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 | JOURNAL OF APPLIED CRYSTALLOGRAPHY |
accessThe equation of state of the Pmmn phase of NiSi
aSchool of Earth Sciences, University of Bristol, Wills Memorial Building, Queen's Road, Bristol BS81RJ, UK, and bDepartment of Earth Sciences, University College London, Gower Street, London WC1E 6BT, UK
*Correspondence e-mail: oliver.lord@bristol.ac.uk
The equation of state of the orthorhombic phase of NiSi with Pmmn symmetry has been determined at room temperature from synchrotron-based X-ray diffraction measurements of its lattice parameters, made in a diamond anvil cell. Measurements were performed up to 44 GPa, using Ne as the pressure medium and Au as the pressure standard. The resulting pressure–volume (P–V) data have been fitted with a Birch–Murnaghan equation of state of third order to yield V0 = 11.650 (7) Å3 atom−1, K0 = 162 (3) GPa and K0′ = 4.6 (2). In addition, P–V data have been collected on Ni53Si47 in the B20 structure using both Ne and He as the pressure media and Cu and Au as the pressure standards, also to 44 GPa. A fit using the same Birch–Murnaghan equation of state of third order yields V0 = 11.364 (6) Å3 atom−1, K0 = 171 (4) GPa and K0′ = 5.5 (3).
Keywords: NiSi; equations of state; high pressure; diamond anvil cells.
1. Introduction
Nickel monosilicide (NiSi), which crystallizes in the MnP (B31) structure (space group Pnma) at ambient pressure (Toman, 1951![[Toman, K. (1951). Acta Cryst. 4, 462-464.]](../../../../../../logos/arrows/j_arr.gif "Toman, K. (1951). Acta Cryst. 4, 462-464.")
), has recently been shown to possess a surprisingly rich phase diagram (Lord et al., 2014; Dobson et al., 2015). Both the ∊-FeSi (B20) structure (space group P213) and the CsCl (B2) structure (space group Pm3m) were predicted to become stable at successively higher pressures on the basis of the static (0 K) ab initio computer simulations of Vočadlo et al. (2012). Both were subsequently detected experimentally (Lord et al., 2012). Conversely, a new structure, with Pmmn was first detected in the run products of multi-anvil press (MAP) experiments quenched to room temperature from 1223 to 1310 K at 17.5 GPa and then recovered to atmospheric pressure. This new structure (hereafter referred to as Pmmn-NiSi), in which both the Ni and Si atoms have sixfold coordination, is essentially identical to the γ-CuTi structure type (space group P4/mmn) except that the ab plane of the is slightly distorted from square to rectangular; much more detail can be found in §6 of Wood et al. (2013). Subsequent static ab initio simulations have shown that this new structure has the lowest at 0 K of all structures tested to date at pressure 21 < P < 264 GPa (Wood et al., 2013). This new structure had been missed by previous experimental studies that employed laser heating in a diamond anvil cell (DAC) (Lord et al., 2014, 2012) because the lowest temperature achieved in those studies was higher than the maximum extent of the stability field of Pmmn-NiSi (∼1200 K). It had also been missed by the previous ab initio study (Vočadlo et al., 2012) simply because its rather unusual structure had not been considered.
The NiSi composition is of interest to us primarily because NiSi forms an end member in the Fe–Ni–Si ternary system, which encompasses compositions often employed as models for the cores of the terrestrial planets including the Earth. However, because many planetary bodies within our solar system have central pressures significantly lower than that of Earth (e.g. Mercury, ∼40 GPa, compared to Earth, ∼360 GPa), the low-pressure low-temperature parts of the Fe–Ni–Si system and its end-member constituents are important, including NiSi. For this reason we have studied this composition extensively in the past, including its phase diagram, across a wide range of pressures and temperatures (0–70 GPa and 500–3000 K) in both MAP and DAC experiments, and the equations of state (EoSs) of its constituent phases using both DAC experiments and ab initio simulations. In addition to its geophysical and planetary relevance, NiSi also has technological importance as a thin-film contact material in micro-electronics (e.g. Lavoie et al., 2006). To date, we have ab initio EoSs available for all of the NiSi structures known to be stable, but only experimental EoSs for the B31, B20 and B2 structures. Here, we report the results of synchrotron-based powder X-ray diffraction measurements of the lattice parameters of Pmmn-NiSi in a DAC up to 44 GPa. In addition, we also provide new pressure–volume (P–V) data on slightly Ni enriched, non-stoichiometric NiSi in the B20 structure. The methods employed are described in §2 and the results are presented and discussed in §3, where they are also compared with the existing ab initio and experimental data.
2. Methods
The starting materials for the two experiments reported here were selected from the crushed remains of the multi-anvil press synthesis experiment performed at 17.5 GPa and 1223 K described in §2.2 of Wood et al. (2013). This synthesis produced ∼80 vol.% of Pmmn-NiSi with a composition within error of the 1:1 NiSi stoichiometry (see §2.3 of Wood et al., 2013) and ∼20 vol.% of material in the B20 (∊-FeSi) structure (space group P213) with a composition of Ni53Si47. As observed by Wood et al. (2013), the sample underwent slight back-transformation to the ambient-pressure B31 (MnP) structure (space group Pnma) during decompression. As a result, a trace of this phase is evident in our diffraction patterns, primarily as a broad feature at ∼7.8° (see Fig. 1a), which we have not attempted to fit during our Le Bail refinements.
![[Figure 1]](kc5022fig1thm.gif) | Figure 1 Examples of Le Bail fits (red lines), backgrounds (green dashed lines) and residuals (blue lines) for X-ray diffraction data (plus signs) collected in this study. Both patterns are at 17.7 (5) GPa. (a) The Pmmn-NiSi sample and (b) the Au standard. Tick marks represent reflections of, from top to bottom, fcc-Ne, B20-NiSi and Pmmn-NiSi in (a) and fcc-Ne, fcc-Au and hcp-Re (from the gasket; hcp denotes hexagonal close packed) in (b). |
Pressure was generated using a membrane-driven Le Toullec type symmetric DAC with a 60° opening angle (Le Toullec et al., 1988) and anvils of the Boehler–Almax design (Boehler & De Hantsetters, 2004), with culets of 300 µm diameter. Re gaskets were indented to a thickness of 40 µm and then a 150 µm-diameter hole was laser drilled in the centre of each of the indentations to form sample chambers. Into the sample chambers were loaded four spatially separated items, two of which were common to both experiments: a ruby sphere, used as a pressure marker, and a sample of B31-NiSi (for which the results will be presented in a future publication). In addition, experiment 1 contained a ∼25 µm-diameter polycrystalline grain of Pmmn-NiSi (with a trace of B20-Ni53Si47) and an Au pressure marker loaded as a loose polycrystalline aggregate, while experiment 2 contained a ∼25 µm-diameter polycrystalline grain of B20-Ni53Si47 and a Cu pressure marker, also loaded as a loose polycrystalline aggregate. The samples and pressure standards were separated so as to simplify the analysis of the X-ray diffraction patterns. The remaining space in the sample chambers was filled with a pressure transmitting medium of Ne (experiment 1) or He (experiment 2), using the high-pressure loading system at the European Synchrotron Radiation Facility (ESRF). The cells were then sealed, with an initial pressure of ∼0.2 GPa as determined by ruby fluorescence spectroscopy. Ne, which solidifies at 4.8 GPa at 300 K, has been shown to remain essentially hydrostatic up to 15 GPa (Klotz et al., 2009). Even at 50 GPa (which encompasses this study), the degree of non-hydrostaticity of solid Ne is minor, supporting pressure gradients of only ∼0.5 GPa (i.e. 1%; Klotz et al., 2009). He, which solidifies at 12.1 GPa at 300 K and remains essentially hydrostatic up to 20 GPa, is even more effective, supporting pressure gradients of only ∼0.15 GPa at 50 GPa (i.e. 0.3%; Klotz et al., 2009). Note that the use of laser annealing to reduce deviatoric stress after each pressure step was not possible in this study: below ∼12 GPa, both samples would convert, upon heating, to B31-NiSi. Above ∼12 GPa, temperatures amenable to measurement by spectroradiometry (>1200 K) risk pushing the Pmmn-NiSi sample further into the two-phase Pmmn-NiSi + B20-NiSi region of the phase diagram, altering the stoichiometry of the Pmmn-NiSi phase, or even converting it entirely to the B20-NiSi structure (Dobson et al., 2015). Laser annealing of the B20-Ni53Si47 sample was not possible either, owing to the proximity to the B31-NiSi sample, which would convert above 12 GPa to Pmmn-NiSi, B20-NiSi or both, depending on temperature.
The samples were compressed by incrementally increasing the pressure in the membrane of the DAC using an automatic pressure controller. At each step, after waiting for ∼5 min to allow the gasket and sample to relax under the increased load, separate X-ray diffraction patterns were collected, one from each of the two samples and one from the pressure standard (either Au or Cu). X-ray powder diffraction was performed at beamline ID27 of the ESRF (Mezouar et al., 2005) using a monochromatic beam with an energy of 33 keV (λ = 0.3738 Å). Diffracted X-rays were collected using a MAR165 CCD detector at a distance from the sample of ∼260 mm, calibrated exactly using an LaB6 standard. The resulting two-dimensional patterns were integrated into one-dimensional spectra using the Fit2D program (Hammersley, 1997) and then fitted using the Le Bail method (Le Bail et al., 1988) as implemented in the GSAS suite of programs (Larson & Von Dreele, 1994; Toby, 2001).
3. Results and discussion
3.1. Calibration of pressure
In this study, we have opted to use the Au and Cu standards, rather than the Ne pressure medium, as our pressure calibrants because we believe them to be more accurate. This is primarily because Ne (K0 ≃ 1) is so much more compressible than Au (K0 ≃ 170) that small differences in the parameters of the Ne EoS result in significant differences in the calculated pressure. So, while the EoS parameters for Ne reported in the two most recent studies, those of Dewaele et al. (2008) and Dorfman et al. (2012), are in close agreement (K0 = 1.07 GPa versus 1.04 GPa and K0′ = 8.4 versus 8.48), they nevertheless result in significant differences in the calculated pressures (Table 1). The EoSs of Au and Cu do not suffer from this problem, and, for Au, there is consensus between recent EoS studies (Dewaele et al., 2004; Fei et al., 2007). The EoSs for Au and Cu employed here (Dewaele et al., 2004) were determined from samples loaded together in the same noble gas pressure medium as was used in the present study; they diverge from each other by <1 GPa at 50 GPa and should be directly applicable to our experimental design. Another disadvantage of using Ne as the pressure calibrant, especially when laser annealing is not possible (see §2), is that it tends to show a tetragonal distortion under uniaxial compression, making it impossible to accurately fit its Bragg reflections using a face-centred cubic (fcc) (Fig. 1a). Such distortions are less prominent in the Au and Cu pressure standards (Fig. 1b), possibly because the standards are free floating within the Ne or He medium and thus experience quasi-hydrostatic conditions, whereas the Ne bridges the diamond anvils and is therefore subject to significant deviatoric stress. Finally, because Ne does not crystallize until 4.8 GPa at 300 K it cannot be used as a calibrant below this pressure. He scatters X-rays so weakly that it cannot be used as a standard even above its 300 K solidification pressure of 12.1 GPa.
). ‡Based on the EoS of Dewaele et al. (2008 ). §Based on the EoS of Dorfman et al. (2012 ). | |||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||||
3.2. The equation of state of Pmmn-NiSi (experiment 1)
Table 2 compares the lattice parameters of Pmmn-NiSi at ambient pressure as measured in this study with the measurements and ab initio simulations of Wood et al. (2013). The two sets of experimental measurements are almost identical. The ab initio simulations, however, indicate much more significant differences when compared with the experiments, with all three axes being longer, resulting in a volume that is 1.3% larger than the experimental value in this study. This difference is, however, in line with the overestimation of volume of around 1% common in ab initio simulations that employ the generalized gradient approximation (GGA) as was used by Wood et al. (2013); similar discrepancies between DAC experiments and GGA-based ab initio simulations of 1 and 1.4% were observed for B31-NiSi and B20-NiSi, respectively (Lord et al., 2012; Vočadlo et al., 2012).
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The lattice parameters of Pmmn-NiSi from Table 1 are presented as a function of volume in Fig. 2, along with the results of the ab initio simulations of Wood et al. (2013). Those simulations show a pronounced kink in all three lattice parameters (though it is most prominent in a and b), at 10.5 < V < 10.8 Å3 atom−1, such that the a axis actually lengthens over a short interval of compression. In comparison, our experimental data only show such a kink on the a axis, though it is not statistically significant; the b and c axes shorten smoothly over the investigated compression range and all three can be well described with a polynomial function of second order.
![[Figure 2]](kc5022fig2thm.gif) | Figure 2 Lattice parameters of Pmmn-NiSi as a function of unit-cell volume from this study (black circles) and the ab initio simulations of Wood et al. (2013 ; open circles with dashed lines). The solid lines are polynomial fits of second order to the experimental data collected in this study. Note the break in the y axis at y ≃ 3.4. The kink in the ab initio lattice parameters can be seen much more clearly in Fig. 4(a) of Wood et al. (2013). |
The smooth change in the lattice parameters as a function of pressure makes it reasonable to fit all of the compression data using a single EoS, rather than fitting the data separately either side of V ≃ 10.6 Å3 atom−1 as Wood et al. (2013) did. The results of our preferred third-order Birch–Murnaghan fit, in which all three parameters (V0, K0 and K0′) were allowed to vary, is shown in Fig. 3(a) as the solid black line; the fitted parameters are presented in Table 3. As can be seen in Fig. 3(b), all of the data fall within ±0.25% V of the fitted curve and appear randomly distributed around the 0% line; the average mismatch is just 0.08% V. Also plotted in Fig. 3(a), as dash–dot lines, are the high- and low-pressure EoSs from Wood et al. (2013). To facilitate comparison between the experimental and ab initio results, we have corrected the low-pressure ab initio EoS by applying a constant volume offset of −0.129 Å3 atom−1 (−1.1%) such that its V0 is equal to the measured value of 11.650 Å3 atom−1 (the long-dashed line). The same relative offset of −1.1% has been applied to the high-pressure ab initio EoS (the short-dashed line). Though we do not see the `kink' in the lattice parameters that is clearly apparent in Fig. 4(a) of Wood et al. (2013), it is apparent from Fig. 3(a) that their volume-corrected low-pressure EoS matches the data slightly better below ∼25 GPa, while their volume-corrected high-pressure EoS matches the data better at higher pressures. This can be seen more clearly from the variation with pressure in the difference between the volume-corrected and experimental ab initio EoSs (represented by Vai − Vexp; Fig. 3c). This observation might suggest that a does occur in the Pmmn-NiSi structure, but that it is less pronounced at 300 K (the temperature at which the experiments are performed) than it is at 0 K (the temperature at which the simulations are performed).
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![[Figure 3]](kc5022fig3thm.gif) | Figure 3 (a) Volume per atom (Å3) for Pmmn-NiSi as a function of pressure as calculated from the Au pressure marker using the EoS of Dewaele et al. (2004 ; filled circles). The solid line is a third-order Birch–Murnaghan EoS fitted to the data with all three parameters allowed to vary (V0, K0 and K0′). The dashed lines are the volume-corrected EoS fitted to the ab initio simulation results of Wood et al. (2013) over the range 10.75 < V < 12.0 Å3 atom−1 (short dashes) and 6.5 < V < 10.5 Å3 atom−1 (long dashes). The uncorrected ab initio EoSs are represented by the dash–dot lines; see text for details. (b) Residuals of the fit to the data based on the Au standard in which V0 was allowed to vary. The thin dashed lines represent ±0.25% V. (c) Vai − Vexp for the low-pressure (green thick solid line) and high-pressure (blue thick dashed line) ab initio EoSs (both volume corrected). The thin solid line at y = 0 represents the experimental EoS presented in (a) and the thin dashed lines represent ±0.25% V as in (b). |
It is clear from Table 2 that the values for K0 and K0′ from our experimental EoS are reasonably close to the values determined from the fits to the ab initio simulations of Wood et al. (2013). This is in spite of the fact that the range of compression achieved in the experiments is much smaller than that achieved in the simulations, and that K0 and K0′ have a strong negative of −0.95.
3.3. The equation of state of B20-structured Ni53Si47 (experiments 1 and 2)
The P–V data for B20-Ni53Si47 from experiment 1 are presented in Table 1, while the data from experiment 2 are presented in Table 4. All the data are plotted in Fig. 4 as a function of pressure, together with a third-order Birch–Murnaghan fit to the two data sets combined, in which all three fitted parameters were allowed to vary (Table 3). The two data sets are in excellent agreement with each other, which is a reflection of the facts that, firstly, there is little difference between Ne and He as a pressure medium at pressures up to ∼50 GPa and that, secondly, the Cu and Au EoSs are themselves in very close agreement. The new data are also in excellent agreement with the data from the paper by Lord et al. (2012) in which NaCl was used as the pressure medium and pressure calibrant and laser annealing was employed after each compression step to reduce deviatoric stress. This suggests that laser annealing of samples contained in significantly non-hydrostatic pressure media, such as NaCl, is at least as effective at minimizing deviatoric stress as the use of quasi-hydrostatic media such as He and Ne without laser annealing. This also indicates that the EoS of Cu from Dewaele et al. (2004) used in this study and the EoS of NaCl in either the B1 (Dorogokupets & Dewaele, 2007; below 30 GPa) or B2 structures (Fei et al., 2007; above 30 GPa) used by Lord et al. (2012) must be in good agreement over the pressure range of this study.
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![[Figure 4]](kc5022fig4thm.gif) | Figure 4 Volume per atom for B20-Ni53Si47 as a function of pressure as calculated from the Cu pressure marker using the EoS of Dewaele et al. (2004 ; circles). The filled circles are from experiment 1 (in Ne) and the open circles from experiment 2 (in He). The thick solid line is a third-order Burch–Murnaghan EoS fitted to all the data (Table 2). The dashed line is the EoS fitted to the ab initio simulations from Vočadlo et al. (2012), which has been corrected so that its V0 is equal to that of the experimentally determined value. The uncorrected ab initio EoS is represented by the dash–dot line. The thin solid red line is the EoS fitted to the P–V data of Lord et al. (2012; red squares), which was produced using NaCl as the pressure medium coupled with laser annealing on a stoichiometric NiSi sample. |
Comparing the fitted values of K0 and K0′ from this study with those from Lord et al. (2012) indicates that the non-stoichiometric Ni-rich material studied here is somewhat stiffer at ambient pressure than stoichiometric B20-NiSi, while V0 (Table 3) is ∼0.6% smaller. This difference is significant, given the <0.1% difference in the volume of Pmmn-NiSi measured in this study as compared to that of Wood et al. (2013), and is probably due to the slight Ni enrichment of the sample relative to the near stoichiometric sample used by Lord et al. (2012). As is the case for Pmmn-NiSi, the ab initio EoS for stoichiometric B20-NiSi from Vočadlo et al. (2012) [represented by the dash–dot line in Fig. 4(a)] has a significantly larger V0 than the experimentally determined value (about 1.4% larger; see Table 3). As before, we have decided to correct the ab initio EoS by applying a constant volume offset of −0.1641 Å3 atom−1 such that its V0 is equal to the value measured for stoichiometric B20-NiSi by Lord et al. (2012) of 11.4289 Å3 atom−1 [the long-dashed line in Fig. 4(a)]. This corrected ab initio EoS for B20-NiSi matches closely all of the experimental data over this pressure range. However, above 50 GPa (not shown in the figure) the ab initio and experimental EoSs diverge, with the former being more compressible, yielding smaller volumes at a given pressure. This is a consequence of K0′ from the ab initio EoS being significantly smaller than the experimentally determined values (Table 3). The corollary of this is that the uncorrected ab initio EoS, which initially overestimates volume, crosses the extrapolated experimental EoS at ∼150 GPa (see Fig. 5 of Lord et al., 2012). However, compression data for B20-NiSi are only available to 80 GPa; were data available to higher pressure it would be interesting to see whether the uncorrected ab initio and experimental EoSs would in fact cross as extrapolation predicts or, alternatively, converge. If the latter, this would suggest that the ab initio simulations, on this material at least, do a better job of predicting the correct volume at higher pressures. This would also mean that `correcting' an ab initio EoS such that its V0 matched that of its experimental counterpart would not necessarily be a valid approach.
3.4. Comparison with other NiSi structures
Fig. 5 is a summary of the ambient-temperature P–V curves of the polymorphs of NiSi determined to date, including B31-NiSi, B20-NiSi and B2-NiSi results from Lord et al. (2012) and Pmmn-NiSi and B20-Ni53Si47 from this study. These four phases represent all of the constituents of the part of the NiSi phase diagram of relevance to planetary interiors (Lord et al., 2014, 2012; Dobson et al., 2015). At 300 K, the expected sequence of phases with increasing pressure is B31 → Pmmn → B20 → B2. As expected, this sequence is one of decreasing V0, increasing and increasing symmetry. Further, while neither K0 nor K0′ show the expected monotonic increase with increasing stabilization pressure, the product of the two parameters does (B31 = 660 GPa, Pmmn = 745 GPa, B20 = 902 GPa and B2 = 920 GPa). This is a manifestation of the high degree of correlation between these two fitted parameters within the Birch–Murnaghan formalism (see §3.2).
![[Figure 5]](kc5022fig5thm.gif) | Figure 5 Comparison of the experimentally determined P–V curves for the polymorphs of NiSi measured to date. The EoSs of B31-, B20- and B2-NiSi are from Lord et al. (2012 ; thin blue lines), while the EoS of Pmmn-NiSi is from this study (thick red line). The circles represent the P–V data for B20-NiSi from experiments 1 (filled) and 2 (open) of this study. The dashed lines represent the ab initio EoSs from Vočadlo et al. (2012) for B31-, B20- and B2-NiSi; the EoS for Pmmn-NiSi is from Wood et al. (2013) and is the average of their low-pressure and high-pressure EoSs. A constant volume offset has been applied to all the ab initio EoSs so that their V0 values match the relevant measured or estimated experimental values. |
Included in Fig. 5 are the corresponding ab initio EoSs (as dashed lines) from Vočadlo et al. (2012) for B31-NiSi, B20-NiSi and B2-NiSi and from Wood et al. (2013) for Pmmn-NiSi, corrected such that V0 matches the experimentally determined value. In the case of the unrecoverable B2 phase, V0 cannot be measured, and so a correction of the same magnitude as found for the B20 phase, of −1.4%, has been applied. In the case of the Pmmn phase, the plotted curve represents the average of the low-pressure and high-pressure ab initio EoSs, after each has been volume corrected. It is apparent from this analysis that, despite the subtle differences described in the previous sections, the volume-corrected ab initio EoSs match the majority of the experimental data rather well, and within error at all conditions for which experimental data exist. This is impressive given the range of compression and symmetry involved. It is only above ∼80 GPa that significant divergence starts to be apparent, as might be expected for extrapolations beyond the pressure range over which the data were collected.
4. Conclusion
Room-temperature EoSs for Pmmn-NiSi and Ni53Si47 in the B20 structure have been determined experimentally up to 44 GPa from X-ray diffraction measurements in a DAC. In both cases, the new data corroborate previous experimental measurements from Wood et al. (2013) for Pmmn-NiSi at ambient pressure and Lord et al. (2012) for B20-NiSi at high pressure. There is also good agreement with the ab initio P–V data of Wood et al. (2013) for Pmmn-NiSi and Vočadlo et al. (2012) for B20-NiSi, once a constant volume offset has been applied to the ab initio results such that the experimental and ab initio values for V0 are equal. Such a correction is considered valid given that GGA-based ab initio simulations commonly overestimate volume (at least at ambient pressure) by ∼1%. However, we see no strong evidence for the subtle second-order observed by Wood et al. (2013) in the lattice parameters of Pmmn-NiSi at 10.5 < V < 10.8 Å3 atom−1 in their simulations. As a result of this study, experimentally determined ambient-temperature EoSs for all of the constituents of that part of the NiSi phase diagram relevant to planetary interiors are now available.
Supporting information
contains datablocks global, OTL110213ESRF53__001_publ. DOI: 10.1107/S1600576715020087/kc5022sup1.cif
contains datablocks global, OTL110213ESRF53__030_publ, OTL110213ESRF53__030_overall, OTL110213ESRF53__030_phase_1, OTL110213ESRF53__030_phase_2, OTL110213ESRF53__030_p_01. DOI: 10.1107/S1600576715020087/kc5022sup2.cif
| NiSi | b = 3.3381 (5) Å |
| Mr = 86.79 | c = 5.6049 (7) Å |
| Orthorhombic, Pnma | V = 96.79 (1) Å3 |
| a = 5.1731 (5) Å | Z = 4 |
| Least-squares matrix: full | Profile function: CW Profile function number 2 with 18 terms Profile coefficients for Simpson's rule integration of pseudovoigt function C.J. Howard (1982). J. Appl. Cryst.,15,615-620. P. Thompson, D.E. Cox & J.B. Hastings (1987). J. Appl. Cryst.,20,79-83. #1(GU) = 1.000 #2(GV) = 26.478 #3(GW) = 3.768 #4(LX) = 10.133 #5(LY) = 1.384 #6(trns) = 0.000 #7(asym) = 0.0000 #8(shft) = 0.0000 #9(GP) = 0.000 #10(stec)= 0.00 #11(ptec)= 0.00 #12(sfec)= 0.00 #13(L11) = 0.000 #14(L22) = 0.000 #15(L33) = 0.000 #16(L12) = 0.000 #17(L13) = 0.000 #18(L23) = 0.000 Peak tails are ignored where the intensity is below 0.0050 times the peak Aniso. broadening axis 0.0 0.0 1.0 |
| Rp = 0.007 | 7 parameters |
| Rwp = 0.011 | 0 restraints |
| Rexp = 0.018 | (Δ/σ)max = 0.07 |
| χ2 = 0.372 | Background function: GSAS Background function number 1 with 14 terms. Shifted Chebyshev function of 1st kind 1: 2909.61 2: 720.427 3: 134.201 4: -179.301 5: 135.992 6: -79.0348 7: 14.4127 8: -8.63612 9: 6.82976 10: 5.45478 11: 8.51763 12: -3.02808 13: -9.12805 14: 0.624466 |
| 2046 data points |
| NiSi | b = 3.3381 (5) Å |
| Mr = 86.79 | c = 5.6049 (7) Å |
| Orthorhombic, Pnma | V = 96.79 (1) Å3 |
| a = 5.1731 (5) Å | Z = 4 |
| x | y | z | Uiso*/Ueq | ||
| Ni1 | 0.00779 | 0.25 | 0.18752 | 0.015* | |
| Si1 | 0.32128 | 0.75 | 0.0825 | 0.015* |
Experimental details
| Crystal data | |
| Chemical formula | NiSi |
| Mr | 86.79 |
| Crystal system, space group | Orthorhombic, Pnma |
| Temperature (K) | ? |
| a, b, c (Å) | 5.1731 (5), 3.3381 (5), 5.6049 (7) |
| V (Å3) | 96.79 (1) |
| Z | 4 |
| Radiation type | ? |
| Specimen shape, size (mm) | ?, ? × ? × ? |
| Data collection | |
| Diffractometer | ? |
| Specimen mounting | ? |
| Data collection mode | ? |
| Scan method | ? |
| 2θ values (°) | 2θmin = 0.009 2θmax = 35.931 2θstep = 0.018 |
| Refinement | |
| R factors and goodness of fit | Rp = 0.007, Rwp = 0.011, Rexp = 0.018, χ2 = 0.372 |
| No. of parameters | 7 |
Computer programs: GSAS.
Acknowledgements
This work was supported by the Natural Environment Research Council (NERC) by grants awarded to LV at UCL (grant No. NE/H003975/1). OTL would like to acknowledge support from NERC through a postdoctoral research fellowship (NE/J018945/1). We wish to thank Mohamed Mezouar and Gaston Garbarino for their help with the preparation and running of experiments at the ESRF.
References
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