Production method of grain-oriented magnetic plate steel. RU patent 2508411.

FIELD: metallurgy.

SUBSTANCE: invention involves hot rolling of material from silicon steel containing the following, wt %: Si 0.8 to 7, Al diluted in acid 0.01 to 0.065, N 0.004 to 0.012, Mn 0.05 to 1 and B 0.0005 to 0.0080, C 0.085 or less, Ti 0.004 or less, at least one element chosen from the group consisting of S and Se, which are 0.003 to 0.015 wt %, Fe and inevitable impurities are the rest, annealing of a hot-rolled steel strip, single or multiple cold rolling, decarburising annealing for primary recrystallisation, application of an annealing separator containing MgO as its main component and final annealing for secondary recrystallisation; besides, between the beginning of decarburising annealing (stage S4) and occurrence of crystals of secondary recrystallisation at final decarburisation (stage S5) there performed is nitrate treatment (stage S6) for increase in content of N in a decarburised annealed steel strip, and at hot rolling (stage S1) material of silicon steel is exposed at the temperature of 1000 to 800°C during 300 seconds or longer, and then, finish rolling is performed.

EFFECT: providing high density of a magnetic flux in steel.

9 cl, 11 dwg, 16 tbl, 19 ex

The technical field

[0001] the Present invention relates to a method of manufacturing textured magnetic steel sheet, suitable for iron cores or similar electronic devices.

The level of technology

[0002] Textured electrical sheet steel is magnetic soft material and is used for iron cores or similar electrical equipment, such as transformers. The content of Si in textured electrical sheet steel is approximately 7 wt.% or less. Grains of textured electrical sheet steel are strongly integrated in the orientation {110} <001> the Miller indices. The orientation of the crystal grains regulate, using the phenomenon of the catastrophic growth of grains, called the term «secondary recrystallization».

[0003] To regulate secondary recrystallization it is important to adjust the structure (the structure of primary recrystallization)received by the primary recrystallization before secondary recrystallization, and adjust the fine-grained selection, called «inhibitor» or « on grain boundary element». Function inhibitor is that it promotes a preferred growth of crystalline grains with a focus {110} <001> in the structure of primary recrystallization and inhibits the growth of other crystal grains.

[0004] Thus, the traditional range of suggestions were made for the effective allocation inhibitor.

[0005] However, when traditional technologies were unable to provide a stable industrial production textured electrical sheet steel of a high magnetic flux density (magnetic induction).

List of references

[0006] - Patent literature

- Patent literature 1: publication of the Japanese considered the patent application № 30-003651

- Patent literature 2: the publication of the Japanese considered the patent application № 33-004710

- Patent literature 3: publication of the Japanese considered the patent application № 51-013469

- Patent literature 4: publication of the Japanese considered the patent application № 62-045285

- Patent literature 5: a Japanese patent publication № 03-002324

- Patent literature 6: U.S. patent # 3905842

- Patent literature 7: U.S. patent # 3905843

- Patent literature 8: a Japanese patent publication No 01-230721

- Patent literature 9: a Japanese patent publication № 01-283324

- Patent literature 10: a Japanese patent publication № 10-140243

- Patent literature 11: a Japanese patent publication № 2000-129352

- Patent literature 12: a Japanese patent publication № 11-050153

- Patent literature 13: a Japanese patent publication № 2001-152250

- Patent literature 14: a Japanese patent publication № 2000-282142

- Patent literature 15: a Japanese patent publication № 11-335736

[0007] non-patent literature

Non-patent literature 1: Trans. The Met. Soc. AIME, so 212, C. 769/781, 1958

Non-patent literature 2: Japan J. Inst. Metals, I. 27, n 186, 1963

Non-patent literature 3: Tetsu-to-Hagane (Iron and Steel), 53, C. 1007-1023, 1967

Non-patent literature 4: Japan J. Inst. Metals, I. 43, C. 175-181, 1979; and Japan J. Inst. Metals, I. 44, S. 419/424, 1980

Non-patent literature 5: Materials Science Forum, so 204-206, C. 593-598, 1996

Non-patent literature 6: IEEE Trans. Mag., T. MAG-13, C. 1427

The essence of the invention

Technical problem

[0008] the Objective of this invention is to provide a method for the production of textured magnetic sheet steel oriented structure), which provides a stable industrial production textured magnetic sheet steel with high magnetic flux density.

[0009] Method of production textured electrical sheet steel according to the first aspect of the present invention includes: hot rolling of material from silicon steel for obtaining hot-rolled steel strip, with material from silicon steel contains from 0.8 wt.% up to 7 wt.% Si, from 0.01 wt.% to 0,065 wt.% soluble in acid Al, from 0.004% Mas. to 0,012 wt.% N, from 0.05 wt.% up to 1 wt.% Mn and from 0.0005 wt.% to 0,0080 wt.% B, material from silicon steel additionally contains at least one member selected from the group consisting of S and Se, components in the amount from 0.003% Mas. to 0.015% contents C is 0,085 wt.% or less, and the rest consists of Fe and unavoidable impurities; annealing hot-rolled steel strip for receipt of annealed steel strips; single-entry or multiple-entry cold rolling annealed steel strips for obtaining cold-rolled steel strip; annealing cold-rolled steel strip for obtaining annealed steel strips, in which is caused by primary recrystallization; application of separator for annealing, containing MgO as their main component steel strip; and invoking secondary recrystallization final annealing annealed steel strips in a way that includes in addition to conducting processing, which increases the N content annealed steel strip, between the beginning of the annealing and the emergence of secondary recrystallization in the final annealing, hot rolling includes: keeping material from silicon steel in the temperature range of between 1,000 degrees C and 800 degrees C in 300 seconds or longer; and then conducting of finishing.

[0010] Method of production textured electrical sheet steel according to the second aspect of the present invention is a method according to the first aspect, additionally including before hot rolling heating material from silicon steel at a given temperature, which represents the temperature T1 (C) or less, in the case, when in a piece of silicon steel does not contain Se, and the temperature T1 is expressed below in equation (1).

,82-log([Mn]

[S]))-273 (1)

Here [Mn] is the Mn content (wt.%) in the material from silicon steel, and [S] is the content of S (wt.%) in the material from silicon steel.

[0011] Method of production textured electrical sheet steel according to the third aspect of the present invention is a method according to the first aspect, additionally including before hot rolling heating material from silicon steel at a given temperature, which represents the temperature T2 (C) or less, in the case, when in a piece of silicon steel does not contain S, the temperature T2 is expressed below equation (2).

,08-log([Mn]

[Se]))-273 (2)

Here [Mn] represents the Mn content (wt.%) in the material from silicon steel, and the [Se] represents the contents of the Se (wt.%) in the material from silicon steel.

[0012] Method of production textured electrical sheet steel according to the fourth aspect of the present invention is a method according to the first aspect, additionally including before hot rolling heating material from silicon steel at a given temperature, which represents the temperature T1 (C) or less and temperature T2 (C) or less, in the case, when in a piece of silicon steel contains S and Se, and the temperature T1 expressed by equation (1), and the temperature T2 expressed by equation (2).

[0013] Method of production textured electrical sheet steel according to the fifth aspect of the present invention is a method, in accordance with any of the aspects of the first to fourth in which treatment is carried out under condition that the content of N [N] steel band received after processing satisfies the following inequality (3).

14/27[Al]

14/47[Ti] (3)

Here the [N] is the N content (wt.%) the steel band received after processing, [Al] is soluble in acid Al (wt.%) the steel band received after processing [B] represents the content of B (wt.%) the steel band received after processing, and the [Ti] represents the contents of Ti (wt.%) the steel band received after processing.

[0014] Method of production textured electrical sheet steel according to the sixth aspect of the present invention is a method, in accordance with any of the aspects of the first to fourth in which treatment is carried out under condition that the content of N [N] steel band received after processing satisfies the following inequality (4).

14/47[Ti] (4)

6 represents the image of the results of the second experiment (the ratio between the number of B, not emitted in the form of BN, and magnetic property after the final annealing);

Fig.7 is a picture of the results of the second experiment (the ratio between the terms of the hot rolling and magnetic property after the final annealing);

Fig.8 is a picture of the results of the third experiment (the ratio between the secretions in the hot-rolled steel strip and magnetic property after the final annealing);

figure 9 represents the image results of the third experiment (the ratio between the number of B, not emitted in the form of BN, and magnetic property after the final annealing);

figure 10 represents the image of the results of the third experiment (the ratio between the terms of the hot rolling and magnetic property after the final annealing);

figure 11 represents the ratio between the separated number BN, temperature exposure and exposure times.

Description of options for the implementation

[0017] the Authors of the present invention believe that in the case of production textured electrical sheet steel material silicon steel, a specified substance containing B released form B can affect the behavior of secondary recrystallization, and, therefore, conducted a variety of experiments. Here will be briefly described the method of production textured electrical sheet steel. Figure 1 is a block diagram showing the way to the production of textured electrical sheet steel.

[0018] First, as shown in figure 1, stage S1 material from silicon steel (slabs) with a given composition, containing B, is hot rolling. By hot rolling receive hot-rolled steel strip. Then on the stage of the S2 hold annealing and hot-rolled steel strip to normalize (arrange) the structure of hot-rolled steel strip and adjust the selection inhibitors. By annealing receive a steel band. After this stage S3 carrying cold rolling annealed steel strips. Cold rolling treatment can only be performed once, or it can be a lot of times, carrying between intermediate annealing. By cold rolling receive a cold rolled steel strip. Thus, in the case of intermediate annealing, you can also skip annealing of hot-rolled steel cold rolling of strip before, spending annealing (stage S2) for intermediate annealing. That is, annealing (stage S2) can be carried out on hot-rolled steel strip, or you can also hold the annealing of steel strip, obtained after a single cold rolling and before the final cold rolling.

[0019] After cold rolling on the stage of the S4 hold annealing cold-rolled steel strip. In the process of annealing is a primary recrystallization. In addition, by annealing receive a steel band. Next on stage S5 on the surface annealed steel strips put a separator for annealing, containing MgO (magnesium oxide) as its main component, and spend the final annealing. When the final annealing occurs secondary recrystallization, and on the surface of the steel strip is formed and cleaned glass film containing forsterite as its main component. In the result of secondary recrystallization receive secondary structure, having texture . By the final annealing get ready a steel band. In addition, between the beginning of the annealing and the emergence of secondary recrystallization in the final annealing spend processing (phase S6), which increases the amount of nitrogen in steel strip.

[0020] in This way, can be obtained textured electrical sheet steel.

[0021] in addition, although the details will be described later, but as a material from silicon steel used material containing 0.8 wt.% up to 7 wt.% Si, from 0.01 wt.% to 0,065 wt.% soluble in acid Al, from 0.004% Mas. to 0,012 wt.% N and from 0.05 wt.% up to 1 wt.% Mn and optionally containing specified number of S and/or Se, and B and C is 0,085 wt.% or less, and the rest consists of Fe and unavoidable impurities.

[0023] will be explained Further experiments conducted by the authors of the present invention.

The first experiment

[0024] In the first experiment initially receive a variety of slabs from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,008 wt.% N, from 0.05 wt.% to 0.19% Mas. Mn, 0,007% Mas. S and from 0,0010 wt.% to 0,0035 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1100 & deg C to 1250 C and subjected to hot rolling. During hot rolling of conducted rough rolling 1050°C, and then pursued the finishing rolling 1,000 degrees Celsius, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that on hot rolled steel strips sent a jet of water, cooling water, resulting in hot rolled steel strips were cooled to is 550 (C, and after that hot rolled steel strips were cooled in the atmosphere. After this was carried out annealing and hot-rolled steel strips. Further pursued cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then cold-rolled steel strips heated with a speed of 15 C/s, and subjected annealing at the temperature of 840°C, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and spent the final annealing. In such a way received various samples.

[0025] After that investigated the correlation between the secretions in the hot-rolled steel strip and magnetic property after the final annealing. The results of the study are presented in Fig. 2. In Fig. 2 horizontal axis shows the value (wt.%), received recalculation of the emitted amount of MnS in the number of S, and the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. Horizontal axis corresponds to the number of S, which stood out in the form of MnS (wt.%). In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in Fig. 2, in each of the samples containing emitted quantity of each of the MnS and BN, amounting to less than a certain value, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0026] also investigated the ratio between the number of B, which is not allocated in the form of BN, and magnetic property after the final annealing. The results of the study are presented in Fig. 3. In Fig. 3 horizontal axis shows the content of B (wt.%), while the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. in addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in Fig. 3 in each of the samples containing the number of B, not emitted in the form BN, amounting to a value, or more, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0027] in addition, the research forms of allocations in each of the samples with a good magnetic property, it appeared that the MnS is becoming the center of crystallization (germ)and BN allocated the MnS. Such composite allocation are effective as inhibitors, which stabilize the secondary recrystallization step.

[0028] also investigated the correlation between the conditions of hot rolling and magnetic property after the final annealing. The results of the study are presented in Fig. 4. In Fig. 4 horizontal axis shows the Mn content (wt.%), while the vertical axis shows the temperature (C) slab heating during hot rolling. In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. In addition, the curve in Fig. 4 shows the temperature T1 (C) dissolution of the MnS, expressed below in equation (1). As shown in Fig. 4, was that the samples in which heating of the band performed at a determined in accordance with the content of Mn temperature or below receive a high magnetic flux density B8. In addition, it also appeared that this temperature roughly matches the temperature T1 dissolution of the MnS. That is, it was found that can be effectively conduct heating slab in the temperature zone, where MnS is not fully absorbed in solid solution.

,82-log([Mn]

[S]))-273 (1)

Here [Mn] represents the Mn content (wt.%), [S] is the content of S (wt.%).

[0029] in addition, as a result of studies of the behaviour of the allocation of the MnS and BN was that, if there MnS, BN stood out mainly with the MnS, serving as a center of crystallization, and the temperature zone selection BN is from 800 degrees C to 1000 C.

[0030] in addition, the authors of the present invention investigated conditions, effective allocation BN. In this study first received different slabs with thickness of 40 mm from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,006 wt.% N, 0.1 wt.% Mn, 0,007% Mas. S and 0,0014 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1200 C and subjected to rough rolling when 1100C to get a thickness of 15 mm After that, the obtained slabs from silicon steel was kept in a furnace at a temperature of 1050°C to 800 degrees C for a given period of time. Then spent the finishing rolling, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that, hot rolled steel strips water cooled to room temperature, and researched selection. The result was that if the slab of silicon steel is kept in a temperature range between 1,000 degrees C and 800 degrees C in 300 seconds or longer between roughing rolling and finishing rolling, formed excellent composite selection.

The second experiment

[0031] In the second experiment, initially receive a variety of slabs from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,007% Mas. N, from 0.05 wt.% to 0.20 wt.% Mn, 0,007%Mas. Se and from 0,0010 wt.% to 0,0035 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1100 & deg C to 1250 C and subjected to hot rolling. During hot rolling of conducted rough rolling 1050°C, and then pursued the finishing rolling 1,000 degrees Celsius, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that, hot rolled steel strips sent a jet of water, cooling water, resulting in hot rolled steel strips were cooled to is 550 (C, then hot rolled steel strips were cooled in the atmosphere. After this was carried out annealing and hot-rolled steel strips. Further pursued cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then cold-rolled steel strips heated with a speed of 15 C/s, and subjected annealing at the temperature of 840°C, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and spent the final annealing. In such a way received various samples.

[0032] After that investigated the correlation between the secretions in the hot-rolled steel strip and magnetic property after the final annealing. The results of the research are shown in figure 5. Figure 5 the horizontal axis shows the value (wt.%), received recalculation of the emitted amount of MnSe in the number of Se, and the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. Horizontal axis represents the number of Se, which is separated in the form of MnSe (wt.%). In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in figure 5, in each of the samples containing emitted quantity of each of MnSe and BN, amounting to less than a certain value, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0033] also investigated the ratio between the number of B, not emitted in the form of BN, and magnetic property after the final annealing. The results of the research are shown in Fig.6. 6 the horizontal axis shows the content of B (wt.%), while the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in Fig.6, in each of the samples containing the number of B, not emitted in the form BN, amounting to a value, or more, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0034] in addition, the research forms of allocations in each of the samples with a good magnetic property, it turned out that MnSe becomes the center of crystallization and BN allocated on MnSe. Such composite allocation are effective as inhibitors, which stabilize the secondary recrystallization step.

[0035] also investigated the correlation between the conditions of hot rolling and magnetic property after the final annealing. The results of the survey are presented in figure 7. Figure 7 the horizontal axis shows the Mn content (wt.%), while the vertical axis shows the temperature (C) slab heating during hot rolling. In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. In addition, the curve in Fig. 7 shows the temperature T2 (C) dissolution MnSe expressed below in equation (2). As shown in Fig. 7, it appears that in samples in which heating of the slab was determined in accordance with the content of Mn temperature or below receive a high magnetic flux density B8. In addition, it also appeared that this temperature roughly matches the temperature T2 dissolution MnSe. It appeared that to effectively heating slab in the temperature zone, where MnSe not fully absorbed in solid solution.

,08-log([Mn]

[Se]))-273 (2)

Here [Se] represents the contents of the Se (wt.%).

[0036] in addition, as a result of studies of the behaviour of the allocation of the MnSe and BN was that, if there MnSe, BN provided mainly with MnSe, serving as a center of crystallization, and the temperature zone selection BN is from 800 degrees C to 1000 C.

[0037] in addition, the authors of the present invention investigated conditions, effective allocation BN. In this study first received different slabs with thickness of 40 mm from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,007% Mas. N, 0.1 wt.% Mn, 0,007% Mas. Se and 0,0014 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1200 C and subjected to rough rolling when 1100C to get a thickness of 15 mm After that, the obtained slabs from silicon steel was kept in a furnace at a temperature of 1050°C to 800 degrees C for a given period of time. Then spent the finishing rolling, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that hot rolled steel strips water cooled to room temperature, and researched selection. The result was that, if the slab of silicon steel is kept in a temperature range between 1,000 degrees C and 800 degrees C in 300 seconds or longer between roughing rolling and finishing rolling, formed excellent composite selection.

The third experiment

[0038] In the third experiment, initially receive a variety of slabs from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,026 wt.% soluble in acid Al, 0,009 wt.% N, from 0.05 wt.% to 0.20 wt.% Mn, 0.005% S, 0,007% Mas. Se and from 0,0010 wt.% to 0,0035 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1100 & deg C to 1250 C and subjected to hot rolling. During hot rolling of conducted rough rolling 1050°C, and then pursued the finishing rolling 1,000 degrees Celsius, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that on hot rolled steel strips sent a jet of water, cooling water, resulting in hot rolled steel strips were cooled to is 550 (C, then hot rolled steel strips were cooled in the atmosphere. After this was carried out annealing and hot-rolled steel strips. Further pursued cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then cold-rolled steel strips heated with a speed of 15 C/s, and subjected annealing at the temperature of 840°C, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and spent the final annealing. In such a way received various samples.

[0039] After that investigated the correlation between the secretions in the hot-rolled steel strip and magnetic property after the final annealing. The results of the study are presented in Fig. 8. In Fig. 8 horizontal axis shows the amount (wt.%) the value obtained by the conversion of the emitted amount of MnS in the number of S, and the value obtained by multiplying the value obtained by the conversion of the emitted amount of MnSe in Se, 0.5, while the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. in addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in Fig. 8, in each of the samples containing emitted quantity of each of the MnS, MnSe and BN, amounting to less than a certain value, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0040] also investigated the ratio between the number of B, not emitted in the form of BN, and magnetic property after the final annealing. The results of the study are presented in Fig. 9. In Fig. 9 horizontal axis shows the content of B (wt.%), while the vertical axis shows the value (wt.%), received recalculation of the emitted amount BN in B. in addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. As shown in Fig. 9, in each of the samples containing the number of B, not emitted in the form BN, amounting to a value, or more, magnetic flux density B8 was low. This indicates that the secondary recrystallization was unstable.

[0041] in addition, the research forms of allocations in each of the samples with a good magnetic property, it appeared that the MnS or MnSe becomes the center of crystallization and BN allocated the MnS or MnSe. Such composite allocation are effective as inhibitors, which stabilize the secondary recrystallization step.

[0042] also investigated the correlation between the conditions of hot rolling and magnetic property after the final annealing. The results of the study are presented in Fig. 10. In Fig. 10 the horizontal axis shows the Mn content (wt.%), while the vertical axis shows the temperature (C) slab heating during hot rolling. In Fig. 10 the horizontal axis shows the content of B (wt.%), while the vertical axis shows the temperature (C) slab heating during hot rolling. In addition, each white circles indicates that the magnetic flux density B8 was 1,88 T or more, and each of the black squares indicates that the magnetic flux density B8 was less than 1,88 THB. In addition, the two curves in Fig. 10 show temperature T1 (C) dissolution of the MnS, expressed by the equation (1), and the temperature T2 (C) dissolution MnSe expressed by equation (2). As shown in Fig. 10, it appeared that the samples in which heating of the slab is carried out at a determined in accordance with the content of Mn temperature or below receive a high magnetic flux density B8. In addition, it also appeared that this temperature roughly matches the temperature T1 dissolution of the MnS and the temperature T2 dissolution MnSe. It appeared that to effectively heating slab in the temperature zone, where the MnS and MnSe not completely pass in solid solution.

[0043] in addition, as a result of studies of the behaviour of the allocation of the MnS, MnSe and BN was that, if there are MnS and MnSe, BN stood out mainly with the MnS and MnSe serving as a center of crystallization, and the temperature zone selection BN is from 800 degrees C to 1000 C.

[0044] in addition, the authors of the present invention investigated conditions, effective allocation BN. In this study first received different slabs with thickness of 40 mm from silicon steel, containing 3.3 wt.% Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,007% Mas. N, 0.1 wt.% Mn, 0,006 wt.% S, 0,008 wt.% Se and 0.0017 wt.% B, and the rest consisted of Fe and unavoidable impurities. Next slabs from silicon steel heated at a temperature of 1200 C and subjected to rough rolling when 1100C to get a thickness of 15 mm After that, the obtained slabs from silicon steel was kept in a furnace at a temperature of 1050°C to 800 degrees C for a given period of time. Then spent the finishing rolling, with the result of hot rolled steel strip, thickness of each of which comprised 2,3 mm After that hot rolled steel strips water cooled to room temperature, and researched selection. The result was that, if the slab of silicon steel is kept in a temperature range between 1,000 degrees C and 800 degrees C in 300 seconds or longer between roughing rolling and finishing rolling, formed excellent composite selection.

[0045] According to the results of the first-third of the experiments found that the regulation of the energy released form BN makes possible stable improvement of the magnetic properties of textured electrical sheet steel. To date the reason why the secondary recrystallization becomes unstable, thus making it impossible to get a good magnetic properties in the case when B is not allocated the MnS or MnSe in the form BN, not been clarified, but it is considered next.

[0049] Material from silicon steel used in this embodiment, contains from 0.8 wt.% up to 7 wt.% Si, from 0.01 wt.% to 0,065 wt.% soluble in acid Al, from 0.004% Mas. to 0,012 wt.% N, from 0.05 wt.% up to 1 wt.% Mn, 0,003% Mas. to 0.015 wt.% the sum S and Se and from 0.0005 wt.% to 0,0080 wt.% B, content of C is 0,085 wt.% or less, and the rest consists of Fe and unavoidable impurities.

[0050] Silicon (Si) electrical resistance increases, reducing the core losses. However, when the content of Si exceeds 7%, it becomes difficult to make cold rolling, and the likely occurrence of cracks during cold rolling. Thus, the content of Si set at the level of 7 wt.% or less, preferably 4,5 wt.% or less, and it is preferable to 4 wt.% or less. In addition, when the content of Si is less than 0.8 wt.% during the final annealing is called γ-transformation, which violates the orientation of the crystals textured electrical sheet steel. Thus, the content of Si set at 0.8 wt.% or more, preferably 2 wt.% or more, and it is preferable to 2.5 wt.% or more.

[0051] Carbon (C) represents the element effective to regulate the structure of primary recrystallization, but adversely affects the magnetic property. Thus, in this embodiment before the final annealing (stage S5) conduct annealing (stage S4). However, when the contents of the C exceeds 0,085 wt.% increases the time required for annealing, and decreases the performance of industrial production. Thus, the content of C set at the level of 0.85 wt.% or less, and preferably 0,07 wt.% or less.

[0052] Soluble in acid aluminium (Al) is connected with the N, standing out as (Al,Si)N, and acts as a inhibitor. In that case, when the content of soluble in acid Al is in the range from 0.01 wt.% to 0,065 wt.% secondary recrystallization is stabilized. Thus, the content of soluble in acid Al set at the level of not less than 0.01 wt.% and not more than 0,065 wt.%. In addition, the content of soluble in acid Al is preferably 0,02 mass% or more, and it is preferable to 0,025 wt.% or more. In addition, the content of soluble in acid Al is preferably 0,04 wt.% or less, and it is preferable to 0,03% Mas. or less.

[0053] Boron (B) is connected with the N, standing out on the MnS or MnSe as BN, and acts as a inhibitor. In the case when B is in the range from 0.0005 wt.% to 0,0080 wt.% secondary recrystallization is stabilized. Thus, the content of B set at the level of not less than 0,0005% Mas. and not more than 0,0080 wt.%. In addition, the content of B is preferably 0,001 mass% or more, and it is preferable to 0,0015 wt.% or more. In addition, the content of B is preferably 0,0040 wt.% or less, and it is preferable to 0,0030 wt.% or less.

[0054] Nitrogen (N) connects to the B or Al and functions as an inhibitor. When the contents of N is less than 0,004% it is impossible to get enough inhibitor. Thus, the content of N set at the level of 0.004 wt.% or more, preferably 0,006 wt.% or more, and it is preferable to 0.007 mass.% or more. On the other hand, when the N content exceeds 0,012% the steel strip cold-rolled formed in the cavity, called sinks. Thus, the content of N set at the level of 0,012 wt.% or less, preferably 0,010% by wt or less, and it is preferable to 0,009 wt.% or less.

[0055] Manganese (Mn), sulphur (S) and selenium (Se) form the MnS and MnSe as centers of crystallization, which allocated BN, and these composite allocation act as an inhibitor. In that case, when the Mn content is in the range 0.05 wt.% up to 1 wt.%, secondary recrystallization is stabilized. Thus, the content of Mn set at the level of not less than 0.05 wt.% and not more than 1 wt.%. In addition, the Mn content is preferably 0,08 wt.% or more, and it is preferable to 0,09 wt.% or more. In addition, the Mn content is preferably 0,50 wt.% or less, and it is preferable to 0.2 wt.% or less.

[0056] moreover, in case when the total content of S and Se is in the range from 0.003% Mas. to 0.015% secondary recrystallization is stabilized. Thus, the total content of S and Se set at the level of not less than 0,003 wt.% and no more than 0,015 wt.%. Furthermore, with regard to the prevention of occurrence of cracks during hot rolling, preferably running the following inequality (5). While in the material from silicon steel can contain either S or Se, or in the material from silicon steel may contain S, and Se. In that case, when contained and S, and Se, can contribute to a more sustainable allocation of BN, and steadily improve the magnetic property.

[Mn]/([S]

[0057] Titanium (Ti) forms TiN, influencing the extracted quantity BN and (Al,Si)N acting as an inhibitor. When the contents of the Ti exceeds 0,004% not easy to get a good magnetic property. Thus, the content of Ti is preferably 0,004 wt.% or less.

[0058] Besides, the piece of silicon steel can also contain one or more element(s)selected from the group consisting of Cr, Cu, Ni, P, Mo, Sn, Sb, Bi, within the following ranges.

[0059] Chromium (Cr) improves the oxide layer formed during annealing, and is effective for the formation of glass films produced during the reaction of the oxide layer and MgO, which is the main component of the separator for annealing, during the final annealing. However, when the content of Cr by more than 0.3 wt.% decarburization significantly reduced. Thus, the content of Cr can be set at 0.3 wt.% or less.

[0060] Copper (Cu) resistivity increases, reducing the core losses. However, when the content of Cu exceed 0.4%, there is a saturation of this effect. In addition, during the hot rolling sometimes formed surface defects, called «copper ». Thus, the content of Cu can be set at the level of 0.4% of or less.

[0061] Nickel (Ni) resistivity increases, reducing the core losses. In addition, Ni regulates the metal structure of hot-rolled steel strip, improving the magnetic property. However, when the contents of Ni is more than 1 wt.% secondary recrystallization becomes unstable. Thus, the Ni can be set at a level to 1 wt.% or less.

[0062] Phosphorus (P) increases resistivity, reducing the core losses. However, when the content of P exceeds 0.5% due to embrittlement during cold rolling easily cracks. Thus, the content of P can be set at the level of 0.5 wt.% or less.

[0063] Molybdenum (Mo) improves the ability of a surface during hot rolling. However, when the contents of Mo exceed 0.1 wt.% there is a saturation of this effect. Thus, the contents of Mo can be set at the level of 0.1 wt.% or less.

[0064] Tin (Sn) and antimony (Sb) are on grain boundary elements. Material from silicon steel used in this embodiment, contains Al, so that in some cases Al oxidized moisture allocated from the separator for annealing, depending on the provisions of the final annealing. In this case the change of power inhibitor occur depending on its position in textured electrical sheet steel, and magnetic property also sometimes changed. However, when contained on grain boundary elements, you can suppress the oxidation Al. That is, Sn and Sb inhibit the oxidation of Al, suppressing the change of magnetic properties. However, when the total content of Sn and Sb greater than 0.30% the oxide layer is not easy formed during annealing, and as a result, education glass films produced during the reaction of the oxide layer and MgO, which is the main component of the separator for annealing, during the final annealing becomes insufficient. In addition, significantly prevented decarburization. Thus, the total content of Sn and Sb can be set at 0.3 wt.% or less.

[0065] Bismuth (Bi) stabilizes the discharge, such as sulfides, augmenting the action as a inhibitor. However, when the contents of the Bi exceed 0.01 wt.% it adversely affects the formation of glass film. Thus, the content of Bi can be set at the level of 0.01 wt.% or less.

[0066] Next will be explained every type of processing in this embodiment.

[0067] Material from silicon steel (slabs), containing the above components can be produced in such a way that, for example, steel is melted in a furnace, electric furnace or other source, and the molten steel is subjected to a vacuum as needed, and then subjected to continuous casting. In addition, the material from silicon steel can also be set so that instead of a continuous casting receive ingot, rolled in . The thickness of the slab of silicon steel set at the level of, for example, from 150 mm to 350 mm, and preferably from 220 mm to 280 mm in addition, you can also use the so-called thin slab, having a thickness from 30 mm up to 70 mm In the case when the produce thin slab, rough rolling done upon receipt of hot-rolled steel strip, you can exclude.

[0068] After the manufacture of slab of silicon steel spend slab heating and hot rolling stage S1). After that, in this version the implementation of the conditions slab heating and hot rolling positioned so that it makes BN allocated the MnS and/or MnSe, and that the quantity of discharge BN, MnS and MnSe in hot-rolled steel strip meet the following inequalities (6)-(8).

Here «B BN » represents the number of B, which is separated as BN (wt.%), «S MnS » represents the number of S, which stood out as an MnS (wt.%), and «Se MnSe » represents the number of Se, which stood out as a MnSe (wt.%).

[0070] Each of the MnS and MnSe acts as a center of crystallization, which allocated BN. Thus, to ensure the sufficient allocation BN and thereby improve the magnetic property, quantity of discharge MnS and MnSe adjusted so that the inequality (8).

[0071] Condition, expressed in the inequality (7)follows from Fig. 3, Fig. 6 and Fig. 9. In Fig. 3, Fig. 6 and Fig. 9 found that in the case when the [B] (B BN 0.001 wt.% or they get a good magnetic flux density, which is a magnetic flux density B8 1,88 T or more.

[0072] Conditions expressed in the inequality (6) and the inequality (8), follow from Fig. 2, Fig. 5 and Fig. 8. It was found that in the case when B BN is 0,0005 wt.% or more, and S MnS is 0.002 wt.% or more, in Fig. 2 obtained a good magnetic flux density, which is a magnetic flux density B8 1,88 T or more. Similarly, it was found that in the case when B BN is 0,0005 wt.% or more, and Se MnSe is 0.004 wt.% or more, in Fig. 5 received a good magnetic flux density, which is a magnetic flux density B8 1,88 T or more. Similarly, it was found that in the case when B BN is 0,0005 wt.% or more, and the amount of S MnS + 0,5 x Se MnSe is 0.002 wt.% or more, in Fig. 8 received a good magnetic flux density, which is a magnetic flux density B8 1,88 T or more. Further, provided that S MnS is 0.002 wt.% or more, the amount of S MnS + 0,5 x Se MnSe inevitably becomes equal 0,002 wt.% or more, and provided that Se MnSe is 0.004 wt.% or more, the amount of S MnS + 0,5 x Se MnSe inevitably becomes equal 0,002 wt.% or more. Thus, it is important that the sum S MnS + 0,5 x Se MnSe was 0,002 wt.% or more.

[0073] in addition, during hot rolling, to allocate a sufficient number of BN, you must pass the material from silicon steel (slabs) at temperatures between 1,000 degrees C and 800 degrees C in 300 seconds or longer during hot rolling, as shown in Fig. 11. If holding temperature lower than 800 degrees C, the speed of diffusion B and N are small, and increases the period of time required for the allocation BN. Meanwhile, if holding temperature exceeds 1,000 degrees C, BN becomes more soluble, emitted number of BN is not sufficient and can not be obtained high magnetic flux density. In addition, if the exposure time is less than 300 seconds, the diffusion length B and N are short, and the isolated number of BN is not enough.

[0074] Method extracts of the material from silicon steel (slab) in the temperature range of between 1,000 degrees C and 800 degrees C is not specifically restricted. For example, an effective is the next way. First conduct a heavy rolling and steel band take up in the form of a coil. After that, a steel band stand or slowly cooled equipment such as the intermediate coiling device. Then spend the finishing rolling in the temperature range of between 1,000 degrees C and 800 degrees C, simultaneously unwinding steel band.

[0075] Way of marking the MnS and/or MnSe not specifically restricted. For example, it is preferable that the temperature of the heating slab was installed to satisfy the following conditions:

(i) in the case of S and Se in the floor slab of silicon steel temperature T1 (C) expressed in equation (1) or below, and the temperature T2 (C) is expressed by equation (2) or below;

(ii) in the case of absence of Se in the floor slab of silicon steel temperature T1 (C) expressed in equation (1) or less;

(iii) in the absence of S floor slab of silicon steel temperature T2 (C) is expressed by equation (2) or below:

,82-log([Mn]

[S]))-273 (1)

,08-log([Mn]

[Se]))-273 (2)

[0076] This is because when a slab heating is carried out at these temperatures, MnS and MnSe not completely transformed into solid solution during the heating of a slab, and allocation processes MnS and MnSe during hot rolling accelerated. As is clear from Fig. 4, Fig. 7 and Fig. 10, temperature T1 and T2 dissolution roughly correspond to the upper limit of the heating temperature of the slab, which enables to get the magnetic flux density B8 1,88 T or more.

[0077] in addition, more preferably to set the temperature of heating of the slab to also meet the following conditions. This serves a selection of the preferred number of MnS or MnSe during heating slab:

(i) in the case of absence of Se in the floor slab of silicon steel temperature T3 (C) expressed in equation (9) or less;

(ii) in the case of absence S floor slab of silicon steel T4 temperature (C) expressed in equation (10) or below:

[0078] In the case when the temperature of the heating slab is excessively high, MnS and/or MnSe sometimes completely transformed into solid solution. In this case becomes a difficult call allocation MnS and/or MnSe during hot rolling. Thus, the heating of the slab should preferably be carried out at temperatures T1 and/or temperature T2 or below. In addition, if the temperature of the heating slab is equal to the temperature T3 or T4 or below, during the heating of the slab is allocated preferable number of MnS or MnSe, and, thus, it is possible to cause the selection BN the MnS or MnSe, easy to forming effective inhibitors.

[0079] After hot rolling (stage S1) conduct annealing and hot-rolled steel strip (stage S2). Next, perform a cold rolling stage S3). As described above, cold rolling treatment can only be performed once, or it can be also spend a lot of time with the execution of the intermediate annealing between these operations. In cold rolling degree of finishing cold rolling preferably set at the level of 80% or more. It is necessary for the development of good aggregate structure of primary recrystallization.

[0080] Then spend annealing (stage S4). As a result of this, remove the C contained in a steel band. annealing carried out, for example, in a humid atmosphere. In addition, annealing preferably spend a time when, for example, the diameter of grains received at primary recrystallization becomes equal to 15 microns or more in the temperature range from 770°C to 950 deg C. This is necessary to obtain a good magnetic properties. Then spend the application of the separator for annealing and final annealing (stage S5). As a result, when secondary recrystallization preferably grow grain, aimed at orientation {110} <001>.

[0081] in addition, conduct processing between the beginning annealing and the emergence of secondary recrystallization in the final annealing (stage S6). It is necessary for education inhibitor (Al, Si)N. processing can be performed during annealing (stage S4) or may also be held during the final annealing (stage S5). In that case, when processing is done during the annealing, annealing can be conducted in an atmosphere containing with the ability to gas nitriding were investigated, such as ammonia. In addition, processing can be performed during the passage of the heating zone or the zone aging in continuous annealing furnace, or processing can also be performed at any stage after ageing areas. In that case, when processing is done during the final annealing, the separator for annealing may be added powder, with the ability to nitriding were investigated, such as MnN.

[0082] To conduct secondary recrystallization step more stable, it is desirable to adjust the degree of the nitriding processing (stage S6) and adjust structures (Al,Si)N the steel strip after processing. For example, according to the contents Al, the content of B and content inevitably present Ti, the degree of nitriding preferably adjusted so that the following inequality (3), and preferably degree nitriding is adjusted so that the following inequality (4). Inequality (3) and the inequality (4) show the number N, which is preferable to link B in the form BN, effective as an inhibitor, and the number N, which is preferable to link Al in the form of AlN or (Al,Si)N, effective as an inhibitor.

Here the [N] is the N content (wt.%) the steel band received after processing, [Al] is soluble in acid Al (wt.%) the steel band received after processing [B] represents the content of B (wt.%) the steel band received after processing, and [Ti] represents the contents of Ti (wt.%) the steel band received after processing.

[0083] Method for final annealing (stage S5) is also not specifically restricted. It should be noted that in this embodiment inhibitors are exacerbated by BN, so that the rate of rise in temperature range from 1,000 degrees C to 1100C preferably set at the level of 15 C/h or less in the heating process for final annealing. In addition, instead of regulating heating rate also effectively conduct isothermal annealing at which the steel strip is kept in a temperature range from 1,000 degrees C to 1100C for 10 hours or longer.

[0084] According to this variant of implementation as indicated above, it is possible stable production textured electrical sheet steel with excellent magnetic properties.

[0085] will be explained Further experiments conducted by the authors of the present invention. Conditions and other characteristics of these experiments are examples used to confirm the practical applicability and effects of the present invention, and the present invention is not limited to these examples.

The fourth experiment

[0086] In the fourth experiment was confirmed by the effect of the maintenance B in case of absence of the Se.

[0087] In the fourth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,008 wt.% N, 0.1 wt.% Mn, 0,006 wt.% S and B in the amount indicated in table 1 (from 0 wt.% up to 0,0045 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated when 1180°C and subjected to hot rolling. During hot rolling of conducted rough rolling 1100C, annealing was performed in which the slabs to be kept at 950°C in 300 seconds, and then spent the finishing rolling 900ºc C. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,024 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that measured the magnetic property (magnetic flux density B8) after the final annealing. Magnetic property (magnetic flux density B8) was measured based on the standard of JIS C2556. The results of the measurements are shown in table 1.

[0089] As shown in table 1, in a comparative example # 1A with zero content of B in the floor slab magnetic flux density was low, but in each instance №№ 1B-1E with a corresponding number of B contained in the floor slab, received a good magnetic flux density.

Fifth experiment

[0090] In the fifth experiment confirmed the effects of the content of Mn and the heating temperature of the slab in case of absence of the Se.

[0091] In the fifth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,007% Mas. N, 0,006 wt.% S, 0,0015 wt.% B, and Mn in the amount indicated in table 2 (0.05 wt.% up to 0.2 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and subjected to hot rolling. During hot rolling, some samples (examples №№ 2A1-2A4) conducted a rough rolling 1100C, annealing was performed in which the slabs to be kept at 1,000 degrees C for 500 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm on The other hand, for other samples (examples №№ 2B1-2B4), conducted a preliminary rolling 1100C, and then spent the finishing rolling 1020 degrees Celsius without holding annealing. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then annealing was performed in the humid gas at 830°for 100 seconds, which received annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 2.

[0093] As shown in table 2, good magnetic flux density obtained in the examples №№ 2A1-2A4, each slab kept at a given temperature at an intermediate stage of the hot rolling, but the magnetic flux density was low in comparative examples №№ 2B1-2B4, each with specified extract has been conducted.

Sixth experiment

[0094] In the sixth experiment confirmed the effects of temperature exposure and the exposure time during hot rolling in case of absence of the Se.

[0097] As shown in table 3, a good magnetic flux density obtained in the examples №№ 3B-3D, each slab kept at a given temperature for a given period of time at an intermediate stage in the hot rolling mill. But magnetic flux density was low in comparative examples №№ 3A, 3E-3G, each holding temperature or time exposure installed outside of the interval according to the present invention.

Seventh experiment

[0098] In the seventh experiment confirmed the effect of the N content after processing in case of absence of the Se.

[0099] In the seventh experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,006 wt.% N, of 0.15 wt.% Mn, 0,006 wt.% S and 0.002% Mas. B, content of which is the admixture of Ti was 0,0014 wt.% and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and then spent annealing, which slabs kept at 950°for 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then pursued annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up to the level of 0,012 wt.% to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 4.

[0101] As shown in table 4, in example # 4C, in which the content of N after processing satisfies the condition of the inequality (3) and condition of the inequality (4), received a particularly good magnetic flux density. On the other hand, in example # 4B, in which the content of N after processing satisfies the condition of the inequality (3), but does not satisfy the condition of the inequality (4), magnetic flux density was slightly lower than in example # 4C. In addition, the example № 4A, in which the content of N after processing does not satisfy the condition of the inequality (3) and condition of the inequality (4), magnetic flux density was slightly lower than in example # 4B.

Eighth experiment

[0102] In the eighth experiment confirmed the effect of the components of the slab in case of absence of the Se.

[0103] In the eighth experiment first produced slabs, containing the components listed in table 5, and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and then spent annealing, which slabs kept at 950°for 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Further pursued cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 860°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,023 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 5.

[0105] As shown in table 5, in the examples №№ 5A-5O, each of which used the slab with suitable product, obtained a good magnetic flux density, but in a comparative example # 5P, in which the content of S is below the lower limit of the interval of the present invention, magnetic flux density was low.

Ninth experiment

[0106] In the ninth experiment confirmed the effect of the maintenance B in case of absence of S.

[0107] In the ninth experiment first produced slabs, containing 3,2% Mas. Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,008 wt.% N, 0,12% Mas. Mn, 0,008 wt.% Se and B in the amount indicated in table 6 (0 wt.% to 0,0043 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated when 1180 C and subjected to hot rolling. During hot rolling of conducted rough rolling 1100C, annealing, which slabs kept at 950°C in 300 seconds, and then spent the finishing rolling 900ºc C. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,024 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 6.

[0109] As shown in table 6, in a comparative example № 6A at zero content of B in the floor slab magnetic flux density was low, but in the examples №№ 6A-6E, each slab contain the appropriate number of B, obtained a good magnetic flux density.

Tenth experiment

[0110] In the tenth experiment confirmed the effects of the content of Mn and the heating temperature of the slab in case of absence of S.

[0111] In the tenth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,026 wt.% soluble in acid Al, 0,007% Mas. N, 0,009 wt.% Se, 0,0015 wt.% B, and Mn in the amount indicated in table 7 (from 0.1 wt.% to 0.21 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and subjected to hot rolling. During hot rolling, some samples (examples №№ 7A1-7A3) conducted a rough rolling 1100C, annealing, which slabs kept at 1,000 degrees C for 500 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm On the other hand, for other samples (examples №№ 7B1-7B3) conducted a rough rolling 1100C, and then spent the finishing rolling 1020 degrees Celsius without holding annealing. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then pursued annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 7.

[0113] As shown in table 7, a good magnetic flux density obtained in the examples №№ 7A1-7A3, each slab kept at a given temperature at an intermediate stage of the hot rolling, but the magnetic flux density was low in comparative examples №№ 7B1-7B3, each such exposure has been conducted.

Eleventh experiment

[0114] In the eleventh experiment confirmed the effects of temperature exposure and the exposure time during hot rolling in case of absence of S.

[0119] In the twelfth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,008 wt.% N, 0,12% Mas. Mn, 0,007% Mas. Se and 0,0016 wt.% B, content of which is the admixture of Ti was 0,0013 wt.% and the rest consisted of Fe and unavoidable impurities. Next slabs heated when 1180 C and then spent annealing, which slabs kept at 950°C in 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up to level from 0.015% Mas. to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). Measurement results are shown in table 9.

[0121] As indicated in table 9, in example # 9C, in which the content of N after processing satisfies the condition of the inequality (3) and condition of the inequality (4), received a particularly good magnetic flux density. On the other hand, in example # 9B, in which the content of N after processing satisfies the condition of the inequality (3), but does not satisfy the condition of the inequality (4), magnetic flux density was slightly lower than in example # 9C. In addition, in example # 9A, in which the content of N after processing does not satisfy the condition of the inequality (3) and condition of the inequality (4), magnetic flux density was slightly lower than in example # 9B.

Thirteenth experiment

[0122] In the thirteenth experiment confirmed the effect of the components of the slab in case of absence of S.

[0123] In the thirteenth experiment first produced slabs, containing the components listed in table 10 and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and then spent annealing, in which the band kept at 950°C in 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 860°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,023 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 10.

Material composition of silicon steel (wt.%)

Magnetic property

Magnetic flux density B8 (THB)

A comparative example

[0125] As indicated in table 10, the examples №№ 10A-10O, each of which used the slab with suitable product, obtained a good magnetic flux density, but in a comparative example # 10P, in which the Se is below the lower limit of the interval of the present invention, magnetic flux density was low.

Fourteenth experiment

[0126] In the fourteenth experiment confirmed the effect of the maintenance B in the case of the presence of S and Se.

[0127] In the fourteenth experiment first produced slabs, containing 3,2% Mas. Si, 0.05 wt.% C, 0,028 wt.% soluble in acid Al, 0,008 wt.% N, 0.1 wt.% Mn, 0,006 wt.% S, 0,006 wt.% Se and B in the amount indicated in table 11 (0 wt.% up to 0,0045 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated when 1180 C and subjected to hot rolling. During hot rolling of conducted rough rolling 1100C, annealing, which slabs kept at 950°C in 300 seconds, and then spent the finishing rolling 900ºc C. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,024 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 11.

[0129] As indicated in table 11, in a comparative example # 11A zero-B in the floor slab magnetic flux density was low, but in the examples №№ 11B 11E, each slab contain the appropriate number of B, obtained a good magnetic flux density.

Fifteenth experiment

[0130] In the fifteenth experiment confirmed the effects of the content of Mn and the temperature of the heating slab in case of presence of S and Se.

[0131] In the fifteenth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,006 wt.% N, 0,006 wt.% S, 0,004 wt.% Se, 0,0015 wt.% B, and Mn in the amount indicated in table 12 (0.05 wt.% up to 0.2 wt.%), and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and subjected to hot rolling. During hot rolling, some samples (examples №№ 12A1-12A4), conducted a preliminary rolling 1100C, annealing, which slabs kept at 1,000 degrees C for 500 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm on The other hand, for other samples (examples №№ 12V1-12V4), conducted a preliminary rolling 1100C, and after that spent finishing rolling 1020 degrees Celsius without holding annealing. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then pursued annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 12.

[0133] As shown in table 12, a good magnetic flux density obtained in the examples №№ 12A1-12A4, each slab kept at a given temperature at an intermediate stage of the hot rolling, but the magnetic flux density was low in comparative examples №№ 12V1-12V4, each such exposure has been conducted.

Sixteenth experiment

[0134] In the sixteenth experiment confirmed the effects of temperature exposure and the exposure time during hot rolling, in the case of the presence of S and Se.

[0135] In the sixteenth experiment first produced slabs, containing 3,1 wt.% Si, by weight 0.06% C, 0,026 wt.% soluble in acid Al, 0,006 wt.% N, 0,12% Mas. Mn, 0,006 wt.% S, 0,007% Mas. Se and 0.0015% Mas. B. Next, slabs heated when 1200C C, then spent annealing at which the slabs to be kept at a temperature of 1050°C up to 700oC C for 100 seconds to 500 seconds, and spent a fine rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm and Then spent annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up 0,021 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 13.

[0137] As shown in table 13, good magnetic flux density obtained in the examples №№ 13B-13D, each slab kept at a given temperature for a given period of time at an intermediate stage in the hot rolling mill. But magnetic flux density was low in comparative examples №№ 13A and 13E-13G, each holding temperature or time exposure installed outside of the interval according to the present invention.

Seventeenth experiment

[0138] In the seventeenth experiment confirmed the effect of the N content after processing in case of presence of S and Se.

[0139] In the seventeenth experiment first produced slabs, containing 3.3 wt.% Si, by weight 0.06% C, 0,028 wt.% soluble in acid Al, 0,006 wt.% N, of 0.15 wt.% Mn, 0.005% S, 0,007% Mas. Se 0,002 wt.% B, content of which is the admixture of Ti was 0,0014 wt.% and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and then spent annealing, which slabs kept at 950°C in 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm Then pursued annealing in the humid gas at 830°for 100 seconds, with the result annealed steel strips. After that annealed steel strips annealed in containing ammonia atmosphere, increase the content of nitrogen in steel bands up to the level of 0,014 wt.% to 0.022 wt.%. Next on the steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 14.

[0141] As shown in table 14, in example # 14C, in which the content of N after processing satisfies the condition of the inequality (3) and condition of the inequality (4), received a particularly good magnetic flux density. On the other hand, in example # 14B, in which the content of N after processing satisfies the condition of the inequality (3), but does not satisfy the condition of the inequality (4), magnetic flux density was slightly lower than in example # 14C. In addition, in example # 14A, in which the content of N after processing does not satisfy the condition of the inequality (3) and condition of the inequality (4), magnetic flux density was slightly lower than in example # 14B.

Eighteenth experiment

[0142] In the eighteenth experiment confirmed the effect of the components of the slab in case of presence of S and Se.

[0147] In the nineteenth experiment first produced slabs, containing 3,2% Mas. Si, by weight 0.06% C, 0,027 wt.% soluble in acid Al, 0,007% Mas. N, 0,14 wt.% Mn, 0,006 wt.% S, 0.005% Se and 0.0015% Mas. B, and the rest consisted of Fe and unavoidable impurities. Next slabs heated at 1200 C and subjected to hot rolling. During hot rolling of conducted rough rolling, annealing, which slabs kept at 950°C in 300 seconds, and then spent the finishing rolling. Thus, the received hot rolled steel strip, thickness of each of which comprised 2,3 mm After this was carried out annealing and hot-rolled steel strips in 1100 & deg C. Next, conducted cold rolling, with the result of cold-rolled steel strips, the thickness of each of which 0,22 mm

[0148] Then, for the sample of comparative example № 16A annealing was performed in the humid gas at 830°for 100 seconds, which received a steel band. In addition, the sample from the sample № 16B annealing was performed in the humid gas at 830°for 100 seconds, and then spent annealing in containing ammonia atmosphere, with the result steel strip, in which the content of N was 0.022 mass.%. In addition, the sample from the sample № 16C annealing was performed in the humid gas at 860°for 100 seconds, with the result steel strip, in which the content of N was 0.022 mass.%. Thus, received three types of annealed steel strips.

[0149] Further on steel strips inflicted separator for annealing, containing MgO as its main component, and steel strips heated up to 1200C C with a speed of 15 C/h, and subjected to final annealing. After that, similarly to the fourth experiment, we measured the magnetic property (magnetic flux density B8). The results of the measurements are shown in table 16.

[0151] As shown in table 16, in example # 16B, which processing spent after annealing, and in example # 16C in which processing spent during annealing, obtained a good magnetic flux density. However, in a comparative example # 16A, in which processing were not, magnetic flux density was low. While the numerical value in the section « processing» comparative example № 16A in table 16 is a value derived from the composition of the annealed steel strips.

Industrial applicability

[0152] the Present invention can be used, for example, in the industrial production of electrical sheet steel and those industries, which use electrical sheet steel.

1. Method of production textured electrical sheet steel, including: hot rolling of material from silicon steel for obtaining hot rolled steel strip, with material from silicon steel contains, mass%: from 0.8 to 7 Si, from 0.01 to 0,065 soluble in acid A1, from 0.004 to 0,012 N, from 0.05 to 1 MP and from 0.0005 to 0,0080 In, the material from silicon steel additionally contains at least one member selected from the group consisting of S and Se, components in the amount from 0.003 to 0.015% content is 0,085 wt.% or less, the content of Ti is 0.004 wt.% or less, Fe and unavoidable impurities else, annealing and hot-rolled steel strip for receipt of annealed steel strips, single-entry or multiple-entry cold rolling of annealed steel strips for obtaining cold rolled steel strip, annealing cold-rolled steel strip for obtaining annealed steel strips, in which is caused by primary recrystallization, application of separator for annealing, containing MgO as its main component, the steel band and the final annealing annealed steel strips for secondary recrystallization, the further conduct processing, which increases the N content annealed steel strip, between the beginning of the annealing and the emergence of secondary recrystallization in the final annealing, and during hot rolling, exercise restraint material from silicon steel in the temperature range of between 1,000 degrees C and 800 OC for 300 or longer and then spend the finishing rolling.

2. The method according to claim 1, which further comprises before hot rolling heating the material from silicon steel temperature in the case, when in a piece of silicon steel does not contain Se, with preset temperature is equal to or less than the temperature T1 (OC), where the temperature T1 is expressed below in equation (1)

,82-log([Mn]

)-273 (1)

where [MP] is the content of the MP (wt.%) in the material from silicon steel, a [S] is the content of S (wt.%) in the material from silicon steel.

3. The method according to claim 1, which further comprises before hot rolling heating the material from silicon steel temperature in the case, when in a piece of silicon steel does not contain S, the set temperature equal to or less than KZT2 (OC), where the temperature T2 is expressed below in equation (2)

,08-log([Mn]

)-273 (2)

), where [MP] is the content of the MP (wt.%) in the material from silicon steel, and the [Se] represents the contents of the Se (wt.%) in the material from silicon steel.

4. The method according to claim 1, which further comprises before hot rolling heating the material from silicon steel temperature in the case, when in a piece of silicon steel contains S and Se, and the desired temperature is equal to or less than each of temperature T1 (C) temperature T2 (OC), where the temperature T1 is expressed below in equation (1), and the temperature T2 is expressed below in equation (2)

,82-log([Mn]

)-273 (1)

,08-log([Mn]

)-273 (2)

where [MP] is the content of the MP (wt.%) in the material from silicon steel, [S] is the content of S (wt.%) in the material from silicon steel, a [Se] represents the contents of the Se (wt.%) in the material from silicon steel.

5. Way but any one of claims 1 to 4, which treatment is carried out provided that the content of N[N] steel band received after processing satisfies the following inequality (3)

where [N] is the N content (wt.%) in steel the band received after processing, [A1] is soluble in acid A1 (wt.%) the steel band received after processing, [In] is content (wt.%) the steel band received after processing, a [Ti] represents the contents of Ti (wt.%) the steel band received after processing.

6. The method according to claim 1-4, which treatment is carried out provided that the content of N[N] steel band received after processing satisfies the following inequality (4):

where [N] is the N content (wt.%) the steel band received after processing, [Al] is soluble in acid Al (wt.%) the steel band received after processing, [In] is content (wt.%) the steel band received after processing, a [Ti] represents the contents of Ti (wt.%) the steel band received after processing.

7. The method according to claim 1-4, in which material from silicon steel additionally contains at least one member selected from the group consisting of, wt.%: 0,3 or less SG, 0.4 or less si, 1 or less Ni, 0.5 or less than P, 0.1 or less Mo, 0.3 or less Sn, 0.3 or less Sb and 0.01 or less Bi.

8. The method according to claim 5, in which material from silicon steel additionally contains at least one member selected from the group consisting of, wt.%: 0,3 or less SG, 0.4 or less Cu, 1 or less Ni, 0.5 or less than P, 0.1 or less Mo, 0.3 or less Sn, 0.3 or less Sb and 0.01 or less Bi.

9. Method according to claim 6, in which material from silicon steel additionally contains at least one member selected from the group consisting of, wt.%: 0,3 or less SG, 0.4 or less Cu, 1 or less Ni, 0.5 or less than P, 0.1 or less Mo, 0.3 or less Sn, 0.3 or less Sb and 0.01 or less Bi.