Effects of fabrication conditions on the microstructure, pore characteristics and gas retention of pure tungsten prepared by laser powder bed fusion
Introduction
Tungsten (W) has unique physical properties, such as a high melting point (3693 K), high density (19.3 g/cm3 at 298 K) and high thermal conductivity (174 W/mK at 300 K). Furthermore, at high temperatures, W has a low coefficient of thermal expansion and excellent strength [1]. Because of these characteristics, W has been widely utilized in various applications, such as radiation beam collimators for medical instruments [2], filaments for electron beam generation, and crucibles for single crystallization. In particular, in the engineering design of fusion reactors such as ITER and the demonstration power plant (DEMO), W is considered the most promising candidate for plasma-facing materials (PFMs) exposed to high heat loads caused by plasma and neutron irradiation [3]. This is due to the specific advantages of low tritium retention, high sputtering resistance and high recrystallization temperature [2], in addition to the generally favourable thermophysical properties discussed above. W is a brittle, body-centred cubic (bcc) metal with a distinct high brittle-ductile transition temperature [4]. Therefore, powder metallurgy (PM), hot rolling, swaging, and hot isostatic pressing (HIP) are applied in W manufacturing processes. However, even with machining or deformation, it is difficult to create complex structures, such as integrated internal fins for a high-performance heat exchanger, using these conventional methods. For wider application of W materials, it is necessary to establish a new processing method that provides high structural flexibility.
Additive manufacturing (AM) is a layer-by-layer processing technology, otherwise known as 3D printing, based on slice data prepared from 3D computer-aided design (CAD) information. The AM technology can be used to produce complex structures that are difficult to fabricate using conventional processes such as casting, machining, and deformation. Recently, the laser powder bed fusion (LPBF) AM method has attracted attention as a new approach to fabrication of high-density metallic components. The LPBF process involves repeated formation of a melted metal layer by selective laser irradiation and material feeding to a powder bed. This technique allows highly accurate manufacturing of complex parts by laser processing. LPBF has potential as a fabrication method that could improve the design and efficiency of thermal devices requiring high heat exhaust performance. Development of an LPBF processing method for W, which will be subject to severe heat loads in fusion devices, may facilitate the creation of a novel plasma-facing component in the future.
In LPBF, optimization of the laser irradiation conditions and material powder is important to obtain high-density metal parts. Appropriate control of laser irradiation conditions, to suppress the formation of defects inside the material, could enhance the mechanical properties of LPBF parts. Sufficient densification (>99% relative density) has been achieved for several materials including titanium alloys [5], aluminium alloys [6,7], and stainless steels [8,9] using LPBF. There have been several studies on pure W materials fabricated using LPBF [[10], [11], [12], [13], [14], [15], [16], [17], [18], [19], [20]]. Tan et al. prepared pure W with a density of 19.01 g/cm3 (relative density: 98.50%) by LPBF using spherical particles [12]. In addition, Chen et al. applied HIP to pure W prepared by LPBF as a post-fabrication treatment to increase the density (as-fabricated: 96.4 ± 0.3%, after-HIP: 96.7 ± 0.3%) [14]. However, it is still difficult to increase the relative density of W to a level comparable to those of other major materials fabricated using LPBF; greater understanding of the effect of fabrication conditions on density is needed.
Cracking and nanopore formation are the main phenomena inhibiting the densification of pure W prepared by LPBF (LPBF-W). Wang et al. described how nanopores caused by the evaporation of tungsten oxide may promote cracking [19]. These defects can degrade mechanical and thermal properties. To achieve densification of LPBF-W, the formation mechanism of nanopores should be further investigated. One phenomenon related to the generation of pores in LPBF parts is entrapment of the shielding gas [21]. Argon (Ar) gas is commonly used as a shielding gas to protect the powder bed from oxidation during the LPBF process. Since it has very low solubility in metal [22], the Ar becomes trapped in cavities, i.e. in microscopic spherical pores with sizes of the order of micro- to nanometers [21,23]. The presence of Ar inside LPBF parts causes serious problems. For example, during HIP processing of titanium LPBF parts, the pressure inside the pore increases as the pore radius decreases and reaches the order of GPa [23]. Although the high temperature environment under HIP slightly increases the solubility of Ar in the material, the trapped Ar inhibits complete densification. For W in particular, the high melting point and extremely high cooling rate (approximately 5 × 106 K/s) [17] associated with its high thermal conductivity may promote gas trapping. Therefore, the amount and composition of internal gas in LPBF-W should be measured to clarify the mechanism of pore generation. Development of effective methods to reduce gas retention should improve the thermomechanical properties of LPBF materials.
In this study, we investigated the effect of fabrication conditions on the density of LPBF-W prepared using pure W powder. Gas retention in LPBF-W was investigated by both microstructure observation and gas analysis. An effective method for increasing the density of LPBF-W is discussed.
Section snippets
Powder material and LPBF procedures
Pure W bulk materials were fabricated from powder, as shown in Fig. 1. The powder was provided by A.L.M.T. Corporation (Tokyo, Japan). The average diameter of the polyhedral W particles for the LPBF experiment was 26.5 μm and the concentrations of the impurities reported by the powder supplier were 230, <10 and 50 ppm for oxygen, nitrogen and carbon, respectively.
Columns 10 mm in diameter and 5 mm in height were fabricated using an LPBF machine (EOSINT M280; EOS, Krailling, Germany) equipped
Optimization of fabrication conditions for densification
Fig. 3 shows OM images of specimen cross-sections perpendicular to the fabrication direction. The laser irradiation parameters and input energy density (Ed) are shown in the OM images. The Ed will be defined later. In the OM images, the metal bulk is grey and the micropores are black. These OM images were segmented into metal bulk (white) and pores (black) regions to estimate the relative density. It can be clearly seen that the number density and size distribution of pores depend on the laser
Conclusions
To increase the density of LPBF-W, fabrication and heat treatment conditions were optimized through microstructure and gas retention analyses. The following conclusions were derived.
- (1)
The density of LPBF-W depended on the Ed of the laser irradiation applied to the powder layer. The maximum relative density obtained at an Ed of 411 J/mm3 was 98.58 ± 0.25% based on Archimedes' principle, and 99.94 ± 0.03% by the image analysis method. This high density was achieved by minimizing the volume of
Declaration of Competing Interest
The authors declare no conflicts of interest associated with this manuscript.
Acknowledgement
The authors would like to thank A.L.M.T. Corporation for providing the pure tungsten powder used in the experiments. This work was supported in part by JSPS Kakenhi JP20K14451.
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