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The first is the intrinsic atomic mobility, /3A or D*, which for a solid is usually determined by the concentration and mobility of point defects. The second factor is the thermodynamics of the solid solution commonly given by the Darken factor (1 +dln yA/dln 7VA). The thermodynamic effect can accelerate diffusion when there is a negative deviation from ideality such that yA is less than 1 but increasing to y A =l as 7VA->1, so that both dyA/dNA>0 and dlnyA/dln7VA>0. The thermodynamic term, where there is a positive deviation from ideality and yA is then more than 1, can equivalently retard diffusion and in the limit when 82G/dNA<0 and dm yA/dln NA< — 1, leads to a negative diffusion and unmixing of unstable solid solutions.

Below such a temperature d2F/dN2 will be negative, and so diffusion even above the critical temperature will be very sluggish, since the Darken factor (1 + dln y/dln N) will, though not yet negative, be very close to zero. All potential spinodally decomposing alloys will be in this situation. 5 Homogenisation above the non-equilibrium melting temperature In a range of solidification studies, Vogel, Cantor and Doherty (1979), Doherty, Feest and Lee (1984), Annavarapu, Liu and Doherty (1992) and Annavarapu and Doherty (1993, 1995) investigated the microstructural changes occurring on annealing polycrystalline alloys just above the solidus temperature.

Howe et al. (1985,1987) have also demonstrated ledge nucleation by precipitate-precipitate intersection. The details of ledge nucleation by precipitate intersection are still, however, an unsolved kinetic problem (Doherty and Rajab 1989). 5. It now appears clear, from both growth and coarsening studies, that growth at rates slower than expected for diffusion control can and does occur for Widmanstatten precipitates due to an apparent lack of growth ledges in certain conditions. However, diffusion controlled growth of ledged precipitates is known to be possible if a sufficiently high density of ledges is present.

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