Abstract
A prerequisite for understanding the physico-chemical properties of network glass-forming materials is knowledge about their atomic-scale structure. The desired information is not, however, easy to obtain because structural disorder in a liquid or glass leads to complexity. It is therefore important to design experiments to give site-specific information on the structure of a given material in order to test the validity of different molecular dynamics models. In turn, once a molecular dynamics scheme contains the correct theoretical ingredients, it can be used both to enrich the information obtained from experiment and to predict the composition and temperature/pressure dependence of a material’s properties, a first step in using the principles of rational design to prepare glasses with novel functional properties. In this chapter the symbiotic relationship between experiment and simulation is explored by focussing on the structures of liquid and glassy ZnCl\(_2\) and GeSe\(_2\), and on the structure of glassy GeO\(_2\) under pressure. Issues to be addressed include extended range ordering on a nanometre scale, the formation of homopolar (like-atom) bonds, and the density-driven mechanisms of network collapse.
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Notes
- 1.
In the literature, the results from RMC or EPSR models are sometimes erroneously referred to as ‘experimental results’ when comparisons are made with molecular dynamics simulations.
- 2.
- 3.
Chalcogenide glass-forming materials are those containing one or more of the chalcogen elements S, Se and Te.
- 4.
A rigorous derivation of the Lorch modification function and its corresponding real-space representation is given in [50].
- 5.
The radii correspond to six-fold coordinated ions.
- 6.
A so-called principal peak or trough at \(k_\mathrm{PP} \simeq \) 2–3 Å\(^{-1}\) is a common feature in the partial structure factors for liquid and glassy materials [47].
- 7.
The \(r\)-space functions for the liquid were obtained from a maximum entropy analysis in which homopolar bonds were not excluded. Those for the glass were obtained from a procedure aimed at removing the effect in \(r\)-space of the modification function \(M(k)\). A more complete discussion is given in [21, 23, 80].
- 8.
For the glass, an estimate of the number of Ge atoms in CS tetrahedra \(N_\mathrm{Ge, CS}\) can be obtained by taking \(N_\mathrm{Ge} = N_\mathrm{Ge, ES} + N_\mathrm{Ge, CS} + N_\mathrm{Ge, homo}\) where \(N_\mathrm{Ge, homo}\) is the number of Ge atoms in homopolar Ge–Ge bonds (see Appendix). If there are no extended chains of ES units then the corresponding coordination number \(\bar{n}_\mathrm{Ge}^\mathrm{Ge} = \left( N_\mathrm{Ge, ES} \times 1\right) /N_\mathrm{Ge}\) = 0.34(5) and if homopolar bonds form only in pairs then the corresponding coordination number \(\bar{n}_\mathrm{Ge}^\mathrm{Ge} = \left( N_\mathrm{Ge, homo} \times 1\right) /N_\mathrm{Ge}\) = 0.25(5). Hence \(N_\mathrm{Ge, CS}/N_\mathrm{Ge}\) = 1 \(-\) 0.34(5) \(-\) 0.25(5) = 0.41(7) such that \(N_\mathrm{Ge, ES}/N_\mathrm{Ge, CS}\) = 0.34(5)/0.41(7) = 0.83(16) [23].
- 9.
In [31] a first-principles molecular dynamics model for liquid GeSe\(_2\) using the Perdew and Wang generalised gradient approximation was given as an example of a class III system. More recent models of this material using the BLYP generalised gradient approximation reduce the chemical disorder and produce a more pronounced FSDP in \(S_\mathrm{CC}(k)\), in better accord with experiment (Fig. 1.9). The measured FSDP in \(S_\mathrm{CC}(k)\) for glassy GeSe\(_2\) is accurately reproduced by first-principles molecular dynamics simulations using the BLYP generalised gradient approximation (Fig. 1.9).
- 10.
A ring is a measure of the network topology and is a closed path usually chosen to pass along the bonds which connect nearest-neighbour atoms. A ring is primitive if it cannot be decomposed into smaller rings [108].
- 11.
As shown in Fig. 1.13b, the Ge–O coordination number obtained at \(\sim \)8 GPa (\(\rho /\rho _0 \sim \) 1.4) from the IXS experiments is large relative to the value obtained from neutron diffraction experiments in a regime for which the IXS data give, relative to molecular dynamics, a much greater fraction of GeO\(_6\) units relative to GeO\(_4\) and GeO\(_5\) units (Fig. 1.14a).
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Acknowledgments
It is a pleasure to thank everyone who has contributed towards the experimental programme of research at Bath and UEA into the nature of network glass-forming materials, including Ian Penfold, Chris Benmore, Paul Lond, Erol Okan, Jian Liu, Shuqin Xin, Jonathan Wasse, Takeshi Usuki, Ingrid Petri, Richard Martin, James Drewitt, Prae Chirawatkul, Dean Whittaker, Kamil Wezka, Keiron Pizzey, Ruth Rowlands, Annalisa Polidori and Harry Bone. Special thanks also go to Adrian Barnes (Bristol), Pierre Chieux (ILL), Wilson Crichton (ESRF), Gabriel Cuello (ILL), Henry Fischer (ILL) and Stefan Klotz (Paris) for their contributions to the experimental work; and to Mauro Boero (Strasbourg), Assil Bouzid (Strasbourg), Sébastien Le Roux (Strasbourg), Dario Marrocchelli (MIT), Carlo Massobrio (Strasbourg), Matthieu Micoulaut (Paris), Alfredo Pasquarello (Lausanne) and Mark Wilson (Oxford) for all their contributions on the molecular dynamics front. The latter are also thanked for agreeing to a close dialogue with the experimental teams, where the feedback has been mutually beneficial in helping to decode the complexity of network glass-forming materials, and has also led to a fuller appreciation of both the advantages and limitations of experimental versus molecular dynamics methods. The support of the EPSRC (Grant: EP/J009741/1) and Institut Laue-Langevin (ILL) is gratefully acknowledged.
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Appendix: Concentration of Defects in GeSe\(_2\) Glass from the Law of Mass Action
Appendix: Concentration of Defects in GeSe\(_2\) Glass from the Law of Mass Action
Following Feltz [127, 128], consider the reversible reaction
where homopolar or defect bonds are formed in pairs, and for which the law of mass action gives an equilibrium constant
where \(\left[ \mathrm{A}{-}\mathrm{B}\right] \) represents the concentration of A\(-\)B bonds, \(\varDelta G\) is the standard reaction Gibbs energy, R is the molar gas constant, and \(T\) is the absolute temperature. From (1.18) it follows that the concentration of Ge\(-\)Ge or Se\(-\)Se defect bonds \(n_d\) = \(\left[ \mathrm{Ge}{-}\mathrm{Ge}\right] \) = \(\left[ \mathrm{Se}{-}\mathrm{Se}\right] \) where the Ge\(-\)Ge homopolar bonds might be in ethane-like Se\(_{3/2}\)Ge\(-\)GeSe\(_{3/2}\) units as suggested by \(^{119}\)Sn Mössbauer spectroscopy experiments [83, 129] and the Se\(-\)Se homopolar bonds might be in dimers linking Ge-centred tetrahedra. Equation (1.19) can therefore be re-written as
where \(n_0 \equiv \left[ \mathrm{Ge}{-}\mathrm{Se}\right] \). If the concentration of defects is small such that \(n_d \ll n_0\) then the latter is approximately equal to the concentration of Ge\(-\)Se bonds in a non-defected system.
\(\varDelta G\) can be estimated from the difference between the Ge\(-\)Se, Ge\(-\)Ge and Se\(-\)Se bond enthalpies which take values of 225, 188 and 227 kJ mol\(^{-1}\), respectively, at 298 K i.e. \(\varDelta G \simeq \varDelta H\) = 2\(\times \)225 \(-\) 188 \(-\) 227 = 35 kJ mol\(^{-1}\) [127]. Hence, an estimate for the fraction of defects in the melt at the glass transition temperature (\(T_g\) = 665 K) is given by \(n_d/n_0 \simeq \) 0.042. Alternatively, if \(n_d \equiv N_d/V\) and \(n_0 \equiv N_\mathrm{bond}/V\), where \(N_d\) is the number of Ge\(-\)Ge or Se\(-\)Se homopolar bonds and \(N_\mathrm{bond}\) is the total number of bonds, it follows that \(N_d/N_\mathrm{bond} \simeq \) 0.042. This ratio is probably a lower limit because the value of \(\varDelta G\) used in the calculation is likely to decrease when the entropy term \(\varDelta S\) is taken into account (\(\varDelta G = \varDelta H - T\varDelta S\) if the absolute temperature \(T\) is constant), and the reaction enthalpy \(\varDelta H\) is likely to be smaller at \(T_g\) as compared to room temperature [127, 128].
Let the total number of atoms in the system be denoted by \(N = N_\mathrm{Ge} + N_\mathrm{Se}\) where \(N_\mathrm{Ge}\) and \(N_\mathrm{Se}\) are the numbers of Ge and Se atoms, respectively, such that the atomic fractions are given by \(c_\mathrm{Ge} = N_\mathrm{Ge}/N\) and \(c_\mathrm{Se} = N_\mathrm{Se}/N\). From the NDIS results on GeSe\(_2\) glass [22, 23], the coordination number for Ge\(-\)Ge homopolar bonds \(\bar{n}_\mathrm{Ge}^\mathrm{Ge}\) = 0.25(5). If these bonds form only in pairs then \(\bar{n}_\mathrm{Ge}^\mathrm{Ge} = \left( N_\mathrm{Ge, homo} \times 1\right) /N_\mathrm{Ge}\) such that the number of Ge\(-\)Ge bonds is given by \(N_\mathrm{Ge{-}Ge} = \left( \bar{n}_\mathrm{Ge}^\mathrm{Ge} \times N_\mathrm{Ge}\right) /2\) where the factor of two avoids double counting and \(N_\mathrm{Ge} = N/3\). It follows that \(N_\mathrm{Ge{-}Ge}\) = 0.042(8)\(N\). Similarly, from the NDIS results the coordination number for Se\(-\)Se homopolar bonds \(\bar{n}_\mathrm{Se}^\mathrm{Se}\) = 0.20(5). If these bonds form only in pairs then \(\bar{n}_\mathrm{Se}^\mathrm{Se} = \left( N_\mathrm{Se, homo} \times 1\right) /N_\mathrm{Se}\) such that the number of Se\(-\)Se bonds is given by \(N_\mathrm{Se{-}Se} = \left( \bar{n}_\mathrm{Se}^\mathrm{Se} \times N_\mathrm{Se}\right) /2\) where the factor of two avoids double counting and \(N_\mathrm{Se} = 2N/3\). It follows that \(N_\mathrm{Se{-}Se}\) = 0.067(17)\(N\). Thus, within the experimental error, \(N_\mathrm{Ge{-}Ge} \sim N_\mathrm{Se{-}Se}\) as in the model of Feltz [127] such that \(N_d \simeq \left( N_\mathrm{Ge{-}Ge} + N_\mathrm{Se{-}Se}\right) /2\) = 0.05(2)\(N\).
For GeSe\(_2\), the number of Ge\(-\)Se bonds in a non-defected system \(N_\mathrm{bond}\) \(=\) \((N_\mathrm{Ge}Z_\mathrm{Ge}\) \(+\) \(N_\mathrm{Se}Z_\mathrm{Se})/2\) = \(\left( c_\mathrm{Ge}Z_\mathrm{Ge} + c_\mathrm{Se}Z_\mathrm{Se}\right) N/2\) where \(Z_\alpha \) is the number of bonds formed by chemical species \(\alpha \). Since \(Z_\mathrm{Ge}\) = 4, \(Z_\mathrm{Se}\) = 2, \(c_\mathrm{Ge}\) = 1/3, \(c_\mathrm{Se}\) = 2/3 it follows that \(N_\mathrm{bond}\) = \(4N/3\). Thus \(N_d/N_\mathrm{bond} \simeq \) 0.04(2) for the NDIS results, which is in agreement with the value \(N_d/N_\mathrm{bond} \simeq \) 0.042 estimated by using the law of mass action.
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Salmon, P.S., Zeidler, A. (2015). The Atomic-Scale Structure of Network Glass-Forming Materials. In: Massobrio, C., Du, J., Bernasconi, M., Salmon, P. (eds) Molecular Dynamics Simulations of Disordered Materials. Springer Series in Materials Science, vol 215. Springer, Cham. https://doi.org/10.1007/978-3-319-15675-0_1
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