Tribological behavior of the isothermally forged and heat-treated Ti-22Al-25Nb (at. %) orthorhombic alloy with lamellar O microstructures was investigated. The friction experiments using a tribometer (UMT-3 CETR) against Si 3 N 4 and Al 2 O 3 were conducted at the load of 10N from 20 to 750 • C and a constant speed of 0.188 m/s. The experiment results indicated that for the friction pair of Al 2 O 3 , the coefficient of friction (COF) was decreased from 0.906-0.359, and for the friction pair of Si 3 N 4 , COF was decreased from 0.784-0.457 as the friction temperature increased from room temperature to 750 • C. The wear rate of the alloy against Al 2 O 3 is in the range of 2.63-8.15 × 10 −4 mm 3 N −1 m −1 , the wear rate against Si 3 N 4 is in the range of 2.44-5.83 × 10 −4 mm 3 N −1 m −1 , respectively. The wear mechanisms of the alloy were changed from plastic deformation and ploughing at lower temperature (20-400 • C) to adhesive wear and oxidative mechanism at higher temperature (600 and 750 • C). The friction and wear behavior of the Al 2 O 3 friction pair was comparable to that of the Si 3 N 4 friction pair.
This article investigates the tensile and creep behaviors of the Ti-22Al-25Nb (at.%) alloy with equiaxed microstructure. The experimental results show that the equiaxed microstructures are formed by isothermal forging in the α2 + B2 + O phase region, and then heat treating in α2 + B2 + O and B2 + O phase regions. The equiaxed particles are determined by isothermal forging and solution heat treating, and the acicular O phase is obtained by adjusting the aging temperature. The strengths of the alloy are sensitive to the thickness of the secondary acicular O phase. Increase in aging temperature improves strength and reduces the ductility. Deformation of the alloy mainly depends on the volume fraction and deformability of the B2 phase. During the high-temperature tensile deformation, the flow stress decreases with the increasing deformation temperature and increases with the increasing strain rate. The microstructure obtained by higher aging temperature (HT-840) has better creep resistance, due to the coarsening of the secondary acicular O phase.
Through room‐temperature compression tests, the microstructure evolution and room‐temperature plastic deformation mechanism of a β‐type Ti–10Mo–1Fe alloy, which exhibits a primary α phase after solution treatment at 780 °C, are studied. When the deformation is small, the existence of the primary α phase makes the distribution of twins between grains uneven. A small amount of intragranular twins grows to the intragranular α phase, and then stops growing. The grain boundary α phase (GBα) plays an important role in inhibiting the growth of twin laths to a certain extent. When the deformation is large, compression cracks appear at the α/β phase interface. The α/β phase interface is weak, and the deformation along the 45° direction is relatively large. Owing to the existence of the primary α phase, the ultimate tensile strength of the alloy increases to 934.5 MPa, and the elongation reaches 21.7%. The room‐temperature plastic deformation mechanism of the Ti‐10Mo‐1Fe alloy solution treated at 780 °C is dominated by {332} <113> twins, as well as by a small amount of {112} <111> twins (0.57%) and stress‐induced orthorhombic martensite α” phase (2.5%).
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