Rapid Growth of TiNi intermetallic compound within undercooled Ti50Ni50 alloy under electrostatic levitation condition

doi:10.1016/j.jmst.2020.10.064

Abstract

Abstract:

The undercooling dependence of the solidification mechanism was systematically explored by the electrostatic levitation (ESL) facility. During the experiments, the maximum undercooling reached up to 406 K (0.26 T_L) and the growth velocity of the primary TiNi phase was in-situ determined at various undercoolings. At the initial increase of alloy undercooling, the value of growth velocity sluggishly rose followed by a power function. In this case, the primary TiNi phase preferentially developed as the equiaxed dendrite, then the remnant liquid participated as Ti₂Ni and α-Ti phases on the grain boundary. Once the undercooling exceeded the critical value of 350 K, the growth velocity of the primary phase displayed a sharply increase tendency. Meanwhile, the TEM results demonstrated that the precipitation of the intermetallic Ti₂Ni compound was gradually restrained during the rapid solidification and the R-phase existing in the TiNi matrix at large undercooling implied that the martensitic transformation was incomplete.

Key words: Undercooling, Ti-Ni alloy, Solidification, Growth kinetics

P.F. Zou, C.H. Zheng, L. Hu, H.P. Wang. Rapid Growth of TiNi intermetallic compound within undercooled Ti₅₀Ni₅₀ alloy under electrostatic levitation condition[J]. J. Mater. Sci. Technol., 2021, 77: 82-89.

Figures/Tables 8

Fig. 1. Basic phase analyses of Ti50Ni50 alloys with different undercoolings: (a). the part of phase diagram for Ti-Ni system and a simple illustration solidification mechanism of Ti50Ni50 alloy under non-equilibrium condition; (b) XRD patterns versus undercoolings.

Fig. 2. The analyses of solidification kinetics forTi50Ni50 alloy: (a) the typical “temperature-time curve” with different undercoolings; (b) the average cooling rate when the liquid alloy solidify; (c) the recalescence degree (Δ Tr) during recalescence; (d) the growth velocity of the TiNi phase.

Fig. 3. The microstructures of Ti50Ni50 alloy with different undercoolings: (a) master alloy; (b) △ T = 80 K; (c) △ T = 127 K; (d) △ T = 236 K; (e) △ T = 317 K; (f) △ T = 350 K.

Fig. 4. The process of FIB: (a) the Pt is plated in suitable region; (b) the state before the TEM specimen is cut.

Fig. 5. The phase analyses of Ti50Ni50 alloy at △ T = 36 K: (a) the morphology taken from TEM; (b) the distribution of Ni element; (c) the distribution of Ti element; (d) the SAED pattern of TiNi phase; (e) the SAED pattern of Ti2Ni phase; (f) the SAED pattern of Ti phase.

Fig. 6. The phase analyses of Ti50Ni50 alloy at △ T = 317 K: (a) the morphology taken from TEM; (b) the distribution of Ni element; (c) the distribution of Ti element; (d) the SAED pattern of TiNi phase; (e) the SAED pattern of Ti phase.

Table 1. The content of Ti and Ni elements in different phases(At least 5 points were tested for each data).

ΔT(K)	TiNi phase		α-Ti phase		Ti₂Ni phase
ΔT(K)	Ti (%)	Ni (%)	Ti (%)	Ni (%)	Ti (%)	Ni (%)
80	48.52 ± 0.48	51.48 ± 0.48	98.00 ± 0.45	2.00 ± 0.45	66.59 ± 0.52	33.41 ± 0.52
127	46.87 ± 0.62	53.13 ± 0.62	98.34 ± 0.66	1.66 ± 0.66	63.87 ± 0.38	36.13 ± 0.38
317	44.76 ± 0.47	55.24 ± 0.47	95.51 ± 0.42	4.49 ± 0.42
370	43.93 ± 0.49	56.07 ± 0.49	94.24 ± 0.62	5.76 ± 0.62

Fig. 7. The various solidification pathways of Ti50Ni50 alloy: (a) the small undercooling; (b) the middle undercooling; (c) the large undercooling.

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Rapid Growth of TiNi intermetallic compound within undercooled Ti₅₀Ni₅₀ alloy under electrostatic levitation condition

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