Effect of Secondary Cold Rolling Reduction Rate on Secondary Recrystallization Behavior of CGO Steel

With the implementation of the “double carbon” policy in various countries in the world, the demand for grain-oriented electrical steel with low iron loss and high magnetic induction is increasing. Reducing the thickness of the steel sheets is an effective method to reduce the iron loss.The sheet thickness reduction means the increasing cold rolling reduction rate, especially the secondary cold rolling reduction rate, will directly affect the texture evolution of the secondary recrystallization process. In this paper, the secondary cold rolling reduction rate of commercial grain-oriented silicon steel was studied by means of X-Ray Diffraction, Electron Backscatter Diffraction. The results showed that Ultra-thin oriented silicon steel cannot be obtained by increasing the secondary cold rolling reduction rate alone; the optimum secondary cold rolling reduction rate was 59.2%. The grain size increased as the secondary cold rolling reduction rate increased and favorable texture content decreased, which was disadvantage to obtain a secondary recrystallization environment

Microstructure and texture evolution of ultra-thin high grade non-oriented silicon steel used in new energy vehicle

The evolutions of microstructure and texture of ultra-thin high-grade non-oriented silicon steel for new energy vehicles were investigated in this paper, and the formation mechanism of typical recrystallized α *-fiber texture was described. The results show that: The microstructure of the hot rolled plate was inhomogeneous along the thickness direction because of the shear force and temperature gradient, resulting in the texture in each layer of the hot rolled plate appearing rotational distribution around the Goss orientation. After normalizing, the fully recrystallized microstructure was obtained, and α *-fiber texture was formed. Banded structure was obtained in the cold rolled sheet, with α -fiber texture {114}〈110〉 dominated. The typical α *-fiber texture was formed after annealing recrystallization, which mainly consist of {114} and {113}. The {114} oriented grains were mainly nucleated within the deformed {114} grains and at the grain boundaries of α -fiber deformed grains, and without size, quantity and strength advantages. {111} is dominated in the early stage of recrystallization, but {114} became the main texture with size, strength and quantitative advantages in the late stage of recrystallization