Phase transformation and microstructure control of Ti2AlNb-based alloys: A review

doi:10.1016/j.jmst.2020.11.022

Abstract

Abstract:

In recent years, the Ti₂AlNb-based alloys are selected as potential alloys for elevated temperature applications to replace conventional Ni-based superalloys owing to their good creep resistance and oxidation resistance which are related to the O precipitates. In this paper, the precipitation mechanisms of O phase, phase transformation and microstructure control of Ti₂AlNb-based alloys are reviewed. Ti₂AlNb-based alloys generally consist of B2/β, α₂, and O phase with different morphologies which are derived from the various heat treatment processes, including equiaxed α ₂/O particles, bimodal microstructure, and Widmannstätten B2/β + O structures etc. As a newly developed strengthening phase, O precipitates can be precipitated from the B2/β matrix or α₂ phase directly as well as generated by means of peritectoid reaction of α ₂ phase and bcc matrix. Microstructural control of the Ti₂AlNb-based alloys can be implemented by refining the original B2/β grain size and regulating the O precipitates. Multidirectional isothermal forging (MIF) and powder metallurgy technique are two effective methods to refine the original B2/β grains and the morphology and size of O precipitates can be regulated by adding alloying components and pre-deformation process. Moreover, the phase diagram as well as coarsening behavior of Ti₂AlNb-based alloys in ageing process is also reviewed. For the further application of these alloys, more emphasis should be paid on the deep interpolation of microstructure-property relationship and the adoption of advanced manufacturing technology.

Key words: Ti₂AlNb-based alloys, Microstructure, O precipitates, Deformation

Hongyu Zhang, Na Yan, Hongyan Liang, Yongchang Liu. Phase transformation and microstructure control of Ti₂AlNb-based alloys: A review[J]. J. Mater. Sci. Technol., 2021, 80: 203-216.

Figures/Tables 17

Fig. 1. The (a) 1300 °C, and (b) 1400 °C isothermal sections of Ti-Al-Nb ternary system calculated from Witusiewicz [ 23] and Cupid [24] and the tie-triangle identified in Xu’s work [25].

Fig. 2. Vertical section of the Ti-Al-Nb phase diagram at 22 at.% Al, adapted from Refs. [6,34].

Table 1 Lattice parameters in the Ti2AlNb-based alloys [40,46,47].

Phase	Structure	Space group	Lattice constant (nm)
Phase	Structure	Space group	a	b	c
α₂	hcp	P6₃/mmc	0.576	-	0.466
β	bcc	$\text{Im}\bar{3}\text{m}$	0.331	-	-
B₂	bcc	$\text{Pm}\bar{3}\text{m}$	0.322	-	-
B₂	hcp	P6₃/mmc	0.458	-	0.552
O₁	O	Cmcm	0.609	0.957	0.467
O₂	O	Cmcm	0.609	0.957	0.467

Fig. 3. The crystallographic prototype structure of (a) α 2 phase (Ti3Al), and (b) completely ordered O precipitate (Ti2AlNb), revealing an ordered orthorhombic Cmcm crystal structure. Crystal structure data is adapted from Refs. [40,48,49].

Fig. 4. The structures of the Ti3Al, O1, O2 and B2 phases in the [0001], [001] and [110] projections, respectively, adapted from Ref. [42].

Fig. 5. TEM micrographs showing different precipitation modes of the O phase in the Ti3Al-Nb alloy in the condition of 1000 °C, 1 h/WQ +650 °C, 24 h/ air cooling: (a) two variants of acicular O in the primary α 2 phase; (b) fine α 2 + O mixtures, adapted from Ref. [52].

Fig. 6. Schematic of phase transformation from α 2 to O.

Fig. 7. The typical microstructures of a Ti2AlNb-based alloy: (a) equiaxed, (b) bimodal, (c) lamellar, and (d) lamellar with coarse secondary O-laths and thick grain-boundary α 2 phase.

Fig. 8. The typical microstructures of a pre-deformed Ti2AlNb-based alloy aged at (a) 910 °C, (b) 930 °C, (c) 950 °C, and (d) 970 °C for 2 h, adapted from Ref. [ 69].

Fig. 9. Schematic of multidirectional isothermal forging (loading direction is vertical), adapted from Ref. [81].

Fig. 10. The microstructure of the as-received Ti2AlNb-based alloy, revealing a Widmannstätten O + B2 structures.

Fig. 11. Comparisons of (a) phase content, (b) width of acicular O precipitates, and (c) micro-hardness of specimens in 950 °C-solution-treated Ti 2AlNb-based alloy aged at different temperatures.

Fig. 12. Microstructures of (a), (c), (e) W-free, and (b), (d), (f) W-modified Ti2AlNb-based alloys under the same heat treatments, adapted from Ref. [93].

Fig. 13. TEM images of the sintered Mo-free Ti2AlNb-based alloy aged at 800 °C for (a) 1 h, (b) 2 h, and (c) 3 h; Mo-modified Ti 2AlNb-based alloy aged at 800 °C for (a) 1 h, (b) 2 h, and (c) 3 h, adapted from Ref. [ 18].

Table 2 Mechanical properties (room temperature) of Ti2AlNb-based alloys.

Materials	Preparation method	Conditions	YS (MPa)	UTS (MPa)	EL (%)	Refs.
Ti-12Al-38Nb	Vacuum arc melting	Pancake forging + pack rolling+650 °C/55 h/WQ	809	869	12.3	[99]
Ti-21Al-22Nb	Vacuum arc melting	Hot rolling	934	1192	13.9	[100]
Ti-22Al-25Nb	HPS	/950 °C/35 MPa/1 h/FC	799	869	3.95	[89]
Ti-22Al-25Nb	HEBM + SPS	Sintering/950 °C/50 MPa/10 min	1092	1105	9.4	[90]
Ti-22Al-27Nb	Plasma arc melting	1150 °C (hot rolling)/1 h/FC (0.1 K/s) +850 °C/33 h/FC	715	945	8.3	[64]
Ti-22Al-24Nb-3Ta	Induction skull melting	Hot rolling + solution treatment in (O + B2) phase region	1100	1110	14	[83]
Ti-25Al-14Nb-2Mo-1Fe	Cold crucible levitation melting	Hot forging + hot rolling+1000 °C/1 h/FC + 800 °C/100 h/AC	705	992	6.3	[101]
Ti-24Al-20Nb-0.5Mo	Non-consumable vacuum arc melting	1160 °C/30 min/FC + 750 °C/24 h	702	785	0.35	[85]

Fig. 14. The typical microstructures of a pre-deformed Ti2AlNb-based alloy aged at 970 °C for various time: (a) 1 h, (b) 6 h, (c) 18 h, and (d) 42 h, adapted from Ref. [ 113].

Fig. 15. The schematic illustration of Ostwald ripening mechanism in Ti2AlNb-based alloy, adapted from Ref. [113].

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Phase transformation and microstructure control of Ti₂AlNb-based alloys: A review

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