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Effect of rare earth Y on microstructure and texture of oriented silicon steel during hot rolling and cold rolling processes

  • Liguang Zhu , Xiangyang Li , Yaxu Zheng EMAIL logo , Zhihong Guo EMAIL logo , Yuanxiang Zhang , Huilan Sun , Pengjun Liu , Yu Liu and Ruifang Cao
Published/Copyright: December 14, 2022
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 41 Issue 1

Abstract

The effect of rare earth Y on precipitates and textures of the grain-oriented silicon steels, the composition, morphology, size, quantity of inclusions and texture evolution of hot-rolled and cold-rolled oriented silicon steel containing rare earth Y were studied using transmission electron microscopy, field emission scanning electron microscope, and electron backscatter diffraction. The results show that there are mainly spherical or ellipsoidal Y2O2S precipitates in the Y bearing silicon steel. Rare earth treatment effectively improves the precipitates’ morphology and restrains the precipitation of the long-strip MnS in the hot-rolled plate. Meanwhile, the microstructure is more uniform, and the recrystallized grains on the surface and the fiber structure in the central layer are larger after hot rolling compared with Y-free steel. Furthermore, with the addition of rare earth Y, the unfavorable brass texture and rotational cube texture in the hot-rolled plate are reduced. Meanwhile, the number of shear bands is increased and the strength of the favorable {111} 〈112〉 texture is improved in the cold-rolled plate, which helps develop the Goss texture during the annealing process.

Keywords: oriented silicon steel; rare earth Y; hot rolling; cold rolling; texture; precipitates

1 Introduction

Oriented silicon steel is a kind of ferrosilicon alloy with a silicon content between 2.9 and 3.6%. It has a single {110} 〈001〉 texture (Goss texture), high magnetic permeability, and low iron loss. It is an important soft magnetic material and is mainly used in the fields of electricity, electronics, and motors. At present, the oriented silicon steel is obtained by secondary recrystallization annealing, which has high composition controlling technology and a complex production process [1,2,3]. During the production and preparation of oriented silicon steel, the microstructure and texture of hot-rolled and cold-rolled plates have an important influence on the formation of sharp Goss texture during recrystallization annealing [4,5,6].

Rare earth is the general name of scandium and yttrium (Y) elements and 15 kinds of lanthanide elements in the periodic table. Some research results have indicated that rare earth elements have unique outer electronic structures, so they have the characteristics of strong chemical activity, variable valence state, and large atomic size [7,8,9]. Rare earth elements play an important role in silicon steel, such as deep purification, inclusion modification, as-cast microstructure and properties improvement, primary recrystallization structure refinement, and so on [10,11,12]. In recent years, some progress has been made in the research of oriented silicon steel with the addition of rare earth elements. It has been reported that the primary recrystallized grains were refined, and the grains after secondary recrystallization grew up obviously with the addition of a small amount of rare earth element Ce [13,14]. This is mainly because rare earth elements can affect the precipitation behavior of inhibitors, including the number, size, distribution and composition. Meanwhile, the addition of rare earth element Ce is beneficial to obtaining dispersed inhibitor particles in the normalized heat treatment process of oriented silicon steel, enhancing the pinning ability in the primary recrystallization stage [13,15].

In addition, segregation of rare earth elements at grain boundaries can effectively reduce the grain boundary energy of the matrix, therefore reducing the driving force for grain growth and effectively pinning the abnormal growth of primary recrystallized grains [16]. Park et al. studied the effect of Y on the structure and texture of oriented silicon steel [17]. The results showed that the addition of rare earth Y inhibited the growth of primary recrystallized grains and that abnormal grain growth was successfully achieved after secondary recrystallization without any other inhibitors. In high-silicon steel, the addition of rare earth Y increases the number of shear bands and the dislocation density of the warm-rolled sheet, weakening the strength of the α and γ textures [18]. However, there are still very limited studies on the effect of rare earth Y on the texture of Fe–3% Si grain-oriented silicon steel so far. Therefore, the objective of this study is to investigate the effect of rare earth Y on the microstructure, texture, and inclusions of Fe–3% Si grain-oriented silicon steel, to provide a reference for the application of rare earth Y in oriented silicon steel.

2 Materials and methods

The basic experimental material is Fe–3wt% Si steel and the chemical compositions are shown in Table 1. The steel 1# is Y free and the content of Y in steel 2# is 0.078%, and the yield of Y is 36.5%. The ingots of the silicon steel were melted by a 50 kg vacuum induction furnace and forged into billets with a size of 500 mm × 200 mm × 20 mm. The rare earth Y was added to the bottom of the mold before tapping. The ingots were heated to 1,150°C for 0.5 h and then hot-rolled for 5 passes into the plate with a thickness of 2.5 mm. The hot-rolled plate after normalizing heat treatment was corroded with a hydrochloric acid aqueous solution to remove the iron oxide scale on the surface. The hot-rolled plate after pickling was rolled to 0.3 mm thickness after 6 passes at a temperature of 300°C. The rolling process is shown in Figure 1.

Table 1

Chemical composition of analysis of 3% grain-oriented electrical steel (mass fraction, %)

Number C Si Mn P S Al N O Y
1# 0.050 2.98 0.22 0.01 0.018 0.028 0.0043 0.0021 —
2# 0.014 2.97 0.22 0.01 0.011 0.035 0.0045 0.0020 0.078
Figure 1 Schematic diagram of the rolling process.
Figure 1

Schematic diagram of the rolling process.

Taking the samples with a size of 6 mm × 10 mm from the hot-rolled plate and cold-rolled plate along the rolling direction, the longitudinal section of the sample (RD-ND surface) was prepared to analyze microstructure and texture. The thickness of the hot-rolled plate is expressed by “S,” and the surface layer, subsurface layer, and central layer are expressed as S = 0, S = ¼, and S = 1/2, respectively.

The field emission scanning electron microscope (FESEM, ZEISS Gemini SEM 300) and electron backscatter diffraction (EBSD, OXFORD Symmetry) were used to analyze large-size inclusions and texture, respectively [19]. The samples for EBSD detection were mechanically grounded and polished first, then electro-polished with 5% perchloric acid to remove stress on the surface. The EBSD scanning step of hot-rolled plate is 2 μm, and the scanning area is 3 mm. The EBSD scanning step of cold-rolled plate is 0.5 μm, and the scanning area is 0.36 mm. The EBSD data was analyzed with CHANNEL 5 software. The small size precipitates were studied using transmission electron microscopy (TEM, Tecnai G2 F20 S-TWIN) and energy dispersive spectrometer (EDS, Tecnai G2 F20 S-TWIN). The TEM samples used to observe the precipitates were prepared by carbon coating methods [20,21].

3 Results and analysis

3.1 Influence of rare earth Y on inclusions in hot-rolled sheets

The inclusions morphology and chemical composition in the hot-rolled sheets are shown in Figure 2. The inclusions are mainly long-strip MnS and irregular MnS–Al2O3 in Y-free steel. With the addition of rare earth Y, the inclusions in hot-rolled sheets are mainly spherical or ellipsoidal Y2O2S. However, there is no MnS or MnS–Al2O3 type inclusion in Y-containing silicon steel. The element distribution of inclusions is shown in Figure 3. The core of MnS–Al2O3 type inclusion is Al2O3 and the outer layer is MnS, as shown in Figure 4. The distribution of O, S, and Y elements in Y2O2S inclusion is uniform, as shown in Figure 5. Rare earth Y easily combines with oxygen and sulfur in molten steel to form spherical yttrium sulfides, yttrium sulfur oxides, or yttrium composite inclusions, which effectively restrains the long-strip MnS inclusions formed in the steel. The Al2O3 inclusions in steel are also modified into rare earth sulfur oxides due to the stronger deoxidization ability of rare earth. The spherical or ellipsoidal rare earth sulfides are dispersed in the steel matrix and maintain their original morphology during hot rolling. This is conducive to improving the machinability of steel [22].

Figure 2 Large inclusions in silicon steels: (a–c) Y-free steel and (d–f) Y-bearing steel.
Figure 2

Large inclusions in silicon steels: (a–c) Y-free steel and (d–f) Y-bearing steel.

Figure 3 Elemental distribution of MnS inclusions in hot-rolled Y-free steel.
Figure 3

Elemental distribution of MnS inclusions in hot-rolled Y-free steel.

Figure 4 Elemental distribution of MnS–Al2O3 inclusions in hot-rolled Y-free steel.
Figure 4

Elemental distribution of MnS–Al2O3 inclusions in hot-rolled Y-free steel.

Figure 5 Elemental distribution of Y2O2S in hot-rolled Y-bearing steel.
Figure 5

Elemental distribution of Y2O2S in hot-rolled Y-bearing steel.

A FE-SEM was used to analyze inclusions in 30 consecutive fields with 500× magnification. The statistical results of different size inclusions per unit area are shown in Figure 6. The percentage of inclusions of 0.5–2 μm in Y-free steel is the highest. The average sizes of inclusions are 3.1 and 2.7 μm for Y-free steel and Y-containing steel, respectively. The total number of inclusions decreases with the addition of Y. Meanwhile, the size of the inclusions in hot-rolled plate is more uniform, mainly in the range of 0.5–5 μm. With the addition of Y, the number of inclusions in the range of 2–5 μm increases, while that smaller than 2 μm and larger than 5 μm decreases.

Figure 6 Statistical results of the number and size of inclusions in experimental steels.
Figure 6

Statistical results of the number and size of inclusions in experimental steels.

Small inclusions in hot-rolled plates of Y-free steel and Y-bearing steel were observed by TEM, as shown in Figures 7 and 8. There are fine spherical MnS–SiO2 composite precipitates in Y-free steel. There are also fine spherical precipitates in Y-bearing steel. The analysis results of EDS show that the particles are mainly composed of O, Si, S, Mn, and Y elements. These fine particles are distributed in an aggregated state. There is no single fine MnS precipitate in experimental steels.

Figure 7 Composition distribution of fine precipitates in Y-free steel.
Figure 7

Composition distribution of fine precipitates in Y-free steel.

Figure 8 Composition distribution of fine precipitates in Y-bearing steel.
Figure 8

Composition distribution of fine precipitates in Y-bearing steel.

3.2 Influence of rare earth Y on the microstructure of hot-rolled sheets

The microstructure of hot-rolled sheets is shown in Figure 9. There are obvious recrystallized equiaxed grains in the surface layer of the hot-rolled plate, and the central layer is mainly composed of deformed grains elongated along the rolling direction. There are a large number of fine recrystallized grains in the surface and center layer of Y-free steel. With the addition of rare earth Y, the ferrite grains in the surface layer are larger and more uniform. The microstructure in the center layer is large deformed ferrite grains. The uniformity of hot rolling structure is improved.

Figure 9 Microstructure of the hot-rolled sheets. (a) Y-free and (b) Y-bearing.
Figure 9

Microstructure of the hot-rolled sheets. (a) Y-free and (b) Y-bearing.

The grain size of different thicknesses of hot-rolled sheets is counted, and the results are shown in Figure 10. At the positions of S = 0 and S = 1/2, the grains of Y-containing steel are obviously larger than those of Y-free steel. At the position of S = 0, the average grain sizes are 12.58 and 10.43 μm for Y-bearing and Y-free steels, respectively. The standard errors of average grain size are 0.5846 and 0.5517 μm, respectively. At the position of S = 1/2, the average grain sizes are 14.38 and 10.75 μm for Y-bearing and Y-free steels, respectively. The standard errors of average grain size are 0.4968 and 0.5267 μm, respectively. However, there is little difference in the average grain size at S = 1/4.

Figure 10 Grain size at different thicknesses of Y-free and Y-bearing hot-rolled sheets: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.
Figure 10

Grain size at different thicknesses of Y-free and Y-bearing hot-rolled sheets: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.

From the inclusions analysis results in Figure 6, the total number of inclusions is reduced with the addition of Y, especially the number of small size inclusions. This indicates that the pinning force on grain boundaries is reduced with the reduction in number of small inclusions. The addition of rare earth Y makes the elongated MnS inclusions transform into large-size spherical rare-earth inclusions, and makes the fine MnS–SiO2 inclusions aggregate together, which reduces the pinning effect on grain growth. Therefore, the addition of Y increases the grain size [23].

3.3 Influence of rare earth Y on the texture of hot-rolled sheets

As shown in Figure 11, there are obvious differences in texture types at different positions of thickness between Y-containing steel and Y-free steel. The φ 2 = 45° ODF diagram of the hot-rolled sheet without Y is shown in Figure 12. At S = 0, there is mainly brass texture ({110} 〈112〉), Goss texture, and weak α texture. There are strong Goss textures, weak rotational cube texture, and α texture at the S = 1/4 position. There is a strong α texture at the S = 1/2 position, whose strength point is located at {112} 〈110〉. There are also strong γ texture and rotational cube texture at S = 1/2 position in addition to the α texture.

Figure 11 Grain orientation diagram of hot-rolled sheets: (a) Y-free and (b) Y-bearing.
Figure 11

Grain orientation diagram of hot-rolled sheets: (a) Y-free and (b) Y-bearing.

Figure 12 ODF diagram of φ 2 = 45° at different thicknesses of Y-free hot-rolled sheet: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.
Figure 12

ODF diagram of φ 2 = 45° at different thicknesses of Y-free hot-rolled sheet: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.

The analysis results of α, γ, and η orientation lines with different positions of the hot-rolled plate without Y are shown in Figure 13. It can be seen from Figure 13(a) that there is a great strength difference in the α texture at different positions. The orientation density of α texture is the highest at the position of S = 1/2, which is mainly concentrated near {001} 〈110〉 and {112} 〈110〉. It is higher than that of S = 0 and S = 1/4 positions in the range of φ = 0–60°. From the analysis results of the γ texture in Figure 13(b), it is found that the strength of the γ texture increases with increase in thickness. The strongest γ texture is in the central layer, and the grain orientation is mainly concentrated near {111} 〈110〉 and {111} 〈112〉. From the η orientation line in Figure 13(c), it can be seen that there is a strong Goss texture at the position of S = 1/4, and its strength is obviously higher than that of S = 0 and S = 1/2. This indicates that the Goss texture mainly originates from the subsurface layer of the hot-rolled sheet.

Figure 13 Distribution of orientation lines on different thicknesses of Y-free hot-rolled sheet: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.
Figure 13

Distribution of orientation lines on different thicknesses of Y-free hot-rolled sheet: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.

The φ 2 = 45° ODF diagram of hot-rolled sheet containing Y at different positions is shown in Figure 14. At S = 0, the texture distribution of hot-rolled sheet is dispersed. There are strong copper textures ({112} 〈111〉), weak cube textures, and Goss textures. The texture changes greatly at the S = 1/4 position, the grain orientation is mainly concentrated near the component of {411} 〈148〉. The copper texture ({112} 〈111〉) disappears. The cube texture and Goss texture are enhanced. There are strong cube textures and strong α textures at the S = 1/2 position, but no obvious Goss texture is observed at this position.

Figure 14 ODF diagram of φ 2 = 45° at different thicknesses of hot-rolled sheet containing Y: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.
Figure 14

ODF diagram of φ 2 = 45° at different thicknesses of hot-rolled sheet containing Y: (a) S = 0; (b) S = 1/4; and (c) S = 1/2.

The analysis results of α, γ, and η orientation lines with different positions of Y-containing hot-rolled plates are shown in Figure 15. It can be seen from Figure 15(a) that the α-oriented textures in Y-containing hot-rolled plates are mainly distributed at the positions of S = 1/4 and S = 1/2, which are concentrated near {114} 〈110〉 and {112} 〈110〉. The strength of γ-oriented texture decreases with the increase in the thickness, as shown in Figure 15(b). The γ-oriented texture at S = 0 is mainly concentrated near the {111} 〈112〉 component, while there is no obvious γ-oriented texture at S = 1/2. It can be analyzed from Figure 15(c) that there is a strong cube texture at different thicknesses of Y-containing hot-rolled plates, the strength reaches the highest at S = 1/2. The Goss texture still exists mainly at S = 1/4, which is consistent with the results of Y-free silicon steel.

Figure 15 Distribution of orientation lines on different thicknesses of hot-rolled sheet containing Y: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.
Figure 15

Distribution of orientation lines on different thicknesses of hot-rolled sheet containing Y: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.

There is a strong Goss texture in the subsurface layer of hot-rolled sheet. In the process of hot rolling, strong Goss-oriented grains are formed on the surface and subsurface of the sheet due to the severe shear stress. With the increase in the thickness of the sheet, the shear stress decreases gradually, and {100} grains elongated along the rolling direction are formed in the central layer. However, due to excessive shear stress, dynamic recrystallization occurs on the surface layer, which greatly decreases the strength of the Goss texture. At present, it is generally believed that the accurate {110} 〈001〉 oriented grains in hot-rolled plates can promote the perfect development of secondary recrystallization in the high-temperature annealing process, thus forming a single Goss texture. This is commonly known as texture inheritance [24].

There is a great difference in texture between the hot-rolled sheet without Y and that containing Y. There is mainly brass texture in the surface layer for the samples without Y, and the strength is 3.26. In addition, there is Goss texture with an orientation density of 1.19. With the addition of Y, the main texture type of the surface layer of the hot-rolled sheet changed to a copper texture ({112} 〈111〉), whose strength is 2.92, and the Goss texture strength is only 1.12. Under high shear stress, the initially formed Goss-oriented grains will rotate around the TD axis. When these grains are hindered by horizontal grain boundary or long-strip MnS formed along grain boundary, they will change direction and rotate around the ND axis to form brass texture ({110} 〈112〉) [25]. The migration rate of Σ5 grain boundaries formed by brass-oriented grains is higher than that of Σ9 grain boundaries formed by Goss-oriented grains. The brass-oriented grains will grow up preferentially in the subsequent annealing stage, which is not conducive to the formation of Goss texture [26]. The addition of rare earth Y suppresses the formation of long-strip MnS, which makes the precipitates in the hot-rolled sheet mainly spherical oxide sulfides of Y. The large size Y-bearing inclusions reduce the inhibition of MnS, and the Goss-oriented grains rotate around the TD axis to form copper-oriented grains. In the process of normalizing annealing, some copper-oriented grains will be swallowed by Goss-oriented grains. In the cold rolling process, the remaining copper-oriented grains transform into rotational cube texture. However, due to their small grain size, they have little effect on the formation of Goss texture.

The subsurface layer of the hot-rolled sheet without Y is mainly composed of strong Goss texture, and its strength reaches 5.05. The grain orientation of the central layer is mainly concentrated in the α and γ orientation lines, in which the strength of the rotating cube texture is 5.32. There are strong α* texture and strong cube texture in the subsurface layer of the hot-rolled sheet containing Y, whose orientation density are 3.12 and 1.87, respectively. However, the Goss texture is weak and the strength is only 1.72. The α* texture is mainly distributed near the {411} 〈148〉 component. In the cold rolling process, the {411} 〈148〉 texture changes to α texture, and its heredity in the original hot-rolled plate is not strong. The cube texture of the central layer of the hot-rolled sheet containing Y is obviously enhanced and the strength is 4.17, while the strength of the rotational cube texture is lower, only 0.86. The rotating cubic texture has low energy storage and it is not easy to rotate during cold rolling, which hinders the development of Goss-oriented grains in the annealing stage. In summary, Y has an important influence on the formation of brass texture ({110} 〈112〉), Goss texture, and rotational cube texture in hot-rolled oriented silicon steel. Although the addition of rare earth Y weakens the strength of Goss texture to some extent, brass texture ({110} 〈112〉) and rotational cube texture are greatly reduced, which is favorable for the development of Goss texture in the future.

3.4 Effect of rare earth Y on the texture of cold-rolled sheets

The effect of rare earth Y on the microstructure of cold-rolled sheet is mainly reflected in the cold-rolled shear bands. It can be seen from Figure 16(a) and (b) that there is large plastic deformation, and obvious shear bands are formed during cold rolling. The formation of shear bands is related to the hindrance of dislocation slip. When the normal dislocation slip is hindered, the material undergoes plastic deformation in the form of amorphous shear bands deformation [27]. The distribution of kernel average misorientation (KAM) in the corresponding region is shown in Figure 16(c) and (d). KAM qualitatively reflects the degree of plastic deformation by calculating the average orientation difference between adjacent scanning points within the grains. During the deformation process of polycrystalline metals, the deformation substructure and dislocation density formed in grains with different orientations vary greatly, but the amount of deformation determines the average level of dislocation density in the material. The greater the amount of deformation, the higher the average level of dislocation density in the material [28]. Therefore, the KAM value is indirectly positively correlated with the average level of dislocation density, that is, the higher the overall dislocation density, the greater the KAM value.

Figure 16 Microstructure of cold-rolled sheet and its corresponding KAM distribution diagram: (a and c) Y-free and (b and d) Y-bearing.
Figure 16

Microstructure of cold-rolled sheet and its corresponding KAM distribution diagram: (a and c) Y-free and (b and d) Y-bearing.

The KAM values are shown in Figure 17, where the abscissa represents the KAM value and the ordinate represents the relative frequency. It can be seen that the statistical graphs of KAM values show the law of centralized distribution, with less distribution at both ends of 0–5° and more distribution in the middle. The KAM peaks of the Y-free and Y-bearing cold-rolled sheets appear at 1.5° and 2.5°, respectively, both have a peak frequency of approximately 40%. The addition of rare earth Y increases the KAM value, which means that the dislocation density increases. This is because rare earth Y reacts with oxygen and sulfur in molten steel to form Y-bearing inclusions. Compared with Al2O3 inclusions, Y2O2S inclusions produce more distortion in the matrix under the same strain and accumulated larger misorientation [29,30]. At the same time, Y easily segregates at grain boundaries, which pins grain boundaries and hinders the movement of dislocations, increasing the number of shear bands.

Figure 17 KAM statistical chart of cold-rolled plate (a) Y-free and (b) Y-bearing.
Figure 17

KAM statistical chart of cold-rolled plate (a) Y-free and (b) Y-bearing.

The φ 2 = 45° ODF diagram of the cold-rolled sheets is shown in Figure 18. The texture types in Y-free cold-rolled sheet are basically the same as those of the Y-bearing sheet, which are mainly strong α-oriented and γ-oriented textures. It is usually considered that this is the result of the large shear stress in the cold rolling process, which makes the textures rotate around the 〈110〉//RD axis and 〈111〉//ND axis [31]. There is no obvious Goss texture in the cold-rolled sheets. From the analysis results of the α texture in Figure 19(a), the textures of cold-rolled plates without Y are mainly concentrated near {001} 〈110〉 and {112} 〈110〉 components, whose strengths are 10.4 and 10.8, respectively. The textures of Y-bearing cold-rolled sheet are mainly concentrated near {112} 〈110〉 components with a strength of 8.5. From the distribution of γ orientation lines in Figure 19(b), it can be seen that the strong texture point of cold-rolled sheet without Y is {112} 〈110〉, and the strength is 5.39. While the texture of Y bearing sheet is concentrated between {111} 〈110〉 and {111} 〈112〉 components, and the strength is 5.93. On the η orientation line, the textures of Y-free and Y-bearing sheets are concentrated near {100} 〈001〉, and the strengths are 0.51 and 1.53, respectively.

Figure 18 ODF diagrams of cold-rolled plates of two kinds of experimental steels at φ 2 = 45°: (a) Y-free and (b) Y-bearing.
Figure 18

ODF diagrams of cold-rolled plates of two kinds of experimental steels at φ 2 = 45°: (a) Y-free and (b) Y-bearing.

Figure 19 Distribution diagram of orientation lines of two cold-rolled sheets: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.
Figure 19

Distribution diagram of orientation lines of two cold-rolled sheets: (a) α orientation line; (b) γ orientation line; and (c) η orientation line.

The experimental results show that the textures of the two experimental sheets are typical cold rolling textures. The cold rolling textures in body-centered cubic metals are mainly {001} 〈110〉, {112} 〈110〉, and {111} 〈110〉 components on α-orientation line and {111} 〈112〉 on γ-orientation line. The rotating cube texture ({001} 〈110〉) on the α orientation line has low energy storage and high stability in the rolling process [32]. Figures 12(c) and 19(a) show that the strong rotational cubic texture in the Y-free cold-rolled sheet comes from the central layer of the hot-rolled plate. Although the strength of the rotating cube texture in the Y-bearing hot-rolled plate is weak, the Y-bearing cold-rolled sheet also inherits the weak rotation cube texture. This indicates that the texture is hereditary in silicon steel.

It can be seen from Figures 14 and 19 that the strength of cubic texture in the Y-bearing cold-rolled sheet is lower than that in the Y-bearing hot-rolled sheet, while the rotational cubic texture is slightly enhanced. During the cold rolling process, the cubic texture in the hot-rolled sheet rotates to both sides around the normal direction to form a rotating cubic texture.

According to the KAM value, the addition of Y greatly increases the number of shear bands in the cold-rolled sheet. Some study results have shown that the {111} 〈112〉 components of the γ-oriented line mainly exist in cold-rolled shear bands. The {111} 〈112〉 components will be swallowed by Goss texture during high-temperature annealing, which promotes the development of secondary recrystallization [33]. The coarse grains formed during hot rolling also play an important role in the formation of cold-rolled shear bands [34]. According to Figure 19(b), the {111} 〈112〉 components in cold-rolled sheets are obviously enhanced by the addition of rare earth Y. There is still a weak Goss texture in the cold-rolled plate, and the strength of the Y-bearing cold-rolled plate is slightly higher than that of Y-free sheet, as shown in Figure 19(c). Generally, the addition of rare earth Y in silicon steel enhances the favorable {111} 〈112〉 component in the cold-rolled sheet and reduces the harmful {001} 〈110〉 component.

4 Conclusion

The main results are summarized as follows:

  1. With the addition of rare earth Y, the surface recrystallized grain and the fiber structure parallel to the rolling direction of the hot-rolled plate are larger. The uniformity of the structure is improved. Rare earth Y combines with oxygen and sulfur in molten steel to transform the MnS–Al2O3 inclusions into spherical or ellipsoidal rare earth sulfur oxides. At the same time, the formation of long MnS inclusions is effectively inhibited. The spheroidization modification of inclusions in steel is realized, which is conducive to improving the machinability of steel.

  2. The addition of rare earth Y reduces the brass texture ({110} 〈112〉) of the surface layer and the rotating cube texture of the central layer of the hot-rolled plate to a certain extent. The texture of hot-rolled plate is improved. The micro-texture types of cold-rolled sheets are mainly α-oriented textures and γ-oriented texture. The addition of rare earth Y can increase the dislocation density and the shear band, weaken the α texture and enhance the γ texture in the cold-rolled plate, which provides a favorable environment for the development of Goss texture in the future.

Acknowledgments

The work was financially supported by the National Nature Science Foundation of China under grant nos. 51974102 and 51974103, Hebei Provincial Foundation under grant nos. E2021208006, E2021208017, and E2019208308, Key R&D projects in Hebei Province under grant nos. QN2019029, 20311003D, and 19211009D.

  1. Funding information: The work is financial supported by National Nature Science Foundation of China under grant Nos. 51974102 and 51974103, Hebei Provincial Foundation under grant Nos. E2021208006, E2021208017 and E2019208308, Key R&D projects in Hebei Province Nos. QN2019029, 20311003D and 19211009D.

  2. Author contributions: Zhihong Guo and Yaxu Zheng conceived the work. Liguang Zhu, Xiangyang Li, Huilan Sun, Pengjun Liu and Yu Liu performed the experiment and analyzed the date. Liguang Zhu wrote the manuscript with help from all the other authors. Zhihong Guo and Yaxu Zheng supervised the whole project.

  3. Conflict of interest: The authors declare that they have no known competing financial interests or personal relationships that could have appeared to influence the work reported in this paper.

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Received: 2022-05-23
Revised: 2022-07-11
Accepted: 2022-07-18
Published Online: 2022-12-14

© 2022 Liguang Zhu et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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https://doi.org/10.1515/htmp-2022-0232
Keywords for this article
oriented silicon steel; rare earth Y; hot rolling; cold rolling; texture; precipitates
Creative Commons
BY 4.0

Articles in the same Issue

  1. Research Articles
  2. Numerical and experimental research on solidification of T2 copper alloy during the twin-roll casting
  3. Discrete probability model-based method for recognition of multicomponent combustible gas explosion hazard sources
  4. Dephosphorization kinetics of high-P-containing reduced iron produced from oolitic hematite ore
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  11. Carbothermal reduction of red mud for iron extraction and sodium removal
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  14. Corrosion behavior of WC–Co coating by plasma transferred arc on EH40 steel in low-temperature
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  16. Application on oxidation behavior of metallic copper in fire investigation
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  18. Prediction model of interfacial heat transfer coefficient changing with time and ingot diameter
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  27. Effect of chloride ion concentration on stress corrosion cracking and electrochemical corrosion of high manganese steel
  28. Prediction of oxygen-blowing volume in BOF steelmaking process based on BP neural network and incremental learning
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