Abstract

Crystal nucleation can be described by a set of kinetic equations that appropriately account for both the thermodynamic and kinetic factors governing this process. The mathematical analysis of this set of equations allows one to formulate analytical expressions for the basic characteristics of nucleation, i.e., the steady-state nucleation rate and the steady-state cluster-size distribution. These two quantities depend on the work of formation, , of crystal clusters of size n and, in particular, on the work of critical cluster formation, . The first term in the expression for describes changes in the bulk contributions (expressed by the chemical potential difference, ) to the Gibbs free energy caused by cluster formation, whereas the second one reflects surface contributions (expressed by the surface tension, : , , where is a parameter describing the size of the particles in the liquid undergoing crystallization), n is the number of particles (atoms or molecules) in a crystallite, and defines the size of the critical crystallite, corresponding to the maximum (in general, a saddle point) of the Gibbs free energy, G. The work of cluster formation is commonly identified with the difference between the Gibbs free energy of a system containing a cluster with n particles and the homogeneous initial state. For the formation of a “cluster” of size , no work is required. However, the commonly used relation for given above leads to a finite value for . By this reason, for a correct determination of the work of cluster formation, a self-consistency correction should be introduced employing instead of an expression of the form . Such self-consistency correction is usually omitted assuming that the inequality holds. In the present paper, we show that: (i) This inequality is frequently not fulfilled in crystal nucleation processes. (ii) The form and the results of the numerical solution of the set of kinetic equations are not affected by self-consistency corrections. However, (iii) the predictions of the analytical relations for the steady-state nucleation rate and the steady-state cluster-size distribution differ considerably in dependence of whether such correction is introduced or not. In particular, neglecting the self-consistency correction overestimates the work of critical cluster formation and leads, consequently, to far too low theoretical values for the steady-state nucleation rates. For the system studied here as a typical example (lithium disilicate, ), the resulting deviations from the correct values may reach 20 orders of magnitude. Consequently, neglecting self-consistency corrections may result in severe errors in the interpretation of experimental data if, as it is usually done, the analytical relations for the steady-state nucleation rate or the steady-state cluster-size distribution are employed for their determination.

Highlights

  • The properties of polycrystalline materials are determined by their chemical composition and volume fraction, shape, size distribution, orientation, and degree of dispersion of the different crystalline phases formed during fabrication [1,2,3,4,5]

  • We show that: (i) This inequality is frequently not fulfilled in crystal nucleation processes. (ii) The form and the results of the numerical solution of the set of kinetic equations are not affected by self-consistency corrections

  • Considering phase formation in a selected glass-forming melt, we demonstrate with the results presented in this figure that the inequality ∆G (1) ∆G is not generally fulfilled. Since both the system of kinetic equations modeling nucleation and growth and the analytical expressions for the steady-state nucleation rate and the steady-state cluster-size distribution depend on the work of cluster formation, self-consistency corrections can be expected to have a significant effect on the theoretical predictions

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Summary

Introduction

The properties of polycrystalline materials are determined by their chemical composition and volume fraction, shape, size distribution, orientation, and degree of dispersion of the different crystalline phases formed during fabrication [1,2,3,4,5]. Considering phase formation in a selected glass-forming melt, we demonstrate with the results presented in this figure that the inequality ∆G (1) ∆G (nc ) is not generally fulfilled Since both the system of kinetic equations modeling nucleation and growth and the analytical expressions for the steady-state nucleation rate and the steady-state cluster-size distribution depend on the work of cluster formation, self-consistency corrections can be expected to have a significant effect on the theoretical predictions. The paper is structured as follows: In Section 2, the basic equations for the description of crystal nucleation and growth are formulated in terms of the model advanced by Farkas R atom is defined as the radius of the atoms or molecules of the liquid undergoing crystallization

Basic Equations of Classical Nucleation Theory
Application of the Capillarity Approximation
Some General Comments
Account of a Temperature Dependence of the Surface Tension for Sub- and
Account of a Curvature or Size Dependence of the Surface Tension for Sub- and
Summary of Results and Discussion
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