Phase Equilibria in the Sn-Rich Corner of the Ni-Sb-Sn System

Mishra, R.; Kroupa, Aleš; Zemanová, Adéla; Ipser, Herbert

doi:10.1007/s11664-012-2395-9

Cited by 8 publications

(3 citation statements)

References 17 publications

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“…18 We also observed threephase regions L + (Sb) + τ, L + α + τ, and L + Ni 3 Sn 2 + α (Fig. 1c-e), which agree well with the Schultz-Scheil diagram derived by Mishra et al 19 The solid solution α (NiSb-Ni 3 Sn 2 ) was observed in all the as-cast samples and has the widest liquidus field, likely being the most stable phase in the system. Thus, the as-cast alloy 2.7Ni-24.7Sn-72.6Sb shows primary crystallisation of the alpha-phase, which is surrounded by NiSb 2 and the last portion of liquid crystallizes with the composition 40Sn-60Sb.…”

Section: Filling Levels Phase Equilibria and Homogeneity Regionsupporting

confidence: 89%

“…[14][15][16][17] A ternary skutterudite in the system Ni-Sn-Sb was first reported by Grytsiv et al 18 who defined a wide homogeneity range at 250 °C and 350 °C by establishing the isothermal sections in the Sn-Sb-NiSb-Ni 3 Sn 2 subsystem at these temperatures. Investigations by Mishra et al 19 in the Snrich part of the Ni-Sn-Sb phase diagram suggested that the phase equilibria determined by Grytsiv et al 18 lies within 10 °C above or below the declared temperatures.…”

Section: Introductionmentioning

confidence: 94%

“…18 The phase equilibria change drastically by increasing the temperature from 250 to 350 °C and the authors 18 suggested that at least two invariant reactions exist in this temperature range. Mishra et al 19 presented a detailed reaction scheme for the Sn-rich part of the system involving three invariant equilibria in the same temperature range. In order to derive the phase equilibria at 450 °C, we annealed several samples at this temperature for at least 30 days.…”

Section: Filling Levels Phase Equilibria and Homogeneity Regionmentioning

confidence: 99%

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Ba-filled Ni–Sb–Sn based skutterudites with anomalously high lattice thermal conductivity

et al. 2016

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Novel filled skutterudites BayNi4Sb12-xSnx (ymax = 0.93) have been prepared by arc melting followed by annealing at 250, 350 and 450 °C up to 30 days in vacuum-sealed quartz vials. Extension of the homogeneity region, solidus temperatures and structural investigations were performed for the skutterudite phase in the ternary Ni-Sn-Sb and in the quaternary Ba-Ni-Sb-Sn systems. Phase equilibria in the Ni-Sn-Sb system at 450 °C were established by means of Electron Probe Microanalysis (EPMA) and X-ray Powder Diffraction (XPD). With rather small cages Ni4(Sb,Sn)12, the Ba-Ni-Sn-Sb skutterudite system is perfectly suited to study the influence of filler atoms on the phonon thermal conductivity. Single-phase samples with the composition Ni4Sb8.2Sn3.8, Ba0.42Ni4Sb8.2Sn3.8 and Ba0.92Ni4Sb6.7Sn5.3 were used to measure their physical properties, i.e. temperature dependent electrical resistivity, Seebeck coefficient and thermal conductivity. The resistivity data demonstrate a crossover from metallic to semiconducting behaviour. The corresponding gap width was extracted from the maxima in the Seebeck coefficient data as a function of temperature. Single crystal X-ray structure analyses at 100, 200 and 300 K revealed the thermal expansion coefficients as well as Einstein and Debye temperatures for Ba0.73Ni4Sb8.1Sn3.9 and Ba0.95Ni4Sb6.1Sn5.9. These data were in accordance with the Debye temperatures obtained from the specific heat (4.4 K < T < 140 K) and Mössbauer spectroscopy (10 K < T < 290 K). Rather small atom displacement parameters for the Ba filler atoms indicate a severe reduction in the "rattling behaviour" consistent with the high levels of lattice thermal conductivity. The elastic moduli, collected from Resonant Ultrasonic Spectroscopy ranged from 100 GPa for Ni4Sb8.2Sn3.8 to 116 GPa for Ba0.92Ni4Sb6.7Sn5.3. The thermal expansion coefficients were 11.8 × 10(-6) K(-1) for Ni4Sb8.2Sn3.8 and 13.8 × 10(-6) K(-1) for Ba0.92Ni4Sb6.7Sn5.3. The room temperature Vickers hardness values vary within the range from 2.6 GPa to 4.7 GPa. Severe plastic deformation via high-pressure torsion was used to introduce nanostructuring; however, the physical properties before and after HPT showed no significant effect on the materials thermoelectric behaviour.

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Section: Filling Levels Phase Equilibria and Homogeneity Regionsupporting

confidence: 89%