Review: Microtextures in Near α and α + β Dual-Phase Titanium Alloys

doi:10.11900/0412.1961.2024.00449

Acta Metall Sin

2026, Vol. 62

Issue (2): 275-288 DOI: 10.11900/0412.1961.2024.00449

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Review: Microtextures in Near α and α + β Dual-Phase Titanium Alloys

ZHAO Zibo¹^,²(

), TAN Haibing³, ZHANG Bohua², LIU Yujing², LIU Jianrong¹, GUO Huiming³, ZENG Weidong⁴, TIAN Wei³(

), WANG Qingjiang¹(

)

1 Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
2 Yuhua Institute of Advanced Material, Baoji Xigong Titanium Alloy Products Co. Ltd., Baoji 721300, China
3 AECC Sichuan Gas Turbine Establishment, Chengdu 610500, China
4 School of Materials Science and Engineering, Northwestern Ploytechnical University, Xi'an 710072, China

Cite this article:

ZHAO Zibo, TAN Haibing, ZHANG Bohua, LIU Yujing, LIU Jianrong, GUO Huiming, ZENG Weidong, TIAN Wei, WANG Qingjiang. Review: Microtextures in Near α and α + β Dual-Phase Titanium Alloys. Acta Metall Sin, 2026, 62(2): 275-288.

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Abstract

Due to their excellent performance, near α and α + β dual-phase titanium alloys are critical materials in aerospace engineering. Enhancing the performance stability of titanium alloy forgings has become a focal point of research in engineering applications. However, the microtextures within these forgings significantly affect key properties such as fatigue resistance, which limits the overall performance of titanium alloy forgings. Recent studies indicate that optimizing the hot working process to improve the crystallographic orientation and microstructure uniformity is an effective means of enhancing alloy performance. This study reviews the origins of microtextures in titanium alloy forgings, their potential negative effects, and the optimization processes involved. Finally, the study presents several research guidelines aimed at improving the microstructural uniformity of titanium alloy forgings.

Key words: titanium alloy crystallographic orientation microtexture uniformity stability

Received: 10 December 2024

ZTFLH:

TG146.2

Fund: National Science and Technology Major Project(J2019-VI-0005-0119)

Corresponding Authors: ZHAO Zibo, professor, Tel: 13664126402, E-mail: zbzhao@imr.ac.cn;
TIAN Wei, professor, Tel: 15802880667, E-mail: tianwei62418@163.com;
WANG Qingjiang, professor, Tel: 13704010136, E-mail: qjwang@imr.ac.cn

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	Articles by authors
	ZHAO Zibo
	TAN Haibing
	ZHANG Bohua
	LIU Yujing
	LIU Jianrong
	GUO Huiming
	ZENG Weidong
	TIAN Wei
	WANG Qingjiang

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00449 OR https://www.ams.org.cn/EN/Y2026/V62/I2/275

Fig.1 Influences of hard-oriented primary α phase within macrozones on dwell-fatigue crack formation in titanium alloys^[14] (a, c) SEM images showing the primary crack nucleation sites (b, d) crystallographic orientations relative to the loading direction in the same region (e) discrete pole figures (PFs) showing crystallographic orientations in locations numbered from 1 to 3 in Figs.1a and c (LD represents loading direction)

Fig.2 Influences of microtexture on tensile strength stability (a) and plasticity after thermal exposure (b) of Ti60 alloy (R_m and A denote the tensile strength and elongation at room temperature, respectively. CV represents coefficient of variation of strength. The multiple data in the figure are taken from forgings with strong and weak microtextures that have undergone the same heat treatment (T_β - 20 ^oC, 2 h, AC + 700 ^oC, 6 h, AC, in which T_β represents β transition temperature, AC represents air cooling)

Fig.3 Effects of primary α phase on variant selection during β→α transformation and its contribution to texture intensity in macrozone^[33] (a, c) inverse pole figures (IPFs) of specimens after compression (960 ^oC, 0.1 s^-1, 30%) and then heat treatments at 980 ^oC (a) and 990 ^oC (c) for 1 h (TD, RD, and CA denotes transverse direction, radial direction, and compression axial direction, respectively) (b, d) IPFs and PFs of microtextured areas from Figs.3a and c (α_p—primary α, α_s—secondary α)

Fig.4 Orientation distribution in different regions after spheroidization of lamellar α phase (The deformation conditions is 970 ^oC, 25%, 0.1 s^-1. Ⅰ—twist zone, Ⅱ—β/β boundary, Ⅲ—α/α boundary, Ⅳ—non-twist zone)

Fig.5 In-grain misorientation axis analysis (IGMA) based on EBSD orientation measurement for α colonies with different orientations in Ti60 alloy^[26,39]
(a) IPF orientation maps(b) {0001} and {11

2 ¯

0} PFs (RD₁ and RD₂ represent radial directions 1 and 2, respectively)(c) IGMA distributions within 1°-5° of the selected A-D grains (The values indicated by the arrows represent the probabilities that the in-grain misorientation axis distributed near the c-axis. pts represent valid data points)

Fig.6 Schematics showing the activation of prismatic <a> slip and induced lattice rotation during thermal compressed deformation^[39]
(a) crystallography of the transformed α and matrix β phases in titanium alloys (a₁-a₃ denote the basal-plane lattice vectors of the hcp α-phase)
(b) schematics showing the variation of crystallographic orientation with the rotation of α lamella

Fig.7 Microstructures and crystallographic orientation evolutions of Ti60 alloy with α lamellae structure during thermal deformation at 900 ^oC (a, c, e) and 980 ^oC (b, d, f) (a, b) SEM images (Insets show enlarged SEM images)^[45] (CD—compression direction) (c, d) IPF orientation maps (Insets show PFs of α texture measured by the XRD method)^[45] (e, f) TEM bright field images^[26,45]

Fig.8 Schematics of the pinning effect of primary α phase on prior β grains during deformation (LAGB—low angle grain boundary, HAGB—high angle grain boundary)
(a) dislocation accumulation(b) formation of sub‑boundaries and grain boundaries(c) grain growth, rotation, and pinning by primary α phase

Fig.9 Evolutions of the α_p/β phase boundary and its effects on microstructure during heat treatment of Ti60 alloy^[26,69] (a1, a2) Burgers orientation relationship (BOR) deviation angle (θ) distributions between α_p grains and the neighboring β grains at 1030 ^oC (a1) and 1040 ^oC (a2) (f_θ_{≤ 10°} denotes the number fraction of θ ≤ 10°)(b) band contrast (BC) map of α_p grains with some special phase boundaries (GB—grain boundary)(c) schematic of β grain boundary (between grains A and B) pinning by an α_p particle (particle C), showing the relevent interfacial energies (γ_AB, γ_AC, and γ_BC denote the interfacial energies of grains A and B, grain A and particle C, and grain B and particle C, respectively)

Fig.10 Microstructure and crystallographic orientation analyses of the TC17 bar after axial and radial compressions (a, b) IPF orientation maps of the deformed microstructure (a) and α_p grains (b) (AD indicates axial direction of the bar)(c) BC map of α_p grains with some special phase boundaries(d, e) interface structures of semi-coherent (d) and non-coherent (e) α_p/β phase boundaries(f) θ distributions ( f_θ_{≥ 15°} denotes the number fraction of θ ≥ 15°)

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