Strengthening by Controlled Al₆Fe Intermetallic Phase in Al-Fe Based Alloys Additive-Manufactured by Laser Powder Bed Fusion

In recent, laser powder bed fusion (L-PBF) has emerged as one of the most representative metal additive manufacturing techniques capable of producing metallic components by using a scanning laser beam to selectively melt consecutive bedded-powder layers. The L-PBF process enables not only the manufacturing of complex geometrical forms but also the fabrication of Al alloys with superior mechanical properties. The L-PBF manufactured Al–2.5Fe (mass%) binary alloy exhibits a high tensile strength of approximately 300 MPa due to the fine morphology of Al₆Fe metastable phase (orthorhombic, <i>oC</i>24). The strength level slightly decreases after long-term exposure at elevated temperatures, indicating the feasibility of employing lightweight heat-resistant materials. However, increasing Fe alloy content significantly reduces L-PBF processability due to the formation of coarsened Al₁₃Fe₄ stable phase. It is therefore required to stabilize the fine Al₆Fe phase by third alloy elements for further strengthening without a loss of L-PBF processability for Al–Fe alloys. The present study was undertaken to investigate the effect of selected third elements (Mn or Cu) on the microstructure and mechanical properties of the Al–Fe binary alloy additive manufactured by the L-PBF process.<br/>In this study, attempts of L-PBF processing using the gas-atomized Al–2.5Fe–2Mn or Al–2.5Fe–2Cu (mass%) ternary alloy powder with an average particle size of about 20 mm were made. Rectangular alloy samples were fabricated using a metal AM ProX DMP 200 machine (3D Systems, USA) under a wide range of laser scan speed (0.6 ~ 1.4 m/s) and laser power (102 ~ 204 W). The applied laser-scanning hatch distance, powder-bed thickness, and beam focus size were 0.1 mm, 0.03 mm, and ~0.1 mm, respectively. The results of measuring the sample density provided the optimum laser parameter sets for the manufacturing of both alloy samples with high relative densities above 99 %, indicating high L-PBF processability for the Mn or Cu added Al–Fe alloy powders. The L-PBF manufactured samples exhibited microstructure consisting of a number of melt pools in which regions locally melted and rapidly solidified due to scanning laser irradiation. The added Mn element was partitioned into the refined Al₆Fe phase, resulting in the formation of Al₆(Fe, Mn) phase with an orthorhombic structure (<i>oC</i>24). A certain amount of solute Mn (approximately 0.8 mass%) was detected in the a-Al matrix. Numerous nanoscale particles of Al₆(Fe, Mn) phase were homogeneously dispersed in the α-Al matrix, whereas relatively coarsened Al₆(Fe, Mn) phases with a cellular morphology appeared localized along melt-pool boundaries. Similar microstructures containing the Al₂₃CuFe₄ phase (orthorhombic, <i>oC</i>24) were observed in the L-PBF processed Al–2.5Fe–2Cu alloy samples. These results indicate the added third element could stabilize the refined Al₆Fe phase formed in rapid solidification by the L-PBF process. The L-PBF processed Al–2.5Fe–2Mn and Al–2.5Fe–2Cu alloys exhibited higher strength of approximately 360 MPa than the Al–2.5Fe binary alloy and an adequate tensile ductility of approximately 10 % in total elongation at ambient temperature. The high-temperature strength of the L-PBF manufactured ternary alloys will be presented.