Evolution of microstructure and texture in Mg-Al-Zn alloys during electron-beam and gas tungsten arc welding

The evolution of microstructure and texture in the Az-series Mg alloys subjected to electron-beam welding and gas tungsten arc welding are examined. Electron-beam welding is demonstrated to be a promising means of welding delicate Mg plates, bars, or tubes with a thickness of up to 50 mm; gas tungsten arc welding is limited to lower-end thin Mg sheets. The grains in the fusion zone (FZ) are nearly equiaxed in shape and similar to8 mum or less in size, due to the rapid cooling rate: The as-welded FZ microhardness and tensile strength are higher than the base metals due to the smaller grain size. The weld efficiency, defined as the postweld microhardness or tensile strength at the mid-FZ region divided by that of the unwelded base metal, is around I 10 to 125 pet for electron-beam welding and 97 to 110 pet for gas tungsten arc welding. There are three main texture components present in the electron-beam-welded (EBW) FZ, i.e., {1011} <1012> (with TD//<1120>), {1121} <1100> (with ND<^> <1120> similar to15 deg), and {1010}<1112> (with WD<^> <1120> similar to30 deg), where TD, ND, and WD are the transverse, normal, and welding directions, respectively. The crystal growth tends to align toward the most closed-packed direction, <1120>. The texture in gas tungsten are welded (GTAW) specimens is more diverse and complicated than the EBW counterparts, due to the limited and shallow FZ and the lower cooling rate. The cooling rates calculated by the three-dimensional (3-D) and two-dimensional (2-D) heat-transfer models are considered to be the lower and upper bounds. The cooling rate increases with decreasing A1 content, increasing weld speed, and increasing distance from the weld top surface. The influences of the FZ location, welding speed, and alloy content on the resulting texture components are rationalized and discussed.