As well as the most of other 3d late transition metals Fe is a good β-Ti stabilizer, has a large solid solubility in β-Ti and owing to the atomic size difference with Ti can enable significant solution strengthening. The structure and mechanical properties of Ti alloys containing significant amount of Fe (or Fe together with Co, Cu and other elements) are reviewed in the present work. At high content of the late transition metals (for example, more than about 15 at% of Fe) the structure of these alloys consist of the rounded primary dendrites of an ordered cP2 intermetallic compound and an eutectic consisting of the cP2 intermetallic compound and a supersaturated cI2 β-Ti solid solution. cP2+cI2 phase Ti–Fe alloys, their derivatives: Ti–Fe–Co, Ti–Fe–Cu, etc…, and cI2 β-Ti solid solution alloys containing Sn and Nb exhibit high compressive strength and plasticity. At lower Fe content a supersaturated β-Ti solid solution single phase structure is formed. However, these alloys also show good mechanical properties especially when alloyed with Sn and Nb. The structure and properties of various kinds of such alloys are discussed in the present paper.

Al–Co–Y alloys were suction cast under identical conditions into a wedge-shaped copper mold for investigating the compositional dependence of glass-forming ability (GFA). The optimal glass-forming composition was determined to be Al₈₉Co_5.5Y_5.5, whose Al content is evidently larger than the findings of the optimal glass formers in other Al–TM–Y alloy systems. A reason is that Co-centered clusters tend to share vertexes and edges rather than faces with the surrounding clusters in Al–Co–Y amorphous alloy, and more Al atoms are required. When Al₈₉Co_5.5Y_5.5 amorphous alloy and its neighbors were isochronally annealed in a differential scanning calorimeter, no glass transition could be observed and the primary crystallization phase was invariably fcc-Al.

The effect of the soaking conditions of ingots on the rate of recovery and recrystallization in an A1050 hot-rolled sheet during annealing at 350°C was investigated. The rate of the recovery and recrystallization with no soaking and 600°C/8 h WQ (water quenching) was slower than that of 450°C/8 h FC (furnace cooling). Many dissolved impurities (Fe, Si), which were contained in the no soaking and 600°C/8 h WQ conditions cause the delay in the recovery and recrystallization. Particularly, in the no soaking condition, no precipitat