The influence of hot rolling deformation on recrystallization and texture evolution of Ti551 alloy
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摘要: 热轧作为典型的形变处理环节，轧制过程织构的演变是影响钛合金强塑性的关键。Ti-5.3Al-1.5Mo-1Zr-1Cr-1V-1Sn-0.1O-0.15Fe（Ti551）合金是服役于深海环境的中强高韧新型材料，目前其在轧制过程的织构演变规律尚不明确。以Ti551锻坯为研究对象，在近β转变温度（Tβ，950 ℃）条件下进行5%、10%、30%、50%不同变形量的热轧试验，通过电子背散射衍射（EBSD）定量分析低角度晶界、晶粒平均定向伸展及α相{0001}织构演化。结果表明：以退火态（变形0）为基准，累积压下率从0增加到30%时，再结晶与应变释放区域面积分数由约55%降至36%，随着变形量进一步提升至50%，再结晶分数几乎不变；其次，热轧后组织形成基面织构，但其整体强度随变形量增加而降低（峰值下降并趋于弥散）。上述规律表明：在近Tβ条件下，轧制方向与锻坯主织构方向垂直时，较高累计压下率更有利于削弱基面织构并促使取向峰弥散，为获得取向团簇尺度更小、组织更均匀的网篮组织提供了终轧变形量选择依据。Abstract: As a representative thermomechanical processing step, hot rolling can generate texture evolution that is critical to the strength–ductility synergy of titanium alloys. Ti551 is a newly developed medium-strength, high-toughness alloy designed for deep-sea service; however, its texture-evolution behavior during rolling remains unclear. In this work, Ti551 as-forged billets were hot rolled at near β-transus temperature region (Tβ, 950 ℃) with reductions from 5% to 50%. Electron backscatter diffraction (EBSD) was used to quantitatively analyze the fractions of low-angle grain boundaries (LAGBs), grain orientation spread (GOS) and the evolution of α {0001} texture. The results show that, taking the annealed condition (0 reduction) as the reference, when the cumulative reduction increases from 0 to 30%, the area fraction of recrystallized/strain-relieved regions decreases from ~55% to ~36%, and remains nearly unchanged as the reduction is further increased to 50%. In addition, hot rolling develops a basal texture, but its overall intensity decreases with increasing reduction (i.e., the peak intensity drops and the texture becomes more diffuse). These finds indicate that under near Tβ condition, when the rolling direction is perpendicular to the dominant texture direction of the forged billet, a higher cumulative reduction is more effective in weakening the basal texture and dispersing the orientation peaks. This can help select the final-pass reduction to obtain a basketweave microstructure with smaller orientation-cluster length scales and improved microstructural uniformity.
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Key words:
- Ti551 /
- hot rolling /
- recrystallization /
- texture
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图 2 热锻后组织形貌
（a）GB图；（b）IPF图；（c）KAM图
Figure 2. Microstructural characterization of samples after hot forging
图 3 950 ℃退火后组织形貌
（a）GB图；（b）IPF图；（c）KAM图
Figure 3. Microstructural characterization of samples after annealing at 950 °C
图 4 950 ℃热轧变形5%、10%后的组织形貌
变形5%:（a）GB图,（b）IPF图,（c）KAM图；变形10%:（d）GB图,（e）IPF图,（f）KAM图
Figure 4. Microstructural characterization of samples after hot rolling at 950 °C with different reductions
图 5 950 ℃热轧变形30%、50%后的组织形貌
变形30%:（a）GB图,（b）IPF图,（c）KAM图; 变形50%: （d）GB图,（e）IPF图,（f）KAM图
Figure 5. Microstructural characterization of samples after hot rolling at 950 °C with different reductions
图 6 不同工艺状态下的GOS分布图
（a）热锻；（b）950 ℃退火；（c）950 ℃变形5%；（d）950 ℃变形10%；（e）950 ℃变形30%；（f）950 ℃变形50%
Figure 6. Grain orientation spread (GOS) distributions of samples after processing under different processing conditions
图 7 不同工艺状态下的局部晶粒取向
（a）950 ℃退火；（b）950 ℃变形5%；（c）950 ℃变形10%；（d）950 ℃变形30%；（e）950 ℃变形50%
Figure 7. Local grain orientation maps of sample after processing under different processing conditions
图 8 不同工艺状态下的α相{0001}极图
（a）热锻；（b）950 ℃退火；（c）950 ℃变形5%；（d）950 ℃变形10%；（e）950 ℃变形30%；（f）950 ℃变形50%
Figure 8. α {0001} pole figures of sample after processing under different processing conditions
表 1 Ti551化学成分
Table 1. Chemical composition of the Ti551 alloy
% Al Mo Zr Cr V Sn O Fe 5.27 1.48 1.06 0.94 0.98 1.05 0.12 0.15 
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