High resolution transmission electron microscopy was made on the alloys which were preaged under the conditions, 100°C ×1000min and 130°C×4000min, in order to develop G. P. (1) and G. P. (1) plus G. P. (2) structures (so far as the binary alloy was concerned) respectively, and reversion heat-treated at 200°C and 250°C for various times.
G. P. zones in the binary alloy reversion heat-treated at 200°C were apt to disappear, but some of large ones remained after all and turned to grow up to form G. P. (2); coarse G. P. zones in the ternary alloy (corresponding to G. P. (2) in the binary alloy, ie. G. P. (X
2)) simply remained and changed into θ' phase in a short time, where 200°C was higher than any solvus temperature of G. P. (1) or G. P. (X
2). Complete reversion of G. P. zones was found in the binary alloy treated at 250°C, but some of G. P. (X
2) changed into θ' in the ternary alloy. The accelerated θ'-formation in the ternary alloy would relate to the Sn-rich phase appearing at the corner of the G. P. (X
2) zone in the early stage of reversion. Heterogeneous precipitation of θ' always appeared during the above reversion heattreatment.
Complete reversion of G. P. zones was not always expected even in the reversion at higher temperature than G. P. zone solvus one. Complete reversion would be closely related to the pre-aging condition as well as reversion temperature. Ideal solid solution could hardly be brought out in general by means of usual reversion heattreatment.
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