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金属学报  2021, Vol. 57 Issue (11): 1455-1470    DOI: 10.11900/0412.1961.2021.00353
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高强韧钛合金组成相成分和形态的精细调控
杨锐(), 马英杰, 雷家峰, 胡青苗, 黄森森
中国科学院金属研究所 师昌绪先进材料创新中心 沈阳 110016
Toughening High Strength Titanium Alloys Through Fine Tuning Phase Composition and Refining Microstructure
YANG Rui(), MA Yingjie, LEI Jiafeng, HU Qingmiao, HUANG Sensen
Shi -Changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
引用本文:

杨锐, 马英杰, 雷家峰, 胡青苗, 黄森森. 高强韧钛合金组成相成分和形态的精细调控[J]. 金属学报, 2021, 57(11): 1455-1470.
Rui YANG, Yingjie MA, Jiafeng LEI, Qingmiao HU, Sensen HUANG. Toughening High Strength Titanium Alloys Through Fine Tuning Phase Composition and Refining Microstructure[J]. Acta Metall Sin, 2021, 57(11): 1455-1470.

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摘要: 

结构钛合金已成为航空、航天、船舶等重大工程领域的关键材料，其强韧化，特别是增韧，是材料研究的核心。应用状态下大部分结构钛合金由α + β两相组成，精细调控两相的成分、比例及形态是深度优化合金强韧性的基础。本文综述了结构钛合金主要的强韧性优化手段，重点介绍了本团队在结构钛合金成分设计、塑性变形方式及显微结构调控方面开展的相关研究工作。研究表明，通过两相的成分优化设计，可提高hcp结构α相及α/β两相界面的协调变形，并抑制脆性ω和Ti3Al相的过量析出；两相微区成分调控同样可诱发α相形变孪晶及β相形变诱发相变，导致孪晶增塑增韧效应。此外，大量研究也表明，制备多尺度显微结构是实现钛合金增塑增韧的重要调控手段。在钛合金微区相成分和形态精确调控的基础上，提出了基于微区调控的高强高韧钛合金设计及工程化制备的研究方法。最后对不同应用领域的高强韧结构钛合金的技术发展进行了总结及展望。
关键词 ： 钛合金,  强韧性,  相成分,  显微结构    
Abstract：

Titanium alloys are key materials for applications in major engineering areas, such as aerospace and marine equipment. Studies on structural titanium alloys focus on strengthening and toughening the alloys, especially the latter. The mainstream structural titanium alloys comprise both α and β phases. The optimization of the strength and toughness balance relies on the control of the compositions, volume fractions, and morphologies of both phases. In this study, some recent advances along the above line are reviewed, focusing on studies on the composition design, plastic-deformation mechanism, and microstructure tuning. Rational design of the compositions of both phases improved the deformation coordination within the α phase and across the α/β interface, suppressed the precipitation of brittle ω and α2 phases, and resulted in improved plasticity and toughness through the α-deformation twin and β-deformation-triggered phase transformation. The multiscale microstructure enhanced the strength and toughness of the titanium alloy. Using the abovementioned approaches, a series of titanium alloys with an improved strength-toughness combination were developed and fabricated. Finally, an attempt was made to predict the prospect of technology development in the field of high-strength and high-toughness titanium alloys for various applications.
Key words： titanium alloy    strength and toughness    phase composition    microstructure
收稿日期: 2021-08-23     
ZTFLH:  TG146  
基金资助:国家重点研发计划项目(2016YFC0304200);国家自然科学基金项目(51871225)
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杨锐
马英杰
雷家峰
胡青苗
黄森森

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https://www.ams.org.cn/CN/10.11900/0412.1961.2021.00353      或      https://www.ams.org.cn/CN/Y2021/V57/I11/1455

图1  第一性原理计算得到的α-Ti-xAl二元合金柱面及基面<a>位错滑移临界剪切应力随Al含量的变化，以及实验测得的Ti-xAl合金屈服强度及断裂韧性随Al含量的变化[7]
AlloyModulus / GPaModulus ratio
EαGαEβGβEβ / EαGβ / Gα
Ti64159.9963.7071.0625.550.440.40
Alloy-1159.6064.1183.5730.470.520.48
Alloy-2155.8161.6788.5532.370.570.52
表1  采用第一原理精确Muffin-Tin轨道方法计算得到的不同合金α和β相的模量
图2  Ti-10V-2Fe-3Al合金单晶微柱变形后的TEM像[18](a) low-magnification bright field (BF) image (The inset is corresponding SEM appearance)(b) [110]β-zone selected area diffraction pattern (SADP) of framed area in Fig.2a(c, d) dark field (DF) images taken from (0001)ω2 and (0001)ω1 diffraction spots of Fig.2b, respectively (Insets show the crystal orientation of ω2 and ω1)
图3  Ti-3Al-5Mo-4.5V合金分别经两相区固溶、固溶+时效热处理后的相组成表征
图4  Ti-3Al-5Mo-4.5V合金不同热处理条件下的真应力-真应变曲线及加工硬化率曲线
图5  多种二元钛合金中ω-β相能量差随成分x的变化[21,22]
图6  Ti-6Al和Ti-8Al合金中Al元素团簇形貌及团簇内Al元素浓度统计分布[39]
图7  经不同时效处理后的光滑及缺口Ti-8Al合金拉伸样品的载荷-位移曲线[40](a) samples without notch(b) samples with notch (The dips in the curves being caused by stress relaxation as loading is halted)
图8  时效168 h后Ti-8Al合金在原位拉伸条件下缺口处的塑性变形特征[40](a) 84 μm (b) 164 μm (c) 364 μm (d) after fracture
图9  Ti64合金在α + β两相区不同温度热处理后的初生α相(αp)、β转变区域(βt) Al和V元素浓度[44]
图10  Ti64合金在两相区920℃保温5 min后的显微组织和沿图示箭头方向的Al、V元素浓度分布[44](a) microstructure with the arrowed line indicating measurement locations and direction(b) composition profiles of Al and V showing local segregation of Al near the αp /βt boundaries indicated by the dashed lines
图11  相场计算模拟Ti64合金在两相区热处理过程中αp/βt界面附近成分演化过程[44]
图12  Ti64合金在两相区920℃保温不同时间条件下的显微组织和Al、V元素浓度分布[44]
图13  具有魏氏组织的Ti64合金裂纹尖端塑性区内的大范围形变孪晶及其EBSD表征分析[51](a) four primary twinning variants in single α colony(b) band contrast map with the red line representing {101ˉ2} twining plane(c) 3D crystal viewer of the corresponding parent and deformation twinning(d) pole figures of {101ˉ2} twinning plane of parent grain and the four twinning variants(e) schematic representation of the crystallo-graphic relationship between the parent grain and twin variants
图14  Ti-3Al-5Mo-4.5V合金在两相区不同温度固溶后的真应力-真应变曲线及加工硬化率曲线[42](a) 700oC (b) 750oC (c) 800oC (d) 880oC
图15  不同热处理温度下Ti-3Al-5Mo-4.5V合金β相的主导塑性变形方式[42]
图16  魏氏组织钛合金疲劳裂纹尖端塑性区形变特征示意图[71]
图17  基于微区调控的多组元、多相、多尺度结构高强高韧钛合金材料研发及工程化应用流程示意图[39,51,72]
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