Recent Advances on 3D Printed Bulk Metallic Glasses

doi:10.11900/0412.1961.2020.00450

Acta Metall Sin

2021, Vol. 57

Issue (4): 529-541 DOI: 10.11900/0412.1961.2020.00450

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Recent Advances on 3D Printed Bulk Metallic Glasses

LI Ning(

), HUANG Xin

School of Materials Science and Engineering, Huazhong University of Science and Technology, Wuhan 430074, China

Cite this article:

LI Ning, HUANG Xin. Recent Advances on 3D Printed Bulk Metallic Glasses. Acta Metall Sin, 2021, 57(4): 529-541.

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Abstract

The application of bulk metallic glasses (BMGs) as structural materials not only involves the challenge of room temperature brittleness but also bottlenecks related to formation and manufacturing. Solving these issues has become one of the research hotspots and difficulties in the material field recently. The recently developed 3D printing technology has gradually become one of the key methods to solve the existing difficulties of BMGs to realize their engineering applications. However, because BMGs have a completely different atomic structure than crystalline materials, the basic theories of material microstructure evolution, defect formation and suppression, and performance adjustment in 3D printing are completely different. The in-depth analysis of the abovementioned scientific issues is very important for the development of BMG 3D printing technology. This article is mainly focused on the research trends at home and abroad with a comprehensive analysis of the above problems and looks forward to the development trends of 3D printing technology.

Key words: bulk metallic glass 3D printing microstructure mechanical property

Received: 09 November 2020

ZTFLH:

TG139.8

Fund: National Natural Science Foundation of China(51971097)

About author: LI Ning, professor, Tel: (027)87559606, E-mail: hslining@hust.edu.cn

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https://www.ams.org.cn/EN/10.11900/0412.1961.2020.00450 OR https://www.ams.org.cn/EN/Y2021/V57/I4/529

Fig.1 3D printing techniques of bulk metallic glasses (BMGs)

Table 1 Summaries of the phase features of 3D-printed BMGs with its original feedstocks^{[12,14,16,17,21-55]}

Fig.2 Heating-cooling curves in the MP (P₁), HAZ (P₂) and un-affected zone (P₃) (a) and heating-cooling curves in the different locations of HAZ (b) (MP—molten pool, HAZ—heat affected zone, T_m represents melting temperature, T_g represents glass transition temperature, T_x represents crystallization temperature)^[24]

Fig.3 Microstructures of the Zr₅₅Al₁₀Ni₅Cu₃₀ BMGs by pulsed laser surface melting (PLSM) with one, six, twelve and twenty pulsed laser irradiations (a), microstructures of the deposits with one, two, four and seven layers (b), SEM image of twenty times irradiations (c), and SEM image of seven deposited layers (d)^[48]

Fig.4 Evolutions of crystal bonds during the SLM process at energy densities of 30.8 J/mm³ (a) and 3.8 J/mm³ (b) (t represents time during the SLM process)^[56]

Fig.5 X-ray diffraction patterns of the Zr_52.5Cu_17.9Ni_14.6Al₁₀Ti₅powder, an as-cast rod and SLM samples produced with varying energy densities (a), synchrotron experiments for sample 3D printed under 13 J/mm³ (b), and diffraction patterns wherein no indication of the presence of crystals and the structure is fully amorphous regardless the position (c) (E represents energy density)^[43]

Fig.6 BSE-SEM images of the SLM-fabricated Zr_52.5Ti₅Cu_17.9Ni_14.6Al₁₀ BMGs at different scan speeds and scanning strategies^[33]

Fig.7 TEM micrograph shows the interface between amorphous lamellae and Cu lamellae, the inserts demonstrate the glassy and fcc microstructure (a), HRTEM image of region “B” that contains nanocrystals (b), EDS profiles along line “C” cross the boundary (c), and high-density dislocations formed in the Cu crystals (d)^[26]

Fig.8 Cracking in alloys produced via SLM

Fig.9 Compressive stress-strain curves of the SLM Zr-based BMG rods,as compared with the as-cast one (σ_max—maximum stress)^[22]

Table 2 Mechanical properties of 3D-printed BMGs^{[16,22,23,25,31,33]}

Fig.10 Compressive stress-strain curves of SLM processed specimens by mixing Cu powder (20%, 35% and 50%, mass fraction), CuNi₂₀, and CuNi₃₅powders (50%, mass fraction), respectively (a) and mechanical properties of SLM processed Fe-based BMG composites by tuning the content or category of the second phase (b)^[26]

Fig.11 Fatigue crack-growth testing results for SLM processed Zr_59.3Cu_28.8Nb_1.5Al_10.4 samples^[64] (ΔK represents stress intensity range, ΔK_th represents threshold stress intensity range, ΔK_max represents the maximum stress intensity range)

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