Recrystallization textures of continuous cast AA 3015 alloy: Development of the P orientation {011} 〈566〉
Recrystallization textures of continuous cast AA 3015 alloy: Development of the P orientation {011} 〈566〉
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DOI：
10.1007/s11661-003-0169-y
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发表时间：
2003-09
期刊：
影响因子：
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通讯作者：
Jian-tao Liu;J. Morris
中科院分区：
文献类型：
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作者：
Jian-tao Liu;J. Morris
直冷（DC）铸造铝合金在热机械加工过程中的织构已得到深入研究。[1-6]一般来说，典型的变形织构的特征是从铜取向{112} 111通过S取向{123} 634延伸到黄铜取向{011} 211的纤维。在进一步退火过程中，立方织构会形成立方体织构。 {001} 100 发展并成为主要的再结晶织构成分。然而，连铸（CC）铝合金的再结晶行为与DC合金有很大不同[7-10]，这导致塑性各向异性存在显着差异。[11]因此，研究 CC 合金在退火过程中的再结晶织构是很有意义的。本研究旨在研究 CC AA 3015 合金退火过程中的再结晶织构。具体来说，提出了冷轧压下量和退火温度对再结晶织构演变的影响。这项工作表明，CC AA 3015 合金中，P 取向 {011} 566 是主要的再结晶织构成分，并且伴随着 R-CubeND 取向 {001} 130。CC AA 3105 合金的商业化热轧带（Al-0.5 wt pct Mn-0.5 wt pct Mg-0.4 wt pct） 使用Si-0.7wt%Fe)。收到的热轧带材直接冷轧至厚度减少 70%、80% 和 90%。然后将冷轧样品在350℃、450℃或550℃下退火30分钟，然后进行水淬。用于微观结构检查的样品是在垂直于法线方向（ND）和轧制方向（RD）的平面上切割的。使用偏光光学显微镜检查阳极氧化样品的微观结构。垂直于 RD 和横向 (TD) 的轧制平面的宏观纹理在半厚度位置通过 Schulz 反射法 [12] 在 D/MAX X 射线测角仪上使用 Cu K 辐射进行测量。测量了三个不完整的极图{111}、{200}和{220}，并针对散焦误差和背景强度进行了校正。使用任意定义单元（ADC）方法[13]根据校正的不完整极图计算三维方向分布函数（ODF）。使用配备定向图像显微镜 (OIM) 的扫描电子显微镜 (SEM) 获得垂直于 ND 和 RD 的纵向平面的微观纹理，以反极图 (IPF) 定向图和 ODF 的形式呈现。 SEM 在 20 kV 下运行。用于微观纹理测量的表面经过机械抛光，然后进行电解抛光
The textures of direct chill (DC) cast aluminum alloys during thermomechanical processing have been intensively studied.[1–6] In general, the typical deformation texture is featured by the fiber that extends from the Copper orientation {112} 111 through the S orientation {123} 634 to the Brass orientation {011} 211. During further annealing, the Cube texture {001} 100 develops and becomes the major recrystallization texture component. However, the recrystallization behavior of continuous cast (CC) aluminum alloys is quite different from that of DC alloys,[7–10] which leads to significant differences in plastic anisotropy.[11] It is, therefore, of interest to study the recrystallization textures of CC alloys during annealing. The present study aims to investigate the recrystallization textures of CC AA 3015 alloy during annealing. Specifically, the effects of cold rolling reduction and annealing temperature on the evolution of the recrystallization texture are presented. This work indicates that the P orientation {011} 566 is the dominant recrystallization texture component and that it is accompanied by the R-CubeND orientation {001} 130 in CC AA 3015 alloy.Commercially produced hot bands of CC AA 3105 alloy (Al-0.5 wt pct Mn-0.5 wt pct Mg-0.4 wt pct Si-0.7 wt pct Fe) were used. The as-received hot bands were directly cold rolled to 70, 80, and 90 pct thickness reductions. Cold-rolled samples were than annealed at either 350 C, 450 C, or 550 C for 30 minutes followed by water quenching. Samples for microstructure examination were cut on planes normal to the normal direction (ND) and to the rolling direction (RD). The microstructure of anodized samples was examined using polarized light optical microscopy. Macrotextures of the rolling plane normal to the RD and the transverse direction (TD) were measured at halfthickness position by means of the Schulz reflection method [12] on a D/MAX X-ray goniometer using Cu K radiation. Three incomplete pole figures {111},{200}, and {220} were measured and were corrected for defocusing error and background intensity. Three-dimensional orientation distribution functions (ODFs) were calculated using the arbitrarily defined cell (ADC) method [13] from the corrected incomplete pole figures. Microtextures of the longitudinal plane normal to the ND and RD, presented in the form of inverse pole figure (IPF) orientation maps and ODFs, were obtained using a scanning electron microscope (SEM) equipped with orientation image microscopy (OIM). The SEM was operated at 20 kV. The surfaces for microtexture measurements had been mechanically polished followed by electropolish-