CXLI. The lattice spacings of solid solutions of titanium, vanadium, chromium, manganese, cobalt and nickel in α-iron

Sutton, A. L.; Hume‐Rothery, W.

doi:10.1080/14786441208521140

Cited by 94 publications

(22 citation statements)

References 10 publications

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“…At first sight, the elastic properties of this system seem to be quite well established from both experimental [3][4][5][6][7][8][9][10][11][12] and theoretical [13][14][15][16][17][18] points of view. However, there are many complicated features of this system on both Fe-and Crrich sides.…”

Section: Introductionmentioning

confidence: 99%

First-principles study of elastic properties of Cr- and Fe-rich Fe-Cr alloys

2011

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Elastic properties of substitutionally disordered Cr-and Fe-rich Fe-Cr alloys are derived from first-principles calculations using the exact muffin-tin orbitals method and the coherent potential approximation. A peculiarity in the concentration dependence of elastic constants in Fe-rich alloys is demonstrated and related to a change in the Fermi surface topology. Our calculations predict high values for the elastic constants of Cr-rich Fe-Cr alloys, but at the same time show that these alloys could be rather brittle according to the Pugh criterion (the ratio between shear and bulk moduli is calculated to be greater than 0.5).

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Section: Introductionmentioning

confidence: 99%

First-principles study of elastic properties of Cr- and Fe-rich Fe-Cr alloys

2011

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“…Substitutional solute (Cr, V) depletion of the matrix, by nitride precipitation, leads to a minor lattice-parameter decrease (À0:0005 Å at:% for Cr in ferrite and À0:001 Å at:% for V in ferrite in the compositional range for the alloys employed in this study [44]), as compared to the observed major lattice-parameter increase (e.g. approx.…”

Section: Discussionmentioning

confidence: 87%

Lattice-parameter change induced by accommodation of precipitate/matrix misfit; misfitting nitrides in ferrite

et al. 2015

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“…The composition dependence of a(x) is shown in Fig. 1 (left panel) along with the experimental data for Fe-Mg (Hightower et al, 1997;Dorofeev et al, 2004) and Fe-Cr (Sutton & Hume-Rothery, 1955;Pearson, 1958). Compared to slight increase on bcc Fe by Cr, Mg strongly enlarge lattice parameter of bcc Fe as shown in Fig.…”

Section: Equation Of State and Formation Energymentioning

confidence: 86%

Thermo-Physical Properties of Iron-Magnesium Alloys

Kádas¹,

Zhang²,

Johansson³

et al. 2011

Magnesium Alloys - Design, Processing and Properties

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IntroductionAccording to the common phase diagrams, iron and magnesium are almost immiscible at ambient pressure Massalski (1986). In the liquid phase, the solubility of Mg in Fe is of the order of 0.025 atomic percent (at.%). The maximum solid solubility of Fe in Mg is 0.00041 at.% and the Fe content in Mg at the eutectic point is less than 0.008 at.% (Haitani et al., 2003). Below 1273 K the solubility of Mg in α-Fe is below the detection limit and about 0.25 at.% Mg can be solved in δ−Fe at the monotectic temperature. The immiscibility of Fe and Mg at ambient conditions is in line with the well-known Hume-Rothery rules, according to which more than 15% atomic size difference between alloy constituents hinders solid solution formation (Massalski, 1996). In spite of the negligible solubility of Mg in Fe, several Fe-rich metastable Fe-Mg solid solution have been synthesized. According to the pioneering work by Hightower et al. (Hightower et al., 1997), mechanical alloying produced Fe-Mg substitutional solid solutions with up to 20 at.% Mg and having the body centered cubic (bcc) crystallographic phase of α-Fe. Later, using the similar alloying procedure, Dorofeev et al. (Dorofeev et al., 2004;Yelsukov et al., 2005) found that about 5 − 7a t . %M gi nα-Fe forms supersaturated solid solution. These authors suggested that the driving force for the formation of Fe-Mg solid solutions is associated with the excess energy of coherent interfaces in the Fe-Mg nanocomposite, which facilitates incorporation of Mg into α-Fe. Indeed, based on semiempirical thermodynamic calculations, Yelsukov et al. (Yelsukov et al., 2005) obtained 6 kJ/mol for the enthalpy of formation for Fe-Mg solid solutions, compared to 20 kJ/mol calculated for the corresponding Fe-Mg nanocomposites. In addition to the mechanical alloying techniques, pressure was also found to facilitate the solid solution formation between Fe and Mg. Dubrovinskaia et al. (Dubrovinskaia et al., 2004) reported that at pressures around 20 GPa and temperatures up to 2273 K, the solubility of Mg in bcc Fe was increased to 4 at.%. They found that the lattice parameter of the bcc Fe-Mg alloy increased approximately by 0.6 % per at.% Mg. Furthermore, recent experimental measurements in combination with theoretical simulations demonstrated that at the megabar pressure range more than 10 at.% Mg could be dissolved in liquid Fe, which then could be quenched to ambient conditions (Dubrovinskaia et al., 2005). The mechanism behind the 4 4

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CXLI. The lattice spacings of solid solutions of titanium, vanadium, chromium, manganese, cobalt and nickel in α-iron

Cited by 94 publications

References 10 publications

First-principles study of elastic properties of Cr- and Fe-rich Fe-Cr alloys

First-principles study of elastic properties of Cr- and Fe-rich Fe-Cr alloys

Lattice-parameter change induced by accommodation of precipitate/matrix misfit; misfitting nitrides in ferrite

Thermo-Physical Properties of Iron-Magnesium Alloys

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