Mg-14.61Gd鎂合金的定向凝固組織及生長取向

Mg-14.61Gd鎂合金的定向凝固組織及生長取向Microstructures and Growth Orientation of Directionally Solidification Mg-14.61Gd Mg Alloy

采用EBSD和CAFE方法研究了Mg–14.61Gd合金在G=30 K/mm和 =ν10-200 μm/s條件下的定向凝固組織和生長取向。研究發現，實驗合金縱向凝固組織呈單一方向的α-Mg枝晶生長形貌，隨著ν的增加，枝晶界面生長方式由凸前生長向平齊生長轉變，枝晶間距減小。同時發現，當ν從10 μm/s增至100 μm/s時，α-Mg枝晶的生長取向由<11-20>和<10-10>轉變為<11-20>，其與凝固熱流的偏離角(θ)由11.070°減小至5.711°，熱流是影響生長取向的主導因素；當ν從100 μm/s增至200 μm/s時，α-Mg枝晶的生長取向仍為<11-20>，但θ卻逐漸增大至10.620°，此時，晶體的各向異性占主導。研究表明，CAFE模型可以合理預測定向凝固鎂合金的晶粒組織和生長取向。

Microstructures and growth orientation of directionally solidified Mg–14.61Gd alloy under G=30 K/mm and ν=10-200 μm/s were investigated by EBSD measurement method and CAFE numerical simulation method. It was found that α-Mg primary phase presented unidirectional dendritic morphologies on longitudinal cross-section. The growth interface appearance of α-Mg changed from the protruding forward growth to the flat growth gradually and the dendritic arm spacing decreased gradually with the increasing ν . Meanwhile, when ν increased from 10 μm/s to 100 μm/s, the main growth orientation of α-Mg changed from <11-20> and <10-10> to <11-20>, and the deviation angle (θ) from solidification heat flow direction reduced from 11.070° to 5.711°, the reason for this lied mainly in the change of the heat flux. Further increasing ν up to 200 μm/s, the main growth direction of α-Mg was still in <11-20>, but the value of θ increased to 10.620°, and the anisotropy of the crystal was the dominant factor then. It was proved that the CAFE numerical simulation model could predict the grain structure and growth orientation reasonably for Mg-alloy.

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