diamond, there are identified graphite and carbon, while the amorphous material is also significant (26%). The diamond peaks show a significant base (2theta) which means that the structure of this phase is probably crypocrystallic and also are symmetrical which means that the diamond phase is well crystallized. The BG/ND sample presents two strong peaks at about 10-13 o 2theta and 25-37 o 2theta, while there are two less intense peaks at about 17-24 o 2theta and 28-55 o 2theta. Significantly, the first peak (10-13 o 2theta) is less intense to the pure BG sample, which indicates a possible transition from the amorphous state to a primary amorphous-cryptocrystallic state. Additionally, the amorphous part of the pure ND sample affects the total amount and the morphology of amorphous in the BG/ND sample, while the peak between 28-55 o 2theta can be attributed to the cryptocrystallic structure of diamond that appears between 43-44 ο 2theta. Amorphous SCS: Sodium Calcium Silicate, Ca SiO 86-0399 ICDD card D: Diamond, C, 06-0675 ICDD card G: Graphite, C, 75-2078 ICDD card C: Carbon, C, 26-1069 ICDD card C G ND pure D SCS SCS 5 15 25 35 45 55 65 75 SCS Amorphous SCS SCS BG/ND SCS SCS SCS SCS SCS SCS SCS 5 10 15 20 25 30 35 40 45 50 55 60 65 70 75 BG pure 80 Amorphous 5 10 15 20 25 30 35 40 45 50 55 60 65 70 75 80 D Fig. 1. XRD patterns of the BG/ND system and of pure BG and ND In Fig. 2 are presented the FTIR spectra of the BG/ND system and pure BG before and after the immersion in c-SBF, for 6, 12 and 24 hours. In the spectra of both samples before the immersion, is observed a broad trend between 840 and 1370cm -1 that can be attributed to the amorphous phase of the samples. The two shoulders at 850 and 965 cm -1 can be assigned to the crystalline phase of dicalcium silicate (Ca 2 SiO 4 ) [9] . Finally, the strong band at 460cm -1 occurs due to the bending mode of Si-O-Si. After 6 hours of soaking, a new band appears at 585cm -1 in both BG/ND system and pure BG, which corresponds to the antisymmetric vibrational mode of P-O in amorphous calcium phosphate phase. After 12 hours in c-SBF, the IR spectrum of both samples is analogous to that observed after 6 hours. However, after 24 hours a double peak at 568 and 602cm -1 is developed to both samples, that are attributed to the bending of P-O mode and proves the development of a crystalline phase of HCAp layer [10] . Comparing the bioactive response of both samples with that of the commercial sol-gel derived bioactive glass [7] (Bioglass® 58S) proves a retardation of our samples, that is probably caused by the growth of the crystalline phase of dicalcium silicate (Ca 2 SiO 4 ). Conclusions The XRD pattern of the BG/ND system indicates that the nanodiamonds result in the re-arrangement of the BG amorphous phase, producing an amorphous phase with a primary amorphous-cryptocrystallic structure. The fact that this new phase is also highly bioactive, even though there is a small retardation of bioactive response in comparison with pure Bioglass® 58S, makes the sol-gel-derived BG/ND system a promising bioactive composite. 2 4 References [1]. Hench LL, Splinter RJ, Allen WC., J Biomed Mater Res, 2, 117, 1971 [2]. Saravanapavan P., Jones J., Pryce R., Hench L., J Biomed Mater Res A., 66, 110, 2003 [3]. Hench L.L. and Andersson O. in An introduction to Bioceramics, editors: Hench L.L. and Wilson J., World Scientific, 41, 1993 [4]. Ekimov E.A., Gromnitskaya E.L., Gierlotka S., Lojkowski W., Palosz B., Swiderska-Sroda A., Kozubowski J.A. and Naletov A.M., J. of Materials science letters, 21, 1699 , 2002 [5]. Kulakova I. I., Physics of the Solid State, 46, 636, 2004 [6]. Xu K. and Xue Q., Physics of the solid state, 46, 649, 2004 [7]. Zhong J., Greenspan D., J Biomed Mater Res, 53, 694, 2000 [8]. Ohtsuki C., Kushitani H., Kokubo T., Kotani S., Yamamuro T., J Biomed Mater Res, 25, 1363, 1991 400 600 800 1000 1200 1400 1600 [9]. Henning O., Cements: the Hydrated Silicates and Aluminates in The Infrared Spectra of Minerals, editor: Farmer V.C. London, Mineralogical Society, 1974 [10]. Kontonasaki E., Zorba T., Papadopoulou L., Pavlidou E., Chatzistavrou X.., Paraskevopoulos K., Koidis P., Cryst. res. technol., 37, 1165, 2002 Absorbance 24h 12h 6h 0h wavelength (cm -1 ) BG/ND pure BG Fig.2. FTIR spectra of pure BG and the BG/ND system before and after 6, 12 and 24h of immersion in c-SBF 183
Energy Loss Rates of Hot Electrons in Semiconducting Carbon Nanotubes Margarita Tsaousidou * Materials Science Department, University of Patras, Patras 26 504, Greece *Email: rtsaous@upatras.gr The study of the energy relaxation provides significant information about the carrier-phonon coupling in low-dimensional semiconductors [1]. In the present paper we calculate the energy loss rate, P, of hot 1D electrons in semiconducting singlewall carbon nanotubes (SWCNTs) due to their coupling to stretching and breathing phonons. A brief description of the theoretical formalism is given and numerical calculations of P are performed for electron temperatures in the range 4-300 K and for various values of the Fermi energy E F . These results can be particularly useful for steady-state electric field heating or time-dependent experiments [2]. The SWCNT can be regarded as a long and infinitesimally thin cylinder of radius R. The electrons are free to move along the direction of the nanotube axis (z-direction) while their motion in the xy-plane is quantized. The electron spectrum consists of several 1D subbands associated with the quantized electron motion. We assume that the electrons are in internal thermal equilibrium at a temperature T e higher than the lattice temperature T lat and their distribution is described by the Fermi-Dirac distribution function. This approximation, the so-called electron temperature model, is valid when the electron-electron relaxation time is much less than the energy loss time of the electrons. For simplicity reasons we consider only electronphonon (e-p) scattering within the lowest 1D electron subband (quantum limit). The Fermi level is assumed to be close to the ground subband minimum in order to eliminate non-parabolicity effects. The e-p interaction is described via a deformation potential. It can be shown that for intrasubband scattering within the ground subband only the stretching and the breathing phonon modes contribute to the e-p coupling. In the long-wavelength limit the stretching mode has a linear dispersion while the breathing mode is dispersionless [3]. The average energy-loss rate due to e-p scattering is given by [4] P = 1 N ∑ q ω where, N is the total number of electrons, ω q is the frequency of a phonon with wave vector q (q is along the z-axis), and dN q /dt is the rate of change of the phonon distribution due to phonon emission and absorption processes. The above equation can be written in the following convenient form: q dΝ dt 1 ep 2 P = ∑ ω | H ( q) | [ N q ( Te ) − N q ( Tlat )] Im χ(q, ω N q q q ) where, |H ep (q)| is the e-p coupling matrix element, N q (T) is the Bose-Einstein distribution at temperature T and Im χ(q,ω q ) is the imaginary part of the electronic polarizability function [5]. For qR
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XXIII ΠΑΝΕΛΛΗΝΙΟ ΣΥΝΕ
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Κοιτώντας τα πρακτ
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ΕΠΙΤΡΟΠΕΣ Οργανωτι
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ΠΡΟΓΡΑΜΜΑ ΣΥΝΕΔΡΙΟ
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21. Οργανικά τρανζίσ
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15:30 15:45 16:00 16:15 16:30 16:45
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41. Modeling and quantitative phase
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Ανοιχτή Συνεδρία «
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«NανοΥλικά και Νανο
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New materials and MOS device concep
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Reliability Characteristics of Rare
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Ο λόγος των ταχυτήτ
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Thus the mean R In-In is expected t
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FIG 1. Schematic representation of
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με 0.80 eV στη διεπιφά
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Εντοπισµός Φορέων
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Παρασκευή και Xαρακ
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Electrical Spin Injection from Fe i
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Electrical Spin Injection of Spin-P
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References [1] CH Lee, J. Meteer, V
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Σχήμα 1: Φωτογραφία
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SEM Image Layout Simulation Εικ
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Μελέτη Ατελειών Σε
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Facet-Stress-Driven Ordering in SiG
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νανοκρυσταλλίτης (a
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Σχήµα 1. Εικόνες περ
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Σχήµα 1. Εικόνες περ
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Οι δομές που αναπτύ
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Raman Intensity (10 -50 cm 3 ) 1,2
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Μελέτη της Επίδρασ
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Annealing Induced Dissociation of N
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`Εναπόθεση με Παλμι
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Μελέτη της Χημείας
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Ανάπτυξη Νέων Μεσο
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Application of Thermal Quadrupoles
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Στοχαστική προσομο
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Νανοτραχύτητα κατά
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Ευαισθησία και Δια
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Optical Properties of CuIn 1-x Ga x
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ανοπτημένο με λέιζ
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Στο σχήμα 3 φαίνοντ
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Id (mA) -0,3 -0,2 -0,1 Vg=0 Vg=-1 V
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Strained-Si Si 1-x Ge x graded Si 1
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Fig. 1. Laser mask movement during
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forwarded to the back interface dur
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Σχήμα 2: Εκθετική εξ
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V th (V) G m,max /G m,max0 (%) I d
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C/ C ox 1,0 0,8 0,6 0,4 0,2 0,0 -4
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και Ta 2 O 5 , των οποίω
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κατασκευή της. Η πα
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ΔP (mW) 12 10 8 6 4 2 0 0 500 1000
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υπολογίσουμε θεωρη
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Σχήμα 2 Σύστημα ηλε
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Μελέτη των Μηχανισ
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Ανάπτυξη και Μελέτ
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Structure and Magnetic Properties o
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Δομή και Μαγνητικέ
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Μετρήσεις Ειδικής
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Further, almost all of the observed
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g-factor 2.019 2.016 2.013 2.010 2.
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ρυθμό 4 C.min -1 , έπειτ
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ΜΕΛΕΤΗ ΤΟΥ ΦΑΙΝΟΜΕ
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Νέοι Εξαφερίτες Ba µ
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Crystal Structure of a new Supramol
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Magnetic Phase Transition in Synthe
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Συσχέτιση πλαστική
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Μετασχηματισμοί φά
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Μελέτη της Επίδρασ
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Resonant Spin Transfer Torque in Do
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3 η Προφορική Συνεδ
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technology, and e-beam lithography.
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ecause it reduces the calculation o
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Υπολογισμός Υψηλής
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The thermodynamic average is obtain
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ΑΠΟΤΕΛΕΣΜΑΤΑ Στην
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προερχόµενη είτε α
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Combining Magnetism and Ferroelectr
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Κρυσταλλική Συµπερ
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Σύνθεση Στερεών ∆ι
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Fabrication and Characterization of
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∆ιερεύνηση δυνατό
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Συγκριτική αξιολόγ
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6 η Προφορική Συνεδ
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Ηλεκτρομαγνητική Α
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Φασματοσκοπική Μελ
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Thermal and Electrical Properties o
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Structure, Mechanical, and Optoelec
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Designing Nanoporous Materials for
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This program was developed to serve
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Νέα Αυτό-οργανούμε
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A Physical Model to Interpret the E
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FIR study of Ag x (As 33 S 33 Se 33
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Mελέτη Μεικτών Γυαλ
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The Structural Role of Fe and Zn in
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ΕΥΡΕΤΗΡΙΟ ΣΥΓΓΡΑΦΕ
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Κομπίτσας Μ…………
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ΕΥΡΕΤΗΡΙΟ ΣΥΓΓΡΑΦΕ
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W Watson I.M………………4 Weg