Effect of Process Parameters on Microstructure and Mechanical Properties of Hot Isostatic Pressing Powder Ti2AlNb Alloy

doi:10.11901/1005.3093.2025.365

Chinese Journal of Materials Research

2026, Vol. 40

Issue (9): 653-664 DOI: 10.11901/1005.3093.2025.365

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Effect of Process Parameters on Microstructure and Mechanical Properties of Hot Isostatic Pressing Powder Ti₂AlNb Alloy

LI Bingbing¹^,², XU Lei², YIN Yifeng¹^,², TIAN Xiaosheng², LU Zhengguan², WU Jie²(

)

^1.School of Materials Science and Engineering, University of Science and Technology of China, Shenyang 110016, China
^2.Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China

Cite this article:

LI Bingbing, XU Lei, YIN Yifeng, TIAN Xiaosheng, LU Zhengguan, WU Jie. Effect of Process Parameters on Microstructure and Mechanical Properties of Hot Isostatic Pressing Powder Ti₂AlNb Alloy. Chinese Journal of Materials Research, 2026, 40(9): 653-664.

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Abstract

To address the performance inconsistency in hot isostatic pressing powder Ti₂AlNb alloys, herein, the influence of processing parameters on the performance of the HIP powder Ti₂AlNb alloys was clarified so that to achieve the process optimization. First, the clean powder pre-alloyed Ti₂AlNb was prepared by electrode induction melting gas atomization (EIGA) technique. The acquired powder exhibited excellent sphericity, low oxygen content (0.072%), and a microstructure predominantly composed of metastable B2 phase. Then the effect of hot isostatic pressing (HIP) parameters (temperature and holding time) and a secondary HIP treatment on the microstructural evolution and mechanical properties of HIP powder Ti₂AlNb alloy was investigated, aiming to precisely control over the B2/O/α₂ three-phase microstructure. The results indicate that with the increasing HIP temperature from 1030 ^oC to 1050 ^oC, the volume fraction of B2-phase increases from 26.8% to 31.2% in the consolidated alloy, which was accompanied by a rise in room-temperature tensile strength to 1168 MPa and an improvement in elongation at 650 ^oC to 11.2%. With the prolonging HIP holding time from 3 h to 5 h, the fraction of α₂-phase reduced to 12.0% and the standard deviation of room-temperature elongation decreased from ±2.7% to ±1.2%, significantly enhancing the consistency of mechanical properties. The secondary HIP effectively promoted the preferential nucleation and precipitation of O-phase at α₂/B2-phase boundaries, resulting in α₂ -phase microstructure with a broadened unimodal size distribution. TEM analysis revealed the specific crystallographic orientation relationships between the O-phase and parent phases: [ $2 1 ¯ 1 ¯ 0$ ] $α 2$ //[ $1 ¯ 1 ¯ 0$ ]_O and [ $111$ ]_B2//[ $1 ¯ 1 ¯ 0$ ]_O, confirming that the O-phase can form via two distinct precipitation pathways. This study elucidates the mechanisms by which HIP process parameters influence the microstructure evolution of the Ti₂AlNb alloy, providing meaningful reference for the fabrication of high-performance Ti₂AlNb alloy components.

Key words: metallic materials powder metallurgy Ti₂AlNb alloy hot isostatic pressing microstructure

Received: 08 December 2025

ZTFLH:

TG146.2

Fund: Advanced Materials-National Science and Technology Major Projects(2025ZD0610602);Key Deployment Project of Chinese Academy of Sciences(KGFZD-145-25-26);Key Deployment Project of Chinese Academy of Sciences(RCJJ-145-24-39);CAS Project for Young Scientists in Basic Research(YSBR-025);Science and Technology Major Project of Liaoning Province(2024JH1/11700027)

Corresponding Authors: WU Jie, Tel: (024)83978073, E-mail: jwu10s@imr.ac.cn

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	LI Bingbing
	XU Lei
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	LU Zhengguan
	WU Jie

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https://www.cjmr.org/EN/10.11901/1005.3093.2025.365 OR https://www.cjmr.org/EN/Y2026/V40/I9/653

Table 1 Impurity content of Ti₂AlNb pre-alloyed powder and compacts (mass fraction, %)

Fig.1 Ti₂AlNb pre-alloyed powders (a) particle size distribution and surface morphology, (b) micro-CT graph, (c) EBSD, (d) EPMA

Fig.2 DSC curve of Ti₂AlNb pre-alloyed powder

Process	Temperature	Pressure	Holding time	Cooling method
HIP1	1010 ^oC/1 h $3 o C / m i n$ 1030 ^oC	140-150 MPa	3 h	Furnace cooling
HIP2	1010 ^oC/1 h $3 o C / m i n$ 1050 ^oC	140-150 MPa	3 h	Furnace cooling
HIP3	1010 ^oC/1 h $3 o C / m i n$ 1030 ^oC	140-150 MPa	5 h	Furnace cooling
Secondary HIP	930 ^oC/2 h $3 o C / m i n$ 1010 ^oC	140-150 MPa	1 h	Controlled cooling

Table 2 HIP parameters of powder metallurgy Ti₂AlNb alloy

Fig.3 HIP processing routes

Fig.4 Microstructures of the Ti₂AlNb alloy under HIP1 (a, b) and HIP2 (c, d) conditions

Fig.5 Phase composition and grain size of Ti₂AlNb alloy under different HIP conditions (a, b) EBSD phase maps and phase fractions for HIP1 (a) and HIP2 (b) condition, (c, d) grain size distribution for O phase (c) and α₂ phase (d)

Fig.6 Microstructure and grain statistics of Ti₂AlNb alloy under HIP3 (a) EBSD phase map, (b, c) grain size distribution for O phase (b) and α₂phase (c)

Table 3 Tensile properties of Ti₂AlNb alloy under various HIP parameters

Process	τ / h						$τ ¯$ / h
Before secondary HIP	43.98	48.20	48.20	49.59	58.58	69.13	52.95
After secondary HIP	42.18	49.95	65.13	66.98	68.58	70.65	60.58

Table 4 Creep rupture life of Ti₂AlNb alloy before and after secondary HIP treatment

Fig.7 Microstructure and corresponding grain size distribution of Ti₂AlNb alloy under secondary HIP (a) EBSD phase map, (b, c) grain size distribution for O phase (b) and α₂ phase (c)

Fig.8 TEM images of Ti₂AlNb alloy before (a) and after (b, c) re-HIP treatment

Fig.9 Tensile properties of Ti₂AlNb alloys before and after re-HIP (a) room temperature, (b) 650 ^oC

Fig.10 Schematic diagram showing microstructural evolution of Ti₂AlNb alloy with various HIP conditions

Fig.11 Ti₂AlNb components prepared from powder metallurgy route (a) unshrouded impeller, (b) impeller bladed disk, (c) rectangular ring

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