[dlnW/dT] The negative slope of the lnW = f(lnT), where W = -T is the reduced activation energy, as it is shown in Figure 2, reveals that the samples are in the insulating state, for which hopping transport is described by the general Mott Variable Range Hopping (VRH) formula [4] σ = σ 0 ⎡ ( ) exp - T 0 / T α ⎤ ⎣ ⎦ The exponent α decreases with thermal aging, from the value 1 at the beginning of the thermal treatment, to a value of about α =1/2 at the end of this process, as it is shown in Figure 3. (1) 1,2 1,1 1,0 0,9 α 0,8 0,7 0,6 0,5 0,4 0 10 20 30 40 50 60 t (h) Figure 3. The exponent α in Equation (1) as a function of the different thermal treatment times for the same PEDOT:PSS sample, as in Figure 1. Percolation theory in conducting polymer networks showed that the value of the exponent α systematically decreases from about α ≈ 1 to 0.25 upon increasing the volume fraction of the conducting polymer into the insulating matrix to the percolation threshold [5,6]. A value of α = 0.5 indicates a variable range hopping process in one dimension, revealing a much better alignment of the polymer chains at the end of the thermal treatment. This seems to contradict the fact that the conductivity declines with thermal treatment. However, Fig.4 shows that the peak corresponding to PSS - -Na bond is decreasing after heat treatment, which indicates that there is an elimination of the PSS-Na salt. Apart from UPS, SEM pictures indicate a decrease of the size of the conductive grains with increasing treatment time. XPS (MgKα) S2p as-received PSS XPS (MgKα) S2p after thermal treatment PSS XPS Intensity (a. u.) PEDOT PSS - (Na + , H + ) PSS 0 PSS - (Na + , H + ) PEDOT PSS 0 162 164 166 168 170 172162 164 166 168 170 172 Binding Energy (eV) Figure 4. S(2p)-XPS peaks from the “as received” sample(a) and after heat treatment(b). It seems reasonable to assume that a decreasing of the grain size at constant separation has as a result the decrease of conductivity, as the number of the potential barriers increases [7, 8]. [1] Choulis S.A., Choong V.-E., Patwardhan A., Mathai M.K., So F., Adv. Fun. Materials, 16, 1075, (2006). [2] de Kok M.M., Buechel M., Vulto S.I.E., van de Weijer P., Meulenkamp E.A., de Winter S.H.P.M., Mank A.J.G., Vorstenbosch H.J.M., Weijtens C.H.L. van Elsbergen V., Phys. Stat. Sol. (a) 201 (2004) 1342. [3] Crispin X., Marciniak S., Osikowicz W., Zotti G., Denier van der Gon A.W., Louwet F., Fahlman M., Groenendaal L., de Schryver F., Salaneck W.R., J. Polym. Sci. Part B: Polym. Phys. 41 (2003) 2561. [4] Kohlman R.S., Joo J., Min Y.G., MacDiarmid A.G., A.J. Epstein, Phys. Rev. Lett. 77 (1996) 2766. [5] Reghu M., Yoon C.O., Yang C.Y., Moses D., Smith P., Heeger A.J., Cao Y., Phys. Rev. B 50 (1994) 13931. [6] Duvail J.L., Rétho P., Garreau S., Louarn G., Godon C., Demoustier-Champaghe S., Synth. Met. 131, (2002) 123. [7] Zhou Y., Yuan Y., Lian J., Zhang J., Pang H., Cao L., Zhou X., Chem. Phys. Lett. 427, (2006) 394. [8] Timpanaro S., Kemerink M., Touwslager F.J., de Kok M.M., Schrader S., Chem. Phys. Lett. 394, (2004) 339. 229
Modeling and quantitative phase analyses of archaic pottery I.M.Siouris 1 , W. Kockelmann 2 1 Department of Production and Management Engineering , Democritus University of Thrace Xanthi, 67 1 00 Xanthis, Greece 2 Rutherford Appleton Laboratory, ISIS Facility, OX11 0QX Chilton, United Kingdom *jsiou@pme.duth.gr Archaeological pottery fragments from two sites in Greece were investigated with neutron diffraction. The measurements included 4th-century BC pottery from the area of Krania and fragments from the Karabournaki excavation site in northern Greece. The neutron diffraction analyses aimed at delivering quantitative phase fractions which are to be used for identifying characteristic signatures of the types of pottery. Further more, a new computer program (Amphoreas) was developed to deal with the various problems that mineral analysis of multiphase ceramics presents. [Fig.1]: Experimental (+), calculated (-) and difference of the diffraction patterns from the Krania sample. [Fig.2]: Initial modeling, Krania sample, using the program Amphoreas [Fig.4]:Final model and fitted parameters. *Bank 2:Indicates forward scattering with detector position at :2θ= 52.6 ◦ and Bank 3:Indicates backscattering with detector position at:2θ= 122.2°. Neutron data on two 4th century B.C. pottery fragments from the specified areas was collected at the ROTAX instrument, using the TOF neutron diffraction facility at ISIS. The data was analysed with the GSAS software and the results were compared with the analysis from Amphoreas software. The neutron diffraction analyses aimed at determining the main crystallographic phases in this type of pottery. The Plots [1] and [4] show the analysed diffraction patterns of the two different fragments. Table [1] shows the final results of the quantitative phase evaluation using both computer software : full pattern analysis from GSAS and the profile/ phase decomposition software Amphoreas. The results are almost identical. The deviation in the calculating phases are within 0.03% , a factor well inside the bounds of the experimental error. The Krania shards are characterised by a high amount of feldspars indicating larger kiln temperatures. 230
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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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υµένια LCMO/STO (100) πολ
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Our scheme is illustrated in Fig. 1
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[6] . Η μελέτη του υλι
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τα πειραµατικά µας
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συµπύκνωµα. Αυτό επ
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και αναδεικνύει τρ
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P P P P P power P copolymers P and
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Αυτο-οργάνωση και Μ
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Viscoelastic Response of Micelles w
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Διηλεκτρική απόκρι
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Light - induced Reversible Hydrophi
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Οι παραπάνω τρεις κ
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AP-PH (a.u.) 0.4 0.3 0.2 0.1 0.0 0
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Synthesis of Polymer Brushes onto I
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Conformational Properties of Dendri
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Structure and Dynamics of Branched
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∆οµή και ∆υναµική
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Επίδραση της Τοπολ
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(α) (β) Σχήμα 2: (α) Απε
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Figure 3. Generation 4 PAMAM-H 2 O
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Από όλα τα παραπάνω
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Το PHEGMA είναι άμορφο
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PS HAuCl 4 P2VP Ion loading PSP2VP
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