Abstract
Ti-Al single crystals up to 5.20 at. % Al oriented for prismatic slip {101̄0}〈1̄21̄0〉 (Schmid factor, 0.49–0.50) were deformed in compression over the temperature range 77–600 K. Dislocation configurations were observed by transmission electron microscopy. Solid solution softening was observed in dilute alloys and attributed to scavenging of interstitials. Beyond 1 at. % Al, the CRSS increased linearly with at. % Al. The main increase in CRSS on cooling in Ti is thought due to an increase in the stress required to overcome the Peierls barrier but there is a component due to interstitials which is removed by adding Al. Below 600 K there is no true athermal region where the flow stress is controlled only by mechanisms which are not subject to thermal activation. Extensive work softening occurs in the 5.2 at. % Al alloy. This was attributed to destruction of short-range order. Mostly screw dislocations remain after small deformation at low temperatures and the screw component increases with per cent Al. However, in low Al alloys with high interstitial contents most of the remaining dislocations are edges.
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