Toughening High Strength Titanium Alloys Through Fine Tuning Phase Composition and Refining Microstructure

doi:10.11900/0412.1961.2021.00353

Acta Metall Sin

2021, Vol. 57

Issue (11): 1455-1470 DOI: 10.11900/0412.1961.2021.00353

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Toughening High Strength Titanium Alloys Through Fine Tuning Phase Composition and Refining Microstructure

YANG Rui(

), MA Yingjie, LEI Jiafeng, HU Qingmiao, HUANG Sensen

Shi -Changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

YANG Rui, MA Yingjie, LEI Jiafeng, HU Qingmiao, HUANG Sensen. Toughening High Strength Titanium Alloys Through Fine Tuning Phase Composition and Refining Microstructure. Acta Metall Sin, 2021, 57(11): 1455-1470.

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Abstract

Titanium alloys are key materials for applications in major engineering areas, such as aerospace and marine equipment. Studies on structural titanium alloys focus on strengthening and toughening the alloys, especially the latter. The mainstream structural titanium alloys comprise both α and β phases. The optimization of the strength and toughness balance relies on the control of the compositions, volume fractions, and morphologies of both phases. In this study, some recent advances along the above line are reviewed, focusing on studies on the composition design, plastic-deformation mechanism, and microstructure tuning. Rational design of the compositions of both phases improved the deformation coordination within the α phase and across the α/β interface, suppressed the precipitation of brittle ω and α₂ phases, and resulted in improved plasticity and toughness through the α-deformation twin and β-deformation-triggered phase transformation. The multiscale microstructure enhanced the strength and toughness of the titanium alloy. Using the abovementioned approaches, a series of titanium alloys with an improved strength-toughness combination were developed and fabricated. Finally, an attempt was made to predict the prospect of technology development in the field of high-strength and high-toughness titanium alloys for various applications.

Key words: titanium alloy strength and toughness phase composition microstructure

Received: 23 August 2021

ZTFLH:

TG146

Fund: National Key Research and Development Program of China(2016YFC0304200);National Natural Science Foundation of China(51871225)

About author: YANG Rui, professor, Tel: (024)23971512, E-mail: ryang@imr.ac.cn

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	Rui YANG
	Yingjie MA
	Jiafeng LEI
	Qingmiao HU
	Sensen HUANG

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https://www.ams.org.cn/EN/10.11900/0412.1961.2021.00353 OR https://www.ams.org.cn/EN/Y2021/V57/I11/1455

Fig.1 Peierls stress (single dislocation critical resolved shear stress, CRSS) τ of Ti-xAl alloys plotted as functions of composition for the relaxed VASP-SQS calculations (a) and mechanical properties of Ti-xAl alloy as functions of Al concentration from experimental measurements (b) (VASP—vienna ab initio simulation package, SQS—special quasirandom structure, $τ a p$ —CRSS of the prismatic <a> slip, $τ a b$ —CRSS of the basal <a> slip)^[7]

Table 1 Young's moduli (E) and shear moduli (G) of α and β phases of Ti64 alloy and two novel titanium alloys developed in the authors' group, calculated by using first principles exact Muffin-Tin orbital method

Fig.2 Transmission electron microscope (TEM) images of the deformed 3 μm micropillar of Ti-10V-2Fe-3Al alloy^[18]

Fig.3 Selected area electron diffraction (SAED) patterns (a, c) and DF TEM images (b, d) of Ti-3Al-5Mo-4.5V alloy of unaged (a, b) and 300^oC aged (c, d) samples

Fig.4 True strain-stress curves (a) and work hardening rate curves (b) of Ti-3Al-5Mo-4.5V specimens under different heat-treatment conditions (750 representing 750^oC, 2 h, water quenching; 750 + 300 representing 750^oC, 2 h, water quenching + 300^oC, 6 h, air cooling; 750 + 500 representing 750^oC, 2 h, water quenching + 500^oC, 6 h, air cooling)

Fig.5 Energy difference (ΔE^ω-β) between ω and β phases of binary Ti-xM (M = Zr, V, Nb, Mo, Cr) alloys vs content of M (x)^[21,22]

Fig.6 3D reconstruction maps and Al cluster morphologies of Ti-8Al (a) and Ti-6Al (c) samples at 16% and 14% (atomic fraction) isosurface, respectively, and the proxigrams across the boundary between the aged matrix and several α₂ precipitates in Ti-8Al (b) and Ti-6Al (d) samples (The dotted vertical lines corresponding to the concentration isosurfaces)^[39]

Fig.7 In-situ tensile load-displacement curves of the Ti-8Al alloy under different heat-treatment conditions (550/24 representing 550^oC, 24 h, air cooling; 550/100 representing 550^oC, 100 h, air cooling; 550/week representing 550^oC, 168 h, air cooling)^[40]

Fig.8 SEM images (left), inverse pole figure (IPF) (middle), and Kernel average misorientation (KAM) (right) with 5° threshold angle of the region near the notch of 168 h aged Ti-8Al specimen at different displacements in in-situ tensile test (The red arrows in Figs.8b and c point to the dislocation slipping, the color bar below the KAM map represents the misorientation with 5° threshold angle)^[40]

Fig.9 Comparison of compositions in the center of primary α (α_p) and β transformation (β_t) between experiments (symbols) and calculations (lines) as a function of α + β solution temperature, where the measurements were made on samples after solution for 30 min and water quenching (The element contents after solution at 970^oC for 16 h are also indicated in the gray rectangle)^[44]

Fig.10 Variation of chemical composition from α_p to β_t after 5 min thermal treatment at 920^oC^[44]

Fig.11 Phase field simulations of alloying element partitioning showing the Al (a) and V (b) element diffusing process and verifying the experimental results, with the arrows pointing the diffusion direction (The red and blue color refers to high and low element contents, respectively)^[44]

Fig.12 Microstructures and Al, V distributions under 920^oC for 2 min (a), 5 min (b), 8 h (c), and 32 h (d) (The α_p grains or β_t is delineated on BSE images and the element distribution pointed by arrows indicate the occurrence of α_p/β_t phase transformation before the elements reach their equilibrium concentration)^[44]

Fig.13 Characterization of deformation twinning in crack tip plastic zone (CTPZ) of Ti64 alloy with Widmannst?tten microstructure^[51]

Fig.14 Tensile true strain-true stress curves and work hardening rate curves of Ti-3Al-5Mo-4.5V alloy at different heat-treatment temperatures (β transus temperature is (860 ± 5)^oC)^[42]

Fig.15 Primary deformation mechanisms of β phase in Ti-3Al-5Mo-4.5V alloy as a function of β phase stability (Points 1, 2, 3, and 4 represent sample heat-treated at 880^oC, 800^oC, 750^oC, and 700^oC, respectively. SIM—stress induced martensite, [Mo]_eq.—Mo equivalent)^[42]

Fig.16 Schematic representation of CTPZ in titanium alloy with Widmannst?tten microstructure, showing expansion of CTPZ range by large-scale slip and deformation twinning (LEFM—linear elastic fracture mechanics)^[71]

Fig.17 Schematic representation of research and development (R&D) of highly alloyed α + β titanium alloys with hierarchical microstructures based on micro-zone optimization for strength-toughness improvement^[39,51,72]

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