Deformation and Textures of Metals at Large Strain

Aernoudt, Etienne; Houtte, Paul Van; Leffers, T.

doi:10.1002/9783527603978.mst0050

Cited by 18 publications

(22 citation statements)

References 83 publications

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“…On the other hand, if the active CBB, i* were as in the original Peeters et al model, and the slip system s* parallel to one CBB intersects the other, load crossing will not bring about as drastic a reduction in the mean free path, and the cross effect will be much smaller in magnitude. The present substructural geometry thus enhances the "barrier" posed to dislocation motion during a cross test along the newly activated slip system s** by the CBB i* formed during rolling, and this enhancement is essential for obtaining reasonable fits in Figure 4 (Aernoudt et al [19] ).…”

Section: Discussionmentioning

confidence: 89%

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Application of a substructure-based hardening model to copper under loading path changes

Mahesh

Tomé

McCabe

et al. 2004

Metall Mater Trans A

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In addition to texture, plastic anisotropy of a polycrystalline fcc metal stems from the directional nature of the dislocation substructure within individual grains. This produces the marked work hardening or softening observed immediately following load path changes. Following the framework of Peeters et al., [1,2] in bcc steel, we develop a dislocation substructure evolution-based stage III hardening model for copper, capable of capturing the constitutive response under load path changes. The present model accounts for the more complicated substructure geometry in fcc metals than in bcc. Using an optimization algorithm, the parameters governing substructure evolution in the model are fit to experimental stress-strain curves obtained during compression along the three orthogonal directions in samples previously rolled to various reductions. These experiments approximate monotonic, reverse, and cross-load paths. With parameters suitably chosen, the substructure model, embedded into a self-consistent polycrystal plasticity model, is able to reproduce the measured flow stress response of copper during load path change experiments. The sensitivity of the parameters to the assumed substructure geometry and their uniqueness are also discussed.

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Section: Discussionmentioning

confidence: 89%

“…The material shows softening, a phenomenon termed the Bauschinger effect. On the other hand, the cross effect, which manifests as hardening or strain softening during cross loading (Barlat et al [17] and Aernoudt et al [19] (Figure 20) has both texture and microstructure causes.…”

Section: Introductionmentioning

confidence: 99%

Application of a substructure-based hardening model to copper under loading path changes

Mahesh

Tomé

McCabe

et al. 2004

Metall Mater Trans A

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“…The {112}h110i component is the stable final orientation for plane-strain compression (rolling) as predicted by the full constraint Taylor model. [4,25,26] This theoretically stable orientation (in conventional rolling) is not preserved when the inclination angle increases to 75 and 90 deg, where the dominant texture is rotated cube and no obvious peak is observed at the {112}h110i position. It should also be noted that inclining the CRD to HRD tends to change The inclination of the CRD to HRD also sharpens the cold-rolling texture: when the angle is 0 deg (conventional rolling) the maximum texture intensity is about 7, while at an angle of 75 deg, the maximum intensity increases to 16 (i.e., more than doubled).…”

Section: A Hot Rolling and Annealingmentioning

confidence: 92%

Texture Evolution of a Non-oriented Electrical Steel Cold Rolled at Directions Different from the Hot Rolling Direction

Hilinski²,

2015

Metall Mater Trans A

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With the objective of optimizing the crystallographic texture of non-oriented electrical steel, i.e., reducing the h111i//ND and h110i//RD fibers and promoting the h001i//ND texture, a new rolling scheme was proposed and tested, in which the cold rolling direction (CRD) was intentionally inclined at an angle to the hot rolling direction (HRD) in order to change the orientation flow paths during cold rolling and alter the final texture of the annealed sheets. A non-oriented electrical steel containing 0.88 wt pct Si was hot rolled using conventional routes and annealed, and a number of rectangular plates were cut from the hot band with the longitudinal directions inclined at various angles, i.e., 0, 15, 30, 45, 60, 75, and 90 deg, to the HRD. These plates were then cold rolled along the longitudinal directions with a thickness reduction of 72 pct. The cold-rolled samples were annealed, temper rolled and annealed again (final annealing). The texture evolution during hot rolling, hot band annealing, cold rolling, and final annealing was characterized by electron backscatter diffraction and X-ray diffraction techniques. By changing the CRD with respect to the HRD, the initial texture and the orientation flow paths were altered, which resulted in apparent differences in the textures as compared to conventional cold rolling. After temper rolling and final annealing, the recrystallization textures consisted of mainly a h001i//ND fiber and there was almost no h111i//ND fiber. The sample cold rolled at an angle of 60 deg to the HRD had the strongest texture (intensity almost 29 of conventional rolling) with a maximum at the cube {001}h100i orientation-a magnetically favorable orientation for non-oriented electrical steels.

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“…It is interesting to compare Eq. (6) with the expression for the rate of plastic work obtained by the Taylor theory for the plastic deformation of polycrystalline materials (see for example: Aernoudt et al, 1993)…”

Section: Plastic Potential In Strain Rate Spacementioning

confidence: 99%

“…Their analytical expressions are based on the concept of dual plastic potentials (Hill, 1987;Van Houtte, 1994) which makes it comparatively easy to identify the parameters of the model (up to several hundreds) by a fitting operation which compares the rates of plastic work predicted by the model for a large number of strain modes, to the average Taylor factors of a given anisotropic material. These are calculated using the Taylor model for the plastic flow of polycrystals [see for example Aernoudt et al (1993); Van Houtte (2001) has described how the average Taylor factors can be efficiently calculated]. The method requires the knowledge of the orientation distribution function (ODF) of the crystallographic texture of the material (Bunge, 1982), a property which can be measured easily with the techniques available today.…”

Section: Introductionmentioning

confidence: 99%