Interfacial Features of Stainless Steel/Titanium Alloy Multi-metal Fabricated by Laser Additive Manufacturing

doi:10.1007/s40195-022-01384-9

Abstract

Abstract:

Laser additive manufacturing (LAM) is promising for fabricating multi-metallic component, but the mechanism of microstructural evolution at the interface of two metals is still needed to research further. In this study, a 316L stainless steel/Ti6Al4V alloy multi-metal was fabricated by LAM, and the mechanism of intermetallic phase transformation was deeply investigated. Results show that a strong reaction zone (SRZ) can be induced at the interface of the multi-metal. The phase constituents at the SRZ vary from χ (Ti₅Fe₁₇Cr₅) + Fe₂Ti + α′-Ti + β-Ti or FeTi to Fe₂Ti + χ when the laser power is increased. When the scanning speed is further decreased, the thickness of the SRZ is significantly increased, and α′-Ti phase is also formed at this region besides Fe₂Ti and χ phases. Moreover, the micro-hardness at the SRZ is increased, caused by the intermetallic phase transformation and elemental interdiffusion at the interface.

Key words: Laser additive manufacturing, Stainless steel/titanium alloy, Multi-metal, Intermetallic phase, Microstructural evolution

Jialin Yang, Xing Li, Hanbo Yao, Yingchun Guan. Interfacial Features of Stainless Steel/Titanium Alloy Multi-metal Fabricated by Laser Additive Manufacturing[J]. Acta Metallurgica Sinica (English Letters), 2022, 35(8): 1357-1364.

Figures/Tables 8

Fig. 1 Schematic of the LAM process for fabricating the 316L stainless steel/Ti6Al4V alloy multi-metal a, scanning path during LAM b, fabricated sample c

Fig. 2 SEM images along with EDS mapping at the interfaces of a Sample 1, b Sample 2, c Sample 3

Fig. 3 Regions for EDS analysis of a Sample 1, b Sample 2, c Sample 3

Table 1 EDS results at regions highlighted in the SEM images of the three samples

Points	Chemical compositions (at%)						Possible phase
Points	Fe	Cr	Ni	Ti	Al	V	Possible phase
1A	30.3	4.28	2.2	54.64	6.36	.22	β-Ti + FeTi
1B	66.33	19.88	6.06	6.08	0.63	1.02	χ
1C	82.89	10.2	5.0	0.29	0.02	0	γ-Fe
2A	33.7	3.92	1.79	54.77	4.22	1.6	β-Ti + FeTi
2B	55.76	8.58	2.77	28.95	2.43	1.5	Fe₂Ti
2C	56.46	23.58	5.01	12.82	1.41	0.72	χ
2D	78.95	10.29	4.23	5.25	0.99	0.29	γ-Fe
3A	35.96	9.25	2.82	40.39	5.12	2.46	β-Ti + FeTi
3B	53.72	6.73	3.73	31.51	2.66	1.65	Fe₂Ti
3C	67.04	20.37	6.2	5.26	2.17	0.96	χ
3D	77.6	9.12	4.01	7.09	1.35	0.83	γ-Fe

Fig. 4 XRD patterns at the local region of the interfaces

Fig. 5 EBSD micrographs showing phase composition at the interfaces: a-c phase maps, d-f orientation imaging maps. (In phase maps, blue region denotes β-Ti and FeTi, green region denotes Fe2Ti, yellow region denotes α′-Ti, red region denotes γ-Fe, white region denotes unidentified phase)

Fig. 6 Schematic diagram of the multi-metal during LAM process: a fluid flow in the melting pool, b-d interfacial elemental distribution, e-g interfacial phase transformation

Fig. 7 Micro-hardness distribution along vertical direction of the interfaces

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