Selective Laser Melting of In Situ TiB/Ti6Al4V Composites: Formability, Microstructure Evolution and Mechanical Performance

doi:10.1007/s40195-020-01021-3

摘要/Abstract

Abstract:

In the present study, a series of in situ TiB/Ti6Al4V composites were fabricated using selective laser melting. The formability, microstructure evolution and mechanical properties of the as-built samples added with different contents of TiB₂ were studied. It is found that the densification level is related to both the content of TiB₂ and laser energy density. The added TiB₂ reinforcement particle can spontaneously react with titanium and then form the TiB phase. The needle-like TiB phase tends to transform into dot-like particles with the decrease in energy density. Additionally, with the increase in TiB₂ content, the TiB phase is coarsened due to the increased nucleation rate and more reactions. The grain morphology is found to largely depend on the translational speed of solid-fluid interface determined by the temperature gradient and cooling rate. Also, the microhardness of the as-built TiB/Ti6Al4V composites is obviously improved. More interestingly, as the energy density increases, the microhardness of the as-built TiB/Ti6Al4V composites firstly increases and then decreases due to the synergy of grain size and different morphologies and distribution of TiB phases. The wear resistance of TiB/Ti6Al4V composites is far superior to that of Ti6Al4V alloy owing to the increased microhardness resulted from the uniform distribution of the hard TiB phase in the matrix.

Key words: Selective laser melting, TiB/Ti6Al4V composites, Energy density, Densification behavior, Microhardness

. [J]. 金属学报英文版, 2020, 33(6): 774-788.

Yue Su, Shun-Cun Luo, Liang Meng, Piao Gao, Ze-Min Wang. Selective Laser Melting of In Situ TiB/Ti6Al4V Composites: Formability, Microstructure Evolution and Mechanical Performance[J]. Acta Metallurgica Sinica (English Letters), 2020, 33(6): 774-788.

图/表 15

Fig.1 SEM micrographs showing the morphologies of a Ti6Al4V powders; b TiB2 powders; c Ti6Al4V + 3 wt% TiB2 powders; d a magnification figure of c

Fig.2 a A process window; b, c surface appearance of the as-built samples

Fig.3 OM and SEM micrographs of cracks in the as-built samples with 3 wt% TiB2 on the longitudinal section at varied energy densities: a, e 156.25 J/mm3; b-d 104.17 J/mm3

Fig.4 SEM micrograph displaying the morphology of side wall of the cracked position

Fig.5 Line graphs showing the variation of density with the content of TiB2 and optical micrographs showing the appearance of pores and cracks at different energy densities

Fig.6 Variation of Gibbs free energy ΔG with temperature

Fig.7 Partial section of the Ti-B binary phase diagram

Fig.8 XRD patterns of the as-built TiB/Ti6Al4V composites with different contents of TiB2

Fig.9 EDS images showing the cross section of the as-built TiB/Ti6Al4V composites

Fig.10 SEM micrographs on the cross and longitudinal sections displaying the morphologies of matrix and TiB needles for the as-built samples at the energy density of 416.67 J/mm3: a, e 1 wt%, cross section; b, f 3 wt%, cross section; c, g 1 wt%, longitudinal section; d, h 3 wt%, longitudinal section

Fig.11 SEM micrographs on the cross section showing the microstructures of the as-built samples with 1 wt% TiB2 and the morphology of TiB phase at varied energy densities: a, e 416.67 J/mm3; b, f 250 J/mm3; c, g 156.25 J/mm3; d, h 104.17 J/mm3

Fig.12 SEM micrographs showing the microstructures of the as-built samples with 1 wt% TiB2 on the longitudinal section at varied energy densities: a 416.67 J/mm3; b 250 J/mm3; c 156.25 J/mm3; d 104.17 J/mm3

Fig.13 Vickers microhardness of the as-built samples with different additions of TiB2 at different energy densities

Fig.14 Variation of friction coefficient with different additions of TiB2

Fig.15 SEM morphologies of the worn surfaces for the as-built samples: a, d Ti6Al4V; b, e 1 wt% TiB/Ti6Al4V; c, f 3 wt% TiB/Ti6Al4V

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