|
|
HETEROGENEOUS MICROSTRUCTURE AND TEXTURE EVOLUTION DURING FABRICATION OF Zr-Sn-Nb ZIRCONIUM ALLOY SHEETS |
CHEN Jianwei1, LUAN Baifeng1, CHAI Linjiang1, YU Hongbing1, LIU Qing1,ZHOU Jun2, LI Zhongkui2 |
1.College of Materials Science and Engineering, Chongqing University, Chongqing 400044
2.Northwest Institute for Nonferrous Metal Research, Xi'an 710016 |
|
Cite this article:
CHEN Jianwei, LUAN Baifeng, CHAI Linjiang, YU Hongbing, LIU Qing,ZHOU Jun, LI Zhongkui. HETEROGENEOUS MICROSTRUCTURE AND TEXTURE EVOLUTION DURING FABRICATION OF Zr-Sn-Nb ZIRCONIUM ALLOY SHEETS. Acta Metall Sin, 2012, 48(4): 393-400.
|
Abstract Zirconium alloys are widely used as fuel cladding and structural materials for nuclear reactors due to the low neutron absorption cross-section, good corrosion resistance and acceptable mechanical properties. These properties are greatly dependent on microstructural and textural features, such as grain morphology, grain size, crystallographic texture and distribution of precipitates. It is necessary to understand microstructure and texture evolution during fabrication in order to optimize the manufacturing process and to improve the service performance. In this work, microstructure and texture evolution during fabrication of Zr-Sn-Nb new zirconium alloy sheets are investigated using XRD, SEM-ECC, TEM and EBSD. The results show that the random texture formed by β quenching transforms into tilt basal texture after hot rolling. The basal texture keeps stable during the following fabrication stages. The texture of the rolling sheets is mainly characterized as <1010> direction parallel to rolling direction (<1010>//RD), while the texture of the annealing sheets is <1210> direction parallel to rolling direction (<1210>//RD). The microstructure evolves from a weave Widmansatten structure of β quenching stage to heterogeneous deformation structures associated with hot and cold rolling and then to a fully recrystallized structure after final annealing. The cold rolling sheets present more heterogeneous structures in which the C axes of less deformed grains mostly concentrate in the normal direction. The larger grains in annealed structures mostly belong to the <1210>//RD basal texture while the smaller grains are in the <1010>//RD orientation. The reason for the heterogeneous deformation structures and texture evolution during annealing are discussed according to the deformation and recrystallization mechanisms.
|
Received: 28 December 2011
|
|
Fund: Chongqing Leading Scientist Program;National Natural Science Foundation of China;Fundamental Research Funds for the Central Universities;Fundamental Research Funds for the Central Universities |
[1] Srivastava D, Dey G K, Banerjee S. Metall Mater Trans,1995; A26: 2707[2] Bickel G A, Griffiths M. J Nucl Mater, 2008; 383: 9[3] Krishna K V M, Sahoo S K, Samajdar I, Neogy S, Tewari R,Srivastava D, Dey G K, Das G H, Saibaba N, Banarjee S. J Nucl Mater,2008; 383: 78[4] Vaibhaw K, Rao S V R, Jha S K, Saibaba N, Jayaraj R N. J Nucl Mater, 2008; 383: 71[5] Kumar M K, Vanitha C, Samajdar I, Dey G K, Tewari R, Srivastava D,Banerjee S. J Nucl Mater, 2004; 335: 48[6] Tewari R, Srivastava D, Dey G K, Chakravarty J K, Banerjee S. J Nucl Mater, 2008; 383: 153[7] Li Z K, Zhou L, Zhang J J, Wang W S, Jin Z H. Rare Met Mater Eng, 2004; 33: 1362 (李中奎, 周廉, 张建军, 王文生, 金志浩. 稀有金属材料与工程, 2004; 33: 1362)[8] Woo O T, Tangri K. J Nucl Mater, 1979; 79: 82[9] Jeong Y H, Rheem K S, Choi C S, Kim Y S. J Nucl Sci Technol,1993; 30: 154[10] Sahoo S K, Hiwarkar V D, Samajdar I, Dey G K, Srivastav D, Tiwari R,Banerjee S. Scr Mater, 2007; 56: 963[11] Kumar M K, Vanitha C, Samajdar I, Dey G K, Tewari R, Srivastava D,Banerjee S. Mater Sci Technol, 2006; 22: 331[12] Dewobroto N, Bozzolo N, Barberis P, Wagner F. Mater Sci Forum,2004; 467-470: 453[13] Zhu K Y, Chaubet D, Bacroix B, Brisset F. Acta Mater,2005; 53: 5131[14] Zhu K Y, Bacroix B, Chauveau T, Chaubet D, Castelnau O. Metall Mater Trans, 2009; A40: 2423[15] Bozzolo N, Dewobroto N, Grosdidier T, Barberis P, Wagner F. Mater Sci Forum, 2004; 467-470: 441[16] Gerspach F, Bozzolo N, Wagner F. Scr Mater, 2009; 60: 203[17] Hiwarkar V D, Sahoo SK, Samajdar I, Satpathy A, Krishna K V M, Dey G K, Srivastav D, Tewari R, Banarjee S. J Nucl Mater, 2011; 412: 287[18] Guo X C, Luan B F, Chen J W, Zhou J, Zhang X Y, Li Z K, Liu Q. Rare Met Mater Eng, 2011; 40: 813 (过锡川, 栾佰峰, 陈建伟, 周军, 张喜燕, 李中奎, 刘庆.稀有金属材料与工程, 2011; 40: 813)[19] Jung Y I, Lee M H, Kim H G, Park J Y, Jeong Y H. J Alloys Compd, 2009; 479: 423[20] Kaschner G C, Gray G. Metall Mater Trans, 2000; A31: 1997[21] McCabe R J, Proust G, Cerreta E K, Misra A. Int J Plast,2009; 25: 454[22] Francillette H, Bacroix B, Gasperini M, Bechade J L. Acta Mater,1998; 46: 4131[23] Castelnau O, Francillette H, Bacroix B, Lebensohn R A. J Nucl Mater, 2001; 297: 14[24] Akhtar A. J Nucl Mater, 1973; 47: 79[25] Biget M P, Saada G. J Phys III France, 1995; 5: 1833[26] Yoo M H, Morris J R, Ho K M, Agnew S R. Metall Mater Trans,2002; A33: 813[27] Akhtar A. Metall Mater Trans, 1975; A6: 1217[28] Humphreys F J, Ferry M G. Acta Mater, 1996; 44: 2717[29] Engler O, Hirsch J, Lucke K. Acta Metall Mater,1995; 43: 121[30] Higginson R L, Aindow M, Bate P S. Mater Sci Eng,1997; A225: 9[31] Benum S, Nes E. Acta Mater, 1997; 45: 4593[32] Ibe G, Lucke K. in: Margolin H ed., Recrystallization,Grain Growth and Textures, Ohio, Metals Park: ASM, 1966: 434[33] Wagner F, Bozzolo N, Van Landuyt O, Grosdidier T. Acta Mater,2002; 50: 1245 |
No Suggested Reading articles found! |
|
|
Viewed |
|
|
|
Full text
|
|
|
|
|
Abstract
|
|
|
|
|
Cited |
|
|
|
|
|
Shared |
|
|
|
|
|
Discussed |
|
|
|
|