Crystallization Behavior of Laser Solid Forming of Annealed Zr55Cu30Al10Ni5 Powder

doi:10.11900/0412.1961.2016.00417

Acta Metall Sin

2017, Vol. 53

Issue (7): 824-832 DOI: 10.11900/0412.1961.2016.00417

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Crystallization Behavior of Laser Solid Forming of Annealed Zr₅₅Cu₃₀Al₁₀Ni₅ Powder

Yuanyuan ZHANG,Xin LIN(

),Lei WEI,Yongming REN

State Key Laboratory of Solidification Processing, Northwestern Polytechnical University, Xi'an 710072, China

Cite this article:

Yuanyuan ZHANG,Xin LIN,Lei WEI,Yongming REN. Crystallization Behavior of Laser Solid Forming of Annealed Zr₅₅Cu₃₀Al₁₀Ni₅ Powder. Acta Metall Sin, 2017, 53(7): 824-832.

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Abstract

Laser solid forming (LSF) provides an innovative way in building the bulk metallic glasses (BMGs) due to its inherently rapid heating and cooling process and point by point additive manufacturing process, which can eliminate the limitation of critical casting size of BMGs. The annealed powder has been demonstrated to be applicable to the preparation of BMGs with high content of amorphous phase using LSF. In this work, the plasma rotating electrode processed (PREPed) Zr₅₅Cu₃₀Al₁₀Ni₅(Zr55) powders annealed at 1000 K are used for LSF of Zr55 BMGs. The influences of powder size and laser processing parameter on the crystallization characteristic of the deposit are investigated, and the crystallization behavior of the remelted zone (RZ) and heat affected zone (HAZ) is analyzed. It is found that the microstructures of the pre-annealed Zr55 powders are composed of the Al₅Ni₃Zr₂, CuZr₂ and Al₂Zr₃phases. As the heat input increases from 7.0 J/mm to 15.7 J/mm, the every deposited layer presents a periodic repeating gradient microstructure (amorphous, NiZr₂ nanocrystal, CuZr₂+ZrCu dendrite-like eutectic, CuZr₂+ZrCu spherulite-like eutectic) from the molten pool to the HAZ. The size of the eutectic phase in the HAZ decreases as the increase of distance from the featureless amorphous zone. On condition that the laser heat input is less than 7.0 J/mm, the deposits contain a high content of amorphous phase. As the increase of laser heat input, the crystallization degree of HAZ does not increase obviously for the deposit prepared by the powder with size range of 75~106 μm. However, the crystallization degree of HAZ increases significantly for the deposit prepared by the powder with size range of 106~150 μm. That is because the lower overheating temperature and shorter existing time of the molten pool enhances the heredity of Al₅Ni₃Zr₂clusters and other intermetallic clusters in remelted alloy melt during LSF of coarser powder, which decreases the thermal stability of the already-deposited layer and induces the severe crystallization. It is deduced that the raw state of annealed powders has a minimal impact on the crystallization behavior of the Zr55 deposited layers when the content of Al₅Ni₃Zr₂ phase is same in different sizes of annealed powders. The thermal history of RZ and HAZ during deposition is the primary factor to affect the crystallization behavior in the Zr55 deposits fabricated by different powder sizes.

Key words: Zr₅₅Cu₃₀Al_l0Ni₅ bulk metallic glass laser solid forming powder state crystallization

Received: 18 September 2016

Fund: Supported by National Natural Science Foundation of China (Nos.51323008, 51271213 and 51475380), National High Technology Research and Development Program of China (No.2013AA031103), National Basic Research Program of China (No.2011CB610402) and Fundamental Research Funds for the Central Universities (No.3102015BJ(II)ZS013)

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	Yuanyuan ZHANG
	Xin LIN
	Lei WEI
	Yongming REN

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https://www.ams.org.cn/EN/10.11900/0412.1961.2016.00417 OR https://www.ams.org.cn/EN/Y2017/V53/I7/824

Table 1 Measured and nominal compositions of the Zr₅₅Cu₃₀Al_l0Ni₅ (Zr55) alloy powder (mass fraction / %)

Table 2 Parameters of laser solid forming (LSF)

Fig.1 SEM-BSE images of original (a, c) and annealed (b, d) Zr55 powders with the size range of 106~150 μm (a, b) and 75~106 μm (c, d) (Inset in Fig.1b shows the enlarged view of faceted phases)

Fig.2 XRD spectra of original and annealed Zr55 powders

Fig.3 Cross-sectional OM images of the LSFed Zr55 deposits prepared by the annealed powders with different sizes(a) specimen 1 (b) specimen 2 (c) specimen 3 (d) specimen 4 (e) specimen 5 (f) specimen 6

Fig.4 XRD spectra of the LSFed specimens 1~6

Fig.5 SEM images of crystalline band between the adjacent tracks in specimen 5 (a) and specimen 6 (b) (Insets show the enlarged views of square areas, the white arrows indicate the directions from RZ to HAZ, RZ—remelted zone, HAZ—heat affected zone)

Fig.6 TEM images and corresponding SAED patterns of dendrite zone (a) and spherulite zone (b) in specimen 3

Fig.7 Simulation results of the thermal field in the deposit during one layer single-track deposition(a, b) temperature distributions for 0.06 s after irradiation with 7.0 J/mm (Points A and B are located at the surface of the molten pool zone, points C and D are located at the top of HAZ, points E and F are at the boundary between the HAZ and already-deposited amorphous zone; T_mis the melting temperature, T_x is the onset crystallization temperature, T_g is the glass transition temperature)(c) continuous heating transformation (CHT)curves for Zr55 bulk metallic glass (BMG) according to thermal cycles at the boundaries (Curves 1~3 denote the temperature profiles during deposited the coarser powder with laser heat input of 7.0, 10.8 and 15.7 J/mm, curves 4~6 denote the temperature profiles during deposited the finer powder with different heat inputs)

Fig.8 Incubation time of CuZr₂ phase and ZrCu phase nucleated from Zr55 melts as function of undercooling (ΔT_c—critical undercooling degree)

Fig.9 Calculated growth rates of lamellar eutectic and dendrites in Zr55 alloy versus undercooling

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