Microstructure, Texture, and Mechanical Properties of Ti2AlNb Alloy Sheet

doi:10.11901/1005.3093.2026.125

Chinese Journal of Materials Research

2026, Vol. 40

Issue (8): 583-594 DOI: 10.11901/1005.3093.2026.125

SPECIAL TOPiC: TITANIUM ALLOY

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Microstructure, Texture, and Mechanical Properties of Ti₂AlNb Alloy Sheet

CHEN Yao¹^,², CHEN Zhiyong¹^,²(

), BAI Chunguang¹^,²

^1.School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China
^2.Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

CHEN Yao, CHEN Zhiyong, BAI Chunguang. Microstructure, Texture, and Mechanical Properties of Ti₂AlNb Alloy Sheet. Chinese Journal of Materials Research, 2026, 40(8): 583-594.

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Abstract

The cold rolled commercial Ti-based alloy Ti₂AlNb sheets of 1 mm in thickness were prepared via multiple folding and rolling, and then subjected to solid solution treatment at 960 ^oC, followed by three type aging treatments in two-phase (B2 + α₂) region: 750 ^oC/4 h, 800 ^oC/4 h and 850 ^oC/4 h respectively. Then the effect of heat treatments on their microstructure, texture, and tensile properties was investigated, in terms of verifying the effect of reducing the anisotropy of alloy sheets and revealing the related formation mechanism of the layered texture structure parallel to the sheet surface within the sheet section. The results show that the microstructure of the sheet consists of B2-matrix, O-phase of various morphologies, and a small amount of equiaxed α₂-phase. The {001}<110> rotated cube texture and the {111}<uvw> texture of the B2-phase are alternately distributed along the thickness direction; the α₂-phase exhibits a typical T-type texture; influenced by orientation relationship inheritance, the orientation distribution of the O-phase is characterized by [100]//ND and [001]//TD. This layered structure originates from the inhomogeneous accumulation of shear strain in the surface region and compressive strain in the center during multi-pass rolling. At room temperatures, the solution-treated sheet exhibits pronounced tensile anisotropy, with the transverse direction (TD) tensile strength being significantly higher than that along the rolling direction (RD). The primary reason is that, under loading along TD, the T-type texture of the α₂-phase renders the prismatic <a> slip systems more difficult to activate, and the elongated lath structure along the rolling direction imposes a stronger geometrical barrier to dislocation motion in the TD. Aging heat treatment not only induces the precipitation of finely dispersed secondary acicular O-phase, thereby improving the microstructural homogeneity, but also weakens the direction dependence of prismatic <a> slip by strengthening the R-type texture of the α₂-phase. The synergistic effect of these two mechanisms significantly reduces the tensile anisotropy of the sheet.

Key words: metallic materials heat treatment Ti₂AlNb alloy sheet texture mechanical property anisotropy

Received: 09 February 2026

ZTFLH:

TG146.2

Fund: National Ministries' Fundamental Research Program Project(JCKY2021204A004)

Corresponding Authors: CHEN Zhiyong, Tel: (024)23971586, E-mail: zhiyongchen@imr.ac.cn

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	CHEN Yao
	CHEN Zhiyong
	BAI Chunguang

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https://www.cjmr.org/EN/10.11901/1005.3093.2026.125 OR https://www.cjmr.org/EN/Y2026/V40/I8/583

Fig.1 Schematic diagram of dimensions (mm) (a) and sampling (b)

Fig.2 Microstructures of RD-ND and TD-ND plane of Ti₂AlNb sheets after different heat treatments (a, b) ST, (c, d) AT-750, (e, f) AT-800, (g, h) AT-850, Note that (a, c, e and g) are samples of RD-ND plane, and others are samples of TD-ND plane

Fig.3 Crystal orientation map in the ST sheet (a) IPF-ND map of three phases, (b) B2 phase, (c) O phase, (d) α₂ phase

Fig.4 Pole figure (PF) of different phases of the ST sheet (a) B2 phase, (b) O phase, (c) α₂ phase

Fig.5 PF of various phases in the sheets after aging at 750 ^oC, 800 ^oC and 850 ^oC (a) B2-{100}, (b) O-{100}, (c) α₂-{0001}

Table 1 Room temperature (RT) tensile property of sheets after different heat treatments

Table 2 650 ^oC tensile property of sheets after different heat treatments

Fig.6 Tensile strength at RT and 650 ^oC after different heat treatments (a) RT, (b) 650 ^oC

Fig.7 EBSD data and microstructures of RD-ND plate (a) IPF-ND map, (b) microstructures in the yellow-framed area of Fig.a, (c, d) distributions of SF for {110}<111> and {112}<111>

Fig.8 Schmid factors (SF) distributions of B2 phase under loading along RD and TD (a) {110}<111>, (b) {112}<111>

Fig.9 SF distributions of basal <a> slip and prismatic <a> slip of O phase under loading along RD and TD (a) {001}<100>, (b) {001}<110>, (c) {010}<100>, (d) {110}<1 $1 ¯$ 0>

Fig.10 SF distributions of pyramidal <c + a> slip of O phase under loading along RD and TD (a) {131}<11 $4 ¯$ >, (b) {201}<10 $2 ¯$ >, (c) {221}<10 $2 ¯$ >, (d) {221}<11 $4 ¯$ >

Fig.11 SF distributions of α₂ phase under loading along the RD and TD (a) basal <a> slip, (b) prismatic <a> slip, (c) pyramidal <c + a> slip

Fig.12 Gripped end microstructures of the ST sheet (650 ^oC tensile test) (a) RD-ND plane, (b) TD-ND plane

Aging treatment	Slip system	Direction	Average SF
AT-750	{10 $1 ¯$ 0}<11 $2 ¯$ 0>	RD	0.2923
AT-750		TD	0.2107
AT-800		RD	0.3015
AT-800		TD	0.2182
AT-850		RD	0.2824
AT-850		TD	0.2316

Table 3 Average SF of prismatic <a> slip system of α₂ phase along the RD and TD in sheets after aging treatments

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