# Effect of Hot Deformation Temperature on Texture Formation Regularity of CGO Silicon Steel under High Deformation Rate

Authors: Zhi-chao Li; Ning Dang; Zhen-li Mi
Journal: Advances in Materials Science and Engineering
 (2016)

---

## Abstract

The influence of hot deformation temperature on microstructure and texture of CGO silicon steel under the condition of a high deformation rate (100s
-
1) was studied by SEM and EBSD techniques. The results indicate that the typical microstructures at room temperature consist of ferrite and pearlite under different hot deformation temperatures. The higher deformation temperature is beneficial to obtain a more uniform recrystallization microstructure and lower pearlite content. Cubic texture {
100
}
001 and rotated cubic texture {
100
}
0
11 are dominant texture components in the tested steels, and {
111
}
112 texture in γ fiber is also strong, the intensity of which is higher than that of {
111
}
110 texture. Goss texture {
110
}
001 is weak. With the rising of the hot deformation temperature, {
100
}
0
11 texture decreases firstly and then increases at 1100°C. When the hot deformation temperature raises from 800°C to 900°C, {
111
}
112 texture shows an increasing trend, while {
111
}
110 texture content is stable. When the temperature further increases to 1100°C and 1150°C, {
111
}
112 and {
111
}
110 textures are slightly weakened.


---

## Body

## 1. Introduction

Grain-oriented silicon steel is an important soft magnetic material which is widely applied in electronic and electric power industry and mainly used for the manufacture of transformers and so forth [1, 2]. The metallurgical factors which affect the magnetic properties include the steel composition, microstructure, crystallographic texture, grain size, and internal stress, of which microstructure and texture are important influencing factors [3]. Due to the obvious inheritance of the textures [4] during manufacturing, the hot rolling textures have significant effect [5] on the texture evolution during the following process of grain-oriented silicon steel. The research on the origin and evolution of textures is beneficial for the optimization of texture control in the production processes. The deformation rate applied to grain-oriented silicon steel in actual hot rolling process is relatively high. Despite numerous researches on the effect of the hot rolling temperature on the microstructure and texture of grain-oriented silicon steel at present, the research under the condition of a high strain rate is not much. Liu et al. [6] studied hot rolling texture distribution at different temperatures using a thermal simulator under low deformation rate condition. In this study, the texture evolution during hot rolling process was simulated by uniaxial compression. The results show that gamma textures which have strong inheritance play an important role in the subsequent process and improve the concentration of textures after secondary recrystallization. Zhang et al. [7] studied hot rolling textures of 3.2% Si grain-oriented silicon steel and the inheritance of textures between hot rolling and subsequent processes, this research focused on microstructure, and texture evolution of the static recrystallization occurred in the process of annealing after the deformation of CGO silicon steel. The results show that there is no obvious heterogeneity along the thickness direction after primary recrystallization, and {
111
}
110 texture is the strongest texture component, and there is a certain intensity of the Goss texture. The texture formation mechanism is different between dynamic recrystallization and static recrystallization. The texture is definitely different between hot compression and hot rolling which is used industrially, and Zhichao et al. [8, 9] have done some researches on the formation and evolution of textures in hot rolling process, but the thermal compression process is not involved in the same deformation conditions, and this process has significant impact on the texture evolution during hot deformation. The rough rolling of CGO steel usually has a high rolling speed which is closed to 100 s
-
1, so that the texture evolution during this process is difficult to analyze, and limited work is available in the literature on this impact. It is therefore important to summarize the texture evolution law under the large deformation rate with different temperatures. This paper investigate the effect of hot deformation temperature on the microstructure and texture of grain-oriented silicon steel under the condition of a high deformation rate, which provides reference to the texture control during the manufacturing process of grain-oriented silicon steel.


## 2. Experimental Materials and Methods

Experimental materials are cut from an ingot which has a chemical composition of 0.065% C, 2.95% Si, 0.15% Mn, and 0.027% S and processed into cylinder specimens. The experimental process is illustrated in Figure1. The specimens were heated to 1300°C at 10°C/s, held for 3 min, and then cooled, respectively, to 800, 850, 900, 1100, and 1150°C at 4°C/s and conducted uniaxial compression with the same deformation rate of 100 s
-
1. Test samples were cut along the axis of compression specimen and their microstructures in center layer were analyzed by field emission scanning electron microscopy (SEM) after mechanical polishing and etching. The orientation distributions were measured by electron back-scattered diffraction (EBSD) attached to Zeiss ultra 55 SEM. The experimental data were analyzed by Channel 5 software and the contents of typical textures were obtained.Figure 1
Processing route of thermal simulation experiment.


## 3. Results and Discussion

### 3.1. Microstructures of Experimental Steels

The phase diagrams of the experimental steels are calculated using Thermo-Calc software. Figure2(a) presents the effect of carbon content on the microstructure of the steel. Figure 2(b) presents the dependence of the relative qualities of austenite, ferrite, cementite, and so forth on the temperature. It can be seen from Figure 2 that when the C content is in a range of 0.04–0.78%, the high temperature microstructure at 1200°C is single-phase austenite. During the cooling process, the proeutectoid ferrite occurs firstly, and two-phase range of austenite and ferrite exists. With the formation of ferrite, the concentration of carbon in ferrite is very low and reduces with the decreasing of temperature, and C atoms diffuse to the surrounding austenite. This process is accompanied with the decreasing of temperature and the formation of ferrite continuously. At the five experimental temperatures between 800 and 1100°C, deformation specimens are at the “ferrite + austenite” two-phase range, the austenite has the highest relative content at 1180°C, and the content will reduce with the decreasing of temperature.Figure 2
Thermodynamic calculated phase diagram. (a) Fe-C phase diagram; (b) the relative amount of different phases change with temperature.
(a)
(b)Figures3(a)–3(e) present the microstructures of the experimental steels at different deformation temperatures under a high deformation rate. Figure 3(f) illustrates the average grain size of different specimens. Typical microstructures consist of ferrite and pearlite, and the microstructure morphologies of the samples show significant differences under various deformation temperatures. The recrystallization grains of the specimens deformed at 850 and 900°C are coarse, and their grain size distributions are inhomogeneous. At the deformation temperatures of 1100°C and 1150°C, the recrystallization degrees of part grains are low and the content of pearlite is higher. With the increases of deformation temperature, the recrystallization grain size decreases gradually and the grain size distribution is more uniform. It can be obtained from Figure 2(b) that, with the increasing of deformation temperature, the austenite proportion becomes larger and the supersaturation of C in austenite decreases. The deformed austenite recrystallizes sufficiently, leading to fine and uniform size of deformed austenite. At the same time, crystal distortion is small and is not conducive for the diffusion of the C atoms from inside of grains to grain boundaries where pearlite nucleates, which lead to the difficulty of alternative growth of pearlite lamellae. The pearlite layer is thinner after high temperature deformation and pearlite area is smaller. In addition, due to the increasing of deformed austenite, pearlite distribution becomes more uniform after phase transformation. During 800~900°C, recrystallization degree is weak, distortion of deformed austenite is large, and it is conductive to the diffusion of C atoms. Coarse pearlite is formed after phase transformation and distributed intensively because of the decreasing of deformed austenite. During rolling in two-phase range of ferrite and austenite, the degree of recrystallization is lower at low temperature. At a higher deformation temperature, ferrite and austenite are compressed and form dislocation-substructure inside of the grains [9]. The higher temperature provides driving force for the grain growth, which leads to the recrystallization and the growth of ferrite grains in a wide range. When the deformation temperature is low, austenite grains are elongated without recrystallization and dislocation-substructures accumulated within grains, which become nucleation sites of phase transformation. The elongated austenite grain boundaries restrict the growth of newly formed microstructures. So it can be observed from Figure 3(b) that the grain bands did not grow up sufficiently between the gaps of larger size grains. During the cooling, ferrite and cementite will generate inside of austenite and the newly formed ferrite has small size because of the limitation of austenite grain boundaries. At lower deformation temperature, there are long strip recovery microstructures which remain in the matrix, such as Figures 3(b) and 3(c).Figure 3
Microstructure of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C; (f) average grain size variation.
(a)
(b)
(c)
(d)
(e)
(f)


### 3.2. Textures of Experimental Steels

The initial textures before high temperature deformation are distributed randomly because the experimental materials are cut from forged CGO silicon steel. The orientation image maps of the experimental steels with high deformation rate at different deformation temperatures were shown in Figure4 and the area fractions of different textures were listed in Table 1 and Figure 5. Various colors represent grains with different orientation, Goss {
110
}
001 oriented grains is red, {
111
}
121 oriented grains is yellow, {
111
}
100 oriented grains is blue, cubic oriented grains is brown, rotated cube {
100
}
011 oriented grains is green, brass-type {
110
}
112 oriented grains is purple, and copper-type {
112
}
111 oriented grains is blue.Table 1
Texture contents of samples under different hot deformation temperatures in tested steels (%).
Hot deforming temperatures/°C
800
850
900
1100
1150
100

001
19.4
7.8
13.4
13.2
17.9
100

011
17.2
15.4
4.8
11.0
22.9
1
1
0

001
2.2
2.0
8.6
2.9
1.3
1
1
0

112
4.8
5.3
5.2
7.7
2.9
1
11

110
9.5
6.5
9.9
7.5
6.7
1
11

112
8.1
8.5
11.2
8.0
7.5
1
12

111
8.3
16.6
8.5
5.9
7.5Figure 4
EBSD analysis of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C.
(a)
(b)
(c)
(d)
(e)Figure 5
ODF analysis of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C; (f) distribution of main orientations in Euler space for silicon steel [10].
(a)
(b)
(c)
(d)
(e)
(f)Cubic texture{
100
}
001, rotated cube texture {
100
}
011, gamma fiber textures including {
111
}
112 and {
111
}
110 textures, Goss texture {
110
}
001, copper-type texture {
112
}
111, and brass-type {
110
}
112 texture are important texture components in grain-oriented silicon steel and their existence in hot rolled plate will influence the subsequent texture development [11–13].As can be seen in Table1, in general, cube texture {
100
}
001 and rotated cube texture {
100
}
011 are dominant texture components at different hot deformation temperatures. In addition, the contents of {
111
}
112 in γ fiber and copper-type {
112
}
111 texture are also higher. Goss texture {
110
}
001 is weak and its content is low. The contents of texture components will change at various deformation temperatures. For instance, with the rising of hot deformation temperature, the content of rotated cube texture {
100
}
011 decreases first and then increases further. The content of {
111
}
112 texture and copper-type texture {
112
}
111 increase first and then reduce.From Table1 and Figure 6 it can be seen that the content of Goss texture {
110
}
001 is low at most of the hot deformation temperatures. Goss texture of hot rolled plate originates from the broken columnar crystal with 100 direction in casting billet [14–16]. During the hot deformation process, Goss texture formed by shear strain will transit to other orientations under high deformation rate because of the migration of the high angle grain boundaries. Goss oriented grains will transform to brass-type texture {
110
}
112 and copper-type {
112
}
111 texture because of the orientation conversion relationship. The intensity of copper-type texture {
112
}
111 is higher than the Goss texture {
110
}
001 which can be seen in Table 1. During the cold rolling, Goss oriented grains descend from the broken columnar grains with 100 direction of casting billet and are prone to transit to {
223
}
110 texture along certain path. However, it is difficult to obtain the final {
223
}
110 texture because of the restriction of certain conditions. In brief, the content of Goss texture {
110
}
001 is low in the steels which experienced thermal deformation.Figure 6
Texture contents of samples under different hot deformation temperatures in tested steel.Rotated cube texture{
100
}
0
11 is the common component in hot rolled plate. From Table 1 and Figure 5 it can be seen that, with the rising of deformation temperature, the content of {
100
}
011 texture decreases first and then increases. The texture characteristics of single crystal under different rolling reductions indicate that when the rolling reduction was greater than 60%, {
211
}
011 and {
100
}
011 texture components are enhanced because of {
211
}
111 slip system during thermal deformation [17, 18], which explains the fact that the content of rotated cube texture {
100
}
110 is high at all the deformation temperature. The rotated cube texture {
100
}
110 is difficult to recrystallize [19] and should be eliminated in the subsequent process. The typical texture during austenite recrystallization is cubic texture. All steels with different deformation temperature therefore have a high proportion of {
100
}
001 cubic texture. However, the cubic texture is an unfavorable component which is formed by the initial columnar crystal in grain-oriented silicon steel. Researches [10] indicated that, in the subsequent process, the repeated rolling and annealing can weaken the heredity of {
100
} texture and decrease the {
100
}
001 cubic texture.As can be seen in Figure4, for the grains with {
111
} crystal plane, when the hot deformation temperature increased from 800°C to 900°C, {
111
}
112 texture shows an increasing trend, while {
111
}
110 texture is relatively stable. When the hot deformation temperature was increased to 1100°C and even 1150°C further, {
111
}
112 texture and {
111
}
110 texture are slightly weakened. {
111
} plane textures are the typical recrystallization texture, whose proportion in experimental steels is closely related to the recrystallization degree. {
111
} plane textures provide nucleation sites for the abnormal growth of Goss grains during secondary recrystallization process [1, 12], which are important growth environment for Goss oriented grains [20, 21]. In the recrystallization after deformation, the stored energies are different in various texture components, which are {
001
}
110, {
112
}
110, {
111
}
110, and {
111
}
112 in an order from strong to weak. {
111
}
110 and {
111
}
112 oriented grains can nucleate and grow preferentially due to higher stored energies. From Figure 4 it can be seen that {
111
}
110 and {
111
}
112 oriented grains present a higher degree of recrystallization. Because it is easier for {
111
}
112 texture to form shear bands compared with {
111
}
110 texture [22], {
111
}
112 oriented grains are more likely to grow up. From Table 1 it can be seen that the intensity of {
111
}
112 texture is stronger than {
111
}
100 texture in multiple thermal deformation temperatures.During the hot compression with high strain rate of CGO silicon steel, scatteredα fiber texture merged into {
100
}
011 texture and cube {
100
}
0
11 texture was formed because of strong rotation of grains. Under high stain rate, cubic texture {
100
}
001 keeps stable and takes a great proportion. Copper texture {
112
}
111 and brass texture {
110
}
112 are typical shear textures. Brass texture {
110
}
112 is derived from shear layer which forms at the subsurface of the plate during hot rolling and is closely related to Goss texture {
110
}
001. The formation of brass texture {
110
}
112 is due to the inhibition of grain boundaries. The rotation of Goss oriented grains along TD direction is impeded so that the grains rotate along ND direction instead.


## 3.1. Microstructures of Experimental Steels

The phase diagrams of the experimental steels are calculated using Thermo-Calc software. Figure2(a) presents the effect of carbon content on the microstructure of the steel. Figure 2(b) presents the dependence of the relative qualities of austenite, ferrite, cementite, and so forth on the temperature. It can be seen from Figure 2 that when the C content is in a range of 0.04–0.78%, the high temperature microstructure at 1200°C is single-phase austenite. During the cooling process, the proeutectoid ferrite occurs firstly, and two-phase range of austenite and ferrite exists. With the formation of ferrite, the concentration of carbon in ferrite is very low and reduces with the decreasing of temperature, and C atoms diffuse to the surrounding austenite. This process is accompanied with the decreasing of temperature and the formation of ferrite continuously. At the five experimental temperatures between 800 and 1100°C, deformation specimens are at the “ferrite + austenite” two-phase range, the austenite has the highest relative content at 1180°C, and the content will reduce with the decreasing of temperature.Figure 2
Thermodynamic calculated phase diagram. (a) Fe-C phase diagram; (b) the relative amount of different phases change with temperature.
(a)
(b)Figures3(a)–3(e) present the microstructures of the experimental steels at different deformation temperatures under a high deformation rate. Figure 3(f) illustrates the average grain size of different specimens. Typical microstructures consist of ferrite and pearlite, and the microstructure morphologies of the samples show significant differences under various deformation temperatures. The recrystallization grains of the specimens deformed at 850 and 900°C are coarse, and their grain size distributions are inhomogeneous. At the deformation temperatures of 1100°C and 1150°C, the recrystallization degrees of part grains are low and the content of pearlite is higher. With the increases of deformation temperature, the recrystallization grain size decreases gradually and the grain size distribution is more uniform. It can be obtained from Figure 2(b) that, with the increasing of deformation temperature, the austenite proportion becomes larger and the supersaturation of C in austenite decreases. The deformed austenite recrystallizes sufficiently, leading to fine and uniform size of deformed austenite. At the same time, crystal distortion is small and is not conducive for the diffusion of the C atoms from inside of grains to grain boundaries where pearlite nucleates, which lead to the difficulty of alternative growth of pearlite lamellae. The pearlite layer is thinner after high temperature deformation and pearlite area is smaller. In addition, due to the increasing of deformed austenite, pearlite distribution becomes more uniform after phase transformation. During 800~900°C, recrystallization degree is weak, distortion of deformed austenite is large, and it is conductive to the diffusion of C atoms. Coarse pearlite is formed after phase transformation and distributed intensively because of the decreasing of deformed austenite. During rolling in two-phase range of ferrite and austenite, the degree of recrystallization is lower at low temperature. At a higher deformation temperature, ferrite and austenite are compressed and form dislocation-substructure inside of the grains [9]. The higher temperature provides driving force for the grain growth, which leads to the recrystallization and the growth of ferrite grains in a wide range. When the deformation temperature is low, austenite grains are elongated without recrystallization and dislocation-substructures accumulated within grains, which become nucleation sites of phase transformation. The elongated austenite grain boundaries restrict the growth of newly formed microstructures. So it can be observed from Figure 3(b) that the grain bands did not grow up sufficiently between the gaps of larger size grains. During the cooling, ferrite and cementite will generate inside of austenite and the newly formed ferrite has small size because of the limitation of austenite grain boundaries. At lower deformation temperature, there are long strip recovery microstructures which remain in the matrix, such as Figures 3(b) and 3(c).Figure 3
Microstructure of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C; (f) average grain size variation.
(a)
(b)
(c)
(d)
(e)
(f)


## 3.2. Textures of Experimental Steels

The initial textures before high temperature deformation are distributed randomly because the experimental materials are cut from forged CGO silicon steel. The orientation image maps of the experimental steels with high deformation rate at different deformation temperatures were shown in Figure4 and the area fractions of different textures were listed in Table 1 and Figure 5. Various colors represent grains with different orientation, Goss {
110
}
001 oriented grains is red, {
111
}
121 oriented grains is yellow, {
111
}
100 oriented grains is blue, cubic oriented grains is brown, rotated cube {
100
}
011 oriented grains is green, brass-type {
110
}
112 oriented grains is purple, and copper-type {
112
}
111 oriented grains is blue.Table 1
Texture contents of samples under different hot deformation temperatures in tested steels (%).
Hot deforming temperatures/°C
800
850
900
1100
1150
100

001
19.4
7.8
13.4
13.2
17.9
100

011
17.2
15.4
4.8
11.0
22.9
1
1
0

001
2.2
2.0
8.6
2.9
1.3
1
1
0

112
4.8
5.3
5.2
7.7
2.9
1
11

110
9.5
6.5
9.9
7.5
6.7
1
11

112
8.1
8.5
11.2
8.0
7.5
1
12

111
8.3
16.6
8.5
5.9
7.5Figure 4
EBSD analysis of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C.
(a)
(b)
(c)
(d)
(e)Figure 5
ODF analysis of samples under different hot deformation temperatures. (a) 800°C; (b) 850°C; (c) 900°C; (d) 1100°C; (e) 1150°C; (f) distribution of main orientations in Euler space for silicon steel [10].
(a)
(b)
(c)
(d)
(e)
(f)Cubic texture{
100
}
001, rotated cube texture {
100
}
011, gamma fiber textures including {
111
}
112 and {
111
}
110 textures, Goss texture {
110
}
001, copper-type texture {
112
}
111, and brass-type {
110
}
112 texture are important texture components in grain-oriented silicon steel and their existence in hot rolled plate will influence the subsequent texture development [11–13].As can be seen in Table1, in general, cube texture {
100
}
001 and rotated cube texture {
100
}
011 are dominant texture components at different hot deformation temperatures. In addition, the contents of {
111
}
112 in γ fiber and copper-type {
112
}
111 texture are also higher. Goss texture {
110
}
001 is weak and its content is low. The contents of texture components will change at various deformation temperatures. For instance, with the rising of hot deformation temperature, the content of rotated cube texture {
100
}
011 decreases first and then increases further. The content of {
111
}
112 texture and copper-type texture {
112
}
111 increase first and then reduce.From Table1 and Figure 6 it can be seen that the content of Goss texture {
110
}
001 is low at most of the hot deformation temperatures. Goss texture of hot rolled plate originates from the broken columnar crystal with 100 direction in casting billet [14–16]. During the hot deformation process, Goss texture formed by shear strain will transit to other orientations under high deformation rate because of the migration of the high angle grain boundaries. Goss oriented grains will transform to brass-type texture {
110
}
112 and copper-type {
112
}
111 texture because of the orientation conversion relationship. The intensity of copper-type texture {
112
}
111 is higher than the Goss texture {
110
}
001 which can be seen in Table 1. During the cold rolling, Goss oriented grains descend from the broken columnar grains with 100 direction of casting billet and are prone to transit to {
223
}
110 texture along certain path. However, it is difficult to obtain the final {
223
}
110 texture because of the restriction of certain conditions. In brief, the content of Goss texture {
110
}
001 is low in the steels which experienced thermal deformation.Figure 6
Texture contents of samples under different hot deformation temperatures in tested steel.Rotated cube texture{
100
}
0
11 is the common component in hot rolled plate. From Table 1 and Figure 5 it can be seen that, with the rising of deformation temperature, the content of {
100
}
011 texture decreases first and then increases. The texture characteristics of single crystal under different rolling reductions indicate that when the rolling reduction was greater than 60%, {
211
}
011 and {
100
}
011 texture components are enhanced because of {
211
}
111 slip system during thermal deformation [17, 18], which explains the fact that the content of rotated cube texture {
100
}
110 is high at all the deformation temperature. The rotated cube texture {
100
}
110 is difficult to recrystallize [19] and should be eliminated in the subsequent process. The typical texture during austenite recrystallization is cubic texture. All steels with different deformation temperature therefore have a high proportion of {
100
}
001 cubic texture. However, the cubic texture is an unfavorable component which is formed by the initial columnar crystal in grain-oriented silicon steel. Researches [10] indicated that, in the subsequent process, the repeated rolling and annealing can weaken the heredity of {
100
} texture and decrease the {
100
}
001 cubic texture.As can be seen in Figure4, for the grains with {
111
} crystal plane, when the hot deformation temperature increased from 800°C to 900°C, {
111
}
112 texture shows an increasing trend, while {
111
}
110 texture is relatively stable. When the hot deformation temperature was increased to 1100°C and even 1150°C further, {
111
}
112 texture and {
111
}
110 texture are slightly weakened. {
111
} plane textures are the typical recrystallization texture, whose proportion in experimental steels is closely related to the recrystallization degree. {
111
} plane textures provide nucleation sites for the abnormal growth of Goss grains during secondary recrystallization process [1, 12], which are important growth environment for Goss oriented grains [20, 21]. In the recrystallization after deformation, the stored energies are different in various texture components, which are {
001
}
110, {
112
}
110, {
111
}
110, and {
111
}
112 in an order from strong to weak. {
111
}
110 and {
111
}
112 oriented grains can nucleate and grow preferentially due to higher stored energies. From Figure 4 it can be seen that {
111
}
110 and {
111
}
112 oriented grains present a higher degree of recrystallization. Because it is easier for {
111
}
112 texture to form shear bands compared with {
111
}
110 texture [22], {
111
}
112 oriented grains are more likely to grow up. From Table 1 it can be seen that the intensity of {
111
}
112 texture is stronger than {
111
}
100 texture in multiple thermal deformation temperatures.During the hot compression with high strain rate of CGO silicon steel, scatteredα fiber texture merged into {
100
}
011 texture and cube {
100
}
0
11 texture was formed because of strong rotation of grains. Under high stain rate, cubic texture {
100
}
001 keeps stable and takes a great proportion. Copper texture {
112
}
111 and brass texture {
110
}
112 are typical shear textures. Brass texture {
110
}
112 is derived from shear layer which forms at the subsurface of the plate during hot rolling and is closely related to Goss texture {
110
}
001. The formation of brass texture {
110
}
112 is due to the inhibition of grain boundaries. The rotation of Goss oriented grains along TD direction is impeded so that the grains rotate along ND direction instead.


## 4. Conclusions

(1)
The typical microstructures at room temperature of CGO silicon steel after hot deformation are ferrite and pearlite, and there are some differences in grain size distributions and morphologies. A high hot deformation temperature is benefit to obtain a more uniform recrystallized microstructure and lower pearlite content. A low deformation temperature leads to higher pearlite content and partial recrystallization.
(2)
The cubic texture{
100
}
001 and rotated cubic texture {
100
}
011 are dominant texture components in the tested steels after hot deformation. The {
111
}
112 texture in γ fiber is also strong, and its strength is higher than that of {
111
}
110 texture, whereas the content of Goss texture {
110
}
001 is very low.
(3)
With the rising of deformation temperature, the content of the rotated cube{
100
}
011 texture decreases first and then increases when the deformation temperature further achieved to 1100°C; when the deformation temperature raises from 800°C to 900°C, {
111
}
112 texture shows an increasing trend, and {
111
}
110 texture is more stable. When the hot deformation temperature continues to increase to 1100°C and 1150°C, {
111
}
112 texture and {
111
}
110 texture are slightly weakened.



---

*Source: 7010613-2016-08-31.xml*