanning electron microscope (with EDX and WDX)• Laser scanning microscope and Light Microscopes, Digital Microscope• FT-IR spectrometer and 2 UV-VIS-NIR spectrometers• 2 X-ray fluorescence spectrometers• Interactive image analysis system• 100 GHz microwave non-destructive testing device,• ESA acoustophoretic analyser• Fluorescence spectrometersProcessing• Kilns and Dryers (glass melting, high-temperature up to 2500 °C, vacuum)• Tape caster and Fibre winding facilities• Low-pressure injection moulding device• Thermal conductivity deviceReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg26

• Electrical measurements up to 1500°C• Screen printer• 3-dimensional optical dilatometer• Laser scattering particle size analyser• Automated polymer pyrolysis furnace• Advanced screen printing device• High precision cutting device• Lamination press• Langmuir-Blodgett trough for monolayer processingEva Springer and Katrin Zimmermann investigating ceramic materialsin the new environmental scanning electron microscopeReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg27

Jürgen Zeschky evaluating rheological parametersof preceramic polymer /filler powder mixtures with the laboratory kneader.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg28

4 RESEARCH PROJECTS / CO-OPERATION WITH INDUSTRYSurvey of Research ProjectsResearch continued to focus on basic aspects of ceramics, glasses and compositesprocessing. Materials for applications in microelectronics, energy, automotive,environmental, chemical technologies and medicine were developed. Fundamentalresearch in the fields of ceramics, glasses and composites was carried out in closecooperation with partners from national and international universities an industriesPROJECT RESEARCHER PROJECTLEADERNovel polymer derived ceramics from condensedmolecular precursorsProduction and properties of biomorphous ceramicfilters for purification of exhaust gasesCellulose derived silicon carbide fibre ceramicsfor thermal engineering applicationsCeramic multilayer technology with integratedmagnetic components for IT applicationsP. Cromme M. SchefflerT. Fey P. GreilO. Rusina H. SieberM. Hagymási A. RoosenMicro lenses in glass R. Hennauer R. WeißmannDevelopment of new glass ceramic composites S. Kemethmüller A. RoosenEnrichment and activation of human cells inbiocompatible gradient materialsPolymer derived ceramic substrates for novel thinfilm solar cellsF. Müller P. GreilM. Scheffler P.GreilBiomimetic materials synthesis H. Sieber P. GreilReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg29

RESEARCH PROJECT RESEARCHER PROJECTLEADERHigh precision manufacturing of polymerceramics for components in vacuum pumpsD. Schwarze P. GreilDevelopment and manufacturing of ceramicsubstrates for Si-thin film solar cellM. Švec/G. BesendörferA. RoosenHigh performance piezoelctric array devices fordigital loud speakers and steered array antennasM. Wagner A. RoosenPolymer ceramics for anti-friction bearing D. Schwarze P. GreilCeramic fibre composite materials for highperformance space craft propulsionFunctionalisation of polymer derived ceramicfoamsL. Weisensel P. GreilJ. Zeschky M. SchefflerBiomorphic ceramics for technical applications C. Zollfrank H. SieberNovel moulding materials for white waremanufacturingManufacturing of porcelain bodies by wetpressingStress-minimised design for manufacturing ofceramic multilayer substratesLight-weight refractories for fast-firing ofadvanced ceramics and porcelainFormation and self-healing of biomimetic apatitecoatings on chemically pre-treated titaniumT. Höfner P. GreilK. Schindler A. RoosenM. Hagymási A. RoosenT. Jüttner H. MörtelL. Jonášová F. MüllerReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg30

Selected Research ProjectsCeramic Processing: Peter GreilPorosity gradient foamsJürgen ZeschkyCeramic foams with a pronounced porosity gradient structure were generated by in-situfoaming of filler loaded preceramic polymer suspensions. Pore structure was tailored bycontrol of the polymer viscosity versus temperature and time. Foaming is based on foambubble nucleation rate, bubble growth rate and migration speed as well as on theconcurrent curing reactions and the resulting viscosity increase. The fractional densityvaried from 0.1 to 0.6 within 30 mm and the structure showed a transition from open cellto closed cell pores, fig. 1. The gradient of the cell porosity is accompanied by variationsof the connectivity density, structure model index and surface to volume ratio.60Fractional Density (%)5040302010Foaming temperature 245 °CFoaming temperature 265 °C00 5 10 15 20 25 30 35Height y (mm)Figure 1: Micro computer tomography of a polymer derived ceramic foam with gradientpore structure and fractional density distribution for two different foamingtemperatures.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg31

High temperature behaviour of Si/SiC filled Si-O-C foamsJürgen Zeschky, Herwig Peterlik (TU Vienna, Austria)The Young’s modulus, shear modulus and compression strength of Si/SiC filled ceramicfoams were measured at temperatures up to 1200 °C. The foams were oxidized up to 200hours and the effect of the oxidation on the surface microstructure was examined byscanning electron microscopy. Formation of porosity in the struts resulted in a reduction ofthe compression strength which, however, remained stable at prolonged oxidationtreatment after 10 hours. The foams were subjected to thermal shock quenching with atemperature difference of 1100 °C and 1400 °C for up to 10 cycles. This treatment reducedthe Young’s modulus and compression strength less than 20 %, fig. 2.Compression Strength (MPa)12111098765432100 200 400 600 800 1000 1200Temperature (°C)9Modulus (GPa)876543210Young's ModulusShear Modulus0 200 400 600 800 1000 1200Temperature (°C)Figure 2: Compression strength and elastic moduli of Si/SiC filled ceramic foams as afunction of the temperature.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg32

Functionalisation of Si/SiC filled ceramic foam from preceramic polymers:Jürgen Zeschky, Thomas Höfner, Michael SchefflerCeramic foams were manufactured from silicone resins, fig. 3. A novel foaming methodusing phenylmethyl silicone resins was developed which does not require additionalchemical or physical blowing agents. The foaming process is activated by heat treatmentbetween 200°C and 300°C. Water and alcohols are released as a result of polymer crosslinkingreaction. In a subsequent pyrolysis process at 1000 °C, Si-O-C micro compositefoams were obtained. The mechanical properties of the ceramic foams can be improvedand physical properties such as thermal expansion and electric conductivity can be adjustedto specific service conditions by adding functional fillers (Si, SiC, Al 2 O 3 , etc.). The opencell morphology makes polymer derived ceramic foams useful as carriers for automotive orimmovable exhausting clean-up catalysts, as carriers for microbes in biotechnology andwaste water purification systems.Figure 3: Open cell ceramic Si-O-C foam loaded with Si and SiC fillersReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg33

Ceramic sandwich panelsThomas Höfner, Jürgen Zeschky, Michael SchefflerLight weight ceramic sandwich structures with a foam core and surface cover tapes weremanufactured from Si/SiC filler loaded preceramic polymer systems. A polymer-fillerblend was in-situ foamed between two green tapes by a controlled heat treatment (blowing,curing and stabilization) at 270 °C. The sandwich element was subsequently pyrolyzed at1000 °C in nitrogen atmosphere to form a Si-O-C micro composite material. Themicrostructure and the mechanical properties of the sandwich structure were characterized,fig. 4.100Fractional Density [%]806040bottomsandwich paneltop20unconstrained foam0 1 2 3 4 5 6 7 8 9Height [mm]Figure 4: Pyrolysed ceramic sandwich and density distribution in dependence on thesample height.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg34

The interface strength between the foam core and the cover tape was controlled by varyingthe filler load of the foam, which effects the dimensional change misfit upon pyrolysis andthermal contraction. The foam of the sandwich structure exhibits a Weibull modulus m =13 (tension) and m = 8 (compression) and a crushing strength exceeding 4 MPa at afractional density of 0.27. The cover tape prevents the release of the gaseouspolycondensation products from the polymer melt. Due to pore ascent and the coalescenceof the pores beneath the cover tape, the porosity increased from the bottom to the top of thecore material.Mg reinforcement with ceramic foams: Jürgen Zeschky, Michael Scheffler,Jason Lo (CANMET, Ottawa, Canada), Jürgen Neubauer (Mineralogy, Erlangen)Due to the high interconnectivity of the pores, the Si/SiC filled Si-O-C foams arepredestined as reinforcement of light metal alloys such as Magnesium or Aluminium,fig. 5. Interpenetrating phase composites (IPCs) were manufactured by infiltrating the opencellular ceramic perform with Mg alloy melt at 680°C and a pressure of 86 MPa. Themechanical properties were found to depend on a reaction zone at the metal/ ceramicinterface with MgO, Mg 2 Si and Al 12 Mg 17 as the major reaction products. The IPCs showeda significantly higher creep resistance at 135°C, compression strength and elastic moduluscompared to the unreinforced magnesium alloys.10 mmFigure 5: Interpenetrating phase composite fabricated by Mg melt infiltration of Si/SiCfilled ceramic Si-O-C foam.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg35

Biomaterials: Frank MüllerBioactive titaniumTitanium treated in NaOH can form an apatite layer on its surface after exposure to SBF.Previous acid etching of titanium in HCl under inert atmosphere was examined as apretreatment to obtain an uniform initial titanium surface prior to alkali treatment. Acidetching in HCl leads to the formation of a micro-roughened surface, which remains afteralkali treatment in NaOH. In NaOH the passive TiO 2 film dissolves and an amorphouslayer containing alkali ions is formed on the surface. When exposed to SBF, the alkali ionsare released from the amorphous layer and hydronium ions enter into the surface layer,resulting in the formation of Ti-OH groups in the surface. The released Na + ions increasethe degree of supersaturation of the soaking solution with respect to apatite by increasingpH, and Ti-OH groups induce apatite nucleation on the titanium surface. The apatitenucleation was uniform, Fig. 6, and the thickness of precipitated HCA layer increasedcontinuously with time. The treatment of titanium by acid etching in HCl and subsequentlyin NaOH is a suitable method for providing the metal implant with bone-bonding ability10 µmFigure 6: HCA layer on chemically pre-treated titanium after 20 days in SBF.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg36

Bioactive gel coatingsCaO-SiO 2 sol-gel coatings were deposited on natural cellulose-based polymers with a 3Dporous network structure. Within 3 days in SBF a homogeneous calcium phosphate layerformed on the sample surface, fig. 7. The Ca/P ratio in the deposited layer was 1.63, whichis close to that of stoichiometric HA. At the beginning of the Ca-P layer precipitationcalcium leaches out from the gel resulting in the formation of Si-OH groups on the surface.The Si-OH groups serve as favourable sites for Ca 2+ 3-and PO 4 absorption from SBFresulting in the formation of a Ca-P enriched layer, which grows by consumption ofcalcium and phosphorus from the surrounding fluid. Sol-gel coatings of porous structurescan be used to enhance osteointegration of porous bone replacement materials andscaffolds for bone tissue engineering.Figure 7: SEM micrographs of Luffa aegyptiaca coated with CaO-SiO 2 gel after 3 days inSBF.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg37

Bioactive cellulose templatesThe basic crystallization behavior of calcium phosphate phases (Ca-P) precipitated from1.5 SBF was investigated using highly oriented Langmuir-Blodgett films of celluloseactivated in Ca(OH) 2 solution. Using transmission electron microscopy it was shown thatthe activated cellulose triggered the formation of nano-crystalline Ca-P phases, whereasspherical nano-aggregates were found on pure cellulose films. The formation of twodifferent Ca-P phases, i.e. octa calcium phosphate (OCP) and hydroxycarbonated apatite(HCA) was observed after 7 days in 1.5 SBF. Ca(OH) 2 pretreated 3D cellulose fabrics(Lyocell ® ) were homogeneously covered with a 30 µm thick HCA layer after soaking in1.5 SBF for 21 days, fig. 8. Thus, chemically pretreated cellulose fabrics with adjustableporosity may serve as a novel scaffold architectures for tissue engineering.250 µmFigure 8: SEM micrographs of 3D cellulose fabrics treated with Ca(OH) 2 after 21 days in1.5 SBF.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg38

Biotemplating: Cordt ZollfrankSoftlithography for Hierarchical Patterning of Ceramics: Reinhold MelcherThe anisotropic design of ceramic nanostructures involves advanced techniques forfabrication of novel functional devices. An interesting biomimetic route is the applicationof anisotropically structured biomacromolecules as templates for directed nucleation ofceramic materials. The polysaccharides exhibit a hierarchical multiscale order as well asself-assembly properties. The nucleation and growth of ceramic phases on biomolecularcellulosic templates was investigated. Softlithographic techniques such as micro contactprinting (µCP) were used to create micro-structured patterns of cellulose. The printedcellulose templates feature a supramolecular sub-structure due to the self-organisation ofthe bio-polymers. A silicon (Si-)wafer structured by conventional photolithography wasused as the master mould, fig. 9a. The stamps were made by curing polydimethylsiloxane(PDMS) on the master, fig. 9b. PDMS exhibits excellent properties for the reproduction ofthe mould patterns. The micro-patterned stamps were wetted with an ink of trimethylsilylcellulose(TMS-cellulose) solution and subsequently printed on solid substrates, fig. 9c.ZnO was nucleated by thermal decomplexation from aqueous Zn-salt solutions, fig. 9d.The materials were characterised by light and scanning electron microscopy (LM, SEM) aswell as FT-IR spectroscopy. Grazing incidence (GI) X-ray diffractometry was applied tocharacterise the cellulosic micropattern and the ceramic phase. The ultrafine structure ofthe printed TMS-cellulose was studied using atomic force microscopy (AFM). A novelbiopolymer ink based on cellulose was developed and the printing characteristics werestudied. A lower limit for the lateral dimensional reproducibility of the stampmicrostructure was approximately 1 µm. The lower limit observed for the TMS-celluloseink and subsequent µCP printing was 10 µm. Under optimum conditions, very fine lines ofthe dimension of 1 µm were transferred onto the substrate, fig. 9c.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg39

a) b) c) d)Figure 9: Light micrographs of the a) moulding master, b) PDMS-stamp, c) printed TMScellulosepattern, d) SEM micrograph of ZnO rods grown on the printed TMScellulosemicropattern.a) b)c) d)Figure 10: a) 3D-AFM-image of printed TMSC-area, b) line scan surface profile, b)PDMS-stamp, c) 3D-Fourier-Transform-(FT) plot of the real image a), d) 2D-FT-image of c) with the corresponding dimensions in real space indicated.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg40

The AFM analysis of the surface of the printed area revealed a sub-structure periodicity ofthe TMS-cellulose, fig. 10. The height of the globular TMSC-particles was 2-4 nm, whichis in the range of the three times the unit cell of TMSC. Individual spheres exhibiteddimensions of approximately 100 nm, according to the line scan given in fig. 10b. A moredetailed analysis of the surface structure was performed using Fourier-Transformation (FT)of the real images, fig. 10. The observed maxima are distributed over a wide range from 90to 360 nm in size, fig. 10d. The global maxima were located at approximately 250 nm. Theamplitudes are spatially distributed over an angle of 140°. FT-maxima are not observed inthe remaining 40°. This result indicates the spatial organisation of the TMSC on thesurface of the substrate. The specific diffraction peaks for TMS-cellulose, obtained by theGI-X-ray diffraction, were compared with conventional powder X-ray spectra of TMScellulose.The ZnO-ceramic phase was deposited on the µCP TMS-cellulose pattern fromzinc salt solution by thermal decomplexation, fig 10d. The ZnO crystallised only on theTMS-cellulose substrate. The prismatic ZnO was deposited on the printed templatestructure with a preferential orientation. The nucleated hexagonal ZnO prisms dominantlygrew with the c-axis perpendicular to the TMS-cellulose template surface, fig. 9d. Theresulting anisotropy is of particular interest for advanced functional applications in nanophotonicsand -electronics.Biotemplate triggered Nucleation of Ca-P-O Phases on Polysaccharides:Peter CrommeBioactive calcium phosphate (Ca-P) ceramics and glass ceramics are important biomedicalmaterials for tissue engineering, bone substitution and repair. The bioactivity of the Ca-Pmaterials can be related to their ability to induce the formation of apatite phases at theceramic to tissue interface. Several efforts have been made to investigate the principles ofbiomineralisation in an artificial system rather than in vivo. It was shown that highlyordered two dimensional organic films prepared by the Langmuir-Blodgett (LB-)techniqueare suitable for investigating the crystallisation of inorganic phases on biotemplates.Trimethylsilylether cellulose (TMS-cellulose) was synthesized from native cellulose.Multilayer templates were prepared on silicon wafers or on TEM grids using the LBtechnique.A part of the templates was converted into regenerated cellulose by cleaving thesilyl groups with hydrochloric acid vapour. The subsequent oxidation yielded the COOH-Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg41

cellulose. Additionally, spin coated chitosan films were prepared using a 1 wt.-% chitosansolution. The formation of apatite from simulated body fluid (SBF) was studied on alldifferent templates. Precipitation was carried out at a constant temperature of 37°C for 3days. AFM micrographs of LB-films of TMS-cellulose on silicon wafer exhibited ahomogeneous template structure with a preferred supramolecular orientation, fig. 11. TheFourier Transformation (FT) of the real image proved a preferential alignment of the TMScellulosesubstructures with a characteristic dimension of approximately 20 nm.Figure 11: a) AFM micrograph of 10 layers of TMS-cellulose. The arrow indicatesdirection of LB-film transfer, b) Fourier-Transformation of the real image.The morphology of Ca-P phases precipitated on TMS-cellulose layers exhibited an unusualneedle like habit, fig. 12a. The Ca/P ratios phases obtained by TEM-EDS analysis rangedfrom 1.3 to 1.6 indicating the formation of octa calcium phosphate (OCP) and hydroxylapatite (HA). The hydroxyl groups of the regenerated cellulose template triggered theprecipitation of nano-spherical aggregates of Ca-P-phases, with an Ca/P of 0.7-1.2,fig. 12b. The precipitates were aligned parallel to the dipping direction. The Ca-Pprecipitates on oxidised cellulose, fig. 12c, and on chitosan films, fig 12d, consisted oflarge spherical aggregates of nano-platelets with a Ca/P-ratio close to that of HA.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg42

Figure 12 : SEM micrographs of Ca-P-Phases after 3 days soaking in SBF on: a) TMScellulose,b) regenerated cellulose, c) oxidized cellulose, d) chitosan film.The different polysaccharide template structures exhibit a distinct influence on thebiomimetic formation of nano-sized Ca-P-phases from SBF. Cellulose and chemicallymodified cellulose templates offer promising characteristics as novel biotemplates forbioactive coatings in bone replacement materials.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg43

Rapid Prototyping: Nahum TravitzkyRapid prototyping (RP) technologies can automatically manufacture near-net shape partswith complicated geometry from Computer-Aided Design (CAD) data. The threedimensional part is built up by powder consolidation in layers (“additive” or “generative”process). For this reason, these techniques are often referred to as solid freeformfabrication or layered manufacturing. In general, a five-step approach of the productdevelopment is commonly applied: creating a CAD model, converting the CAD model intoSTL format, slicing the STL file into cross-sectional layers, fabrication of the product, andfinally surface finishing of the product. RP techniques have many benefits over traditionalmethods for model generation , tools and even construction of production-quality parts. Forinstance, in contrast to “subtractive” processes (e.g., drilling, milling, grinding) the“additive”-RP methods allow fabrication of products with complex internal pore structurethat cannot be manufactured by other approaches. RP techniques can significantly shortenfabrication times with small personnel expenditure and reduce product costs when appliedproperly.The main research objective of Rapid Prototyping Group is to obtain fundamentalknowledge of the use of RP technologies for fabrication of complex shaped ceramic andceramic/metal composite components. An additional goal is to study the effect of postfabricationtreatments (e.g., heat treatments, metal infiltration) on the final phasecomposition, microstructure and surface quality of products fabricated via different RPprocessing routes: Laminated Object Manufacture (LOM), Tree-Dimensional Printing (3D-Printing) and Selective Laser Curing (SLC).Laminated Object Manufacture (LOM): Lars WeisenselLaminated Object Manufacturing is an established rapid prototyping process whichproduces three-dimensional objects with sheets of paper, polymer, metal or a combinationof both. It can be considered as a hybrid between “subtractive” and “additive” processes:the parts are indeed built up in the layer by layer approach (“additive” process), but eachlayer is individually cut by a special tool (“subtractive” process) in the shape of the crosssection of the part. Each layer is bonded to the previous layer by using a heated plate,Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg44

which melts an adhesive coating on the bottom side of the sheets (e.g., paper). We coulddemonstrate, that ceramic parts made of SiSiC can be fabricated by LOM process usingphenolic resin coated carbon paper as starting material. After LOM the carbon precursor ispyrolysed in nitrogen atmosphere and the porous carbon preform is finally infiltrated withliquid silicon. Fabricated SiSiC parts exhibit high resistance to chemically aggressiveenvironments and thermal stability up to 1350°C.Three-Dimensional Printing (3D-Printing): Katrin ZimmermannAt the beginning of the 3D-Printing process, a layer powder is spread, fig. 13. The gantryon which the roller and the print head are mounted moves from left to right, the roller(drawn as a circle) collecting powder which then is spread as a thin layer over the builtpiston. Excess powder is discharged through the powder overflow chute. In the second stepthe gantry moves backwards while the printer assembly (drawn as a square) applies abinder solution to the powder, which causes the powder particles to bind to one anotherand to the printed cross-section one level below. The part is built in the layer-by-layerfashion. Finally the feed piston comes up one layer of thickness and the built piston dropsone layer of the thickness so that the process can be repeated. After building the part, theexcess powder is removed.a bFigure 13 . Schematic presentation of 3D-printing process.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg45

The following figure 14 shows a SiSiC part of complex geometry (engine block having alength of 60 mm) fabricated by 3D-Printing process.15 mmFigure 14: Downscaled model of a SiSiC engine block fabricated by 3D-Printing method.Selective Laser Curing (SLC): Tobias FriedelSelective Laser Curing (SLC) was investigated in co-operation with the Institute ofManufacturing Technology, University Erlangen-Nürnberg. Polymer derived ceramic partsof complex shape were fabricated layer by layer from a powder bed without using anymould or shaping device. Either Al 2 O 3 or SiC loaded polysiloxane thin powder layers weresequentially cured by a CO 2 laser (λ=10.6mm) beam. After building the part, the excesspowder which was supporting the product, was removed. The cured bodies were convertedto Si-O-C/Al 2 O 3 and Si-O-C/SiC ceramic parts in a subsequent pyrolysis treatment at 1200°C in nitrogen atmosphere. Due to the filler loading (40, 50 or 60 vol%) the linearshrinkage after pyrolysis was less than 2 %. Thus, the SLC approach can be considered asa near-net-shape forming process of ceramic components with complex geometries. TheReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg46

properties of the produced parts depend both on the composition of the starting powder andthe parameters of the laser radiation. The scanning speed and the power of the CO 2 -laserbeam were varied, leading to pronounced differences in material properties. Laserirradiation on a powder mixture containing 50 vol-% polymer and 50 vol-% Al 2 O 3 lead torelative green densities of 45% to 65%. Relative densities increased to 53% - 69% afterpyrolysis. The average pore diameters of pyrolysed materials ranged between 1.0 and 3.1µm. A subsequent infiltration with liquid silicon was carried out in order to produce denseparts. A turbine wheel with a diameter of 45 mm was successfully produced as ademonstrator, fig 15.15 mmFigure 15 . A Si-O-C/SiC/Si turbine wheel fabricated by SLC technique.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg47

Mechanical Reliability: Henning DannheimLifetime Prediction for different Ceramic MaterialsLifetime prediction is a very useful tool regarding the reliability of ceramic devices. Tocalculate the fracture probability of ceramic materials, it is necessary to know the Weibullparameter m and the characteristic stress S 0 as well as the parameters n and A of the subcriticalcrack growth. The first parameter were determined by measuring the inert strengthwith different methods like 4-point bending or double-ring testing, the second parametersby the method of dynamic fatigue. From the results SPT - diagrams (Strength-Probability-Time) were generated for various ceramic materials.LTTC multilayer ceramics: Andreas Roosen, Francoise GröningMultilayer ceramics based on LTCC (Low Temperature Co-fired Ceramics) obtainedincreasing interest in the manufacturing of high-integrated devices for microelectronicapplications. In many applications the parts are exposed to mechanical loading stresses,which is an important issue regarding the reliability of the device.4σ = 200 MPa 150 MPa 100 MPaFracture Probability lnln(1/1-F)20-2-4-6-8-10-1299.9463.21.80.0335x10 -6Fracture Probability-145 10 15 20 25 30 35Liftime ln(t B)Figure 16: SPT diagram for a LTCC ceramic.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg48

To predict the lifetime of LTCC multilayer devices and to extend the application range ofLTCC basic mechanical data are needed. Sintered LTCC laminates were investigatedconcerning their flexural strength, crack growth rate, and lifetime prediction. The flexuralinert strength of the investigated LTCC material was in the range of 410 -450 MPa,measured by the ball-on-ring method. Thus, an acceptable lifetime will be achieved Inapplications with a stress level of 100 MPa, like mass flow sensors for the measurement ofinjected fuel quantities.Nondestructive testing of green ceramics with microwaves: Helmut Hädrich,Sandro MartinsFor the non-destructive testing of green bodies a novel high frequency microwave set upwas developed. Operating at a frequency of 94.1 GHz defects with a minimum size of lessthan 300-500 µm can be detected by transmission analysis. As an example figure 17 showsa low pressure injection moulded ß-TCP ceramic bar. A large defect, probably caused byan inadequate mould filling due to an air bubble inclusion in the melted feedstock can beseen near the top of the bar. The capability of high frequency microwave inspection todetect internal defects may allow to identify defect containing green components in anearly stage of manufacturing. Thus, the process variables may be controlled and optimisedto improve the quality of the ceramic injection moulding process.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg49

Figure 17: Low pressure injection moulded ß-TCP specimen and the correspondingmicrowave c-scan.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg50

Silicate Ceramics: Heinrich MörtelNon-conventional fluxes for porcelainGabbro rocks from Sinai were beneficiated by high gradient magnetic separation and grainsize classification to produce plagioclases as a flux for white ware industry. Theplagioclase fraction could be applied successfully to porcelain and stoneware industrywhereas the magnetic minerals containing fraction could be applied to stoneware and tileindustries. A black body for roofing tiles and a black glaze for these roofing tiles could beverified. Dense firing was achieved at remarkably low sintering temperatures.Spodumen-Alumosilicate Composite Ceramicsß-Spodumen-Aluminosilicate composite ceramics were investigated in co-operation withthe National Research Centre, Cairo, Egypt. Conventional mineral raw materials, whichwere extremely fine ground were compared with materials from a sol-gel-process. Themechanical and electrical properties of sintered composites were analysed for potentialapplications as functional materials in electronic industry.Light weight refractoriesFine ground raw materials containing kaolinite, alumina and silicon carbide were foamedby a process analogue to the aerated concrete manufacturing technology. After foamingwith aluminium powders the highly porous green products were sintered at hightemperatures. Novel light weight refractories could be verified with applicationtemperatures exceeding 1300 °C. Light weight refractory materials which are stable up to1650 °C were manufactured at laboratory scale. The role of stabilising agents for tailoringthe pore microstructure of the foams and the role of different aluminium powders wereinvestigated in co-operation with the Technical University, Riga, Lativa, fig. 18.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg51

a)b)Figure 18: a) Light weight refractories with different pore sizes;b) typical microstructure the light weight refractories.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg52

Glass: Rudolf WeißmannInfluence of Al on the spectral –hole-burning mechanism in borate glassesThe persistent spectral hole burning (SHB) method has been applied to study the dynamicsof spectral hole burning in inorganic glasses doped with rare-earth ions. The latter providethree burning mechanisms that act at different temperatures and yield different holelifetimes: photoreduction, photophysical arrangement and photoionisation mechanism.Photo-ionisation mechanism has the potential to create the thermally most stable holes. Anexample is SHB in divalent Samarium in silicate and borate glasses. The Sm 2+ -dopedglasses is one of the few materials in which persistent holes can be burned at roomtemperature. Sm 2+ -doped solids are especially attractive because of the two-photon natureof the photoionisation process, which makes the holes resistant against read-out. The alkaliborate glasses combine two properties that affect the impurity electronic spectra - a rigidnetwork of light atoms and a variety of structural units. The first of these properties leadsto high phonon frequencies and a relatively weak thermal broadening of the homogeneousline widths of the electronic transitions. The variety of the boron-oxygen structural unitsleads to large inhomogeneous widths of the transitions. These properties together with thephotoionisation mechanism provided by divalent Samarium ions and electron traps makethe Sm 2+ -doped borate glass one of the few materials in which persistent spectral holes canbe burned at room temperature.The effect of modifying the structure of borate and borosilicate glasses with Al wasinvestigated in detail. Changes of the local environmental of the ions, caused by modifiedchemical composition, are reflected in the spectral characteristics of these ions. It is wellknownthat Al has the favourable effect of narrowing the holes. This effect is ascribed tothe capturing of non-bridging oxygen from around the Sm 2+ ions by Al ions which leads tolower density of low-frequency vibrations. In addition to the measurement of temperaturedependencies of the hole-widths in the 5 D 0 - 7 F 0 transition of Sm 2+ in sodium borate andsodium borosilicate glasses with different Al content, the effect of Al to theinhomogeneous broadening and shift of this transition was studied. In contrast toalumosilicate glasses the hole burning efficiency decreases with the increasingconcentration of Al.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg53

Edge strength of flat glassThe edge strength plays an important role for production, machining, transport and designof flat glasses. Applications in the motor vehicle range, commercial and residentialbuildings, large-area glass substrates for solar cells and display glasses for thecommunication technology are some examples. Under uniform load a glass plate can faileither along an edge or on an interior surface depending on plate geometry and the relativeseverities of surface and edge flaws. For example, under thermal action a glass plate willbreak only at a point along the edges because largest stresses occur along the glass edges.Unfortunately there is a severe lack of reliable data about the edge strength and nostandardised test equipment available. In collaboration with the glass and automotiveindustry a mechanical test device was established for determining the edge strength ofannealed and heat strengthened glass.Figure 19: Four point bending set-up for edge strength investigationThe device is based on a 4-point vertical fixture with a support span of 92 mm and a loadspan of 50 mm, fig. 19. This equipment allows testing of glass specimens – 1-8 mm thick,100-120 mm long and approximately 10-20 mm high with different edge finishes. Contraryto the common 4-point test method after DIN EN 1288 the height of the glass sample (10-20 mm) can not be neglected compared to the load span of 50 mm. The tensile stresses atthe edge within the load span is not constant. FEM-simulation proves that the maximum ofthe tensile stress is not located in the central region but about 18 mm from the midpoint,fig. 20. For this reason, depending from the origin of fracture, it is necessary to correct theReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg54

tensile stresses calculated from the standard 4-point bending formula to get the correctfracture strength. The frequency distribution of the fracture origin measured on 720samples confirms this fact, fig. 211,051,00Normalized stress0,950,900,850,80FEM - dataB0,75-30 -20 -10 0 10 20 30Distance from the Centre mmFigure 20: Stress distribution around the centre of the edge lineFrequnecy2001801601401201008060402000 5 10 15 20 25 30Origin of fracture from the centre in mmFigure 21: Frequency distribution of the fracture originReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg55

Functional Ceramics: Andreas RoosenSintering of ferrite/dielectric LTCC-Tape Composites: Marcel HagymásiThe miniaturisation potential of LTCC devices would be drastically improved ifinductances were available which can be directly integrated into the multilayer structure. Anewly developed ferrite green tape with a permeability of µ rel > 10 at a frequency above0.2 GHz on the basis of a BaFe 12 O 19 - glass composites enables integration of new passivedevices, e.g. circulators. In order to fabricate a composite structure of these two differentgreen tapes via LTCC technology, the ferrite tape must also sinter at temperatures as lowas 900°C. Co-firing of ferrite tapes in combination with various commercial dielectrictapes was investigated. Green microstructure, thermo-mechanical behaviour, binderburnout and sintering behaviour were analysed. The shrinkage behaviour was studied bymeans of an optical dilatometer which allows the observation of warpage and delaminationeffects of ceramic green tapes. The investigated LTCC tapes showed a complexdensification behaviour concerning temperature and totl shrinkage. The sintering processof conventional dielectric tapes starts at 680-710 °C and is finished at 850 °C when theglass phase crystallised. In contrast to dielectric tapes, the shrinkage of the ferrite tapebegins at higher temperatures above 710 °C and requires a higher peak temperature above850 °C and a dwell time of 3 hours. Moreover, the tapes show different values of totalshrinkage: dielectric tapes shrinks about 9-13 %, the ferrite tape exhibits a shrinkage ofmore than 20 %. Due to these differences, transient stresses are likely to occur at differentsintering stages and may lead to defects like cracks, delaminations and warpage, fig. 22.One source for stress generation are dissimilar densification kinetics caused by differentsintering temperature and shrinkage values. If the thermal expansion coefficient differs, amismatch stress can also be generated during the cooling stage. In addition, debonding ofthe interface ferrite/dielectric tape and warpage effects occur.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg56

Adielectric tapeBferrite tape 100 µmFigure 22: a) Warpage of a dielectric/ferrite composite tape after the co-firing process.b) Cracks in tensile layer of such composites due to the mismatch of thermalexpansion, generated during cooling.Manufacturing of defect-free composites requires further improvements of the greendensity of the ferrite tape to reduce total shrinkage. The sintering profile concerningheating rate, dwell time and peak temperature as well as cooling rate must be optimised.Furthermore, the adhesive forces between the tape interface must be controlled, since theymust be high enough to prevent delamination. This is also important for zero-shrinkageconcepts in LTCC manufacturing, which will be investigated in the future.Development of Glasses for Glass-Ceramic Composites: Stefan Kemethmüller, incooperation with R. Hennauer, R. WeissmannLow Temperatures Co-fired Ceramics (LTCC) offer new opportunities to miniaturisemicroelectronic devices. For high frequency applications in the GHz range, materials oflow or medium dielectric constant and of low dielectric losses are required. Such LTCCmaterials must densify below 900 °C, and in the sintered state they must exhibit acoefficient of thermal expansion (CTE) which is close to silicon. These requirements arefulfilled by the use of glass-ceramic composites. The glass must form a low viscosity meltat low temperatures (< 900°C) to achieve liquid phase sintering. At frequencies in the GHzrange, a glass exhibits higher dielectric losses than a crystalline phase, so the glass fractionhas to be reduced after densification by crystallisation. The ceramic filler is selected tooptimise the dielectric, thermal and other properties. The filler material should exhibit asimilar CTE to the glass- system and should also have a limited solubility in the glass. TheReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg57

most relevant filler materials are Al 2 O 3 and mullite or mixtures of both. In a joint projectwith Torrecid S.A., Spain, a crystallisable cordierite glass system was developed suitablefor LTCC processing. Cordierite exhibits a low dielectric constant in the high-frequencyregion and a low CTE, but a melting temperature of 1470 °C. Crystallisable cordieriteglass usually has a softening point of 870 °C. The softening temperature was lowered to650 °C by addition of specific oxides. In order to achieve a crystallization at temperaturesbelow 900°C and to increase the crystallization velocity different nucleation agents wereadded. A statistic design of experiments (DoE) was performed in order to select theoptimum processing parameters. As a result of the DoE-approach, glass-ceramic samplescould be sintered at 870 °C for 2 hrs, which exhibited an amount of 37 wt.-% ofcrystallised cordierite. TEM and SEM investigations were carried out to study the kineticsof the crystallisation, fig. 23.FillerGlassFillerGlasscordierite2 µm 2 µm0.5 h at 870°C 2.0 h at 870°CFigure 23 : SEM micrographs of the glass-ceramic composite after 0.5 h and 2.0 h holdingtime at 870°C in airReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg58

Biomimetic Materials Synthesis: Heino SieberOver the last years, various high-temperature biotemplating techniques were developed formanufacturing of ceramic materials with biomorphic microstructures. Considerable effortshave been devoted to the production of dense biomorphous SiSiC-ceramics by reactivemelt infiltration with liquid Si of different species of pyrolysed wood preforms. Highlyporous, cellular, single-phase SiC-ceramic were obtained by vapour phase reaction withdifferent Si-containing gases. All of the developed techniques require at least a two-stephigh-temperature treatment to obtain the final microcellular SiC-based ceramics: i)pyrolysis of the biotemplate into biocarbon, and ii) an infiltration step with an additionalhigh-temperature treatment, e.g. reactive melt, vapour or metal-organic solution. Theknowledge of the reaction mechanism and the parameters controlling the microstructureare important tools for designing the properties of the ceramics in terms of grain size,phase composition and phase distribution.Microstructure evolution in biomorphous SiSiC-ceramic composites: Cordt ZollfrankLiquid Si-infiltration (LSI) of wood derived biocarbon templates (C B -templates) yieldsbiomorphous SiSiC-ceramics with a morphology of the initial biological preform, fig. 24.The biomorphous SiSiC-ceramic consists of solidified Si in the cell lumina, polycrystallineβ-SiC and residual carbon islands located at the position of former wood cell walls. Twodifferent SiC-morphologies are formed: coarse SiC-grains with average grain sizes ofabout 15 µm at the Si/SiC-interface and a nano-grained SiC-phase with average grain sizesof 10-80 nm, located at the SiC/C-interface. The final amounts of the individual phasesdepend on the anatomy of the initial biocarbon template as well as on the reaction time.The microstructure evolution during LSI-processing of biocarbon templates can beexplained by a stepwise mechanism for the reactive SiC-phase formation involvingdiffusion as well as dissolution and re-crystallization processes. The reactive LSI-processand the SiC-phase formation were investigated in detail in biocarbon templates due to thewell-defined (uni-directed) pore morphology.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg59

a)Vb)LWEWLF100 µmc)LWEW100 µmd)SiCCSiT100 µm 100 µmLWEWFigure 24: SEM-micrographs of the biocarbon template of a) beech and c) pine wood,biomorphous SiSiC-ceramic derived from c) beech and d) pine wood after LSIat 1550°C. EW: earlywood, LW: latewood, LF: libriform fibres, V: vessels, T:tracheids, C: carbon, Si: silicon, SiC: silicon carbide, dotted line: annual ring.The results obtained from the SiC-reaction mechanism and microstructure evolution inbiomorphous SiSiC-ceramics may be applied in general to the SiC-phase formation inconventional LSI-materials. Major steps in the reactive infiltration process include, fig. 25:a) nucleation stage at T

Figure.25: Schematic sketch of the four proposed reaction steps for the LSI-processing ofporous, biocarbon templates into SiSiC-ceramic composites.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg61

Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg62

5 PUBLICATIONSPapers (alphabetical order)1/03 W. Acchar, D. Schwarze, P. GreilSintering of Al 2 O 3 -NbC composites using TiO 2 and MnO additives: preliminaryresults, Materials Science and Engineering A 351 (2003) 299-3032/03 J. Cordelair, P. GreilApplication of the method of images on electrostatic phenomena in aqueousAl 2 O 3 and ZrO 2 suspensions, Journal of Colloid and Interface Science 265 (2003)359-3713/03 T. Jüttner, M. Mörtel, V. Svinka, S. Krebs, C. SchlenkNovel Lightweight - Refractories for high Temperature Application in CeramicsIndustry, Stahl und Eisen, Special (2003) 154-1584/03 U. Lohbauer, J. Walker, S. Nikolaenko, J. Werner, A. Clare, A. Petschelt,P. GreilReactive fibre reinforced glass ionomer cements, Biomaterials 24 (2003) 2901-29075/03 R. Melcher, P. Cromme, M. Scheffler, P. GreilCentrifugal Casting of Thin-Walled Ceramic Tubes from Preceramic Polymers,Journal of the American Ceramic Society 86 (7) (2003) 1211-136/03 F.A. Müller, L. Jonášová, P. Greil,Biomimetic apatite formation on bioinert metals and polymers. Biomaterialien 4(2003) 231Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg63

7/03 P. GreilPyrolysis of Active and Passive Filler-loaded Preceramic Polymers, Handbook ofAdvanced Ceramics, ed: S. Somiya, Elsevier Pub. (2003) 369-3908/03 W. Pompe, H. Worch, M. Epple, W. Friess, M. Gelinsky, P. Greil, U. Hempel,D. Scharnweber, K. SchulteFunctionally graded materials for biomedical applications, Materials Science andEngineering, A362, (2003) 40-609/03 R.M. Rocha, P. Greil, J.C. Bressiani, A.H.A. BressianiDevelopment and Characterization of Si-Al-O-N-C Ceramic Composites Obtainedfrom Polysiloxane - Filler Mixtures, Materials Science Forum Vols.416-418 (2003)505-51010/03 M. Scheffler, E. Pippel, J. Woltersdorf, P. GreilIn situ formation of SiC -Si 2 ON 2 micro-composite materials from preceramicpolymers, Materials Chemistry and Physics 80 (2003) 565 – 57211/03 R. Schmidt, A. Stiegelschmitt, A. Roosen, A.W. BrinkmanScreen printing of co-precipitated NiMn 2 O 4+δ for production of NTCR thermistors.J. Europ. Ceram. Soc. 23 (2003) 1549-155812/03 N. Travitzky, P. Kumar, K.H. Sandhage, R. Janssen, N. ClaussenRapid syntheses of Al 2 O 3 reinforced Fe-Cr-Ni composites. Mat. Sci. Eng. A344(2003) 245-252.13/03 N. Travitzky, P. Kumar, K.H. Sandhage, R. Janssen, N. ClaussenIn-situ synthesis of Al 2 O 3 reinforced Ni-based composites. Adv. Eng.Mat. 5(4),(2003) 256-259.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg64

14/03 N. Travitzky, I. Gotman, N. ClaussenAlumina-Ti Aluminide Interpenetrating Composites: Microstructure andMechanical Properties. Mat. Lett. 57 (2003) 3422-3426.15/03 L. Weisensel, F. Müller, N. Travitzky, P. GreilMicrostructure and mechanical properties of AIN /Al-Si multilayer compositesfrabricated by reactive melt infiltration technique, Journal of Materials ScienceLetters 22, (2003) 721 – 72316/03 C.C.T. Yang, W.C.J. Wei, A. RoosenElectrical conductivity and microstructures of La 0.65 Sr 0.3 Mn 3 - 8 mol% yttriastabilizedzirconia, Mater. Chem. Phys. 81 (2003) 134-14217/03 J. Zeschky, F. Goetz-Neunhoeffer, J. Neubauer, S.H. Jason Lo, B. Kummer,M. Scheffler, P. GreilPreceramic polymer derived cellular ceramics, Composites Science and Technology63 (2003) 2361-2370Proceedings (alphabetical order)18/03 A. El-Maghraby, H.A. Mobarak, I. Bakr, H. Mörtel, S.M. NagaAnorthite ceramics based on plagioclases concentrated from gabbro, Cimtec 2002 -10 th International Ceramics Congress , Int. Symposium: Science for NewTechnology of Silicate Ceramics, (2003) 319-32519/03 P. GreilWerkstoffentwicklungen an der Schnittstelle zur BiolgieChemie und Gesundheit – Visonen, WING-Werkstoffinnovationen für Industrieund Gesellschaft, PTJ, Weimar (2003) 122-131Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg65

20/03 D. Pohle, M. Wagner, A. Roosen:Processing-oriented technique to characterise the shrinkage behaviour of thick-filmpastes and green tapes, in: 14 th European Microelectronics and PackagingConference, Friedrichshafen, June 2003, IMAPS Germany, 2003, 427-43221/03 H. Sieber, C.R. Rambo, J. BenešManufacturing of biomorphous TiC-based ceramics Ceramic Engineering andScience Proceedings 24 (3),, 27 th Annual Cocoa Beach Conference on Composites,Advanced Ceramics, Materials, and Structures: B, ed. by W. Kriven and H.T. Lin,The American Ceramic Society (2003) 135-14022/03 V. Svinka, H. Mörtel, S. KrebsNovel light weight refractory bricks, Cimetec 2002, 10th Int. Ceramics Congress,Int. Symposium: Refractories: Trends and Research and Applications, (2003) 149-161,23/03 V. Svinka, H. Mörtel, S. KrebsNew technology for kaoline based refractory bricks, Cimtec 2002 - 10 thInternational Ceramics Congress, Int. Symposium, Refractories: Trends in Researchand Applications, (2003) 167-17524/03 R. WeißmannStresses and Stress Measurement in Glasses, in: Strength of Glass, Basic and TestProcedures, Verlag der Deutschen Glastechnischen Gesellschaft, Offenbach/Main200325/03 R. WeißmannPrüfung der Kantenfestigkeit von Flachglas mittels Vierpunktbiegemethode, HVG-Mitteilung Nr. 2040, April 2003Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg66

26/03 R. WeißmannKantenfestigkeit von Glasscheiben, in Glas im Automobil II, Ed. E. Steinmetz,Expert Verlag 200327/03 R.Weißmann, W. ChongGlasses for Thick Film Resistors, Proceedings of the Joint technical CommiteeMeeting of DGG and DKG, Glass and Ceramics-Synergies for Innovations, Berlin2001, S 65-7028/03 R. WeißmanIonenaustausch, in: Oberflächenveredelung von Glas, Verlag der DeutschenGlastechnischen Gesellschaft, Offenbach/Main 200329/03 R. WeißmannGlas-Polymer-Verbund, in: Oberflächenveredelung von Glas, Verlag der DeutschenGlastechnischen Gesellschaft, Offenbach/Main 200330/03 C. Zollfrank, H. Sieber, P. GreilBiomorphous ceramics from wood for engineering applications. Proc. of the 12 thISWPC Vol. II: poster presentation, University of Wisconsin-Madison, June 9-12,2003 WI-USA, 223-22631/03 C. Zollfrank, O. ParisThermal degradation of wood and microstructure of biocarbon. Proc. of the 12 thISWPC, Vol. I: oral presentation, University of Wisconsin-Madison, June 9-12,2003, WI-USA, 349-352Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg67

Fluorescence spectrometry on biomorphous oxide ceramic compositesReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg68

Conferences, Seminars, Invited LecturesConferences and Seminars organised by members of the InstituteSymposium “Optoceramics”, March 27 th , 2003, Munich, A. Roosen: chairmanSymposium “Hans-Walter-Hennicke Preis 2003” of the Deutsche KeramischeGesellschaft, September 16 th , 2003, Munich, A. Roosen: chairmanDKG-Symposium on Ceramics Processing: “Computer Aided Manufacturing in CeramicIndustries”, December 2 nd - 3 rd , 2003, Erlangen, A. Roosen: chairmanMaterials Week/Ceramitec 2003, Session "BiomimeticMaterials, Munich,September 16-18, H. Sieber: chairmanPeter Greil (mid) discussing scientific issueswith Heino Sieber(right) and Cordt Zollfrank (left)Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg69

Invited Lectures08.01.03 C. Zollfrank:"Structural cellulose chemistry"Chemistry department, University of Bremen, Bremen, Germany06.02.03 P. Greil:"New Materials - Key Technologies in Bavaria"Bavarian Mission in Berlin, Diplomatic Corps, Germany10.02.03 P. Greil:"Cellulose Templates for Multiscale Processing of Ceramics"Mat. Sci. Symp., Nagoya Inst.of Technology, Nagoya, Japan12.02.03 P. Greil:"High Precision Manufacturing of Polymer Derived Ceramics"NGK Spark Plugs, Nagoya, Japan05.05.03 R. Weißmann:"Strength and strength enhancement of flat glass"Fachschulkolloquium, Zwiesel, Germany07.05.03 R. Weißmann:"Specific properties of glass and ceramics"Bavarian workshop on laser applications, Erlangen, Germany12.05.03 C. Zollfrank, P. Cromme:"Cellulose: A versatile tool for hierarchical structuring of ceramicmaterials",Centre of excellence for polysaccharide research, Jena, Germany22.05 03 R. Weißmann:"Edge strength of flat glass",Seminar Glass in Automobiles, Essen, Germany27.05.03 R. Weißmann:"Investigation of the edge strength of flat glass by a four point bending test"77. Symposium glass technology, Leipzig, GermanyReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg70

25.06.2003 C. Zollfrank:"Ultrastructure and structure evolution of biomorphous, carbide ceramics"Institute for Microstructure Characterisation, University of Erlangen-Nuernberg, Germany30.06.03 C. Zollfrank:"Assembly of ceramics via biotemplates"Institute for General Botany, University of Mainz, Germany09.07.03 C. Zollfrank, R. Melcher:"Structuring of ceramic phasesby micro contact printing"Forschungszentrum Karlsruhe, Germany11.07.23 P. Greil:"Biotemplating of Ceramics"DGM-Tag, Erlangen16.09.03 C. Zollfrank, P. Cromme, R. Melcher, P. Greil:"Structuring of ceramics using biotemplates"Materials Week, Munich, Germany16.09.03 P. Greil:"Biomorphous Ceramics – Materials Design inspired by Nature"European Tech. Ceramics Federation Meeting, Materials Week, Munich01.10.03 R. Weißmann:"Glass – Nature, Structure, Manufacturing"Seminar for Teachers, Faculty for educational science, Erlangen,18.10.03 A. Roosen:"Rheology and flow behaviour of high loaded ceramic suspensions duringthe tape casting process".Dechema-GVC-Jahrestagung 2003, Mannheim, Germany18.10.03 F.A. Müller:"Bioactive calcium phosphate surfaces"IPEN-DMC, Department of Materials Engineering, Sao Paulo, BrasilReport 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg71

26.10.03 F.A. Müller, L. Jonášová, P. Greil:"Bioactive apatite formation on pretreated bioinert materials surfaces"SPB-Mat.-MRS-Brasil, Rio de Janeiro, Brasil29.10.03 P. Greil:"Development of novel materials at the interface of biology"1. WING Conference, BMBF, Weimar, Germany03.11.03 S. Kemethmüller:"Development of glasses for glass-ceramic composites". National TaiwanUniversity Taipei, Taiwan20.11.03 P. Greil:"Biomorphous Ceramics from Natural Templates"PTECH 2003, Latin Am. Powd. Techn .Conf., Guaruja, Brasil12.12.03 H. Sieber:"Processing of Ceramics by Biotemplating of Cellulose Fibre Preforms"MRS-Division of India / Calcutta University, Kolkata, West Bengal/India17.12.03 H. Sieber:"Biomorphic ceramics - processing, properties and applications"Central Glass and Ceramic Research Institute, Calcutta, West Bengal/IndiaReport 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg72

Seminar Presentations by External Lecturers07.01.03 Dr. D.C. Lupascu:"Fatigue of ferroelectric functional materials"Materials Science, NAW, University of Technology, Darmstadt, Germany15.04.03 Dr. R. Lucke:"Ferrites: a classic ceramic material for advanced productcs"EPCOS AG, Munich, Germany24.06.03 Dr. W. Krenkel:"Ceramic fibre reinforced matrix-compositesfor high temperature applications"Institute of Structures and Design, German Aerospace Centre for Materialsand Structures, Stuttgart, Germany20.11.03 Dr. O.P. Chakrabarti"LSI (liquid Silicon infiltration) for manufacturing of SiSiC-ceramics:Processing and Applications"Central Glass and Ceramic Research Institute (Council of Scientific &Industrial Research), Calcutta, West Bengal/India, Non-Oxide CeramicSection,Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg73

PatentsP. Greil, R. Sindelar, T. te BaayPolymeric materials with thermal expansion characteristics similar to those of metals,(Polymer-Ceramics II), DE 102 24 377.8-45, PCT/EP 00/07 614R. Kirmeier, A. Molinero, H. Sieber, O. Rusina, P. GreilProcess for manufacturing carbide and oxide ceramics, DE 10348798.0R.Mayer-Pittroff, W.Ruß, H.Mörtel:Process of thermal treatment of diatomite and application of such treated diatomees,DE 102 35 866.4, WO PCT/DE 03/02667F.A. Müller, U. Bast, P. GreilThermal barrier coating systems, EP 1352985A1H. Sieber, L. Weisensel, P. GreilHighly porous ceramic parts based on SiC and process for manucfaturing thereof,DE 10351057.5V. Švinka, H. Mörtel, St. Krebs:Foam Ceramics with oriented open pore structure, DE 101 34 524 A1M. Wagner, A. Roosen, H. Oostra, R. HöppenerMethod of making a laminated ceramic with a non-planar structure,EP02023464, 2003A. Zampieri, T. Selvam, W. Schieger, F. Scheffler, H. Sieber, P. Greil,Zeolite coated SiSiC ceramics and preparation thereof.Report 2003: Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg74

6 ADDRESS AND MAPDepartment of Materials Science - Glass and CeramicsFriedrich-Alexander University of Erlangen-NuernbergMartensstr. 5D- 91058 Erlangen, GERMANYPhone: ++49-(0) 9131-852-7543 (Secretary)Fax: ++49-(0) 9131-852-8311e-mail: ww3@ww.uni-erlangen.deInternet: http://www.glass-ceramics.uni-erlangen.de/By car:Highway A3 exit Tennenlohe;direction to Erlangen (B4).Follow the signs „UniversitätSüdgelände“. After junction„Technische Fakultät“ pleasefollow the map.By train:Railway station Erlangen.Bus line No. 287 direction„Sebaldussiedlung“. Bus stop„Technische Fakultät“. 50 meters to a layout plan; search for „Institut für Werkstoffwissenschaften“.Report 2003 Department of Materials Science, Glass and Ceramics, University of Erlangen-Nuernberg75