Coupled evolution of composition and chemical order under irradiation

image944Many engineering alloys contain ordered phases or precipitates to optimize their properties, in particu­lar mechanical properties. It is thus important to

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investigate how these optimized microstructures evolve under irradiation. It is anticipated that, under appropriate conditions, ballistic mixing can lead to the dissolution of precipitates, and to the disordering of chemically ordered phases.129 Matsumura et at}30 used a 1D PF approach on a model binary alloy system to specifically investigate what evolution irra­diation may produce. In that model, the composition field is represented by the globally conserved order parameter X(r), while the degree of order is repre­sented by the nonconserved order parameter S(r). X is chosen to vary from — 1 to +1 for pure A and pure B composition, respectively, and S takes a value ranging from 0 to 1 for fully disordered and fully ordered phases, respectively. The free energy func­tional of the system is written as

 

f (X, S, T)

 

(X — Xm)2 — b(T ){X0(T )2 — X2}S2 + b(T )2 X1(T )2S4

 

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[29;

 

where f0 is the mean field free energy of the disor­dered phase with composition xm, and a, b, xj2 are positive constants depending on temperature. The equilibrium phase diagram for this model system is given in Figure 10. Notice, in particular, that at low temperature and for compositions sufficiently far from the equiatomic composition, an ordered phase coexists with a disordered phase.

The kinetic evolution of these two fields is gov­erned by

 

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dr

 

[30]

 

[28]

 

and

 

where f(X, S, T) is the mean field free energy of a homogeneous alloy, and H and K are positive constants of the interfacial energy coefficients in the presence of varying field X and S, respectively. The homogeneous free-energy density is given by a Landau expansion

 

@S, 8F({X, S, T})

— =-£fS — M(T, f) ({8’s’ })

 

[31]

 

where f is the atomic displacement rate, m is the chemical potential, Dmix and e are positive coefficients characterizing the efficiency of mixing and disordering

 

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Figure 10 Equilibrium phase diagram for model alloy system given by eqns [28] and [29]. The dotted lines correspond to the metastable extrapolation of the order-disorder transition into the miscibility gap. Reprinted with permission from Matsumura, S.; Muller, S.; Abromeit, C. Phys. Rev. B 1996, 54(9), 6184-6193. Copyright by the American Physical Society.

 

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Подпись: Figure 11 Steady-state phase diagrams under irradiation for (a) a low irradiation flux and (b) an irradiation flux 10 times larger. The two-phase field is barely present in (a), and is no longer stable in (b). Reprinted with permission from Matsumura, S.; Muller, S.; Abromeit, C. Phys. Rev. B 1996, 54(9), 6184-6193. Copyright by the American Physical Society.

by irradiation, and L and M are the mobility coeffi­cients for the conserved and nonconserved fields. Note that here there is no kinetic coupling between these two fields. There is, however, thermodynamic coupling through the expression chosen for the homogeneous free-energy density, eqn [29].

Although point defects are not explicitly used as PF variables, the dependency of the mobility co­efficients M and L with temperature, irradiation flux, and sink density (c$) is obtained from a rate theory model for the vacancy concentration under

irradiation in a homogeneous alloy.1 The steady-state phase diagrams for two irradiation flux values are given in Figure 11. At the higher flux, the phase diagram is composed of homogeneous disordered and ordered phases only. At low enough temperature, the ballistic mixing and disordering dominate the evolution of the alloy, leading to the destabilization of the ordered phase at and near the stoichiometric composition X = 0, and to the disappearance of the two-phase coexistence domains for off-stoichiometric compositions.

The model has also been used to study the disso­lution of ordered precipitates under irradiation. In agreement with prior lattice-based mean field kinetic simulations,131 it is found that two different dissolution paths are possible, depending upon the composition and irradiation parameters. Ordered precipitates may either disorder first and then slowly dissolve or they may dissolve progressively while retaining a finite degree of chemical order until their complete dissolution. These two kinetic paths have indeed been observed experimentally in Nimonic PE16 alloys irradiated with 300-keV Ni ions.132,133