Influence of Al+Ti on Microstructure and Mechanical Properties of a Ni-Cr-based Alloy

doi:10.11901/1005.3093.2025.332

Chinese Journal of Materials Research

2026, Vol. 40

Issue (9): 665-676 DOI: 10.11901/1005.3093.2025.332

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Influence of Al+Ti on Microstructure and Mechanical Properties of a Ni-Cr-based Alloy

ZHANG Fengzhi¹^,², WU Yunsheng², GUAN Xianjun², HOU Jieshan²(

), ZHOU Lanzhang²

^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:

ZHANG Fengzhi, WU Yunsheng, GUAN Xianjun, HOU Jieshan, ZHOU Lanzhang. Influence of Al+Ti on Microstructure and Mechanical Properties of a Ni-Cr-based Alloy. Chinese Journal of Materials Research, 2026, 40(9): 665-676.

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Abstract

Two test alloys, based on a low Nb-containing solid solution-strengthened Ni-Cr-based alloy with addition of 0.2Al+0.2Ti or 0.5Al+0.5Ti, were made by vacuum melt-casting, and then subjected to solution treatment at 1200 ^oC for 1 h and water cooling, followed by long-term aging for 10,000 h at 650 ^oC and 700 ^oC respectively. Then the effect of the Al+Ti contents on the microstructure and mechanical properties of the test alloys was investigated through thermodynamic calculations, microstructural characterization, and mechanical testing. Results show that an increase in Al+Ti content reduces the solid-liquid phase transition temperature, narrows the solidification range, and promotes the segregation of Nb and Al elements. After long-term aging treatment, the main second phase is M₂₃C₆ carbides for the 0.2Al+0.2Ti alloy, whereas for the 0.5Al+0.5Ti alloy is mainly γ′-precipitates. With the increasing exposure time, the γ′-phase undergoes significant coarsening, and its morphology transforms from cubic to rounded square. The effect of Al+Ti content on solid solution strengthening is limited, and the strength difference between the two alloys remains insignificant even after aging treatment for 10000 h, although their strengthening mechanisms differ. In the 0.2Al+0.2Ti alloy, the fine and discretely distributed M₂₃C₆ carbides effectively enhance the alloy strength during thermal exposure. In contrast, in the 0.5Al+0.5Ti alloy, the larger γ′-phase turns to split after aging for 10000 h, leading to smaller in particle size while higher in quantity and density, thereby contributing to an increase in strength.

Key words: metallic materials Ni-based alloy Al+Ti content microstructure evolution tensile property

Received: 10 November 2025

ZTFLH:

TG132.32

Fund: National Key Research and Development Program of China(2021YFB3704103)

Corresponding Authors: HOU Jieshan, Tel: (024)83978469, E-mail: jshou@imr.ac.cn

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https://www.cjmr.org/EN/10.11901/1005.3093.2025.332 OR https://www.cjmr.org/EN/Y2026/V40/I9/665

Table 1 Chemical composition of the experimental alloys (mass fraction, %)

Fig.1 Schematic diagram of tensile specimen (unit: mm)

Fig.2 Equilibrium phase diagram of 0.2Al+0.2Ti (a, b) and 0.5Al+0.5Ti (c, d) alloys

Fig.3 SEM microstructures of as-cast 0.2Al+0.2Ti (a, b) and 0.5Al+0.5Ti (c, d) alloys (b) NbC carbide, (d) TiC carbide

Fig.4 Dendrite segregation ratios in 0.2Al+0.2Ti and 0.5Al+0.5Ti alloys

Fig.5 DTA data of the 0.2Al+0.2Ti and 0.5Al+0.5Ti alloys

Fig.6 SEM microstructures of 0.2Al+0.2Ti (a) and 0.5Al+0.5Ti (b-d) alloys after solution treatment

Fig.7 Microstructures of 0.2Al+0.2Ti (a-c) and 0.5Al+0.5Ti (d-f) alloys after thermal exposure at 650 ^oC for 1000 h (a, d), 5000 h (b, e) and 10000 h (c, f)

Fig.8 Microstructures of 0.2Al+0.2Ti (a-c) and 0.5Al+0.5Ti (d-f) alloys after thermal exposure at 700 ^oC for 1000 h (a, d), 5000 h (b, e) and 10000 h (c, f)

Fig.9 HADDF-STEM image and EDS elemental maps of 0.2Al+0.2Ti alloy after thermal exposure at 650 ^oC for 5000 h (a), high resolution image of block-like M₂₃C₆ carbide (b, c) and needle-like M₂₃C₆ carbide (d, e)

Fig.10 HADDF-STEM image and EDS elemental maps of 0.5Al+0.5Ti alloy after thermal exposure at 650 ^oC for 5000 h (a), high resolution image of γ′ phase (b) and M₂₃C₆ carbide (c)

Fig.11 Variations of diameter D (a) and $D t 3 - D 03$ of γ′ precipitates (b) with thermal exposure time t

Fig.12 Phase precipitation behavior at grain boundaries in 0.2Al+0.2Ti (a, b) and 0.5Al+0.5Ti (c, d) alloys after thermal exposure at 700 ^oC for 1000 h (a, c) and 5000 h (b, d)

Fig.13 BF-STEM images and EDS elemental maps of 0.2Al+0.2Ti (a) and 0.5Al+0.5Ti (b) alloys at grain boundaries after thermal exposure at 700 ^oC for 5000 h

Fig.14 Effect of Al+Ti content on tensile properties of solution heat treated alloy at room temperature (a) and 650 ^oC (b)

Fig.15 Effect of Al+Ti content on tensile properties at room temperature after thermal exposure at 650 ^oC (a, b) and 700 ^oC (c, d) for different time

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