Strain Energy Release Maximization Model Research Articles

Recrystallization Texture of Electrodeposited Zinc

Electrodeposited zinc layers help prevent the corrosion of steel surfaces. The microstructure, surface morphology, and texture of the electrodeposits are related to the deposition variables. Herein the surface morphology and microstructure are investigated as functions of the special electrodeposition variables, such as electrolyte composition, over-potential, current density, electrolyte temperature and pH. Upon heat treatment, the texture of the electrodepositd layers changes into a recrystallization texture. The texture of the as-electrodeposited and recrystallized zinc layers are studied. The //normal direction (ND) texture of the zinc electrodeposit can be obtained from zinc oxide, sodium hydroxide, potassium chloride, and sodium cyanide solution baths. The //ND texture of the zinc electrodeposit did not change even after recrystallization. This phenomenon of zinc eletrodeposits could be described by the strain-energy release maximization model.

The Cube Recrystallization-Texture Related Component in the β-Fiber Rolling-Texture FCC Metals

The cold-rolling texture of fcc sheet metals with medium to high stacking fault energies is known to consist of the brass {011}<211>, Cu {112}<111>, Goss {011}<100>, S {123}<634>, and cube {100}<001> components. The recrystallization (Rex) texture of cold-rolled Al, Cu and their alloy sheets is well known to be the cube texture. The 40°<111> orientation relationship between the S and cube components, which has been taken as a proof of the oriented growth theory, has made one believe that the S orientation is responsible for the cube Rex texture. The oriented growth theory is claimed to be associated with grain boundary mobility anisotropy. However, some data indicate the Cu component is linked with the cube component. There is no 40°<111> orientation relationship between the Cu and cube components. The strain-energy-release-maximization model (SERM), in which the strain energy due to dislocations is importantly taken into account, suggests that the Cu and S components in the rolling texture are linked with the cube and ~{031}<100> components in the Rex texture, respectively.

Recrystallization-Texture Theories in Light of Strain-Energy-Release-Maximization

The oriented-nucleation and oriented-growth for recrystallization (Rex) textures of electrodeposits, vapor deposits, and plastically deformed metallic materials have been discussed based on the strain-energy-release-maximization (SERM) model. When the Rex orientation predicted by the SERM model from major components of the deformation texture is the same as a minor component in the deformation texture that is calculated to be thermally stable by the SERM model, the calculated Rex orientation is sure to become the main component of the Rex texture. This implies that the oriented-nucleation and the oriented-growth affect the evolution of the Rex texture. For polycrystalline materials, the Rex orientation predicted by the SERM model is likely to be measured because heterogeneous nucleation can occur in grain boundaries even when shear bands are absent. In other words, the grain boundaries are unlikely to control the Rex texture and the oriented growth dominates the Rex texture.

Self-Annealing Textures of Copper Damascene Interconnects

The properties of deposited metal films and interconnect structures at submicrometer scale are sensitive functions of microstructural features. Therefore, understanding of the factors which control microstructural evolution is necessary for the development and design of reliable, manufacturable interconnect structures, especially in copper damascene interconnects. The annealing textures of copper interconnects depend on their deposition textures and geometries. The copper interconnects are subjected to stresses even at room temperature, which in turn give rise to strain energies. The stress distributions in interconnects are not homogeneous, which in turn give rise to non-fiber type textures after annealing. The self-annealing textures of interconnects is discussed based on the strain-energy release maximization model, in which grains whose Young’s modulus direction is parallel to the absolute, maximum stress direction grow in preference to others.

The effect of precipitation on the evolution of recrystallization texture in AA8011 aluminum alloy sheet

An AA8011 aluminum alloy sheet cold rolled by 95% had a typical β-fiber texture, which runs from the copper orientation {112}〈111〉 over the S-orientation {123}〈634〉 to the brass orientation {110}〈112〉 in the Euler space. The development of annealing textures depended on annealing temperatures due to the interaction between precipitation and recrystallization. Upon annealing at a low temperature of 275 °C, substantial precipitation took place before recrystallization. This led to a weak recrystallization texture consisting of the P-orientation {011}〈122〉, the cube orientation {001}〈100〉, and the RD rotated cube orientation {hk0}〈001〉, among which the P-orientation, which developed near large FeAl 3 particles, was the main component and the cube orientation originated from the matrix was relatively weak. After annealing at 350 and 500 °C, the cube orientation strongly developed, while the P-orientation did weakly, even though precipitation occurred before or as soon as recrystallization took place. The results were discussed based on the interaction between precipitation and recrystallization. When the cube component developed during annealing, the copper component in the rolling texture disappeared most rapidly in agreement with the prediction of the strain energy release maximization model.

Deformation and Recrystallization Textures in Cross-Rolled Copper Sheet

A study has been made of the deformation and recrystallization textures of 99.99% pure copper sheets which were cross rolled by 82 and 96% reduction in thickness and recrystallized in a salt bath at 450°C for 1h. The deformation texture was approximated by the {011}〈755〉 orientation as the major component and {001}〈100〉 as a minor component. These deformation texture components were well simulated using the rate sensitive relaxed constraints model. The {001}〈100〉 orientation was calculated to be metastable while the {011}〈755〉 orientation was located in the middle of the rotation path between the stable orientations in two cross rolling directions. The recrystallization texture in the center layer of the 96% cross-rolled copper sheet was approximated by {86 50 9}〈10 34 94〉 for each rolling direction. The evolution of the recrystallization texture was discussed based on the strain energy release maximization model.

Strain energy release maximization model for evolution of recrystallization textures

In 1995, the author advanced a model for the evolution of recrystallization texture, in which the absolute maximum internal stress direction due to dislocations generated during deformation or fabrication in the deformed material is aligned with the minimum Young's modulus direction in recrystallized grains, whereby the energy release during recrystallization can be maximized. This comes from the fact that the material concerned does not macroscopically change its shape and volume during recrystallization, and so the recrystallization is a displacement-controlled process. This strain energy release maximization model originates from the presumption that the stored energy due to dislocations is the major driving force for the recrystallization. The absolute maximum internal stress direction may be obtained from the operating slip systems, which are related to the deformation mode and texture. If one slip system is activated, the absolute maximum normal stress direction is parallel to the slip direction, or the Burgers vector direction. If more than one slip system is activated, the absolute maximum normal stress direction can be determined by the vector sum of related slip directions, by taking into account their contribution to slip. This paper reviews recrystallization textures of plastically deformed metals, based on the SERM model.

Deformation and annealing textures of silver wire

Abstract Silver is a rare material in which the major axial orientation component is 〈111〉 at low drawing reductions (less than about 90%) as other f.c.c. metals, but changes to 〈100〉 at high reductions (99%). Either orientation reduced to 〈100〉 after recrystallization. The further annealing gave rise to the 〈111〉 growth texture. The recrystallization texture could be explained based on the strain energy release maximization model, in which the absolute maximum internal stress direction determined by slip systems becomes parallel to the minimum Young’s modulus direction of recrystallized grains. The growth texture was discussed based on the mobility of the 〈100〉 and 〈111〉 tilt grain boundaries.

The Evolution of the Goss Texture in Silicon Steel

The Goss orientation, {110}‹001›, in about 3% silicon steel has been the subject of speculation from its scientific and technological points of view. The grain oriented silicon steel is made by hot rolling at about 1300°C, cold rolling, followed by annealing. The Goss texture is formed near the surface layer of a steel sheet when it is rolled in the α phase region at elevated temperatures, because the friction between the sheet and rolls tends to increase with increasing temperature, which in turn increases the shear deformation. The Goss texture remains unchanged even after recrystallization of steel. The Goss texture, which is not stable with respect to plane strain deformation, rotates toward the {111}‹112› orientation. The relaxed constraints (RC) model, in which shear strains parallel to the rolling direction may occur, simulates the formation of the {111}‹112› orientation. The {111}‹112› rolling component is known to lead to the Goss orientation after annealing. The strain energy release maximization model for recrystallization texture advanced by the author predicts the recrystallization texture of {441}‹118› from the {111}‹112› rolling texture. The {441}‹118› orientation yields the Goss orientation when the {441}‹118› orientation is expressed by the Gauss type scattering calculated with a half width angle of 12°. The model also predicts the fact that the Goss texture formed during rolling remains unchanged even after annealing.

Relationship between deposition and recrystallization textures of copper and chromium electrodeposits

The 〈100〉, 〈111〉 and 〈110〉 textures of copper electrodeposits obtained from copper sulfate baths changed to the 〈100〉, 〈100〉 and 〈 $$\sqrt {\text{3}} 10$$ 〉 textures, respectively, after recrystallization. The textures of chromium electrodeposits obtained from the standard Sargent bath remained unchanged after recrystallization. The results are in agreement with the prediction of the strain energy release maximization model, in which the recrystallized grains orient themselves so that their minimum elastic modulus direction can be parallel to the absolute maximum internal stress direction due to dislocations in the non-recrystallized grains.

Strain energy release maximization model for recrystallization textures

In 1995, the author advanced a model for the evolution of recrystallization texture. In the model the absolute maximum internal stress direction due to dislocations generated during deformation or fabrication in the fabricated material is aligned with the minimum Young’s modulus direction in recrystallized grains, whereby the energy release during recrystallization can be maximized. This comes from the fact that material concerned does not change macroscopically its shape and volume during recrystallization, and so the recrystallization is a displacement controlled process. This strain energy release maximization model originates from the presumption that the stored energy due to dislocations is the major driving force for the recrystallization. The absolute maximum internal stress direction may be obtained from the operating slip systems, which are related to the deformation mode and texture. If one slip system is activated, the absolute maximum normal stress direction is parallel to the slip direction, or the Burgers vector direction. If more than one slip system is activated, the absolute maximum normal stress direction can be determined by the vector sum of related slip directions, taking their contribution to slip into account. This paper discusses recrystallization textures of plastically deformed and electrodeposited metals, based on the model. A brief comment was made also on the growth textures of axisymmetrically deformed copper and silver and electrodeposited silver and Fe-Ni alloy.

Recrystallization Textures of Silver Electrodeposits

The recrystallization texture of silver electrodeposits obtained from cyanide baths containing no additive were investigated. The textures of as‐deposited and recrystallized specimens were determined from the pole figures, from which orientation distribution functions and inverse pole figures were calculated. The orientation components of experimentally determined textures were quantified using the Gauss distribution of ideal orientation components. The , , and , , deposition textures changed to the same , recrystallization texture when the specimens were annealed, where subscript T denotes the twin component of the preceding orientation. The (110) deposition textures changed to the recrystallization with its twin components. The evolution of recrystallization textures has been explained by the strain energy release maximization model, in which the absolute maximum internal stress direction in electrodeposits due to dislocations becomes parallel to the minimum elastic modulus direction of recrystallized grains, whereby the strain energy release of the material can be maximized. © 1999 The Electrochemical Society. All rights reserved.

Recrystallization texture of aluminum bicrystals with S orientations deformed by channel die compression

Abstract The texture changes during recrystallization in high-purity aluminum bicrystals with S orientations, e.g. (123)[41 2 ] / (123)[ 4 1 2] and (123)[41 2 ] / ( 1 2 3 )[41 2 ] , deformed by channel die compression were investigated by Blicharski et al. There was no 〈111〉 rotational relationship between the recrystallized and the deformed matrix phases. This result could be explained by the strain energy release maximization model, in which the direction of absolute maximum internal stress due to dislocations in the deformed matrix becomes parallel to the minimum Young’s modulus direction in recrystallized grains, whereby the energy release during recrystallization can be maximized.