Formation Mechanism of $\{10\bar{1}2\}$ Twins and Selection Rule of Martensitic Variants During Tensile Deformation in TC4 Titanium Alloy Laser Surface Remelting Layer

doi:10.11900/0412.1961.2024.00286

Acta Metall Sin

2026, Vol. 62

Issue (9): 1517-1527 DOI: 10.11900/0412.1961.2024.00286

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Formation Mechanism of $\{10\bar{1}2\}$ Twins and Selection Rule of Martensitic Variants During Tensile Deformation in TC4 Titanium Alloy Laser Surface Remelting Layer

YANG Pengfei¹(

), SUN Lei¹, SUN Qi², YANG Zhiyuan³, ZHAO Yuan¹, GAO Ying¹, ZHANG Jiazhen⁴

1 College of Engineering, Zhejiang Normal University, Jinhua 321004, China
2 Key Laboratory of Advanced Technologies of Materials (Ministry of Education), School of Materials Science and Engineering, Southwest Jiaotong University, Chengdu 610036, China
3 Sinoma Advanced Nitride Ceramics Co. Ltd., Zibo 255000, China
4 Beijing Aeronautical Science and Technology Research Institute of COMAC, Beijing 102200, China

Cite this article:

YANG Pengfei, SUN Lei, SUN Qi, YANG Zhiyuan, ZHAO Yuan, GAO Ying, ZHANG Jiazhen. Formation Mechanism of $\{10\bar{1}2\}$ Twins and Selection Rule of Martensitic Variants During Tensile Deformation in TC4 Titanium Alloy Laser Surface Remelting Layer. Acta Metall Sin, 2026, 62(9): 1517-1527.

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Abstract

Laser surface remelting (LSR) technology significantly enhances the mechanical properties of the TC4 titanium alloy. A comprehensive investigation into the microstructural evolution of TC4 alloy during LSR and its effects on subsequent tensile deformation mechanism is essential for optimizing LSR. In this study, LSR treatment was applied to both the front and back of full martensitic TC4 specimens, followed by tensile testing. TEM and EBSD were used to analyze the microstructural evolution during tensile deformation, focusing on the formation and distribution characteristics of ${10 1 ¯ 2}$ twins. The results show that rapid cooling during LSR induces significant residual stress. This in turn not only promotes the preferential formation of specific martensite variants but also lowers the critical shear stress required for twinning. In addition, the evaporation of aluminum during laser treatment decreases the c / a ratio of the TC4 alloy, weakens the anisotropy of the crystal lattice, and further promotes the formation of ${10 1 ¯ 2}$ twins. These twins are primarily concentrated in several martensite variants with specific orientations, exhibiting a clear tendency for preferential formation under rapid cooling conditions.

Key words: TC4 titanium alloy laser surface remelting heterostructure

{10 1 ˉ 2}

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{10 1 ˉ 2}

twin full martensite

Received: 19 August 2024

ZTFLH:

TG178

Fund: National Natural Science Foundation of China(52475219);Fundamental Research Funds for the Central Universities(2682023ZTPY006);Fundamental Research Funds for the Central Universities(2682024GF00);Natural Science Foundation of Sichuan Province(2023NSFSC0411)

Corresponding Authors: YANG Pengfei, Tel: 15608083713, E-mail: yangpf@zjnu.edu.cn

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	YANG Pengfei
	SUN Lei
	SUN Qi
	YANG Zhiyuan
	ZHAO Yuan
	GAO Ying
	ZHANG Jiazhen

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https://www.ams.org.cn/EN/10.11900/0412.1961.2024.00286 OR https://www.ams.org.cn/EN/Y2026/V62/I9/1517

Fig.1 All-Euler-angle image (a) and inverse pole figure (IPF) (b) of laser remelted layer close to fracture surface of the WQ-LSR sample (RD—rolling direction, TD—transverse direction, ND—normal direction, WQ—water quenching, LSR—laser surface remelting)

Fig.2 TEM image of the { $10 1 ¯ 2$ } twin on the fracture surface of the WQ-LSR sample and corresponding SAED patterns (Inset shows the orientation of the hexagonal prism corresponds to matrix A, and the highlighted plane represents the { $10 1 ¯ 2$ } twin plane. EB—electron beam)

Fig.3 EBSD orientation analyses of tensile fracture surface of WQ-LSR sample
(a) EBSD orientation maps
(b) grain boundary maps corresponding to Fig.3a
(c) crystal orientation maps of twins and the matrix corresponding to Fig.3a

Matrix orientation in Euler angle / (°)	Twin type	Twin orientation in Euler angle / (°)	Twin variant
(93.7, 91.4, 45.0)	T1	(9.2, 74.2, 55.8)	( $1 ¯ 102$ )[ $1 1 ¯ 01$ ]
	T2	(178.6, 105.1, 0.0)	( $1 1 ¯ 02$ )[ $1 ¯ 101$ ]
	T4	(9.8, 134.9, 3.4)	( $1 ¯ 012$ )[ $10 1 ¯ 1$ ]
	T5	(168.5,164.6, 45.7)	( $0 1 ¯ 12$ )[ $01 1 ¯ 1$ ]
	T6	(32.7, 16.0, 30.6)	( $01 1 ¯ 2$ )[ $0 1 ¯ 11$ ]

Table 1 Analyses of twin variants in Fig.3a

Fig.4 Schmid factor (SF) distribution images and corresponding statistical histograms (insets) of prismatic slip (a) and basal slip (b) in WQ-LSR sample

Fig.5 SF distribution images and statistical histograms (insets) of prismatic slip (a) and basal slip (b) in WQ sample

Table 2 STEM-EDS elemental analyses of WQ and WQ-LSR samples

Variant	Plane parallel	Direction parallel	Rotation angle/axis from V1
V1	$1 1 ¯ 0 β / / 0001 α$	$111 β / / 11 2 ¯ 0 α$	-
V2	$1 1 ¯ 0 β / / 0001 α$	$11 1 ¯ β / / 11 2 ¯ 0 α$	$10.53 ° / 0001$
V3	$110 β / / 0001 α$	$1 1 ¯ 1 β / / 11 2 ¯ 0 α$	$90 ° / 1 2.38 ¯ 1.38 0$
V4	$110 β / / 0001 α$	$1 ¯ 11 β / / 11 2 ¯ 0 α$	$90 ° / 1 2.38 ¯ 1.38 0$
V5	$10 1 ¯ β / / 0001 α$	$1 1 ¯ 1 β / / 11 2 ¯ 0 α$	$60.83 ° / 1.377 ¯ 1 2.377 0.359$
V6	$10 1 ¯ β / / 0001 α$	$111 β / / 11 2 ¯ 0 α$	$60 ° / 11 2 ¯ 0$
V7	$01 1 ¯ β / / 0001 α$	$1 ¯ 11 β / / 11 2 ¯ 0 α$	$60.83 ° / 1.377 ¯ 1 2.377 0.359$
V8	$01 1 ¯ β / / 0001 α$	$111 β / / 11 2 ¯ 0 α$	$60 ° / 11 2 ¯ 0$
V9	$011 β / / 0001 α$	$1 1 ¯ 1 β / / 11 2 ¯ 0 α$	$63.26 ° / 10 ¯ 5 5 3 ¯$
V10	$011 β / / 0001 α$	$11 1 ¯ β / / 11 2 ¯ 0 α$	$60.83 ° / 1.377 ¯ 1 2.377 0.359$
V11	$101 β / / 0001 α$	$1 ¯ 11 β / / 11 2 ¯ 0 α$	$63.26 ° / 10 ¯ 5 5 3 ¯$
V12	$101 β / / 0001 α$	$11 1 ¯ β / / 11 2 ¯ 0 α$	$60.83 ° / 1.377 ¯ 1 2.377 0.359$

Table 3 Twelve α variants in TC4 titanium alloy resulting from the β→α phase transition calculated by Burgers orientation relationship^[9,23,24]

Fig.6 Prior β grains and α variant orientations reconstructed from WQ (a) and WQ-LSR (b) samples

Table 4 Euler angles and area fractions of the prior β grain and twelve α variants in WQ and WQ-LSR samples

Fig.7 Misorientation histograms of WQ (a) and WQ-LSR (b) samples

Table 5 α/α grain boundary length fractions of variants in WQ and WQ-LSR samples

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