Ostwald ripening in concentrated alloys

Calderón, H.A.; Voorhees, Peter W.; Murray, J. L.; Kostorz, G.

doi:10.1016/0956-7151(94)90293-3

Cited by 222 publications

(95 citation statements)

References 25 publications

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“…Unfortunately, such approaches are not possible in solid-solid systems, and thus in most cases interfacial energies of coherent interfaces have been determined through recourse to kinetic, and not equilibrium, measurements. Extracting accurate measurements of interfacial energies from, for example, measured coarsening kinetics can be quite difficult [44]. However, a field against which the .…”

Section: Discussionmentioning

confidence: 99%

The equilibrium shape of a misfitting precipitate

Thompson¹,

Su²,

Voorhees³

1994

Acta Metallurgica et Materialia

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262

111

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Abstract-We examine the equilibrium morphologies of precipitates with either a tetragonal or purely dilatational misfit in an elastically anisotropic medium with cubic symmetry under conditions of plane strain. We find that particles with a dilatational misfit are nearly spherical at " "Les, take on four-fold symmetric shapes at intermediate sizes and then undergo a supercritical s-breaking bifurcation to two-fold symmetric shapes aligned along the elastically soft directions of the crystal. A tetragonal misfit breaks this four-fold to two-fold supercritical bifurcation when the direction of the tetragonality is coincident with one of the elastically soft directions of the crystal. Such a tetragonal misfit can lead to two-fold equilibrium particle shapes which are local energy minima, or metastable, and in some cases have large negative interfacial curvatures. When the tetragonality is not in an elastically soft direction, the supercritical bifurcation is not broken and the particles can take on unusual diamond-like or S-shaped morphologies.

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Section: Discussionmentioning

confidence: 99%

The equilibrium shape of a misfitting precipitate

Thompson¹,

Su²,

Voorhees³

1994

Acta Metallurgica et Materialia

Self Cite

262

111

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“…The most rigorous modification is that of Calderon et al [13], which describes the coarsening of a phase that is not necessarily a terminal solid solution, and at the same time removes the limitation that the parent (matrix) phase be a dilute solid solution. The rate constant k in the theory of Calderon et al [13] is expressed by the equation…”

Section: A Brief Historymentioning

confidence: 99%

A1-L12 interfacial free energies from data on coarsening in five binary Ni alloys, informed by thermodynamic phase diagram assessments

Ardell

2011

J Mater Sci

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The data on coarsening of c 0 -type precipitates (Ni 3 X, with the L1 2 crystal structure) in Ni-Al, Ni-Ga, Ni-Ge, Ni-Si, and Ni-Ti alloys are re-evaluated in the context of recent (TIDC) and classical (LSW) theories of coarsening, with the objective of ascertaining the best values possible of interfacial free energies, r, of the c/c 0 interfaces in these five alloy systems. The re-evaluations include fitting of the particle size distributions, reanalyzing all the available data on the kinetics of particle growth and kinetics of solute depletion, and using thermodynamic assessments of the binary alloy phase diagrams to calculate curvatures of the Gibbs free energies of mixing. The product of the work is two sets of interfacial free energies, one set for the analysis using the recent TIDC theory and the other for the analysis using the classical LSW theory. The TIDC-based analysis yields lower values of r by about a factor of 2/3. All the interfacial energies are considerably larger, by factors ranging from *4 to 10, than those previously reported, which were for the most part calculated from data on coarsening assuming idealsolution thermodynamics. In the TIDC theory the width of the interface, d, is allowed to increase with particle size, r. A simple equation relating r to the ratio of the gradient energy and d is used to show that r can remain constant even though d increases with r. Published work supporting this contention is presented and discussed.

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“…Recently, Li et al [34] have shown how a combination of CALPHAD calculations and existing theory of Ostwald ripening [35,36,37] can be used to calculate coarsening rates of Ni-based superalloys to a high level of accuracy. The CALPHAD calculations provides critical information concerning the composition of and and allows the calculation of the / and / interfacial energy ( ) for use in the relevant kinetic equation shown below.…”

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confidence: 99%

Modelling the Material Properties and Behaviour of Ni-Based Superalloys

Saunders¹,

Guo²,

Li³

et al. 2004

Superalloys 2004 (Tenth International Symposium)

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At the last two Superalloy meetings at Seven Springs, work on the development of thermodynamic modelling tools for application to multi-component Ni-based superalloys has been presented. Such modelling has become quite widespread, providing significant benefit. However, its applicability often falls short from directly providing the information that is actually required and, by itself, cannot be directly used to model properties being targeted by the end user, e.g. TTT/CCT diagrams, mechanical properties, thermophysical and physical properties. To overcome these limitations a new computer programme has been developed, called JMatPro, an acronym for Java-based Materials Properties software. The properties which can be calculated are wide ranging, including thermo-physical and physical properties (from room temperature to the liquid state), TTT/CCT diagrams, stress/strain diagrams, proof and tensile stress, hardness, coarsening of and and creep.

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Ostwald ripening in concentrated alloys

Cited by 222 publications

References 25 publications

The equilibrium shape of a misfitting precipitate

The equilibrium shape of a misfitting precipitate

A1-L12 interfacial free energies from data on coarsening in five binary Ni alloys, informed by thermodynamic phase diagram assessments

Modelling the Material Properties and Behaviour of Ni-Based Superalloys

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