The non-isothermal crystallization kinetics with heating rates ranging from 10 K s-1to 80 K s-1and the isothermal crystallization kinetics during annealing from the glass transition temperature to the crystallization onset temperature of a Zr57Cu15.4Ni12.6Al10Nb5 amorphous alloy were studied in detail using X-ray diffraction and differential scanning calorimetry. During non-isothermal crystallization, it is more difficult to nucleate than to grow, and the crystallization resistance increases first and then decreases. During isothermal crystallization of the alloy from 713- 728 K, there are two exothermic peaks corresponding to a diffusion-controlled growth process with decreasing nucleation rate and increasing nucleation rate. From 733- 748 K, only one exothermic peak appears, and the growth process is controlled by the interface with decreasing nucleation rate. Isothermal crystallization is a process in which the crystallization resistance increases. The resistance of isothermal crystallization is less than that of non-isothermal crystallization.

Plastic anisotropy of the as-rolled 7050 aluminum alloy plate with T7451 temper was investigated by tensile tests, OM, SEM and TEM. The results show that the as-rolled 7050 aluminum alloy plate shows plastic anisotropy. The values of the as-rolled 7050 aluminum alloy plate deformed along ST, LT and RD are 7.178%, 10.69% and 12.877%, respectively. The as-rolled 7050 aluminum plate can be considered as a materials with two phases. Microstructure, especially grain shape and precipitate configuration, is the main source of plastic anisotropy of the as-rolled 7050 aluminum alloy plate with T7451 temper.

Compression tests of 7050 aluminum alloy have been conducted at different temperatures (340, 380, 420, and 460 °C) with strain rate of 0.1 s-1. The deformation behavior and service performance of the alloy are investigated using EBSD technique, TEM and hardness measurement. Results show that the volume fraction of recrystallized grains increases with the increase of deformation temperature. The primary softening mechanisms of the alloy deformed at 340, 380, and 420 °C are dynamic recovery, and dynamic recrystallization is the main softening mechanism of the alloy deformed at 460 °C. The hardness of the 7050 aluminum alloy deformed increases with increasing deformation temperature. Dynamic precipitation appears when the 7050 aluminum alloy was deformed at 340, 380, and 420 °C, and strengthening mechanisms include mechanical hardening and precipitation strengthening. When deformation temperature is 460 °C, solid solution strengthening and grain boundary strengthening are primary strengthening mechanisms.

1.5 mm, 0.7 mm and 0.3 mm thicknesses TiNP/2014Al composite sheets were obtained by hot rolling deformation carried out on as-extruded TiNP/2014Al composite rod. The effect of hot rolling deformation on high strain rate superplastic deformation behavior of the composite was researched by tensile experiment, OM, and SEM. Results show that 0.7mm thickness TiNP/2014Al composite sheet can gain the maximum elongation of 351% at 818 K and 3.3×10-1 s-1, and the m value is 0.43. The optimum strain rate increases with decreasing thickness of the TiNP/2014Al composite sheets. Flow stress and work hardening ability show contrary change tendency to optimum strain rate. The 0.7 mm thickness TiNP/2014Al composite sheet has medium flow resistance stress and shows excellent stability of plastic flow. Fracture surfaces show that the main superplastic deformation mechanism of the TiNP/2014Al composite includes in grain boundary sliding. Subgrain boundary sliding maybe another superplastic deformation mechanism.

The non-isothermal crystallization kinetics with heating rates ranging from 10 K s-1to 80 K s-1and the isothermal crystallization kinetics during annealing from the glass transition temperature to the crystallization onset temperature of a Zr57Cu15.4Ni12.6Al10Nb5 amorphous alloy were studied in detail using X-ray diffraction and differential scanning calorimetry. During non-isothermal crystallization, it is more difficult to nucleate than to grow, and the crystallization resistance increases first and then decreases. During isothermal crystallization of the alloy from 713- 728 K, there are two exothermic peaks corresponding to a diffusion-controlled growth process with decreasing nucleation rate and increasing nucleation rate. From 733- 748 K, only one exothermic peak appears, and the growth process is controlled by the interface with decreasing nucleation rate. Isothermal crystallization is a process in which the crystallization resistance increases. The resistance of isothermal crystallization is less than that of non-isothermal crystallization.