为探究TC4钛合金在不同热压缩变形条件下的微观组织演变及织构形成机理，进而达到调控织构和弱化“宏区”的目的，本工作通过热压缩实验、OM、EBSD及高温β相组织重构技术研究了TC4钛合金在α + β相区、β相区以及跨相区连续热压缩后α相微观组织及织构的演变规律。结果表明，试样在α + β相区压缩后主要由等轴α相组成，变形时{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}<\mathrm{11}\overline{\mathrm{2}}\mathrm{0}>柱面滑移系开动导致α相首先转动至{\mathrm{11}\overline{\mathrm{2}}\mathrm{0}}//FD取向(FD为压缩方向)；随形变量和形变速率增加，α晶粒逐渐转动至{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD取向。在β相区保温或压缩后的冷却过程中主要形成具有{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD相变织构的片层α相；在β相区施加30%的变形后β晶粒转动至\left\{\mathrm{001}\right\}//FD取向，β相\left\{\mathrm{001}\right\}//FD织构的增强促进了冷却过程中α相{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD相变织构的形成；随β相区形变量和形变速率增加，动态再结晶被促进，β晶粒尺寸减小，相变生成的片层α相晶粒尺寸也明显减小，且晶粒取向分散，因此α相{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构强度也相应降低。在跨相区连续热压缩后主要形成{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构，柱面滑移对织构的形成起主要作用。当试样以0.01 s^-1的形变速率分别在β相区和α + β相区压缩30%时，相变析出的α晶粒首先转动至{\mathrm{11}\overline{\mathrm{2}}\mathrm{0}}//FD取向，因此抑制了{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构的形成；而随着α + β相区形变量增加，晶粒取向进一步转向{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD取向，因此{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构强度增加；对于在β相区保温(未变形)后降温至α + β相区以0.01 s^-1的形变速率压缩60%的试样，其α相动态析出过程中的变体选择较弱，且α + β相区较大的形变量在一定程度上促进了α相的动态再结晶，因此其具有最弱的α相{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构；当形变速率为0.05 s^-1时，较大的形变量会导致α相发生动态再结晶，同样达到弱化{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD织构的效果。因此，采用跨相区连续热压缩工艺可以获得弱织构片层组织的钛合金。随后对试样在室温(约20 ℃)下进行了力学性能测试，在1020 ℃、5 min (未变形) + 920 ℃、60%、0.01 s^-1条件下变形的试样整体织构最弱，且α相晶粒尺寸较小，抵抗裂纹萌生和扩展的能力较强，因此具有最高的延伸率。

Titanium alloy has emerged as the preferred structural material in the aerospace and marine industries because of its exceptional strength-to-weight ratio, corrosion resistance, and fatigue resistance. The primary application of titanium alloy in aerospace is evident in aeroengines, emphasizing the importance of developing lightweight, high-performance components to enhance engine reliability. Despite these advantages, challenges arise during hot processing because the alloy forms a strong texture, resulting in anisotropic mechanical properties. In addition, the formation of “macrozones”, areas with similar grain orientations during hot processing, further complicates matters by facilitating stress concentration during hot deformation, thereby increasing the likelihood of crack nucleation. Rapid crack propagation within “macrozones” reduces the service life of titanium alloy components, necessitating a thorough investigation of the formation mechanism and control methods for “macrozones”. This study delves into the microstructure evolution and texture formation of TC4 titanium alloy under various hot compression conditions, aiming to elucidate the role of weakening texture and “macrozone”. The microstructure and texture evolution of the α phase after α + β phase field, β phase field, and continuous through-transus thermal compression were examined in TC4 alloy through thermal compression tests, optical microscopy, electron backscatter diffraction, and reconstruction of the high-temperature β phase. The results indicate that specimens primarily comprised equiaxed α phase after compression in the α + β phase field. The activation of {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}<\mathrm{11}\overline{\mathrm{2}}\mathrm{0}> prismatic slip systems caused α phase rotation toward {\mathrm{11}\overline{\mathrm{2}}\mathrm{0}}//forging direction (FD) orientation during deformation. With increased deformation and strain rate, α grains gradually rotated to {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD orientation. Cooling after holding or compression in the β phase field resulted in the development of lamellar α phase with a {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture. In the β phase field, 30% compression induced β grain rotation to \left\{\mathrm{001}\right\}//FD orientation, enhancing β phase\left\{\mathrm{001}\right\}//FD texture and promoting the formation of α phase{\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD transformation texture during cooling. Increased deformation and strain rate facilitated dynamic recrystallization of the β phase, reducing β grain size, weakening α phase {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture, and refining α grain size. After continuous through-transus thermal compression, the dominant {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture formation occurred because of prismatic slip system activation. Under specific conditions, such as 30% compression in the β phase field and 30% compression in the α + β phase field at 0.01 s^-1, inhibition of {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture formation was observed as α grains rotated to {\mathrm{11}\overline{\mathrm{2}}\mathrm{0}}//FD orientation during dynamic precipitation. Increased deformation in the α + β phase field led to further rotation of α grains to {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD orientation, intensifying {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture. Conversely, holding in the β phase field (undeformed), then cooled to the α + β phase field and compressed at 0.01^-1 to a 60% reduction resulted in weak variant selection during dynamic precipitation of α phase, with large deformation promoting dynamic recrystallization of α phase and yielding the weakest α phase {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture. And at a strain rate of 0.05 s^-1, extensive deformation promoting dynamic recrystallization of α phase, and weakening {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture. Continuous through-transus thermal compression was identified as a method for obtaining lamellar-structured titanium alloys with weak texture. Subsequent mechanical property testing at room temperature (around 20 ^oC) revealed that the through-transus thermal compressed specimen at 1020 ^oC, 5 min (undeformed) + 920 ^oC, 60%, and 0.01 s^-1 exhibited the weakest {\mathrm{10}\overline{\mathrm{1}}\mathrm{0}}//FD texture intensity and the smallest grain size of α phase. This specimen demonstrated strong crack initiation and propagation resistance, resulting in the highest elongation.