Open Access

Network-Forming Nanoclusters in Binary As–S/Se Glasses: From Ab Initio Quantum Chemical Modeling to Experimental Evidences

Nanoscale Research Letters201712:45

Received: 16 November 2016

Accepted: 13 December 2016

Published: 17 January 2017


Network-forming As2(S/Se)m nanoclusters are employed to recognize expected variations in a vicinity of some remarkable compositions in binary As–Se/S glassy systems accepted as signatures of optimally constrained intermediate topological phases in earlier temperature-modulated differential scanning calorimetry experiments. The ab initio quantum chemical calculations performed using the cation-interlinking network cluster approach show similar oscillating character in tendency to local chemical decomposition but obvious step-like behavior in preference to global phase separation on boundary chemical compounds (pure chalcogen and stoichiometric arsenic chalcogenides). The onsets of stability are defined for chalcogen-rich glasses, these being connected with As2Se5 (Z = 2.29) and As2S6 (Z = 2.25) nanoclusters for As–Se and As–S glasses, respectively. The physical aging effects result preferentially from global phase separation in As–S glass system due to high localization of covalent bonding and local demixing on neighboring As2Sem+1 and As2Sem−1 nanoclusters in As–Se system. These nanoclusters well explain the lower limits of reversibility windows in temperature-modulated differential scanning calorimetry, but they cannot be accepted as signatures of topological phase transitions in respect to the rigidity theory.


Chalcogenide glasses Nanocluster Reversibility window Ab initio calculation


Chalcogenide glasses (ChG) of binary As–Ch system (Ch = S, Se) are representatives of disordered covalent network solids, which clearly demonstrate glass-forming tendencies predicted in terminology of rigidity theory initially developed by Phillips and Thorpe [1, 2]. Within this approach, the strongest glass-forming ability is a character for ChG possessing structural network with the number of degrees of freedom equals to the number of Lagrangian constraints per atom n c associated with nearest-neighbor bond-bending and stretching forces (so in this case, the short-range configuration entropy and network strain energy tend to zero). In such a way, an average coordination number of glass network should be close to Z = 2.40 for best glass-forming compounds (i.e., stoichiometric As2S3 and As2Se3), which are optimally constrained (n c  = 3) and thus, not affected by physical aging. The optimally constrained (rigid but unstressed) intermediate phase (IPh) in ChG is expected in narrow compositional domain between under-constrained floppy phase (FPh, n c  < 3) and over-constrained stressed rigid phase (SRPh, n c  > 3) [3, 4]. In respect to theoretical calculations [4], the typical width of such IPh is expected to be rather narrow in ChG, since the saturated covalent-bonded glassy network exists at a cost of very low entropy as topologically self-organized phase (n c  = 3).

Since the earliest 2000s, Boolchand et al. [58] tried to prove experimentally the IPh employing the method of temperature-modulated differential scanning calorimetry (TM-DSC) as probe for ChG with nearly vanishing non-reversing enthalpy (ΔH nr) forming the so-called reversibility window (RW). Nevertheless, the experimentally detectable RW in ChG of binary As–S (Z = 2.225 ÷ 2.29) [6] and As–Se (Z = 2.29 ÷ 2.37) [68] systems occurs essentially shifted towards Ch side and too compositionally stretched to be accepted as realistic IPh signatures. Additionally, the compositional boundaries for RW in TM-DSC experiments were instable, showing an obvious trend to physical aging with prolonged duration [812] and changed storage conditions [8, 13, 14]. Furthermore, the notable dependence of aging time scales on the distance from glass transition region [15], which plays a decisive role in view of the known Williams–Landel–Ferry relation [16], was also ignored in these measurements.

Despite this argumentation, testifying that compositional boundaries of IPh in As–S/Se ChG determined as TM-DSC-probed RW [58] are rather artifacts of measuring procedure (revealing essential variation in sensitivities to different atomic entities [15, 17, 18]), origin of these compositional anomalies in a vicinity of Z = 2.225 (As–S system) and Z = 2.29 (As–Se system) remains still controversial. In this work, this specificity for As–S/Se ChG systems will be traced using ab initio quantum chemical modeling known as cation-interlinking network cluster approach (CINCA) [1922] applied to As2(S/Se)m nanoclusters.

Although As–S and As–Se are isotypical ChG systems, their network-forming tendencies differ essentially. Thus, the region of glass formation stretches from Z 2.00 (elemental Se) to Z 2.60 (As3Se2 glassy alloy) in As–Se system [2326], whereas it is distinctly narrower in As–S system being in the range of ~2.05 < Z < (2.44–2.46) [2326]. Myers and Felty [26] explained this by different melting behaviors of these systems. The region of stable homogeneous glasses depends on melt-quenching glass preparation technological route. For example, Hruby [27] pointed out that a second glass-forming region in As–S system exists at Z = 2.51 ÷ 2.66, when the melt was held for several hours at 300 ÷ 400 °C above the liquidus temperature.

Taking into account the phase diagrams of As–Ch systems (Ch = Se, S) [26, 28, 29], two intrinsic decomposition processes are to be expected for Ch-rich glass compositions (Z ≤ 2.40). The first process can be attributed to instability in a glassy network composed by As2Chm atomic clusters interlinked by Ch chains due to local demixing on compositionally close As2Chm+1 and As2Chm−1 clusters [12], this local chemical decomposition obeying scheme:
$$ 2\cdotp A{s}_2C{h}_m\leftrightarrow A{s}_2C{h}_{m+1} + A{s}_2C{h}_{m-1} $$
The second decomposition process is connected with global possibility of glassy network to be separated on two distinct phases, the stoichiometric As2Ch3 and “pure” chalcogen Ch. Noteworthy, this global phase separation in As2Chm ChG results in two corner-shared AsCh3/2 pyramids (i.e., As2Ch3 cluster) and Chm−3 remainder according to the reaction [12]:
$$ A{s}_2C{h}_m\leftrightarrow A{s}_2C{h}_3 + C{h}_{m-3}. $$

The main goal of this paper is to make comparison and discuss boundaries of structural phase stability in As–S/Se ChG in the light of currently available experimental evidences.


Nanoclusters Modeling Procedure

Within most generalized approach, atomic clusters of As2(S/Se)m chemical compositions which represented themselves as trigonal As(S/Se)3/2 pyramids linked by (S/Se)m–3 chains are principal network-forming clusters (NFC) in Ch-rich ChG of As–(S/Se) systems [25, 26, 30]. This simplification allows usage a simple simulation route for relatively small atomic entities and available software like Hyper Chem Release 7.5 program [31, 32], instead of complicated and time-consuming modeling procedures for multi-atomic glassy networks evolved hundreds or even thousands of atoms. The detailed information on main principles of developed modeling route (CINCA) you can find elsewhere [1922].

This approach applied recently to As–Se ChG based on As2Sem NFC [30] shows instability onset near Z = 2.25, where these glasses demonstrate strong tendency towards both global phase separation due to reaction (2) and local chemical decomposition due to reaction (1). In this work, the same CINCA simulation procedure will be applied to As2Sm NFC (m = 3 ÷ 9), which serves as a basis for S-rich ChG of binary As–S system.

Thus, the glass-forming tendencies in ChG of As–Ch system (Ch = S, Se) will be examined through a row of NFC built so to reflect most essential chemical interactions between high-coordinated cation-like atoms as branch points (threefold coordinated As atoms) [22]. Each As atom is supposed to form cation-centered polyhedron such as trigonal AsCh3/2 pyramid, which (in respect to chain-crossing model [25, 26]) is linked with other such pyramid by twofold coordinated Ch atoms. To quantify inter-cluster interaction, the outer part of atomic cluster (shell) should be distinguished from the remainder (core), and only “pure” interaction between these neighboring cations surrounded by the same cluster shells will be considered. It means that principle of the same topological shielding will be employed to reflect network-forming tendencies (the simplest cluster shell coincides with boundary of cation-centered cluster itself). Further, we allow slight deviations which enlarge cluster shell by equal amount of additional Ch atoms and reduce the number of Ch atoms between neighboring As cations, until this procedure is possible for chosen ChG composition. Difference in length of cluster core and shell determined by number of Ch half-atoms Δl describes deviation of network-forming tendency from chain-crossing model (Δl = 0 corresponds to chain-crossing arrangement, when all As atoms in cores and shells are interconnected by equivalent Chn chains). In this research, we consider only integer Δl values proper to symmetric clusters (with equivalent legs in cluster shell), while fractional ones proper to asymmetric clusters with different legs in shell are ignored. We suppose these asymmetric clusters will be ranged in their cluster-forming energy (CFE) between corresponding values for neighboring symmetric clusters. This simplification allows reliable quantum chemical calculations for smaller symmetric clusters with equivalent inter-cluster legs in cluster shells.

Thus, the CFE, i.e., energy of geometrically optimized NFC averaged per atom, is probed using the CINCA modeling supported by ab initio RHF/6-311G* calculations (this basis set is chosen as reliable for all clusters, despite their length and symmetry) [1922]. The geometrical optimization and single-point energy calculations are carried out with the Fletcher–Reeves conjugate gradient method until root-mean-square gradient of 0.1 kcal/Å mol is reached (the CFE is also corrected on H atoms terminated outer Ch atoms).

Results and Discussion

The average CFE for As2Sm NFC (m = 3 ÷ 9) in As–S system are gathered in Table 1 along with previously calculated data for As2Sem NFC (m = 3 ÷ 7) in As–Se ChG system [30]. Numerical values of CFE for geometrically optimized AsSe3/2 (E f  = −72.309 kcal/mol) and AsS3/2 (E f  = −79.404 kcal/mol) pyramids were taken as reference points for respective ChG.
Table 1

Average CFE for geometrically optimized As2Sm NFC in As–S system as compared with analogous data for As2Sem NFC in As–Se ChG [30] (best CFE are italicized)



E f , kcal/mol

Δl = 0

Δl = 1

Δl = 2

Δl = 3

Δl = 4

Δl = 5

Δl = 6

As–Se system






























As–S system














































The energetic barriers of intrinsic decomposition processes, denoted as ΔE(1) or ΔE(2) in accord to reactions (1) and (2), were calculated using bold-distinguished values of best CFE from Table 1. In calculations concerning decomposition of stoichiometric As2S3, the CFE of geometrically optimized As2S4/2 NFC (m = 2) based on bridging homonuclear As–As chemical bonds (E f  = −77.683 kcal/mol) was taken into account. To estimate an energetic preference of global chemical decomposition due to reaction (2), the CFE for geometry-optimized Sm−3 and Sem−3 nanoclusters were taken from [30, 33]. The corresponding compositional dependencies of energetic barriers ΔE(1) and ΔE(2) for best geometrically optimized NFC in As–Se/S ChG are depicted in Fig. 1 (the positive values are accepted for right-shifted equilibria, and errors are within symbol points).
Fig. 1

Compositional dependencies of energetic barriers of local chemical decomposition (a, c) and global phase separation (b, d) for geometrically optimized NFC in As–Se (a, b) and As–S (c, d) glassy systems (compositional domains of expected optimally constrained phase determined in respect to TM-DSC [58] are shadowed)

It is seen that As2Chm nanoclusters in both ChG systems show similar oscillating behavior in tendency to local chemical decomposition in respect to reaction (1). This decomposition on As2Chm+1 and As2Chm−1 clusters is energetically favorable for ChG with Z = 2.33, Z = 2.25, and Z = 2.20, while ChG of stoichiometric As2Ch3 (Z = 2.40) and As2Ch5 (Z = 2.29) compositions are stable against decomposition showing notable negative values of ΔE(1) barriers (Fig. 1a, c).

As to global phase separation on corner-shared AsCh3/2 pyramids (i.e., NFC of As2Ch3 composition) and Chm−3 remainder (i.e., NFC of “pure” Ch2/2 chemical composition) in respect to reaction (2), the behavior of examined As–Se and As–S ChG is principally different.

With going from Ch-rich compositions towards stoichiometry (i.e., As2Ch3 composition) in As–Se system, the most compliant ChG correspond to lowest Z (2.22 and 2.25), while other glasses with Z = 2.29, 2.33, and 2.40 are rather resistant to decomposition. This tendency is very weak because of the small difference in ΔE(2) barriers not exceeding 1.1 kcal/mol, but it is quite stable, especially as compared in a sum of two ΔE(1) and ΔE(2) barriers. In final, we can distinguish the As2Se5 glass (Z = 2.29), installing onset to As–Se ChG, which are most resistant against decomposition in respect to both reactions (1) and (2). Noteworthy, this As2Se5 composition coincides with beginning of RW (i.e., the rigidity transition) in binary As–Se ChG determined in TM-DSC experiments [68].

In contrast, decomposition processes are more significant in As–S ChG. Despite energetic barriers of global phase separation ΔE(2) in this system attain only negative values, this parameter clearly shows threshold-like behavior in a vicinity of Z = 2.22–2.25 (Fig. 1d). Initially, at higher Ch content (Z = 2.18, 2.20, 2.22), these ChG are rather well subjected to phase separation with nearly the same possibility defined by ΔE(2)  −0.9 kcal/mol. But with further tending towards stoichiometry, the As−S ChG becomes resistant to global phase separation in respect to reaction (2), this transition being revealed abruptly just near Z = 2.25. The latter seems to be responsible for eventually earlier rigidity transition in this ChG system at Z = 2.225 as detected using TM-DSC [6]. So, the glasses of As2S6 composition (Z = 2.25) can be accepted as introducing the compositional onset for decomposition-stable As-S ChG.

The geometrically optimized configurations of these NFC, i.e., As2Se5 (Z = 2.29, Δl = 2) and As2S6 (Z = 2.25, Δl = 0), introducing stability onsets in Ch-rich As-Se/S ChG, are presented in Fig. 2a and b, respectively, and the corresponding structural parameters of these glasses being given in Table 2. The model bond distances and angles for these nanoclusters occur to be close to the ones proper for known experimental prototypes [34, 35].
Fig. 2

Geometrically optimized configurations of NFC introducing stability onset in As–Se/S ChG: a As2Se5 (Z = 2.29, Δl = 2); b As2S6 (Z = 2.25, Δl = 0)

Table 2

Geometrical parameters of optimized NFC introducing stability onset in As-Se/S ChG: As2Se5 (Z = 2.29, Δl = 2) and As2S6 (Z = 2.25, Δl = 0)

Nanocluster, Z

Bond distance, [10−4 nm]

Bond angle, [deg]






As2Se5, Z = 2.29
























As2S6, Z = 2.25





















Specifically, in binary As–Se system, the stability onset corresponds to As2Se5 (Z = 2.29, Δl = 2) NFC, introducing locally inhomogeneous structural network, where each AsSe3/2 pyramid is connected with neighboring ones through two short =As–Se–As= bridges (i.e., single-atom Ch chain) and one long =As–Se–Se–Se–As= linkages (i.e., triple atoms Ch chain). That is why the As3Se7 glass corresponding to Z = 2.30, which is nominally composed of trigonal AsSe3/2 pyramids interlinked via double-atoms Ch chains (i.e., =As–Se–Se–As= units), demonstrates an obvious propensity to long-term physical aging due to local decomposition on short =As–Se–As= and long =As–Se–Se–Se–As= chain-like structural fragments, as it was convincingly evidenced from recent Raman scattering, NMR and high-resolution XPS measurements [36, 37]. More generally, the local chemical decomposition by reaction (1) dominates over global phase separation by reaction (2) in binary As–Se ChG, thus meaning shift in the stability onset of this system towards Ch-less compositions (Z ≥ 2.29).

Alternatively, the ChG of binary As–S system demonstrates an obvious tendency to keep ideal chain-crossing arrangement built of As2S6 NFC (Z = 2.25, Δl = 0) character for highly homogeneous structural network, where all trigonal AsS3/2 pyramids are interconnected via the same double-Ch atoms =As–S–S–As= links. The global phase separation by reaction (2) prevails over the local chemical decomposition by reaction (1) in this system (Fig. 1c, d), thus resulting in S-phase extraction for S-rich compositions with Z < 2.22, which is in an excellent harmony with well-known experimental data [2325, 3739]. In terms of potential energy landscape [4042], this binary As–S glass system can be described by distinguished double-well potentials for structural fragments based on double Ch atoms =As–S–S–As= and single Ch atom =As–S–As= linkages. Due to high difference in the energetic barriers that separated these states, this system tends towards Ch-phase extraction at higher S content, but not towards local decomposition on neighboring intrinsic compounds.

Therefore, the effects of long-term physical aging in the studied ChG belonging to the RW defined using TM-DSC [58] result preferentially from global phase separation via reaction (1) in As–S system (due to high localization of covalent chemical bonding) and local demixing on compositionally neighboring As2Sem+1 and As2Sem–1 clusters via reaction (2) in As–Se system. It means that the IPh determined as TM-DSC-defined RW for both As–Se/S systems [58] are only artifacts of this experimental measuring procedure, which have no any relation to realistic topological phase transitions in respect to the rigidity theory [1, 2].

Interestingly, the minimal barriers in global phase separation ΔE(2) for both As–S/Se ChG roughly coincide with the center of compositional domains ascribed to the TM-DSC-defined RW [58]. Thus, the As2Se4 (Z = 2.33) and As2S6 (Z = 2.29) ChG possess the ΔE(2) barriers reaching respectively −0.918 kcal/mol and −3.734 kcal/mol. So it should be expected that long-term physical aging will be also revealed in ChG of these chemical compositions, as it was well documented experimentally [1113, 18].

The region of stable homogeneous glass-forming ability in ChG is known to be strongly dependent on glass preparation conditions (melting temperature, quenching rate, etc.) [2326]. The obtained results show energetic preference of some cluster-forming tendencies. The structures of more extended configurations are determined by specifics of covalent chemical bonds with characteristic fluctuations in charge density distribution and bond directionality. The network-forming clusters in this research reflect principal conditions of covalent-like interactions, chemical composition, and space topology for ideal bond-saturated network in thermodynamically equilibrium conditions (there are no surfaces, coordination defects or dangling bonds, etc.). Anomalous preparation conditions provide ChG with different structural defects, which cannot be strictly evaluated within this simplified approach.


Chalcogen-rich As–S/Se glassy systems are traced using ab initio quantum chemical modeling known as cation-interlinked network cluster approach applied to As2(S/Se)m nanoclusters to recognize expected variations in a vicinity of some remarkable compositions accepted as signatures of optimally constrained, rigid but unstressed intermediate topological phases in earlier temperature-modulated differential scanning calorimetry experiments. The examined As2(S/Se)m network-forming nanoclusters show similar oscillating character in tendency to local chemical decomposition but obvious step-like behavior in preference to global phase separation on boundary chemical compounds. The global phase separation is dominant in S-rich As–S glasses, keeping chain-crossing arrangement character for highly homogeneous structural networks, while local demixing on compositionally neighboring nanoclusters prevails in Se-rich As–Se glasses possessing inhomogeneous structural networks. The geometrically optimized configurations of As2Se5 (Z = 2.29) and As2S6 (Z = 2.25) nanoclusters introducing onsets of stability in binary As–Se/S systems are simulated. These compositions are shown to coincide well with lower limits of reversibility windows in temperature-modulated differential scanning calorimetry.



Cluster-forming energy




Chalcogenide glasses


Cation-interlinking network clusters approach


Floppy phase


Intermediate phase


Network-forming cluster


Reversibility window


Stress-rigid phase


Temperature-modulated differential scanning calorimetry



This research was performed in the framework of agreement on scientific-technological cooperation between the Lviv Scientific Research Institute of Materials of Scientific Research Company “Carat” (Ukraine) and the Institute of Physics of Jan Dlugosz University of Czestochowa (Poland). It is a pleasure to thank Prof. Oleh Shpotyuk for the helpful discussions.

Authors’ Contributions

MH performed the CINCA calculations for all NFC in As–Se/S systems, developed the model explaining compositional variations, and prepared and submitted the manuscript. The author read and approved the final manuscript.

Competing Interests

The author declares no competing interests.

Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (, which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

Authors’ Affiliations

Institute of Physics of Jan Dlugosz University of Czestochowa
Lviv Scientific-Research Institute of Materials of Scientific Research Company “Carat”


  1. Phillips JC (1979) Topology of covalent non-crystalline solids I: short-range order in chalcogenide alloys. J Non-Cryst Sol 34:153–81View ArticleGoogle Scholar
  2. Thorpe MF (1983) Continuous deformations in random networks. J Non-Cryst Sol 57:355–70View ArticleGoogle Scholar
  3. Selvanathan D, Bresser WJ, Boolchand P, Goodman B (1999) Thermally reversing window and stiffness transitions in chalcogenide glasses. Solid State Commun 111:619–24View ArticleGoogle Scholar
  4. Thorpe MF, Jacobs DJ, Chubynsky MV, Phillips JC (2000) Self-organization in network glasses. J Non-Cryst Sol 266-269:859–66View ArticleGoogle Scholar
  5. Boolchand P, Georgiev DG, Goodman B (2001) Discovery of the intermediate phase in chalcogenide glasses. J Opt Adv Mat 3:703–20Google Scholar
  6. Boolchand P, Chen P, Vempati U (2009) Intermediate phases, structural varience and network demixing in chalcogenides: the unusual case of group V sulphides. J Non-Cryst Sol 355:1773–85View ArticleGoogle Scholar
  7. Georgiev DG, Boolchand P, Micoulaut M (2000) Rigidity transitions and molecular structure of AsxSe1-x glasses. Phys Rev B 62:R9228–31View ArticleGoogle Scholar
  8. Chen P, Boolchand P, Georgiev DG (2010) Long term aging of selenide glasses: evidence of sub-T g endotherms and pre-T g endotherms. J Phys: Condens Matter 22:065104Google Scholar
  9. Saiter JM, Arnoult M, Grenet J (2005) Very long physical ageing in inorganic polymers exemplified by the GexSe1-x vitreous system. Phys B: Condens Matter 355:370–6View ArticleGoogle Scholar
  10. Elabbar AA, Abu-Sehly AA (2011) Structural relaxation and rigidity transition in aged and rejuvenated AsxSe100-x glasses. Phys B: Condens Matter 406:4261–5View ArticleGoogle Scholar
  11. Golovchak RY, Gorecki C, Kozdras A, Shpotyuk OI (2006) Physical ageing effects in vitreous arsenic selenides. Solid State Commun 137:67–9View ArticleGoogle Scholar
  12. Golovchak R, Jain H, Shpotyuk O, Kozdras A, Saiter A, Saiter JM (2008) Experimental verification of the reversibility window concept in binary As-Se glasses subjected to a long-term physical aging. Phys Rev B 78:014202-1-6View ArticleGoogle Scholar
  13. Shpotyuk O, Golovchak R, Kozdras A (2014) Physical ageing of chalcogenide glasses. In: Adam J-L, Zhang X (eds) Chalcogenide glasses: preparation, properties and applications. Woodhead Publishing Series in Electronic and Optical Materials, Philadelphia-New Delhi, pp 209–264View ArticleGoogle Scholar
  14. Golovchak R, Kozdras A, Shpotyuk O, Gorecki C, Kovalskiy A, Jain H (2011) Temperature-dependent structural relaxation in As40Se60 glass. Phys Lett A 375:3032–36View ArticleGoogle Scholar
  15. Zhao HY, Koh YP, Pyda M, Sen S, Simon SL (2013) The kinetics of the glass transition and physical aging in germanium selenide glasses. J Non-Cryst Sol 368:63–70View ArticleGoogle Scholar
  16. Williams ML, Landel RF, Ferry JD (1955) The temperature dependence of relaxation mechanisms in amorphous polymers and other glass-forming liquids. J Am Chem Soc 77:3701–7View ArticleGoogle Scholar
  17. Lucas P, King EA, Gulbiten O, Yarger JL, Soignard E, Bureau B (2009) Bimodal phase percolation model for the structure of Ge-Se glasses and the existence of the intermediate phase. Phys Rev B 80:2141140-1-8Google Scholar
  18. Shpotyuk O, Kozdras A, Golovchak R, Iovu M (2011) Is the marginality of non-reversible heat flow in MDSC experiments a sufficient criterion for self-organization in network glass-formers? Phys Status Solidi C 8:3043–6View ArticleGoogle Scholar
  19. Shpotyuk O, Boyko V, Shpotyuk Y, Hyla M (2009) CINCA: cation-interlinking network cluster approach in application to binary glassy chalcogenides. Visnyk Lviv Univ Ser Phys 43:226–32Google Scholar
  20. Hyla M, Boyko V, Shpotyuk O, Filipecki J (2009) Two-cation corner- and edge-sharing interlinked clusters in As/Ge-S glasses. Visnyk Lviv Univ Ser Phys 43:118–25Google Scholar
  21. Shpotyuk O, Boyko V, Hyla M (2009) Cation-interlinking network cluster approach in application to extended defects in covalent-bonded glassy semiconductors. Phys Status Solidi C 6:1882–5View ArticleGoogle Scholar
  22. Shpotyuk O, Hyla M, Boyko V (2013) Structural-topological genesis of network-forming nanoclusters in chalcogenide semiconductor glasses. J Opt Adv Mat 15:1429–37Google Scholar
  23. Borisova ZU (1981) Glassy semiconductors. Plenum Press, New YorkView ArticleGoogle Scholar
  24. Borisova ZU (1972) Chemistry of glassy semiconductors. Izd LGU, LeningradGoogle Scholar
  25. Feltz A (1993) Amorphous inorganic materials and glasses. VCH Publishers, New YorkGoogle Scholar
  26. Myers MB, Felty EJ (1967) Structural characterizations of vitreous inorganic polymers by thermal studies. Mat Res Bull 2:535–46View ArticleGoogle Scholar
  27. Hruby A (1978) A study of glass-forming ability and phase diagram of the As-S system. J Non-Cryst Sol 28:139–42View ArticleGoogle Scholar
  28. Blachnik R, Hoppe A, Wickel U (1980) Die Systeme Arsen-Schwefel und Arsen-Selen und die thermodynamischen Daten ihrer Verbindungen. Z Anorg Allg Chem 463:78–90View ArticleGoogle Scholar
  29. Okamoto H (1998) As-Se (Arsenic-Selenium). J Phase Equlibria 19:488View ArticleGoogle Scholar
  30. Shpotyuk O, Hyla M, Boyko V (2015) Compositionally-dependent structural variations in glassy chalcogenides: the case of binary As-Se system. Comp Mat Sci 110:144–51View ArticleGoogle Scholar
  31. Henre WJ, Stewart RF, Pople JA (1969) Self-consistent molecular orbital methods I. Use of Gaussian expansions of Slater type atomic orbitals. J Chem Phys 51:2657–64View ArticleGoogle Scholar
  32. McLean AD, Chandler GS (1980) Contracted Gaussian basis sets for molecular calculations. I. Second row atoms, Z = 11–18. J Chem Phys 72:5639–48View ArticleGoogle Scholar
  33. Boyko V, Hyla M, Shpotyuk O (2009) Chain- and ring-like sulphur clusters: modeling within HyperChem program. Visnyk Lviv Univ Ser Phys 43:233–7Google Scholar
  34. Renninger AL, Averbach BL (1973) Atomic radial distribution functions of As-Se glasses. Phys Rev B 8:1507–14View ArticleGoogle Scholar
  35. Yang CY, Paesler MA, Sayers DE (1989) Chemical order in the glassy AsxS1-x system: An X-ray-absorption spectroscopy study. Phys Rev B 39:10342–50View ArticleGoogle Scholar
  36. Golovchak R, Bureau B, Shpotyuk O, Boyko V, Hyla M (2013) Bond-changing structural rearrangement in glassy As3Se7 associated with long-term physical aging. J Non-Cryst Sol 377:43–5View ArticleGoogle Scholar
  37. Deschamps M, Roiland C, Bureau B, Yang G, Le Polles L, Massiot D (2011) 77Se solid-state NMR investigations on AsxSe1-x glasses using CPMG acquisition under MAS. Solid State Nucl Magn Reson 40:72–7View ArticleGoogle Scholar
  38. Tsuchihashi S, Kawamoto Y (1971) Properties and structure of glasses in the system As-S. J Non-Cryst Sol 5:286–305View ArticleGoogle Scholar
  39. Maruno S, Noda M (1972) Microstructure of glasses in the system As2Sx with x < 3. J Non-Cryst Sol 7:1–11View ArticleGoogle Scholar
  40. Golovchak R, Kovalskiy A, Shpotyuk O, Jain H (2011) In search of energy landscape for network glasses. Appl Phys Lett 98:171905-1-3View ArticleGoogle Scholar
  41. Goldstein M (1969) Viscous liquids and the glass transition: a potential energy barrier picture. J Chem Phys 51:3728–39View ArticleGoogle Scholar
  42. Stillinger H (1995) A topographic view of supercooled liquids and glass formation. Science 267:1935–9View ArticleGoogle Scholar


© The Author(s). 2017