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
Cite this article:
LI Jinshan, TANG Bin, FAN Jiangkun, WANG Chuanyun, HUA Ke, ZHANG Mengqi, DAI Jinhua, KOU Hongchao. Deformation Mechanism and Microstructure Control of High Strength Metastable β Titanium Alloy. Acta Metall Sin, 2021, 57(11): 1438-1454.
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.
Fund: National Key Research and Development Program of China(2016YFB0701303);National Natural Science Foundation of China(51801156);Chongqing Natural Science Foundation(cstc2020jcyj-msxmX1056)
About author: FAN Jiangkun, associate professor, Tel: (029)88460294, E-mail: jkfan@nwpu.edu.cn LI Jinshan, professor, Tel: (029)88460294, E-mail: ljsh@nwpu.edu.cn
Fig.1 Schematic diagrams illustrating the evolution of deformation mechanism of metastable β titanium alloys
Fig.2 Characterization of the core structure and morphology of screw dislocations in bcc metallic materials
Fig.3 Microstructural features of hierarchical dense α phase in metastable β titanium alloys
Fig.4 Factors affecting the slip transfer from β matrix to different α variants (The orientation relationship between these two components was represented by the pole figure. Slip traces crossing β matrix and α variant were highlighted in a magnified micrograph inserted. The Schmid factors of slip system in β matrix (SFβ) as well as its counterparts for basal and prismatic slip systems in α variant (SFα), and the corresponding geometrical compatibility factors (m') between different these in-coming and out-going systems, were listed in the table)[35]
Fig.5 Precipitation behavior of grain boundary α phase of Ti-7333 alloy during isothermal compression deformation[67]
Fig.6 Dislocation plugging at grain boundary of Ti-7333 alloy after hot deformation (αGB—α phase at grain boundary)[67]
Fig.7 Microstructure evolutions of Ti-55531 alloy during hot deformation (EBSD orientation maps of Ti-55531 alloy treated at 763oC. Dark grain boundaries correspond to high angle boundary (15°-180°). Subgrain boundaries (less than 15°) are represented with grey lines. The α grains (black) are embedded in the β phase. Compression axis is vertical) [63]
Fig.8 Schematics of the microstructural evolution of Ti-5553 alloy during the hot compression at high (a1-a3)[83] and low (b1, b2)[85] temperatures in α + β region (σ is the applied load)
Fig.9 EBSD micrograph and corresponding angular deviation from the BOR between α and β of Ti-5553[83]
Fig.10 Different stages of the thermomechanical process (T—temperature) (a) and the associated microstructural evolutions with their geometrical simplifications (b) [94]
Fig.11 Schematics of the competition between dynamic recovery/dynamic recrystallization (DRV/DRX) and phase transformation (The two insets are schematic diagrams of phase transformation and DRV/DRX, respectively. Ttrans—transition temperature) (a), and time-temperature-transformation (TTT) curves of Ti-5553 alloy under thermo-mechanical conditions (b)[99]
Fig.12 Technology roadmap of titanium alloy microstructure control based on integrated calculation (HR—high resolution)
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