高强亚稳<strong><i>β</i></strong>钛合金变形机制及其组织调控方法

doi:10.11900/0412.1961.2021.00352

金属学报

2021, Vol. 57

Issue (11): 1438-1454 DOI: 10.11900/0412.1961.2021.00352

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高强亚稳β钛合金变形机制及其组织调控方法

李金山¹^,²(

), 唐斌¹^,², 樊江昆¹^,²(

), 王川云¹, 花珂¹, 张梦琪¹, 戴锦华¹, 寇宏超¹^,²

^1.西北工业大学凝固技术国家重点实验室西安 710072
^2.西北工业大学重庆科创中心重庆 401135

Deformation Mechanism and Microstructure Control of High Strength Metastable β Titanium Alloy

LI Jinshan¹^,²(

), TANG Bin¹^,², FAN Jiangkun¹^,²(

), WANG Chuanyun¹, HUA Ke¹, ZHANG Mengqi¹, DAI Jinhua¹, KOU Hongchao¹^,²

^1.State Key Laboratory of Solidification Processing, Northwestern Polytechnical University, Xi'an 710072, China
^2.Chongqing Technology Innovation Center, Northwestern Polytechnical University, Chongqing 401135, China

引用本文:

李金山, 唐斌, 樊江昆, 王川云, 花珂, 张梦琪, 戴锦华, 寇宏超. 高强亚稳β钛合金变形机制及其组织调控方法[J]. 金属学报, 2021, 57(11): 1438-1454.
Jinshan LI, Bin TANG, Jiangkun FAN, Chuanyun WANG, Ke HUA, Mengqi ZHANG, Jinhua DAI, Hongchao KOU. Deformation Mechanism and Microstructure Control of High Strength Metastable β Titanium Alloy[J]. Acta Metall Sin, 2021, 57(11): 1438-1454.

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摘要:

亚稳β钛合金具有密度低、比强度高以及成形能力好等优异的综合特征，已经在对强韧性要求极高的航空航天结构件上获得应用，用以替代传统的高强度钢，实现显著的结构减重的同时大幅度提升飞行器性能。热成形技术与热处理工艺相结合是制备高强亚稳β钛合金结构件的主要手段，而制定优化工艺的前提是对合金的变形机制形成完整的认识，进而实现合金构件的组织-性能一体化调控。同时，明晰高强亚稳β钛合金的变形机制与宏观力学性能间的关系也有助于进一步研发新型合金，满足飞行器对更高性能材料的需求。因此，本文围绕高强亚稳β钛合金变形机制及其组织调控方法，首先概述了合金的室温塑性变形机制研究进展，阐述了β基体稳定性的影响因素及其相应的变形机制演变规律，分析了α析出相的特征对位错运动的综合影响，以及由此所造成的力学性能表现。然后，总结了高强亚稳β钛合金的热变形行为与机制，分析了合金在不同相区以及不同变形阶段所对应的组织演变规律和变形机制，探讨了合金在热变形过程中的加工硬化与流变软化行为。最后，简述了高强亚稳β钛合金组织调控过程中动态回复/动态再结晶与动态相变的复杂交互作用，论述了多尺度计算模型在合金组织与性能预测方面的研究现状与发展趋势。

关键词 ：亚稳β钛合金, 变形机制, 组织调控, 再结晶, 相变

Abstract：

Metastable β titanium alloy has excellent overall properties, including low density, high specific strength, and good forming ability. Therefore, it has been successfully used to replace traditional high-strength steels in aerospace structural components with extremely-high strength requirements, resulting in significant structural weight reduction effects and greatly improved aircraft performance. The main method for preparing high-strength metastable β titanium alloy structural components is the combination of hot forming technology and heat treatment. The prerequisite for formulating and optimizing the processes is a thorough understanding of the alloy's deformation mechanism, followed by integrated control of the microstructure and properties of the components. Meanwhile, elucidating the relationship between the high-strength metastable β titanium alloy's deformation mechanism and its micromechanical properties will aid in the development of new alloys to meet the needs of aircraft for higher performance materials. Therefore, in this article, the deformation mechanism of the high-strength metastable β titanium alloy and its microstructure control methods was focused on and discussed, and first summarizes the research progress of the plastic deformation mechanism at room temperature, expounds the factors affecting the stability of the β matrix and the corresponding deformation mechanism evolution, analogizes the comprehensive influence of α phase characteristics on dislocation movement and the resulting mechanical performance. Furthermore, this article summarizes the hot deformation behavior and mechanism of a high-strength metastable β titanium alloy, analyzes the alloy's microstructure evolution and deformation mechanism in different phase regions and deformation stages, and discusses the alloy's work hardening and softening behaviors during hot deformation. Finally, the complex interaction of dynamic recovery or dynamic recrystallization and dynamic phase transformation in the microstructure control process of high-strength metastable β titanium alloy is briefly described, and the research status and development trend of multi-scale calculation models in alloy microstructure and performance prediction are discussed.

Key words： metastable β titanium alloy deformation mechanism microstructure control recrystallization phase transformation

收稿日期: 2021-08-23

ZTFLH:

TG146.23

基金资助:国家重点研发计划项目(2016YFB0701303);国家自然科学基金项目(51801156);重庆市自然科学基金项目(cstc2020jcyj-msxmX1056)

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	李金山
	唐斌
	樊江昆
	王川云
	花珂
	张梦琪
	戴锦华
	寇宏超
44.8K

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https://www.ams.org.cn/CN/10.11900/0412.1961.2021.00352 或 https://www.ams.org.cn/CN/Y2021/V57/I11/1438

图1 亚稳β钛合金室温变形机制演化示意图 [12~14](a) deformation induced martensite transformation/mechanical twinning[12](b) multimodal mechanical twinning[13] (c) dislocation slip[14]

图2 bcc金属材料中螺位错结构与形态特征分析[14,21,22](a) differential displacement map illustrating the core structure of screw dislocations in bcc metals[21](b) in-situ TEM observation of the screw dislocations during the straining of Ti-23Nb-0.7Ta-2Zr-0.4Si alloy (t—framing time. The imaging condition was indicated by the g vector and Burgers vector b, of dislocations. Dislocations with different morphological features were highlighted by A and B, respectively)[22](c) dislocation dipoles in deformed microstructure of Ti-11.4Al-11.7Mo-1.9VSi alloy (A diffraction pattern along<11ˉ0> zone axis was inserted to ease the identification of Burgers vector of observed dislocations)[14]

图3 亚稳β钛合金中细密α相多层级组织特征[30,31](a) EBSD map illustrating the microstructure of Ti-5553 alloy containing all Burgers orientation relationship (BOR) α variants(b) pole figures of β matrix and α variants in Fig.3a(c) TEM micrograph presenting ternary α variants indicated by white, red, and blue, respectively (The image was conducted along <111> zone axis with varied g vector selected for dark field (DF) condition as shown in the inserted diffraction pattern)(d) pyramidal arrangement of α vriants[30](e) DF TEM image of microstructure containing dense α precipitates (This micrograph was obtained using a/2 <112> spot highlighted in the corresponding diffraction pattern along <11ˉ0> zone axis. A square area of 1 μm2 was inserted to ease the quantitative investigation on the density of nano-precipitates)[31]

图4 β基体滑移切过不同α变体的影响因素分析[35](a) a deformed micropillar with a high geometrical compatibility factor regarding to the slip systems in β matrix and α variant(b) an equivalent investigation on the micropillar having an intermediate m' between the slip systems in β matrix and α variant

图5 Ti-7333合金在等温热压缩变形过程中晶界α相的析出行为[67](a) SEM image of Ti-7333 alloy after hot deformation (b) high magnified image of the area in Fig.6a(c) strain distribution map and corresponding high magnified map of Ti-7333 alloy after hot deformation (LD—loading direction. The color of the ruler represents the strain of each point relative to the base point)(d) strain-stress curve of the Ti-7333 alloy after hot deformation (E—elastic modulus)

图6 Ti-7333合金热变形后显示的晶界处的位错塞积[67]

图7 Ti-55531合金热变形过程中的微观组织演化[63](a) non deformed (b) 0.2 of strain at 0.01 s-1 (c) 0.7 of strain at 0.01 s-1 (d) 0.7 of strain at 1 s-1

图8 Ti-5553合金在两相区高温区间和低温区间热压缩变形过程中显微组织演变示意图[83,85]

图9 Ti-5553合金EBSD像及α/β偏离BOR角度计算[83](a) heat treated at 800oC for 40 min(b) hot compressed at 800oC to strain of 1.2 under a strain rate of 0.0005 s-1 (CD—compression direction, RD1—radial direction 1, RD2—radial direction 2)

图10 热机械过程的不同阶段和对应微观组织演变及其示意图[94]

图11 热力耦合作用下Ti-5553合金DRV/DRX和相变过程竞争机制及相转变曲线(TTT)示意图[99]

图12 基于集成计算的钛合金组织调控技术路线图

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