International audienceShort range order in glassy 0.9(Ge0.1As0.15Te0.75)–0.1Cu (GATC1) and 0.9(Ge0.05As0.55Te0.4)–0.1Cu (GATC2) was studied by neutron- and X-ray diffraction as well as EXAFS (extended X-ray absorption fine structure) measurements at the K-edges of all components. The reverse Monte Carlo simulation technique was used to create models consistent with all experimental datasets. It was found that Cu binds predominantly to Te in GATC1 while Cu–As and Cu–Cu bonding is also significant in GATC2. Ge and As atoms have 4 and 3 Ge/As/Te neighbors in both compositions. In GATC1 the formation of ‘extra’ Te–Te bonds can be observed, similarly to GeTe4–AgI glasse

Bednarčik, Jozef

Beuneu, Brigitte

Bureau, Bruno

Jóvári, Pal

Kaban, Ivan

Lucas, Pierre

Pantalei, Claudia

Yang, Zhiyong

Journal of Non-Crystalline Solids

Short range order in glassy 0.9(Ge0.1As0.15Te0.75)–0.1Cu (GATC1) and 0.9(Ge0.05As0.55Te0.4)–0.1Cu (GATC2) was studied by neutron- and X-ray diffraction as well as EXAFS (extended X-ray absorption fine structure) measurements at the K-edges of all components. The reverse Monte Carlo simulation technique was used to create models consistent with all experimental datasets. It was found that Cu binds predominantly to Te in GATC1 while Cu–As and Cu–Cu bonding is also significant in GATC2. Ge and As atoms have 4 and 3 Ge/As/Te neighbors in both compositions. In GATC1 the formation of ‘extra’ Te–Te bonds can be observed, similarly to GeTe4–AgI glasses

Jóvári, Pál

DESY

On the structure of Ge–As–Te–Cu glasses

DESY Publication Database

Pál Jóvári

Pierre Lucas

Zhiyong Yang

Bruno Bureau

Ivan Kaban

Brigitte Beuneu

Claudia Pantalei

Jozef Bednarčik

Crossref

HAL-CEA

On the structure of Ge–As–Te–Cu glassesPal Jo´va´ri, Pierre Lucas, Zhiyong Yang, Bruno Bureau, Ivan Kaban, BrigitteBeuneu, Claudia Pantalei, Jozef BednarcˇikTo cite this version:Pal Jo´va´ri, Pierre Lucas, Zhiyong Yang, Bruno Bureau, Ivan Kaban, et al.. On the struc-ture of Ge–As–Te–Cu glasses. Journal of Non-Crystalline Solids, Elsevier, 2016, 433, pp.1–5.<10.1016/j.jnoncrysol.2015.11.003>. <hal-01236430>HAL Id: hal-01236430https://hal-univ-rennes1.archives-ouvertes.fr/hal-01236430Submitted on 9 Dec 2015HAL is a multi-disciplinary open accessarchive for the deposit and dissemination of sci-entific research documents, whether they are pub-lished or not. The documents may come fromteaching and research institutions in France orabroad, or from public or private research centers.L’archive ouverte pluridisciplinaire HAL, estdestine´e au de´poˆt et a` la diffusion de documentsscientifiques de niveau recherche, publie´s ou non,e´manant des e´tablissements d’enseignement et derecherche franc¸ais ou e´trangers, des laboratoirespublics ou prive´s.On the structure of Ge-As-Te-Cu glasses  Pál Jóvári1, Pierre Lucas2, Zhiyong Yang2,a , Bruno Bureau3, Ivan Kaban4, Brigitte Beuneu5, Claudia Pantalei5, Jozef Bednarčik6   1Wigner Research Centre for Physics, Institute of Solid State Physics, H-1525 Budapest, POB 49, Hungary 2Department of Materials Science and Engineering, University of Arizona, Tucson, AZ, USA 85721 3Equipe Verres et Ceramiques, Laboratoire Sciences Chimiques de Rennes UMR-CNRS 6226, France 4 IFW Dresden, Institute for Complex Materials, P.O. Box 270116, 01171 Dresden, Germany 5Laboratoire Léon Brillouin, CEA-Saclay 91191 Gif sur Yvette Cedex France 6 Deutsches Elektronen-Synchrotron DESY, Photon Science, Notkestrasse 85, 22603 Hamburg, Germany a Now at Jiangsu Key Laboratory of Advanced Laser Materials and Devices, School of Physics and Electronic Engineering, Jiangsu Normal University, Xuzhou, Jiangsu 221116, China   Abstract  Short range order in glassy 0.9(Ge0.1As0.15Te0.75)-0.1Cu (GATC1) and 0.9(Ge0.05As0.55Te0.4)-0.1Cu (GATC2) was studied by neutron- and X-ray diffraction as well as EXAFS (extended X-ray absorption fine structure) measurements at the K-edges of all components. The reverse Monte Carlo simulation technique was used to create models consistent with all experimental datasets. It was found that Cu binds predominantly to Te in GATC1 while Cu-As and Cu-Cu bonding is also significant in GATC2. Ge and As atoms have 4 and 3 Ge/As/Te neighbors in both compositions. In GATC1 the formation of ‘extra’ Te-Te bonds can be observed, similarly to GeTe4-AgI glasses.  1. Introduction  As-Te alloys can be vitrified over a broad composition range (~20-60 at.% As). A detailed study of As-Te glasses by diffraction techniques and EXAFS revealed that they could be considered as random covalent networks, without any type of preferred bonding [1-3]. The Ge-Te system behaves in a completely different way: liquid Ge-Te alloys can be vitrified only in the vicinity of the eutectic composition (15-20 at. % Ge). A reverse Monte Carlo simulation study using EXAFS and diffraction datasets showed that Ge-Ge bonding is not significant in these glasses [4]. Later this finding was confirmed by EXAFS and X-ray photoelectron spectroscopy [5]. Given the sensitivity of the experimental techniques applied it means that the Ge-Ge coordination number is not higher than ~0.3, thus amorphous Ge-Te alloys around the eutectic composition should be regarded as chemically ordered.   Ge-As-Te (GAT) alloys can be vitrified between ~80% and ~35% Te content. The different behaviour of As and Ge in binary tellurides is also inherited by the ternary glasses. There is a pronounced ordering around Ge atoms, which prefer Te to As and Ge while As-As bonding is significant even in Te-rich compositions (e.g. Ge10As15Te75) [6].   Glass formation in the Ge-As-Te-Cu (GATC) system has been reported recently [7]. GATC glasses have excellent transmission in the IR range and possess high conductivity. This favorable combination of properties makes them suitable for detecting charged biomolecules by electrodepositing them and measuring their IR spectra.  The aim of the present study is the determination of the short range order in GATC. Comparison of the structure of GAT and GATC glasses reveals how Cu atoms modify the Ge-As-Te covalent network. This question is especially interesting because glassy tellurides can host modifiers by entirely different mechanisms. For example, in 0.75GeTe4-0.25AgI the total coordination number of Te is close to 3 and the sum of Te-Ge and Te-Te coordination numbers is 2.76 [8]. Therefore, in this case Ag and I induce a strong rearrangement of the Ge-Te covalent network. On the other hand, in Ge-Ga-Te [4] and Te-rich Ge-Cu-Te [9] glasses the sum of Te-Te and Te-Ge coordination numbers remains close to 2 but the total coordination number of Te is significantly higher than 2, showing that modifying atoms form additional bonds with Te but do not rearrange the host network.   Chemical short range order in an alloy can be characterized by the partial pair correlation functions. The number of these functions in case of an n-component system is n(n+1)/2. As four-component glasses have ten partial pair correlation functions the detailed description of the short range order of Ge-As-Te-Cu glasses is a rather challenging goal. Close distances (e.g. Ge-Te, As-Te, Cu-Te) can be separated reliably only by combining various experimental techniques. For this reason we have carried out neutron and X-ray diffraction experiments as well as EXAFS measurements at the K absorption edges of all components. Large scale structural models have been created by fitting simultaneously the 6 experimental datasets in the framework of the reverse Monte Carlo simulation technique [10, 11]. Besides fitting experimental data, this method is also capable of incorporating existing physical and chemical information (e.g. density, preferred coordination numbers, chemical ordering) in the models created. The use of various constraints also gives the possibility of estimating the uncertainty of coordination numbers or assessing the validity of various structural models, in general.   2. Sample preparation  Both glass samples were prepared using high purity elements (99.999% Ge and Cu, 99.99999% As, and 99.9999% Te) introduced in a silica ampoule which was flame sealed under high vacuum. The melt was homogenized for 8h in a rocking furnace at 850°C. After homogenization, the temperature of the furnace was lowered to 600°C to reduce the vapour pressure and after an isothermal heating for 1 hour the ampoule was quenched in water. The ampoule containing the glass was then immediately annealed at 20°C below the glass transition temperature Tg for 3 hour. The resulting glass rod was recovered by breaking the silica ampoule.  3. Experimental   The neutron diffraction experiment was carried out at the 7C2 liquid and amorphous diffractometer of the Laboratoire Léon Brillouin (Saclay, France). Powdered samples were filled into thin walled vanadium sample holders (diameter: 6 mm, wall thickness: 0.1 mm). 0.9(Ge0.1As0.15Te0.75)-0.1Cu was measured with the old ‘banana’ detector filled with BF3. The new 3He-filled detector system was used to measure 0.9(Ge0.05As0.55Te0.4)-0.1Cu. Raw data were corrected for background scattering and detector efficiency. The offset of the detector position and the wavelength of the incident neutron beam (0.72 Å) were determined by measuring a Ni standard.   The X-ray diffraction and EXAFS experiments are described in ref. [6].  4. Reverse Monte Carlo simulation   The reverse Monte Carlo simulation technique was used to generate particle configurations fitting all experimental datasets and using available physical information. Simulation boxes contained 20000 atoms.   Density measurements of Ge15Te85-Cu glasses [12] revealed that the partial molar volume of the Ge15Te85 host matrix (i.e. the volume in which 0.15 mole Ge and 0.85 mole Te can be found) does not depend significantly on the Cu content (up to 10 atomic %). Molar volume of GATC1 was therefore estimated by multiplying the molar volume of Ge10As15Te75 [6] by 0.9. Similar measurements showed that the partial molar volume of As50Te50 is ~1.8% greater in As50Te50-10%Cu than in the undoped binary glass [12]. It is reasonable to assume that the ‘breathing’ of the host matrix increases with decreasing Te content due to the decreasing average distance of the atoms. Thus the molar volume of GATC2 was taken to be only 6% smaller than that of Ge5As55Te40 (see Table 1). Test runs revealed that small (±3%) changes of the density have no significant effect on short range order parameters.  Minimum interatomic distances are listed in Table 2. Backscattering factors needed to calculate the model EXAFS curves from partial pair correlation functions [13] were obtained by the feff8.4 programme [14]. Raw χ(k) data were filtered in two steps: first k3χ(k) was forward Fourier-transformed into r-space using a Kaiser-Bessel window (α=1.5). The k-range of transformation was around 1.8 Å-1 -14 Å-1 for the As and Te K edges and around1.8 Å-1 -12.5 Å-1 for the Ge and Cu edges. The resulting r-space data were backtransformed using a rectangular window (usually over the r-space range 1.2 Å-3.2 Å).  5. Results and discussion   5.1. 0.9(Ge0.1As0.15Te0.75)-0.1Cu  First the environment of Ge atoms was investigated. It was found that the elimination of Ge-Ge, Ge-As and Ge-Cu bonds does not influence the quality of fits. Therefore Ge atoms were allowed to have only Te neighbors and the Ge-Te coordination number was constrained to be 4. The Ge-Te bond length (2.60±0.02 Å) is in a good agreement with literature values [4, 6 15, 16].  Arsenic binds mostly to Te but As-As bonding also improved fit qualities. The total coordination number of As was constrained to be 3. NAsAs, the As-As coordination number is 0.33±0.2 which is very close to the corresponding value (0.39) of Ge10As15Te75 glass [6].   Cu has on the average 3.37±0.3 Te neighbors. The mean Cu-Te distance is 2.56±0.02 Å, which agrees with the value found in amorphous GeCu2Te3 [17]. It was established that the fit of the Cu K-edge EXAFS data was improved upon allowing Cu-Cu bonding. However, the position of the first peak of gCuCu(r), the Cu-Cu partial pair correlation function, was strongly sensitive to the parameters of the fit (e.g. fitting range, weight of the Cu EXAFS dataset). Therefore it has been concluded that Cu-Cu bonding in the model is an artefact and the real Cu-Cu coordination number is most likely below the sensitivity of our approach.   The total coordination number of Te is 2.74±0.2. The average number of Cu atoms around Te is 0.50±0.1 while the number of ‘covalent’ neighbours (Ge, As, Te) is 2.24±0.2. Comparison with Ge10As15Te75 reveals that the first minimum of gTeTe(r) becomes less well defined upon adding Cu (Fig. 3). The shoulder at 2.9 Å suggests that ‘extra’ Te atoms appear in the first coordination sphere of Te and increase the average coordination number of Te by forming a third covalent bond, similarly to the GeTe4-AgI system [8].   5.2. 0.9(Ge0.05As0.55Te0.4)-0.1Cu  As this composition is strongly Te-poor Ge cannot be fourfold coordinated without significant Ge-As bonding (see Table 2). Nevertheless, Ge-Te bonds are clearly preferred to Ge-As ones. Neither Ge-Ge nor Ge-Cu bonding was found to improve fit quality therefore these pairs were forbidden by raising the corresponding minimum interatomic distances (Table 2). Besides Ge, arsenic is mostly surrounded by Te and As. However, test runs showed that Cu also binds to arsenic. The Cu-As coordination number is 1.43±0.7. Given the high percentage of As, this value still indicates that Cu-Te bonds are strongly preferred to Cu-As ones. The Cu-Cu coordination number is 1.83±1. The individual uncertainties of Cu-X coordination numbers are rather high but they largely cancel each other, similarly to the case of GATC1. Therefore the total coordination number of Cu is relatively well defined (4.45±0.4). Though Te-Te bonding was allowed, the Te-Te coordination number is only 0.03. This value is well below the sensitivity of our approach therefore Te-Te bonding is not significant in GATC2.   5.3. Comparison with the structure of other amorphous chalcogenides  The Ge-Te distance is 2.60±0.02 Å both in GATC1 and GATC2. The same bond length was found in several Ge-Te based glasses [4, 6, 15, 16] showing that the strength of Ge-Te bonds is not strongly sensitive to the composition. This is definitely not true for the Te-Te distance that shows a great variation even in amorphous Ge-Te films, with a well-defined maximum around Ge20Te80 [18]. The Te-Te distance also seems to depend on how the modifier binds to the atoms of the host network: in case of covalent bonding (e.g. Se and I) the bond length becomes smaller (2.70-2.73 Å) while Ga increases the mean Te-Te distance to 2.79-2.80 Å [4]. In GATC1 and in Ge10As15Te75 the Te-Te bond length is 2.78±0.02 Å and 2.76±0.02 Å, respectively.  Cu-Te distances also lie in a rather narrow range (2.56-2.58 Å) in GATC1, GATC2, and GeCu2Te3 [17]. The electronegativity of Cu is 1.9 while that of Te is 2.1. These are very close, hence the Cu-Te bond is expected to be covalent. This is confirmed by the fact that the investigated Ge-As-Te-Cu glasses are amorphous semiconductors with a bandgap around 1 eV [7], which is much smaller than the typical values of ionic compounds.  On the other hand, the scattering of Cu-Cu bond lengths is rather large (2.55-2.81 Å). We believe that this is only partly due to the somewhat higher uncertainty of Cu-related structural parameters. The Cu-Cu distance is strongly sensitive to the environment of Cu atoms. For example in Cu2Te it is as short as 2.446 Å [19] while in crystalline Cu1.4Te (rickardite) nearest Cu-Cu distances are 2.58 Å and 2.81 Å [20]. Cu-Cu distances found in various amorphous and crystalline copper tellurides are listed in Table 5.  6. Conclusions  The structure of 0.9(Ge10As15Te75)-0.1Cu and 0.9(Ge5As55Te40)-0.1Cu chalcogenide glasses has been investigated by diffraction and EXAFS measurements. Experimental data (six datasets for each composition) have been fitted simultaneously by the reverse Monte Carlo simulation technique. Ge is fourfold coordinated in both compositions. In Ge5As55Te40-10Cu the total coordination number of As is higher than 3 due to the formation of Cu-As bonds. Cu-Cu bonding is significant in Ge5As55Te40-10%Cu thus the prevalence of CuTe4 structural units can be ruled out in this composition.    Acknowledgments  The research leading to these results has received funding from the European Community's Seventh Framework Programme (FP7/2007-2013) under grant agreement no. 312284. P.J. was supported by OTKA (Hungarian Basic Research Fund) Grant No. 083529. This research was supported by the Partner University Fund, and the CNRS International Associated Laboratory for Materials & Optics (LIA-MATEO).  . References  [1] P. Jóvári, S.N. Yannopoulos, I. Kaban, A. Kalampounias, I. Lischynskyy, B. Beuneu, O. Kostadinova, E. Welter, A. Schöps, J. Chem. Phys. 129 (2008) 214502 [2] D. C. Kaseman, I. Hung, K. Lee, K. Kovnir, Z. Gan, B. Aitken, S. Sen, J. Phys. Chem. B 119 (2015) 2081 [3] A. Tverjanovich, K. Rodionov, E. Bychkov, J. Solid State Chem. 190 (2012) 271  [4] P. Jóvári, I. Kaban, B. Bureau, A. A. Wilhelm, P. Lucas, B. Beuneu, D. A. Zajac, J. Phys. Condens. Matter 22 (2010) 404207 [5] R. Golovchak, L. Calvez, B. Bureau, H. Jain, J. Chem. Phys. 139 (2013) 054508 [6] P Jóvári, P. Lucas, Z Yang, B Bureau, I Kaban, B Beuneu, J Bednarčik, J. Am. Ceram. Soc. 97 (2014) 1625 [7] Z. Yang , A.A.Wilhelm, P. Lucas, J. Am. Ceram. Soc. 93 (2010) 1941 [8] P Jóvári, S Cui, V Nazabal, I Kaban, B Beuneu, M Dussauze, C Boussard-Plédel, B Bureau, J. Am. Ceram. Soc. 98 (2015) 1034 [9] L. Rátkai, A.P. Gonçalves, G. Delaizir, C. Godart, I. Kaban, B. Beuneu, P. Jóvári, Cu and Te coordination environment in Cu-doped Ge-Te glasses, Solid State Communications 151 (2011) 1524 [10] R.L. McGreevy, L. Pusztai, Mol. Simul. 1 (1988) 359 [11] O. Gereben, P. Jóvári, L. Temleitner, L. Pusztai, J. Optoelectron. Adv. Mater. 9 (2007) 3021  [12] Z.U. Borisova, Glassy Semiconductors, Plenum, New York (1981) [13] M. Winterer, J. Appl. Phys., 88 (2000) 5635 [14] A.L. Ankudinov, B. Ravel, J.J. Rehr, S.D. Conradson, Phys. Rev. B, 58 (1998) 7565 [15] P. Jóvári, I. Kaban, J. Steiner, B. Beuneu, A. Schöps, M.A. Webb, Phys. Rev. B 77 (2008) 035202 [16] P. Jóvári, I. Kaban, J. Steiner, B. Beuneu, A. Schöps, M.A. Webb, J. Phys.: Condens. Matter 19 (2007) 335212  [17] P. Jóvári, Y. Sutou, I. Kaban, Y. Saito, J. Koike, Scripta Mater. 68 (2013) 122  [18] P Jóvári, A Piarristeguy, R Escalier, I Kaban, J Bednarčik, A. Pradel, J. Phys.: Condens. Matter 25 (2013) 195401 [19] H. Nowotny, Z. Metallkd. 37 (1946) 40 [20] S.A. Forman, M.A. Peacock, Amer. Mineralogist 34 (1950) 441 [21] L. Bindi, C. Carbone, D. Belmonte, R. Cabella, R. Bracco, Mineralogical Magazine 77 (2013) 475 [22] Y.C. Wang, F.J. DiSalvo, J. Solid State Chem. 156 (2001) 44 [23] K.O. Klepp, J. Less-Common Met. 128 (1987) 79 Table 1. Estimated molar volumes (in cm3) of GATC1 and GATC2 used in the reverse Monte Carlo simulation. The values of the corresponding undoped glasses [6] are also given for comparison.  GATC1 18.32 Ge10As15Te75 20.35 GATC2 16.88 Ge5As55Te40 17.96   Table 2. Minimum interatomic distances (in Å) used in the reverse Monte Carlo modelling of 0.9(Ge0.10As0.15Te0.75)-0.1Cu and 0.9(Ge0.05As0.55Te0.4)-0.1Cu (values in parentheses)  Ge-Ge Ge-As Ge-Cu Ge-Te As-As As-Cu As-Te Cu-Cu Cu-Te Te-Te 3.6 3.6 (2.35) 3.1 2.35 2.35 3.1 (2.65) 2.35 3.1 (2.45) 2.35 2.5   Table 3. Coordination numbers of 0.9(Ge0.10As0.15Te0.75)-0.1Cu and 0.9(Ge0.05As0.55Te0.4)-0.1Cu obtained by simultaneous fitting of diffraction and EXAFS datasets. Values in bold were obtained by coordination number constraints, therefore no uncertainty is given.   GATC1 GATC2 NGeAs - 1.80±0.6 NGeTe 4.00 2.20±0.6 NAsGe - 0.16±0.05 NAsAs 0.37±0.2 1.48±0.3 NAsCu - 0.28±0.1 NAsTe 2.62±0.2 1.36±0.3 NCuAs - 1.40±0.4 NCuCu - 1.91±0.4 NCuTe 3.37±0.3 1.23±0.4 NTeGe 0.53 0.28±0.08 NTeAs 0.52±0.04 1.87±0.4 NTeCu 0.50±0.1 0.35±0.1 NTeTe 1.19±0.2 0.03 NGe 4.00 4.00 NAs 2.99 3.28±0.1  NCu 3.37±0.3 4.54±0.3 NTe 2.74±0.2 2.53±0.2      Table 4. Nearest neighbour distances (in Å) found in 0.9(Ge0.10As0.15Te0.75)-0.1Cu and 0.9(Ge0.05As0.55Te0.4)-0.1Cu and in some Ge-Te, Ge-As-Te and Ge-Cu-Te glasses  GATC1 GATC2 Ge20Te80[18] GAT1[6] GAT2[6] GeCu2Te3[17] rGeAs - 2.47±0.02 - - -  rGeTe 2.60±0.02 2.60±0.02 2.60±0.02 2.60±0.02 2.61±0.02 2.61±0.02 rAsAs 2.45±0.02 2.45±0.02 - 2.45±0.02 2.43±0.02  rAsCu - 2.76±0.02 - - -  rAsTe 2.60±0.02 2.62±0.02 - 2.60±0.02 2.62±0.02  rCuCu - 2.62±0.04 - - - 2.55±0.02 rCuTe 2.56±0.02 2.57±0.02 - - - 2.58±0.02 rTeTe 2.78±0.02 - 2.76±0.02 2.76±0.02 2.80±0.03 2.75±0.02  Table 5. Cu-Cu distances in some crystalline and amorphous copper tellurides (in Å)   Composition rCuCu Cu2Te [19] 2.446 Cu1.4Te (rickardite) [20] 2.58, 2.81 Cu1.79Te (weissite) [21] 2.493-2.722 BaCu2Te2 [22] 2.847 TlCu3Te2 [23] 2.474-2.890 GeCu2Te3 [17] 2.58±0.03 Ge5As55Te40-10%Cu 2.62±0.04  Figure captions  Figure 1. Comparison of measured diffraction and filtered experimental EXAFS datasets of 0.9(Ge5As55Te40)-0.1Cu (symbols) and the model curves (solid lines) obtained by reverse Monte Carlo simulation.   Figure 2. Partial pair correlation functions of 0.9(Ge10As15Te75)-0.1Cu (solid lines) and 0.9(Ge5As55Te40)-0.1Cu (symbols).  Figure 3. Comparison of the Te-Te partial pair correlation functions of Ge10As15Te75 [6] and 0.9(Ge10As15Te75)-0.1Cu. Figure 1.   Figure 2.  Figure 3.   

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On the structure of Ge–As–Te–Cu glasses

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