Thermostructural and Elastic Properties of PbTe and Pb 0.884 Cd 0.116 Te: A Combined Low-Temperature and High-Pressure X-ray Diffraction Study of Cd-Substitution Effects

: Rocksalt-type (Pb,Cd)Te belongs to IV–VI semiconductors exhibiting thermoelectric properties. With the aim of understanding of the inﬂuence of Cd substitution in PbTe on thermostructural and elastic properties, we studied PbTe and Pb 0.884 Cd 0.116 Te (i) at low temperatures (15 to 300 K) and (ii) at high pressures within the stability range of NaCl-type PbTe (up to 4.5 GPa). For crystal structure studies, powder and single crystal X-ray diffraction methods were used. Modeling of the data included the second-order Grüneisen approximation of the unit-cell-volume variation, V ( T ), the Debye expression describing the mean square atomic displacements (MSDs), < u 2 >( T ), and Birch–Murnaghan equation of state (BMEOS). The ﬁtting of the temperature-dependent diffraction data provided model variations of lattice parameter, the thermal expansion coefﬁcient, and MSDs with temperature. A comparison of the MSD runs simulated for the PbTe and mixed (Pb,Cd)Te crystal leads to the conﬁrmation of recent ﬁndings that the cation displacements are little affected by Cd substitution at the Pb site; whereas the Te displacements are markedly higher for the mixed crystal. Moreover, information about static disorder caused by Cd substitution is obtained. The calculations provided two independent ways to determine the values of the overall Debye temperature, θ D . The resulting values differ only marginally, by no more than 1 K for PbTe and 7 K for Pb 0.884 Cd 0.116 Te crystals. The θ D values for the cationic and anionic sublattices were determined. The Grüneisen parameter is found to be nearly independent of temperature. The variations of unit-cell size with rising pressure (the NaCl structure of Pb 0.884 Cd 0.116 Te sample was conserved), modeled with the BMEOS, provided the dependencies of the bulk modulus, K , on pressure for both crystals. The K 0 value is 45.6(2.5) GPa for PbTe, whereas that for Pb 0.884 Cd 0.116 Te is signiﬁcantly reduced, 33.5(2.8) GPa, showing that the lattice with fractional Cd substitution is less stiff than that of pure PbTe. The obtained experimental values of θ D and K 0 for Pb 0.884 Cd 0.116 Te are in line with the trends described in recently reported theoretical study for (Pb,Cd)Te mixed crystals. the study presents detailed quantitative information on the thermostructural and elastic properties of rocksalt-type crystals of PbTe and Pb 0.884 Cd 0.116 Te; such data are not yet available for alloys of the Pb 1 − x Cd x Te system. The obtained results show a consistent image of inﬂuence of the partial substitution of Pb ions by Cd ions, in the PbTe lattice, on the thermostructural properties. Namely, the obtained results show how the lattice parameter, the thermal expansion coefﬁcient, the atomic mean-square displacements and other thermostructural properties (compressibility, Debye temperature, Grüneisen parameter and others) depend on the cadmium content. In particular it was found, that the Pb 0.884 Cd 0.116 Te lattice is less stiff than that of PbTe, whereas thermal expansion of the mixed crystal is discernibly larger. The described extension of the knowledge on the studied properties is expected to be proﬁtable in a further work on the application of the fractionally substituted Cd lead telluride.


Knowledge on Thermostructural and Elastic Properties for PbTe and Pb 1−x Cd x Te
Numerous studies on thermostructural and elastic properties of PbTe have been performed. However, some are not very detailed, and not many of them include the lowest (below 100 K) temperatures. Among the studies, the most detailed work is that of ref. [29], in which neutron powder diffraction was used to determine variations of the lattice parameter, thermal expansion coefficient (TEC), and mean square atomic displacements (MSDs) as a function of temperature. Other experimental studies refer to narrower temperature ranges or describe selected variables only. One of the frequently considered characteristics of thermoelectric materials is the degree of ordering [30]. Some recent studies focus on appearance of the cation disorder in PbTe and related chalcogenides [31][32][33][34]. The introduced disorder can affect the thermal conductivity of the crystal [31]. The substitutional disorder in the (Pb,Cd)Te alloys system has also been recently discussed in ref. [35]. However, the analysis of disorder based on temperature-dependent properties is still lacking for this ternary system.
The PbTe-CdTe phase diagram [13] (for theoretical considerations, see ref. [66]) shows that the solubility, with equilibrium conditions at room temperature, of CdTe in PbTe is marginal. This is a consequence of the difference in their crystal structure-a rocksalt type for PbTe and a zinc-blende type for CdTe. However (as mentioned in the Introduction section), the Pb 1−x Cd x Te solid solution of the rocksalt type can be prepared in a metastable form. A diffraction study on the structure of Pb 1−x Cd x Te as a function of temperature has shown the decomposition process of metastable Pb 1−x Cd x Te (x = 0.096) during heating [43]; these results led to evaluation of the maximum achievable Cd content in the metastable Crystals 2021, 11, 1063 7 of 32 solid solution [13]. Some theoretical calculations based on first principles have been presented in ref. [68].
Experimental investigations show that the transition to a high-pressure polymorph occurs at about 6-7 GPa [70,[77][78][79][80][81][82][83], (see also theoretical studies [67,84,85]). The space group of this phase is Pnma, the lattice parameters at 7.5 GPa are a = 11.91 Å, b = 4.20 Å, c = 4.51 Å [70]. From about 18 GPa to at least 50 GPa, a CsCl type phase exists [83]. Recently, a topological transition at 4.8 GPa was reported in a density functional theory study [86]. Interestingly, the combination of the features of immiscibility and latticeparameter similarity of the PbTe and CdTe components leads to the opportunity for the growth of heterostructures (which can be applied in the construction of room-temperature infrared detectors, for example [87]).

Aim
The purpose of this study is to systematically determine the influence of cadmium substitution on the thermostructural and elastic properties of PbTe. To achieve this goal, these properties (lattice parameter, thermal expansion, atomic displacements, bulk modulus and their variation with temperature or pressure) were studied and compared for two crystals, PbTe and Pb 0.884 Cd 0.116 Te. The literature data for PbTe are reviewed and taken into account in the comparative analysis of properties of these two crystals.

Materials and Methods
The PbTe and Pb 1−x Cd x Te single crystals were obtained by the self-selecting vapor growth (SSVG) method described in refs. [88,89]. High purity polycrystalline PbTe and CdTe compounds were used as reaction components. The conditions were similar to those used in earlier work [19]. To produce the PbTe-CdTe solid solution, the synthesis was performed using a mixture of PbTe and CdTe enclosed in a sealed quartz ampoule located in a furnace with a gradient of about 1 deg/cm at a temperature of about 850°C. The process of growth of homogeneous (Pb,Cd)Te crystals lasted two weeks. Further details of the growth procedure can be found in refs. [19,90]. The Cd content, x = 0.116, was derived from the a(T) dependence reported in ref. [19].
Synchrotron-radiation techniques offer valuable experimental approaches for studies of materials; in particular, thermoelectric materials [91]. Here, we focus on the use of synchrotron radiation diffraction to extract the structural information on PbTe and Pb 1−x Cd x Te. The in-situ low-temperature measurements were performed using synchrotron X-ray powder diffraction [92] at HASYLAB, Hamburg. The Debye-Scherrer geometry with monochromatic radiation (λ = 0.5385 Å) and an image plate detector [93] were applied. The incident beam size was 1 × 15 mm 2 . The measurements were performed in the 2θ range of 7-58 • (corresponding d-spacing range is 4.410-0.555 Å), and for samples mounted in glass capillaries (Hilgenberg) of 0.3 mm diameter, the X-ray powder diffraction patterns were recorded with a 0.004 • (2θ) step.
The samples were prepared as a mixture of powdered Pb 1−x Cd x Te crystals and fine diamond powder (Sigma-Aldrich #48,359-1 synthetic powder), of~1 µm monocrystalline grain size and purity of 99.9%). Addition of diamond powder served for both, (i) a diluent and (ii) an internal diffraction standard, avoiding the possible influence of wavelength instabilities (the use of such a standard has been proposed in ref. [94]). Low-temperature conditions (temperature range 15-300 K) were ensured by a closed-circuit He-cryostat. For the structural analysis, the Rietveld method [95,96] was applied using the refinement program, Fullprof.2k(v.7) [97]. In calculations, the pseudo-Voigt profile-shape function was assumed. The following parameters were refined: scale factor, lattice parameters, isotropic mean square displacement parameters, peak shape parameters, and systematic line-shift parameter. The background was set manually.
A Merrill-Bassett diamond-anvil cell (DAC) [98] was used in high-pressure experiments. The single-crystal sample was mounted inside the DAC chamber with a MeOH:EtOH:H 2 O (16:3:1) mixture as the pressure-transmitting medium. The pressure was calibrated with a Photon Control spectrometer by the ruby-fluorescence method [99], assuring a precision of 0.02 GPa. The experiments were conducted at a temperature of 296 K. High-pressure single-crystal X-ray diffraction data were collected at a four-circle KUMA X-ray diffractometer equipped with a graphite monochromator for the applied MoKα radiation. The gasket shadowing method was used for crystal centering and data collection [100]. The size of the diamond culets was 0.7 mm, the size of crystal for PbTe was 0.2 × 0.05 × 0.15 mm 3 , for Pb 0.884 Cd 0.116 Te was 0.23 × 0.05 × 0.17 mm 3 (only one crystal was loaded into DAC). UB-matrix determinations and data reductions were performed with the program CrysAlisPro [101]. The structures were solved by direct methods using the program ShelXS and refined by full-matrix leastsquares on F 2 using the program ShelXT incorporated in Olex2 [102,103]. For high-pressure data analysis, the fitting procedures were conducted with the EoSFit7 program [104,105]. The data provided by powder and single-crystal X-ray diffraction methods allowed the determination of the structural and elastic properties of PbTe and Pb 1−x Cd x Te (x = 0.116) in the 15-300 K temperature range and separately, in 0.1 MPa-4.5 GPa pressure range. Consequently, the properties measured at the same conditions for each of two crystals could be analyzed, leading to the understanding of the effect of Cd substitution on the crystal characteristics.
For pure PbTe, most of these properties were known in advance, but the information regarding temperatures below 105 K has been mostly based on the results of neutron powder diffraction of ref. [29]. The present study is one of few X-ray diffraction studies of the thermostructural properties of PbTe, covering an extended temperature range, and jointly analyzing all the three a(T), α(T), and <u 2 >(T) experimental variations, completed by the V(p) study. For the Pb 1−x Cd x Te system, the detailed investigations at non-ambient temperature and pressure have been almost completely lacking.
Phase analysis showed that the samples were single phase crystals. The analysis of powder diffraction data of PbTe and Pb 0.884 Cd 0.116 Te by the Rietveld method yielded direct information on (i) the temperature dependencies of unit-cell size, a(T), and (ii) mean square displacements, <u 2 >(T), of both, cations and anions. Illustrative examples of structure refinement plots for PbTe and Pb 1−x Cd x Te at temperatures 15 K and 300 K are given in Appendix A ( Figure A1). Subsequent analysis of the a(T) data led to the derivation of the temperature variation of the thermal expansion coefficient, α(T). The modeling of the temperature variations of the studied quantities allowed for independent determination also of other properties, for both the cationic and anionic sublattices of studied crystals. The experimental lattice parameter of PbTe varies in the 15-300 K range in a monotonic way (see Figure 2). The unit-cell volume, V(T), variation was modeled by the second-order Grüneisen approximation, taking into account the Debye internal-energy function [106,107]: where: Q and b are constants. E(T) in Equation (1), expressed as represents the Debye energy model of lattice vibrations, n is the number of atoms in the unit cell, k B = Boltzmann constant, θ D is the characteristic Debye temperature. The parameters Q, V (T=0) and b are obtained through fitting of experimental V(T) data modeled by Equation (1) (refined parameters are quoted in Appendix C, Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a).
represents the Debye energy model of lattice vibrations, n is the number of atoms in the unit cell, kB = Boltzmann constant, θD is the characteristic Debye temperature. The parameters Q, ( =0) and b are obtained through fitting of experimental V(T) data modeled by Equation (1) (refined parameters are quoted in Appendix C, Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see APPENDIX C, Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34,39,[41][42][43] quoted in Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value, 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer to those obtained from fitted Equation (1) in this work and in the cited literature), with recent literature data, 6.42962 Å , is negligible (1 × 10 −4 Å ). As for the value at 300 K, our result of data fitting is 6.46148(87) Å . It agrees perfectly with the average of the high represents the Debye energy model of lattice vibrations, n is the number of atoms in the unit cell, kB = Boltzmann constant, θD is the characteristic Debye temperature. The parameters Q, ( =0) and b are obtained through fitting of experimental V(T) data modeled by Equation (1) (refined parameters are quoted in Appendix C, Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see APPENDIX C, Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34,39,[41][42][43] quoted in Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value, 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer to those obtained from fitted Equation (1) in this work and in the cited literature), with recent literature data, 6.42962 Å , is negligible (1 × 10 −4 Å ). As for the value at 300 K, our result of data fitting is 6.46148(87) Å . It agrees perfectly with the average of the high ), ref. [29] (thin dashed line), ref. [39] ( ), ref. [34] ( As for Pb0.884Cd0.116Te, the increase of the thermal expansion coefficient, α(T), studied temperature range is more pronounced than that observed for PbTe (Figu At 300 K, the coefficient reaches the value of 20.7(8) MK −1 , the increase in respect to being about 6.5% at this temperature (the rise is comparable at lower temperatures)

Variation of Mean Square Displacements with Temperature
The temperature dependencies of experimental mean square isotropic atom placement parameters for cations and anions of PbTe and Pb0.884Cd0.116Te display a parent monotonically increasing behavior with rising temperature (Figure 4).
). The inset provides a comparison with theoretical data of ref. [45] (+ and dashed line), ref. [46] ( represents the Debye energy model of lattice vibrations, n is the number of atoms in the unit cell, kB = Boltzmann constant, θD is the characteristic Debye temperature. The parameters Q, ( =0) and b are obtained through fitting of experimental V(T) data modeled by Equation (1) (refined parameters are quoted in Appendix C, Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see APPENDIX C, Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34,39,[41][42][43] quoted in Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value, 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer to those obtained from fitted Equation (1) in this work and in the cited literature), with recent literature data, 6.42962 Å , is negligible (1 × 10 −4 Å ). As for the value at 300 K, our result of data fitting is 6.46148(87) Å . It agrees perfectly with the average of the high and dashed line), ref. [39] ( represents the Debye energy model of lattice vibrations, n is the number of atoms in the unit cell, kB = Boltzmann constant, θD is the characteristic Debye temperature. The parameters Q, ( =0) and b are obtained through fitting of experimental V(T) data modeled by Equation (1) (refined parameters are quoted in Appendix C, Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see APPENDIX C, Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34,39,[41][42][43] quoted in Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value, 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer to those obtained from fitted Equation (1) in this work and in the cited literature), with recent literature data, 6.42962 Å , is negligible (1 × 10 −4 Å ). As for the value at 300 K, our result of data fitting is 6.46148(87) Å . It agrees perfectly with the average of the high and dashed line), and ref. [50,108] (dot-dash line).
A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see Appendix C, Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34,39,[41][42][43] quoted in Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value, 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer to those obtained from fitted Equation (1) in this work and in the cited literature), with recent literature data, 6.42962 Å, is negligible (1 × 10 −4 Å). As for the value at 300 K, our result of data fitting is 6.46148(87) Å. It agrees perfectly with the average of the high quality records for PbTe stored in the ICSD database [26] (the quality is based on ICSD-staff evaluation). There are five such records; their a(293 K) values are 6.462(1) Å, 6.459(1) Å, 6.461(1) Å, 6.461(1) Å, and 6.460(1) Å; the average is 6.46060(15) Å. After temperature correction from 293 to 300 K the average increases by 0.00088 Å (based on present a(T) results) leading to the ICSD derived value at 300 K to be 6.46148 (15) Å. This value is identical to the above-quoted present one. All these perfect agreements point out both, the high quality of the sample and precision of applied measurement approach, including the instrument calibration. This observation can justify recommendation of the present a(T) run as a reference for the PbTe lattice parameter as a function of temperature; particularly in the near-RT temperatures, through interpolation of the data of Table A2 (Appendix B). The recommended a(300 K) value at 300 K is 6.46148(87) Å (thsi result is quoted together with other ones in Table 7). References: (a) [29], (b) [44]. The values of the fitted model (Equation (1)) for present and literature data are starred. References: (a) [31], (b) [29], (c) [34], (d) [39], (e) [41], (f) [26], (g) [42,43]. ($)-range of five high-quality results (see text for details); the average is corrected for thermal expansion of PbTe (the source values refer to T = 293 K). The values of the fitted model (Equation (1)) for present and literature data are starred.
Also of interest is the compatibility of the experimental and theoretical data. Apparently, the shapes of the present (and other) experimental a(T) variations are generally in line with earlier theoretical ones reported in refs. [39,45,46], whereas the absolute values differ by only 0.3% [46] to 2% [45]. For the best matching data of ref. [46], the increase of the a value across the 15-300 K range is only slightly larger than those experimentally observed (see Figure 2b).
The fitted Equation (1) describing the unit-cell size as a function of temperature perfectly approximates the experimental runs of both crystals, as shown in Figure 2a. The lattice parameter of Pb 0.884 Cd 0.116 Te in the whole temperature range is reduced in respect to that of pure PbTe, and the reduction across the whole range is 0.53%, which is apparently larger than the value of 0.50% quoted at the beginning of this section for PbTe.

Variation of Thermal Expansion Coefficient with Temperature
For Pb 0.884 Cd 0.116 Te, the lattice parameter, according to the fitted model, increases from 6.37725(6) Å to 6.41133(116) Å. The difference in respect to PbTe in the slope of the cell-size dependence on temperature is visualized in Figure 2a, presenting the temperature variation of the cell volume for both studied crystals. The experimental dependence of the linear-thermal-expansion coefficient on temperature, α(T), was derived from the V(T) Grüneisen approximation (Equation (1)), using the equation: For both materials, the general character of the α(T) variation is typical, with a nearly constant value up to 10 K, and with a pronounced increase observed up to~100 K; above this temperature, the rise progressively becomes much smaller. In the~170-300 K range, the variation of α with temperature is weak and nearly linear.
For PbTe, the TEC dependence on temperature obtained in the present work shows a fairly good matching with experimental results based on different earlier exploited techniques: dilatometry [51] and neutron powder diffraction [29] (see Figure 3). In particular, the resulting experimental TEC value of 19.6 (6) Table 8) (this discrepancy is as low as 1.5%).  As for Pb0.884Cd0.116Te, the increase of the thermal expansion coefficient, α(T), in the studied temperature range is more pronounced than that observed for PbTe (Figure 3b). At 300 K, the coefficient reaches the value of 20.7(8) MK −1 , the increase in respect to PbTe being about 6.5% at this temperature (the rise is comparable at lower temperatures).  Table A5). For PbTe, the lattice parameter increases by 0.50% over the whole temperature range. The run of the a(T) (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). As for Pb0.884Cd0.116Te, the increase of the thermal expansion coefficient, α(T), in the studied temperature range is more pronounced than that observed for PbTe (Figure 3b). At 300 K, the coefficient reaches the value of 20.7(8) MK −1 , the increase in respect to PbTe being about 6.5% at this temperature (the rise is comparable at lower temperatures). References: (a) [51], (b) [29], (c) [50,108], (d) [41]. (*)-theory.
A remarkable agreement of the present experimental thermal expansion data of PbTe is observed with the theory reported in ref. [50,108] (compare to the experimental and theoretical curves in Figure 3c). The agreement is visualized through the difference curve, and it is worth noting that the little bump of 2% height, observed at this curve would be twice as small if the temperature axis of the theoretical curve was shifted by only −0.7 K. The consistency with other theoretical data is not as perfect, but the trends of these results are generally compatible with the experiments described herein and others. In particular, the present data marginally differ from theoretical ones ref. [46] up to 100 K, whereas the discrepancy markedly increases at higher temperatures.
As for Pb 0.884 Cd 0.116 Te, the increase of the thermal expansion coefficient, α(T), in the studied temperature range is more pronounced than that observed for PbTe (Figure 3b). At 300 K, the coefficient reaches the value of 20.7(8) MK −1 , the increase in respect to PbTe being about 6.5% at this temperature (the rise is comparable at lower temperatures).

Variation of Mean Square Displacements with Temperature
The temperature dependencies of experimental mean square isotropic atomic displacement parameters for cations and anions of PbTe and Pb 0.884 Cd 0.116 Te display an apparent monotonically increasing behavior with rising temperature (Figure 4).  The experimental data were modeled using Equation (4) <u 2 >(T) = <u 2 >dyn(T) + <u 2 >stat where the mean square displacement takes into account the temperature-dependent dynamic disorder term (Debye expression [109]) and the temperature-independent static disorder term <u 2 >stat in the same way as that used in ref. [110]. The first term at the right side, <u 2 >dyn(T), is the Debye function based on simplifying the assumption that takes into account the acoustic branches, whereas the optical branches are ignored:  Table A5). For PbTe, the lat tice parameter increases by 0.50% over the whole temperature range. The run of the a(T (see inset in Figure 2b) is marginally different from the recent experimental data obtained in a wide temperature range (10-500 K) by neutron powder diffraction [29], and in the 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) curve to literature data is documented in Figure 2b (for refined parameters of all models see APPENDIX C Table A5, whereas the numerical a(T) data are quoted in Appendix B). The comparison based on this figure and on the recently reported experimental values near 0 K (data from refs. [29,44] quoted in Table 6 Table 7), shows that the discrepancies between the present and earlier values of lattice parameter are quite small. Namely, near 0 K the discrepancy of the present a value 6.42972(5) Å (the lattice parameter values given in this work with five decimal places refer   Table A5). For PbTe, the latver the whole temperature range. The run of the a(T) different from the recent experimental data obtained 00 K) by neutron powder diffraction [29], and in the iffraction [31] (Figure 2a). The experimental data were modeled using Equation (4) <u 2 >(T) = <u 2 > dyn (T) + <u 2 > stat (4) where the mean square displacement takes into account the temperature-dependent dynamic disorder term (Debye expression [109]) and the temperature-independent static disorder term <u 2 > stat in the same way as that used in ref. [110]. The first term at the right side, <u 2 > dyn (T), is the Debye function based on simplifying the assumption that takes into account the acoustic branches, whereas the optical branches are ignored: In the above expression, T stands for temperature, m for atomic mass, θ D for the Debye temperature, k B for the Boltzmann constant, andh for the reduced Planck constant. The second term in Equation (4), <u 2 > stat is an empirical term attributed to the temperatureindependent static disorder that can be connected in unsubstituted crystals, e.g., with the presence of point defects [111] (the presence of such defects is known to influence the electrical and other properties of thermoelectric crystals [112]), and in substituted crystals-with the presence of foreign atoms at the cationic or anionic sites.
The run of each <u 2 >(T) curve shows (i) a characteristic nearly linear dependence at high temperatures, having a specific slope, and with (ii) a curvilinear behavior at low temperatures, characterized by a value of <u 2 >(T = 0). Each of these features has its own meaning. The given curve representing either the cationic or anionic site has its own characteristics determined by the fixed material parameter m, by the Debye temperature, θ D , and by the disorder term, <u 2 > stat . Basically, <u 2 > stat and θ D are fittable parameters, and m could also be fitted if the composition was not well specified.
Examination of Figure 4 leads to following observations: (1) The fitted <u 2 > stat (T) curves for PbTe and Pb 0.884 Cd 0.116 Te behave differently. Namely: (a) The MSDs at 0 K, <u 2 >(T = 0), increase significantly (by about 0.002-0.004 Å 2 ) with x rising from 0 to 0.116. We attribute this increase to the appearance of the static disorder expressed by the nonzero <u 2 > stat term resulting from fitting Equation (4) (the values of <u 2 > stat are quoted in Table 9). This effect is graphically presented in the insets of Figure 4a,b, where the variation of fitted <u 2 > stat values is displayed. Appearance of marginally small negative fitted value for anionic site in PbTe (instead of zero that represents the lack of disorder) is attributed to be the effect of imperfections of fitted <u 2 >(T) data points.
At higher temperatures, the cationic MSDs are nearly equal for the two crystals, whereas the anionic ones differ markedly in the whole temperature range. (c) The slope of the cationic <u 2 >(T) curve decreases with rising x, whereas the anionic one apparently increases. The property of Equation (4) is that the slope of <u 2 >(T) is governed at high temperatures by the Debye temperature (for high slope the Debye temperature is low and vice versa; the corresponding θ D values are discussed in detail in Sections 3.3 and 4). A comparison of the MSDs for PbTe to literature data shows a similarity of runs with the detailed neutron-scattering based data [29,38] and with some other data based on X-ray diffraction [31,34,37] (see Figure 5). The differences in slopes of the quasilinear parts of experimental <u 2 >(T) runs can be connected with differences in the defect structure of studied single crystals and polycrystals. (2) The MSDs for the cationic and anionic sites behave differently for x = 0 than for x = 0.116.
(3) Comparison of Figure 4a,b shows that the cationic and anionic MSDs of Pb0.884Cd0.116Te are of comparable values in a broad temperature range. As this effect must depend on x, we expect that for x < 0.116, the <u 2 > values of anions are lower than those of cations, whereas for x > 0.116 (if the structure is stabilized), the anionic ones are higher.
A comparison of the MSDs for PbTe to literature data shows a similarity of runs with the detailed neutron-scattering based data [29,38] and with some other data based on Xray diffraction [31,34,37] (see Figure 5). The differences in slopes of the quasilinear parts of experimental <u 2 >(T) runs can be connected with differences in the defect structure of studied single crystals and polycrystals.
Among the theoretical MSD data, a better matching above 50 K with our experiments is found for the most recent molecular-dynamics-based data of ref. [39]. Near 0 K, the present experimental values match well the theoretical data of ref. [58,59], as shown in Figure 5.

Effect of Substitution of Cd in the PbTe Lattice on Variation of Unit-Cell Size and of Bulk Modulus with Pressure
The in-situ high-pressure X-ray diffraction study was performed under pressures ranging up to 4.5 GPa. The NaCl-type structure found for PbTe and Pb0.884Cd0.116Te single crystals at ambient conditions (T = 295 K and p = 0.1 MPa) was conserved at the applied high-pressure conditions. The structure refinement yielded the lattice parameter monotonically varying with increasing pressure (for values see Table A3 in Appendix B).  As for Pb0.884Cd0.116Te, the increase of the thermal expansion co studied temperature range is more pronounced than that observed At 300 K, the coefficient reaches the value of 20.7(8) MK −1 , the increa being about 6.5% at this temperature (the rise is comparable at lowe  Table A5). tice parameter increases by 0.50% over the whole temperature range. T (see inset in Figure 2b) is marginally different from the recent experime in a wide temperature range (10-500 K) by neutron powder diffractio 105-300 K range by X-ray powder diffraction [31] (Figure 2a). A comparison of both the experimental points and the fitted a(T) c data is documented in Figure 2b (for refined parameters of all models s Table A5, whereas the numerical a(T) data are quoted in Appendix B) based on this figure and on the recently reported experimental values n refs. [29,44] quoted in Table 6) and near 300 K (data from refs. [26,29,31,34 in Table 7), shows that the discrepancies between the present and earlie ), and ref. [39] (dotted line).
Among the theoretical MSD data, a better matching above 50 K with our experiments is found for the most recent molecular-dynamics-based data of ref. [39]. Near 0 K, the present experimental values match well the theoretical data of refs. [58,59], as shown in Figure 5.

Effect of Substitution of Cd in the PbTe Lattice on Variation of Unit-Cell Size and of Bulk Modulus with Pressure
The in-situ high-pressure X-ray diffraction study was performed under pressures ranging up to 4.5 GPa. The NaCl-type structure found for PbTe and Pb 0.884 Cd 0.116 Te single crystals at ambient conditions (T = 295 K and p = 0.1 MPa) was conserved at the applied high-pressure conditions. The structure refinement yielded the lattice parameter monotonically varying with increasing pressure (for values see Table A3 in Appendix B).
In the analysis, the Birch-Murnaghan equation of state [104] was adopted. Its thirdorder variant is described by the following formula: where p is the pressure, K 0 is the bulk modulus, and K is the pressure derivative of the bulk modulus, f E = [(V 0 /V) 2/3 − 1]/2 is the Eulerian strain (V is the volume under pressure p, and V 0 is the reference volume). When K = 4, Equation (6) is reduced to a simpler, second order equation, applied in the present study (an equation of the second order has also been used in a recently reported experimental diffraction study of PbTe [83]). The experimental relative unit-cell volume is well approximated for both crystals as a function of pressure by BMESO equation (see Figure 6; numerical data of the model are quoted with 0.5 GPa step in Table A4). The resulting bulk modulus value for PbTe K 0 is 45.6(2.5) GPa, which is consistent with previously reported values, in particular with those obtained from X-ray diffraction studies, 38.9 GPa [78,80] and 44(1) GPa [82] as well as with those from early ultrasonic wave velocity measurements of refs. [29,52,63,113], quoted in Table 10. second order equation, applied in the present study (an equation of the second order has also been used in a recently reported experimental diffraction study of PbTe [83]). The experimental relative unit-cell volume is well approximated for both crystals as a function of pressure by BMESO equation (see Figure 6; numerical data of the model are quoted with 0.5 GPa step in Table A4). The resulting bulk modulus value for PbTe K0 is 45.6(2.5) GPa, which is consistent with previously reported values, in particular with those obtained from X-ray diffraction studies, 38.9 GPa [78,80] and 44(1) GPa [82] as well as with those from early ultrasonic wave velocity measurements of refs. [29,52,63,113], quoted in Table 10.     References: (a) [78,80], (b) [83], (c) [52], (d) [113], (e) [63], (f) [29]. (s)-adiabatic; (t)-isothermal; (*)-calculation after PbTe data of ref. [52].
Abbreviations are explained at the end of this study.
The room-temperature bulk modulus of Pb 0.884 Cd 0.116 Te is found to be 33.5(2.8) GPa, providing the first experimental evidence that Cd substitution reduces the stiffness of the PbTe matrix. For both crystals, bulk modulus increases with pressure, in the range from 0.1 MPa to 4.5 GPa by about 50% (Figure 6, for numerical data see Table A4). For PbTe, the K(p) dependence is in line with the theoretical one reported in ref. [64].

Effect of Cd Substitution on Values of Debye Temperature
Modeling three variations, V(T), <u 2 >(T) and V(p), namely the V(T) variations using the second-order Grüneisen approximation (Equation (1)), the <u 2 >(T) variation involving the Debye expression (Equation (4)), and the V(p) variations using the BMEOS (Equation (6)) led to determination of the Debye temperature, θ D . In general, θ D is frequently considered as a quantity depending on temperature, but for PbTe, the reported θ D variations are weak and are observed mostly at cryogenic temperatures [53,61]. In most studies, including those based on diffraction, θ D is considered a temperature-independent quantity. For compounds of the NaCl structure, different θ D values are reported for the cation and anion sublattices. Such distinction is possible thanks to fitting of atomic displacements of the given (cationic or anionic) sublattice using Equation (4). Consequently, from the given experiment, we get a single overall θ D value from fitting V(T) and a pair of θ D 's from fitting of <u C 2 >(T) and <u A 2 >(T) (the corresponding symbols θ DV , θ DUC , and θ DUA are used here, respectively, to highlight the distinction between these three θ D definitions), whereas the overall θ DU denotes the average of θ DUC and θ DUA .
The earliest diffraction-based studies of PbTe have reported a relatively low overall Debye temperature of PbTe, about 110 K [55,56]. Our overall θ DU and θ DV values for the PbTe sublattices are in line with those determined in ref. [29] by both neutron powder and single crystal X-ray diffraction.
The variation of the direction of overall of (small) θ D changes appearing with Cd substitution is indicated by θ DV reduction by 5.1 K. A small reduction of Debye temperature for Pb 0.884 Cd 0.116 Te (θ DV = 130.1(4.4) K) in comparison with that for PbTe, θ DV = 135.2(3.8) K, is observed.
The present overall θ D values are also in line with the trends observed for those obtained by the non-diffraction methods in Table 12 (their average calculated for roomtemperature data is 138.1 K, i.e., only 3 K larger than our value. The theoretical methods provided overall values with a higher average (Table 13) of 157.9 K, these data vary in an extended range.
The here-obtained cationic and anionic Debye temperature values are close to those obtained by neutron diffraction θ DUC = 99.6(2) K and θ DUA = 156.0(5) K [29] (the discrepancy is less than 8%). The results collected in Table 11 (the present one and those reported earlier) document that the cationic values determined in different laboratories are in very good agreement (between 95.5 and 102.8 K), whereas those for anions exhibit a larger scatter between 127 and 169 K. The θ DUC and θ DUA behave in an opposite way (the former rises, the latter decreases). Interestingly, the contribution of lighter Cd atoms at the Pb sites leads to a reduction of the difference between the cationic and anionic site from 66.2 K for the pure PbTe to 42.9 K in the mixed crystal.
Exploiting the data obtained in this work, the Grüneisen parameter, γ, variation with temperature was evaluated using the formula (see ref. [29] and refs. therein): where α is the thermal expansion coefficient, K 0 is the bulk modulus, and c v describes the isochoric heat capacity. In calculations, the α(T) and V m (T) based on experimental results obtained in this work were used. The K 0 (T) variation reported in ref. [29] for PbTe was rescaled to the present K 0 at room temperature equal 45.6(2.5) GPa for the PbTe sample and to 33.5(2.8) GPa for the Pb 0.884 Cd 0.116 Te sample (for Pb 0.884 Cd 0.116 Te we adopted the rescaled K 0 (T) dependence of PbTe of ref. [29]). For PbTe, the temperature variation of the molar isochoric capacity c v (T) was taken from ref. [29], whereas for the Cd substituted sample the theoretical c v (T) data of Pb 0.88 Cd 0.12 Te [68] were used. The dependencies obtained in this way are shown in Figure 7.
Crystals 2021, 11, x FOR PEER REVIEW 19 of 33 temperature data is 138.1 K, i.e., only 3 K larger than our value. The theoretical methods provided overall values with a higher average (Table 13) of 157.9 K, these data vary in an extended range. The here-obtained cationic and anionic Debye temperature values are close to those obtained by neutron diffraction θDUC = 99.6(2) K and θDUA = 156.0(5) K [29] (the discrepancy is less than 8%). The results collected in Table 11 (the present one and those reported earlier) document that the cationic values determined in different laboratories are in very good agreement (between 95.5 and 102.8 K), whereas those for anions exhibit a larger scatter between 127 and 169 K. The θDUC and θDUA behave in an opposite way (the former rises, the latter decreases). Interestingly, the contribution of lighter Cd atoms at the Pb sites leads to a reduction of the difference between the cationic and anionic site from 66.2 K for the pure PbTe to 42.9 K in the mixed crystal.
Exploiting the data obtained in this work, the Grüneisen parameter, γ, variation with temperature was evaluated using the formula (see ref. [29] and refs. therein): where α is the thermal expansion coefficient, K0 is the bulk modulus, and cv describes the isochoric heat capacity. In calculations, the α(T) and Vm(T) based on experimental results obtained in this work were used. The K0(T) variation reported in ref. [29] for PbTe was rescaled to the present K0 at room temperature equal 45.6(2.5) GPa for the PbTe sample and to 33.5(2.8) GPa for the Pb0.884Cd0.116Te sample (for Pb0.884Cd0.116Te we adopted the rescaled K0(T) dependence of PbTe of ref. [29]). For PbTe, the temperature variation of the molar isochoric capacity cv(T) was taken from ref. [29], whereas for the Cd substituted sample the theoretical cv(T) data of Pb0.88Cd0.12Te [68] were used. The dependencies obtained in this way are shown in Figure 7. The obtained γ(T) dependence for PbTe is comparable with those reported in refs. [51] with value of about 1.5 in the range 30-340 K and ref. [29] with values of about 2.1-2.2 in the range 50-260 K. The parameter γ is frequently considered a constant. Its experimental constant value determined by X-ray diffraction is reported to be 2.03 [29], whereas The obtained γ(T) dependence for PbTe is comparable with those reported in refs. [51] with value of about 1.5 in the range 30-340 K and ref. [29] with values of about 2.1-2.2 in the range 50-260 K. The parameter γ is frequently considered a constant. Its experimental constant value determined by X-ray diffraction is reported to be 2.03 [29], whereas the sound velocity method has given a result of 0.95 [63] and the ultrasonic wave velocity method, 1.96 [13]. Theoretical values obtained by the density functional theory are 1.96-2.18 [45], whereas the molecular dynamics yielded γ = 1.66 [117]. Interestingly, the present results and some of those referring to constant γ consistently suggest that its value is close to 2, whereas the roughly evaluated data on the mixed crystal indicate some decrease of gamma due to Cd substitution (see Figure 7).
The reliability of the γ values at the lowest temperatures, as calculated from Equation (7) depends on the accuracy of the very small, divided values of α and c v , therefore the reduction of γ below~50 K displayed in Figure 7 may be questioned.

Discussion
The results on the thermostructural and elastic properties of rocksalt-type crystals, PbTe and Pb 0.884 Cd 0.116 Te solid solution, described in Section 3, are derived from X-ray diffraction data through fitting of Equations (1), (4) and (6). Temperature dependencies of the lattice parameter, a(T), the thermal expansion coefficient, α(T), and the mean square displacements, <u 2 >(T), are determined for both crystals from X-ray diffraction powder diffraction data. These results for PbTe are consistent with recent literature data, in particular with the most detailed ones [29,31]. Moreover, the diffraction study of the equation of state, V(p), provided the value of the PbTe bulk modulus dependence on pressure. The reliability of the present results is verified by the demonstrated close agreement of the a(T), α(T) and <u 2 >(T) dependencies, as well as of the Debye temperature and bulk modulus variation, for PbTe with earlier experimental and theoretical data. It is also worth noting that the fitted model curves for a(T), <u 2 >(T) and V(p) dependencies match well the experimental points, therefore we do not expect occurrence of significant systematic errors which could add to the statistical errors quoted in Tables A3 and A4. For Pb 0.884 Cd 0.116 Te, the obtained results are novel, they describe the thermal characteristics of this crystal and indicate the direction and magnitude of variation of the considered temperature-dependent properties with rising content of Cd at the cationic site. In other words, the earlier unknown effect of sharing the cationic sites by Pb and Cd atoms on thermal properties is revealed.
In Section 3, it is shown that the results on the PbTe lattice parameter, a(T), are of high accuracy, as judged by the perfect agreement of PbTe data with the earlier-reported neutron powder diffraction data of ref. [29]. Moreover, the a value at 300 K is ideally equal to that derived from high-quality ICSD records [26]. Based on the analysis of the literature data, we show that the values of 6.42972(5) Å and 6.46148(87) Å are good candidates for the reference lattice parameter of PbTe at 0 and 300 K, respectively. The Pb 0.884 Cd 0.116 Te sample shows a similar behavior with temperature. The a(T) run for Cd-substituted PbTe crystal depends on the amount of substituent (as can be deduced from a comparison with earlier results for lower Cd content [42][43][44]). A related influence of substituent on the a(T) runs is observed for Na and Eu substituted PbTe crystals [41]. In the above-cited results, which refer to temperatures exceeding the room temperature, the deviations from regular behavior indicate the decomposition of a metastable mixed crystal.
The here-obtained thermal expansion data for PbTe match other experimental data, especially those of ref. [29] (the discrepancy does not exceed (3%)). Unexpectedly, we found a surprisingly perfect agreement with data from ref. [50,108] in the whole studied temperature range. This agreement clearly suggests that both the present measurements and cited theory yielded accurate results for temperatures ranging up to 300 K. The fractional substitution of Cd atoms at the Pb site results in a discernible increase of the linear thermal expansion coefficient value. In particular, the value at 300 K is 19.6(6) MK −1 for PbTe and 20.7(8) MK −1 for Pb 0.884 Cd 0.116 Te: thus, the expansion rises by 6.2% at this temperature. The investigation of mean square displacements (independently, the cationic and anionic ones) shows their nearly linear variation with rising temperature, except for the lowest temperatures (see Figures 4 and 5). This finding confirms, for the PbTe sample, the behavior known from earlier neutron diffraction and X-ray diffraction studies such as those described in refs. [29,31]. For Pb 0.884 Cd 0.116 Te, the cationic MSDs are comparable to those of PbTe, except in the region of the lowest temperatures. The Cd substitution causes apparent increase of the anionic MSDs. This increase is expected to be proportional to the Cd content.
In fitting the Equation (4), the <u 2 > stat term describing the static disorder was determined, for both, cationic and anionic sublattices, in the unsubstituted and substituted crystal. As expected, the fitting for PbTe gave <u 2 > stat a value close to zero, thus indicating that there is no significant disorder in this crystal (small values have also been reported in refs. [29,31]). We believe that the differences between the, values reported for pure PbTe by different groups can probably be attributed to differences in the defects' kind and density.
The observed increase of the <u 2 > stat term after incorporating Cd into the PbTe lattice proves that alloying causes appearance of substitutional disorder in the mixed Pb 0.884 Cd 0.116 Te. crystal. We observe (see the insets in Figure 4) that the values of cationic and anionic <u 2 > stat terms describing the static disorder are markedly different in the Pb 0.884 Cd 0.116 Te. crystal. Namely, the anionic disorder is significantly larger in this crystal.
The here-reported extraction the information on disorder for both, cationic and anionic sublattices, in a mixed PbTe based crystal, is an important novelty (previously, such calculations have been performed for pure PbTe, only). We notice a significant increase of the static disorder term, showing that information of this kind, extracted from analysis of carefully measured thermostructural properties, can be useful in future studies on IV-VI thermoelectric solid solutions and their application, because the disorder in solid solutions can affect the carrier mobility, electrical conductivity [32,35] and thermal conductivity [31,117] influencing the Seebeck coefficient. We evaluate that the opportunity for detection of disorder can concern low substituent fraction, even much less that x = 0.1 studied in the present work.
For both crystals, the in situ high-pressure single-crystal XRD experiment provided information on the lattice parameter variation for PbTe and Pb 0.884 Cd 0.116 Te, at pressures ranging up to 4.5 GPa. The observed pressure variation is in line with a theoretical result reported in ref. [64]. Modeling of the BMEOS led to determination of the bulk modulus and its pressure variation. At 0.1 MPa, the bulk modulus value is 45.6(2.5) for PbTe, well coinciding within error bars with the value 44(1) GPa reported in the most recent diffraction study [83]. The bulk modulus value significantly decreases with rising Cd content; in other words, the Cd substitution leads to a crystal of lower stiffness.
There are a number of theoretical works investigating the bulk modulus changes upon substitution of an element at the cationic site [8,9,123]; most typically, a reduction is predicted. In ref. [9], for 62 elements fractionally substituting Pb in PbTe, the resulting bulk modulus value is calculated; the same calculation is performed for nine substituents at an anionic Te site. For almost all of them, the bulk modulus is reduced; whereas for V, Nb, Ni and Bi, the K 0 value is larger than the calculated value of 46.61 GPa [9] for pure PbTe.
In ref. [9], the K 0 has been predicted to decrease from 46 44.5 GPa points out the reliability of both, the cited experiment and the calculation.
The above-described fittings of V(T) and <u 2 >(T) models led to the determination of values of Debye temperature, θ D , for both crystals. Together with the Cd substitution, a small reduction of the overall Debye temperature, θ DU , from 135.2(3.8) K to 130.1(4.4) K (i.e., a reduction of 5.1 K) is observed. Theoretical calculations predict reduction by 2.4 K for the composition of x = 0.031 [9]. Extrapolating this result to the composition of the mixed crystal studied in this work, (x = 0.116) gives a prediction of a 9 K (difference between θ D = 187.8 1 K and 178.8 K quoted in Table 13) reduction of the theoretical overall θ D . This theoretical result supports the observed trend of reduction of overall Debye temperature by increasing the cadmium content. Interestingly, the θ D values reported by different authors for the cationic sublattice are in perfect agreement, whereas those for the anionic one are scattered. The influence of Cd substitution on Debye temperatures of cationic and anionic sublattices, described in Section 3.3, is not uniform; these values differ markedly for PbTe, but the difference is reduced for the Cd substituted crystal.
The observed influence of Cd substitution into PbTe lattice on the thermostructural and elastic properties studied can serve as a basis for evaluation of such features for crystals of different Cd content. They can also be useful in studies of more complex systems, such as those with dual cationic/anionic substitutions. As it is noted in ref. [30], various factors influence the Seebeck coefficient value. One of the ways to optimize this value consists of alloying with a selected element, which means a decrease or increase of the atomic order. It is equally possible to investigate other, more complex systems, for example those with lessconventional doubly substituted cationic systems, such as Na 0.03 Eu 0.03 Pb 0.94 Te [112]. The joint cationic/anionic substitution (Pb,Cu)(Se,Te) system has also been studied, providing another example of a dual system [135]. Mixed bi-cationic-bi-anionic systems such as Na 0.03 Eu 0.03 Pb 0.94 Te 0.9 Se 0.1 [112] are the subject of studies as well. It is noteworthy that upon replacing the Te anion by Se or S, the bond ionicity decreases (for the ionicity scale, see ref. [136]). Along the PbTe, PbSe, PbS series, some of the thermostructural/elastic properties (studied here for PbTe) vary monotonically; for example, the lattice parameter (see Figure 1 at x = 0), bulk modulus [46,85,114] and phase transition pressure [77,85].

Conclusions
PbTe of a rocksalt-type structure belongs to a family of thermoelectric materials. A modification of composition, typically by fractional substitution of an element such as Cd, at the Pb cation site, is known to improve the thermoelectric properties. In this work, the combined low-temperature-high-pressure study carried out here describes the effect of sharing the cationic sites by Pb and Cd atoms on the above-mentioned properties. These properties were derived for two samples, PbTe and Pb 0.884 Cd 0.116 Te, from X-ray diffraction data collected at varying temperature and pressure.
The dependencies of the lattice parameter, a(T), the thermal expansion coefficient, α(T), and the mean square displacements, <u 2 >(T), are determined for both crystals. For PbTe, these results and thermal expansion are fully consistent with results of earlier X-ray diffraction, neutron diffraction, dilatometric and other experimental studies, as well as with those of multiple theoretical investigations, and this agreement supports the reliability of the data collected.
The experimental variation of the lattice parameter with temperature was modeled using the Grüneisen-approximation approach whereas the variation of mean square atomic displacements was modeled using the Debye expression. In addition, the equations of state were determined for pressures ranging up to 4.5 GPa, allowing conclusions to be drawn about the value of the bulk modulus and its variations under rising pressure and with varying Cd substitution.
The thermostructural and elastic properties for Pb 0.884 Cd 0. 116 Te crystal determined in the present study indicate the direction and magnitude of variation of the characteristics of Pb 1−x Cd x Te system with rising x. The stiffness of the alloy is smaller than that of pure PbTe, the thermal expansion is larger throughout the whole temperature range, and the atomic mean-square displacements change with Cd substitution in a complex way, indicating (i) opposite variations of the Debye temperatures for both sublattices, as well as (ii) the appearance of substitutional disorder in the mixed crystal.
In summary, the study presents detailed quantitative information on the thermostructural and elastic properties of rocksalt-type crystals of PbTe and Pb 0.884 Cd 0.116 Te; such data are not yet available for alloys of the Pb 1−x Cd x Te system. The obtained results show a consistent image of influence of the partial substitution of Pb ions by Cd ions, in the PbTe lattice, on the thermostructural properties. Namely, the obtained results show how the lattice parameter, the thermal expansion coefficient, the atomic mean-square displacements and other thermostructural properties (compressibility, Debye temperature, Grüneisen parameter and others) depend on the cadmium content. In particular it was found, that the Pb 0.884 Cd 0.116 Te lattice is less stiff than that of PbTe, whereas thermal expansion of the mixed crystal is discernibly larger. The described extension of the knowledge on the studied properties is expected to be profitable in a further work on the application of the fractionally substituted Cd lead telluride. data are not yet available for alloys of the Pb1−xCdxTe system. The obtained results show a consistent image of influence of the partial substitution of Pb ions by Cd ions, in the PbTe lattice, on the thermostructural properties. Namely, the obtained results show how the lattice parameter, the thermal expansion coefficient, the atomic mean-square displacements and other thermostructural properties (compressibility, Debye temperature, Grüneisen parameter and others) depend on the cadmium content. In particular it was found, that the Pb0.884Cd0.116Te lattice is less stiff than that of PbTe, whereas thermal expansion of the mixed crystal is discernibly larger. The described extension of the knowledge on the studied properties is expected to be profitable in a further work on the application of the fractionally substituted Cd lead telluride.      Appendix C Table A5. Fitted values of the parameters of Equations (1), (4) and (6) Appendix D Table A6. Reported theoretical bulk modulus and its derivative for PbTe and Pb 1−x Cd x Te, x = 0.031, 0.116. In a number of papers (e.g., refs. [10,129]), multiple numerical approaches have been applied, so only selected representative values could be cited here. As a rule (with some exceptions), the experimental values refer to room temperature, whereas in the calculated ones (to 0 K), the temperature is marked if explicitly stated in the given reference.