Rolling and Recrystallization Textures in the System Copper-Zinc as Function of the Zn-Content

Virnich, K. H.; Lücke, K.

doi:10.1007/978-3-642-81313-9_37

Cited by 6 publications

(3 citation statements)

References 4 publications

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“…However, the volume fraction of the Goss component increased a little at annealing temperatures of 253 and 278 ºC, at variance with expectation. The brass rolling texture {110}<112> of low stacking fault energy (SFE) alloys such as Cu-22% Zn (SFE: 15 mJ m -2 [14]) and Cu-30% Zn alloys (SFE: 14 mJ m -2 [14]) is known to transform into a texture approximated by the {236}<385> orientation after Rex [15][16][17][18][19][20]. The 40º<111> relationship is approximately satisfied between the brass rolling texture and the {236}<385> Rex texture.…”

Section: Thermec 2016mentioning

confidence: 99%

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Lee

2016

MSF

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The evolution of recrystallization texture in commercially pure aluminum sheet cold-rolled by 90% reduction in thickness was measured by Juul Jensen et al. The cold-rolling texture consisted of the Goss {110}<001>, Brass {110}<112>, S {123}<634>, and copper {112}<111> components. When the cold-rolled aluminum sheet was annealed at temperatures between 253 and 341°C for times between 5 min and 20 h., the cube {001}<100> component evolved. The evolution of the cube texture cannot be explained by either the oriented nucleation theory by Burgers and Louwerse or the oriented growth theory by Barrett. The cube texture evolution originates from the Copper component by the strain-energy-release-maximization (SERM) theory by Lee. Once the Cube oriented, dislocation free nuclei evolve, they are in the best position to grow at the expense of neighboring deformed high energy grains of the Goss, Brass, S, and Copper orientations, and the volume fractions of the Goss, Brass, S, and copper components would decrease. However, the volume fraction of the Goss component increased a little at annealing temperatures of 253 and 278°C, at variance with expectation. Low stacking-fault-energy alloys with the brass {110}<112> rolling texture evolve the {236}<385> texture after recrystallization, whereas high stacking-fault-energy alloys with the brass rolling texture evolve the Goss texture after recrystallization by the SERM theory, resulting in the increase of the volume fraction of the Goss texture.

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Section: Thermec 2016mentioning

confidence: 99%

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Lee

2016

MSF

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“…In the case of the FCC metals (structure of our studied material), which have been deformed by unidirectional lamination (method used to obtain the wires), two types of textures are found (the brass type texture and the copper type texture) [1]. The brass texture is characterized by an orientation closer to the ideal component {110} <112> and develops mainly in silver [2] and in alloys such as the brass [3,4].…”

Section: Introductionmentioning

confidence: 99%

Deformation and Recrystallised Texture Evolution and the Followed Mechanical and Electrical Properties of Drawn and Annealed Copper Wires

Baira

Zidani

Farh

et al. 2017

JERA

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Copper destined for electrical cabling require a compromise of mechanical properties and electrical resistivity. The drawing process accompanied by the formation of crystalline defects, such as gaps and dislocations, which leads to the increase in hardness, and therefore to the increase in resistivity, a very important characteristic for the conductivity and the efficiency of the cable. The scope of this work is to investigate the phenomenon of deformation texture evolution while copper wire drawn destined for electric cable-making and to understand its relationship with the electrical conductivity. In this study, we notice that the hardness and the resistivity increase with an increase of the deformation level. On the other hand, a slight decrease in the resistivity of the wires was observed after a holding time of 30 min at 260°C. The annealing of wires at 260°C for 9 min of holding time leads to a recrystallisation especially for high deformations and a gradual return of the mechanical properties and of the microstructure towards a state close to the state of the wire rod with the extension of time . The recrystallization texture is composed of the same components as the drawing texture, fibers <111>//ND (Normal Direction) and <001>//ND. The decrease in the intensity of the fiber after annealing is observed. On the other hand, the fiber <001> // ND remains stable.

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“…The brass rolling texture {110}<112> of low stacking fault energy (SFE) alloys such as Cu-22%Zn (SFE: 15 mJ˖m -2 [1]) and Cu-30%Zn alloys (SFE: 14 mJ˖m -2 [1]) is known to transforms into a texture approximated by the {236}<385> orientation after recrystallization [2][3][4][5][6][7]. The 40°<111> relationship is approximately satisfied between the brass rolling texture and the {236}<385> recrystallization texture.…”

Section: Introductionmentioning

confidence: 99%

The Evolution of the {110}<001> and {236}<385> Recrystallization Textures in Cu Alloys and High Mn Austenitic Steels with the Brass Rolling Texture

Lee

2016

KEM

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The {110}<112> rolling texture of Cu-22%Zn and Cu-30%Zn sheets having relatively low stacking fault energy transforms into the {236}<385> texture after recrystallization. The 40°<111> relation is approximately satisfied between the {110}<112> and {236}<385> textures. The 40°<111> relation is often addressed as a token of the oriented growth theory for the recrystallization texture evolution. On the other hand, Cu-16%Mn and Cu-1%P alloys and high Mn austenitic steels such as Fe-18%Mn-0.6%C, Fe-18%Mn-1.5%Al-0.6%C, and Fe-18%Mn-3%Al-0.6%C sheets having relatively high stacking fault energy also have the {110}<112> rolling texture, which transforms into the {110}<001> texture after recrystallization. The 40°<111> relation is not established between the {110}<112> rolling texture and the {110}<001> recrystallization texture. The differences are attributed to differences in the stacking fault energies of the materials. The phenomena can be explained by defects that dominates the stored energy of the rolled materials. When the grain boundary energy dominates the stored energy, the {236}<385> texture evolves after recrystallization. On the other hand, when dislocation energy dominates the stored energy, the {110}<001> texture evolves after recrystallization. The {110}<001> recrystallization texture evolution is well explained by the strain-energy-release-maximization theory. The 40°<111> relation is believed to originate in the maximum mobility of <111> tilt boundaries at a rotation angle of 40°.

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Rolling and Recrystallization Textures in the System Copper-Zinc as Function of the Zn-Content

Cited by 6 publications

References 4 publications

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Deformation and Recrystallised Texture Evolution and the Followed Mechanical and Electrical Properties of Drawn and Annealed Copper Wires

The Evolution of the {110}<001> and {236}<385> Recrystallization Textures in Cu Alloys and High Mn Austenitic Steels with the Brass Rolling Texture

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Rolling and Recrystallization Textures in the System Copper-Zinc as Function of the Zn-Content

Cited by 6 publications

References 4 publications

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Evolution of Recrystallization Textures in Cold-Rolled Commercially Pure Aluminum

Deformation and Recrystallised Texture Evolution and the Followed Mechanical and Electrical Properties of Drawn and Annealed Copper Wires

The Evolution of the {110}&lt;001&gt; and {236}&lt;385&gt; Recrystallization Textures in Cu Alloys and High Mn Austenitic Steels with the Brass Rolling Texture

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The Evolution of the {110}<001> and {236}<385> Recrystallization Textures in Cu Alloys and High Mn Austenitic Steels with the Brass Rolling Texture