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<p>Ti<sub>2</sub>AlNb pre-alloyed powder was prepared by electrode induction melting gas atomization (EIGA), and powder metallurgy (PM) Ti<sub>2</sub>AlNb alloy was subsequently fabricated through hot isostatic pressing (HIP). This study systematically investigated the phase transformation behavior and microstructural evolution of PM Ti<sub>2</sub>AlNb alloy during controlled cooling from the B2 phase region at rates spanning 0.05-150&#xa0;°C/s. The results demonstrate that both <i>α</i><sub>2</sub> and O phases precipitated simultaneously from the B2 matrix at a low cooling rate of 0.05&#xa0;°C/s. As the cooling rate increases, the amount of precipitated phases decreases, and <i>α</i><sub>2</sub> and O phases are completely suppressed at 1&#xa0;°C/s and 5&#xa0;°C/s, respectively. The constructed continuous cooling transformation (CCT) diagram reveals a narrowing temperature window for the B2 → O phase transition with accelerated cooling. Tensile testing highlights the critical role of phase morphology: Slow-cooled specimens (0.05&#xa0;°C/s) consisting of <i>α</i><sub>2</sub>, O, and B2 phases demonstrate superior ductility at both room temperature (15.7%) and 650&#xa0;°C (18.2%). In contrast, water-quenched samples exhibit room-temperature elongation of 16.3%, which decreases dramatically to 4.2% at 650&#xa0;°C due to incompatible deformation between the B2 matrix and O phase precipitates.</p>

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Continuous Cooling Phase Transformation Behavior of Powder Metallurgy Ti2AlNb Alloy and Its Effects on Microstructure and Mechanical Properties

  • 期刊论文

  • 发表日期：

    2026年2月24日

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  • Yifeng Yin,
  • Lei Xu,
  • Xiaosheng Tian,
  • Bingbing Li,
  • Zhengguan Lu,
  • Jie Wu

摘要

Ti2AlNb pre-alloyed powder was prepared by electrode induction melting gas atomization (EIGA), and powder metallurgy (PM) Ti2AlNb alloy was subsequently fabricated through hot isostatic pressing (HIP). This study systematically investigated the phase transformation behavior and microstructural evolution of PM Ti2AlNb alloy during controlled cooling from the B2 phase region at rates spanning 0.05-150 °C/s. The results demonstrate that both α2 and O phases precipitated simultaneously from the B2 matrix at a low cooling rate of 0.05 °C/s. As the cooling rate increases, the amount of precipitated phases decreases, and α2 and O phases are completely suppressed at 1 °C/s and 5 °C/s, respectively. The constructed continuous cooling transformation (CCT) diagram reveals a narrowing temperature window for the B2 → O phase transition with accelerated cooling. Tensile testing highlights the critical role of phase morphology: Slow-cooled specimens (0.05 °C/s) consisting of α2, O, and B2 phases demonstrate superior ductility at both room temperature (15.7%) and 650 °C (18.2%). In contrast, water-quenched samples exhibit room-temperature elongation of 16.3%, which decreases dramatically to 4.2% at 650 °C due to incompatible deformation between the B2 matrix and O phase precipitates.