Modelling the evolution of recrystallization texture for a non-grain oriented electrical steel
Graphical abstract
Introduction
As a soft magnetic material with a body-centered cubic (BCC) structure, Si steel exhibits easiest magnetization along the 〈1 0 0〉 crystal direction. For non-grain oriented (NGO) electrical steels, 〈1 0 0〉 directions parallel to sheet surface plane are preferred for superior magnetic properties [1], [2], [3]. Unfortunately, conventional rolling process is known to strengthen α-fiber (〈1 1 0〉//RD) and γ-fiber (〈1 1 1〉//ND), which are unfavorable for the magnetization. In order to transform the crystal orientation developed by cold rolling into texture favorable for the magnetization, recrystallization is essential, but the changes in microstructure and texture during recrystallization are vastly complex and not fully understood. Therefore, in an effort to nurture the easy magnetization direction, the evolution of recrystallization texture for NGO electrical steels is still an ongoing subject of interest.
Because recrystallization texture of a polycrystalline material strongly depends on its processing history [1], [2], [4], [5], [6], [7], [8], [9], [10], [11], [12], [13], [14], [15], [16], [17], [18], diverse processing methods including cold rolling of columnar grains [7], [8], α → γ → α phase transformations [9], [10], and conventional [12], [13], [14] and unconventional rolling schemes [15], [16], [17], [18] have been studied to understand the evolution of recrystallization texture for the NGO electrical steel. While these works laid valuable grounds for how specific orientations may nucleate or grow, very few efforts have been made in actually predicting the evolution of recrystallization texture for the NGO electrical steel, which can significantly aid the development of processing methods.
For a model to properly predict the evolution of recrystallization texture, the model should firstly be able to predict what orientations will be formed during recrystallization, and secondly be able to describe the kinetics of recrystallization. While the latter can be handled by employing Avrami-type equation, the former one is often problematic. Currently, most of the theories used to describe the evolution of recrystallization texture are based on oriented nucleation (ON) and oriented growth (OG) theories, but both theories are not quite clear as to which nuclei are preferred given a certain deformation history. This difficulty often becomes an obstacle in predicting the final recrystallization texture because recrystallization texture heavily depends on deformation history.
A suitable theory to correlate deformation mode with stable recrystallization texture is the strain energy release maximization (SERM) theory [19], [20]. The theory postulates that a stable recrystallized grain is developed if the grain is oriented in a way such that the strain energy by dislocations in the deformed grain is minimized, or the strain energy release upon recrystallization is maximized. This theory has been successfully utilized in a diverse class of materials such as Al containing high Mn austenitic steels [21], Al and Cu [22], Co thin film [23], low carbon steels [24], and grain-oriented electrical steels [25]. Also, in calculating the orientation of the recrystallized grain, the activities of slip systems are used, which means that orientation of the recrystallized grain depends on deformation modes. The fact that the SERM theory accounts for deformation mode is a huge advantage for predicting deformation history dependent recrystallization textures.
In this work, we employed a combined finite element method (FEM) and visco-plastic self-consistent (VPSC) modeling approach to characterize the evolution of deformation texture developed by cold rolling for a hot-rolled NGO electrical steel. Afterwards, the recrystallization orientations that can evolve from each deformed grain were predicted based on the SERM theory, using the slip activities calculated in the combined FEM-VPSC. Finally, the evolution of the recrystallization texture at the specific annealing time and temperature was evaluated using the Avrami-type kinetic equation.
Section snippets
Experimental procedure
The NGO electrical steel used in the present work was fabricated by POSCO, containing 2.9 wt% Si. The cold rolling of a hot-rolled steel sheet was subsequently conducted to a final thickness of 0.35 mm. The cold-rolled sheets were isothermally annealed at 750 °C and 830 °C for the various periods of time in Ar atmosphere using a tube-type furnace.
The microstructure and crystallographic texture were measured on the plane perpendicular to the transverse direction (TD) by the electron backscatter
Finite element method
A 2-D finite element simulation for a cold rolling process was conducted with isotropic von Mises yield criterion, using commercial ABAQUS 6.9 software. The roll diameter was designed to be 127 mm, and the initial dimension of a 2-D plane strain matrix representing the electrical steel sheet was set to the length of 80 mm and thickness of 1 mm. The friction coefficient between the roll and matrix was assumed to 0.08, and the lower boundary of the matrix was constrained along the RD due to the
Characteristics of the initially hot-rolled NGO electrical steel
Prior to predicting the texture evolution by cold rolling and recrystallization, the mechanical properties and microstructure of the initially hot-rolled sheet were preferentially evaluated. For the engineering stress-strain curve in Fig. 2, the yield strength, ultimate tensile strength, and total elongation of the hot-rolled specimen are 388.3 MPa, 518.5 MPa, and 51.6%, respectively. As shown in Fig. 3, the initial microstructure of the specimen is composed of the equiaxed grains with an
Discrepancies between the predicted and experimental recrystallization texture
As shown in Fig. 4c, a small amount of the deformed (1 1 0)//ND, (1 0 0)//ND orientations is formed around the shear bands inclined at angles of 30–45° with respect to RD. From Fig. 9 and published literature [7], [32], it is well established that the shear band in the deformed γ-fiber plays a major role in the formation of Goss oriented nuclei at the early stage of recrystallization. In particular, the intense shear deformation within shear bands enables fast nucleation of Goss, which explains
Conclusion
In this work, the evolution of the recrystallization texture for 2.9 wt% Si non-grain oriented electrical steel was modeled. The deformation texture by cold rolling was calculated combining the finite element method (FEM) and visco-plastic self-consistent (VPSC) model. Afterwards, the possible recrystallization orientations were predicted based on the strain energy release maximization (SERM) theory. Finally, the evolution of the recrystallization texture at 750 °C and 830 °C was predicted
Acknowledgement
This study was supported by Brain Korea 21 PLUS project for Center for Creative Industrial Materials (F16SN25D1706) and POSCO (2016Y040).
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