[0001]The present invention relates to a hot-rolled steel sheets for grain-oriented electrical steel sheet and grain-oriented electrical steel sheet.
Background technique
[0002]
　For example, grain-oriented electrical steel sheet widely used in the core materials of the transformer, is required characteristics crystal orientations are aligned in one direction in order to obtain excellent magnetic properties. Therefore, in the conventional manufacturing method, heating of the slab containing the inhibitor component such as S or Se, before hot rolling to temperatures higher than 1300 ° C.. However, when the slab heating temperature is high, the temperature fluctuation tends to increase in the leading end and the trailing end of the slab, it is difficult to equalize the fine precipitation in the solution and the hot rolling of MnS over the entire length of the slab. Therefore, the magnetic characteristic failure is caused by inhibitors lack the leading edge and the trailing edge of the steel sheet coil obtained from the slab, the case that the magnetic properties are not homogeneous in the entire length of the steel sheet coil. Previously various techniques have been proposed, it is difficult to obtain a homogeneous magnetic characteristics over the entire length of the steel sheet coil.
CITATION
Patent Literature
[0003]
Patent Document 1: JP 58-217630 Patent Publication
Patent Document 2: JP 61-12822 Patent Publication
Patent Document 3: JP-A 6-88171 Patent Publication
Patent Document 4: JP-A 8-225842 Patent Publication
Patent Document 5: JP-9-316537 discloses
Patent Document 6: JP 2011-190485 Patent Publication
Patent Document 7: JP-A-8-100216 Publication
Patent Document 8: JP 59-193216 JP
Patent Document 9: JP 9-316537 JP
Patent Document 10: JP-A 8-157964 JP
Summary of the Invention
Problems that the Invention is to Solve
[0004]
　The present invention aims at providing a hot-rolled steel sheet, etc. for oriented electrical steel sheet and grain-oriented electrical steel sheet of a low iron loss variation in magnetic properties good small over the entire length of the steel sheet coil.
Means for Solving the Problems
[0005]
　The present inventors have conducted extensive studies to solve the above problems. As a result, in the manufacturing method of the grain-oriented electrical steel sheet which require slab heating at high temperature, by using a molten steel containing Cu, it is possible to suppress the temperature dependency of the fine precipitation in the solution and hot rolling of MnS It was revealed. However, when the Cu sulfide will be formed, since unstable precipitation behavior of Cu sulfides, characteristic deterioration of the tip and rear ends of the steel plate coil becomes also clear that tends to occur.
[0006]
　Accordingly, the present inventors have conducted further intensive studies to inhibit the formation of Cu sulfides. As a result, the selectivity of formation of formation and Cu sulfides Mn sulfides, particularly rough rolling and subsequent hot rolling, revealed that significantly depends on the thermal history of the before cold start. Then, the molten steel containing Cu 0.10% or more, if it is possible to suppress the generation of Cu sulfides at the time of the production of hot-rolled steel sheet, MnS was found to have deposited stably. Therefore, to avoid a decrease in inhibitor strength of MnS and AlN during finish annealing, it is possible to sharpen the secondary recrystallization of Goss orientation, the material in the coil due to variations in process conditions at the coil ends It was found that the change can be avoided.
[0007]
　The present inventors have found that further intensive studies based on these findings, and conceived to aspects of the invention described below.
[0008]
　(1)
　in
　mass%,
　Si: 2.0% ~
　5.0%, Mn: 0.03% ~ 0.12%, Cu: 0.10% ~
　1.00%, Sb or Sn or both :
　0.000% to
　0.3% in total, Cr: 0 to 0.3%, P: 0%
　- 0.5%, Ni: 0% - 1%, and
　balance: Fe and impurities,
　in Table has a chemical composition that is,
　in the L direction average diameter in parallel direction L in the rolling direction of the crystal grains observed in the surface of the steel sheet is, in the C direction average diameter in perpendicular direction C to the rolling direction 3.0 times or more oriented electrical steel sheet, characterized in that.
[0009]
　(2)
　oriented electrical steel sheet according to (1), wherein the L direction average diameter is more than 3.5 times the C direction average diameter.
[0010]
　(3) 　mass%,
　　C: 0.015% ~ 　0.10%, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12%, 　acid-soluble Al: 0.010 　~ 0.065%%,　N: 0.0040% ~ 　0.0100%, Cu: 0.10% ~ 1.00%, Cr: 　0% ~ 0.3%, P: 0% ~ 0.5% , 　Ni: 0% - 1%, 　S or Se, or both: 0.005% to 0.050% in 　total, Sb or Sn or both: 0.000% to 0.3% in 　total, Y , Te, La, Ce, Nd , Hf, Ta, Pb , or Bi, or any combination thereof: 0.0000% to 0.01% in total, and 　balance: Fe and impurities, 　organic in the chemical composition represented and, 　both the circle equivalent diameter below 50 nm MnS or MnSe or they are dispersed, Cu 2 S is hot rolled steel sheets for grain-oriented electrical steel sheet characterized in that not substantially precipitated.

[0011]
　(4)
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any combinations: 0.0005% to 0.01% in total
hot rolled steel sheets for grain-oriented electrical steel sheet according to at least one of is possible, characterized in that filled (3).
[0012]
　(5)
　obtaining a slab subjected to continuous casting of molten steel,
　and obtaining a hot rolled steel sheet by performing hot rolling of the slab heated to a temperature range of 1300 ° C. ~ 1490 ° C.,
　the hot-rolled steel sheet 600 ℃ and winding up at a temperature range,
　and performing hot-rolled sheet annealing of the hot-rolled steel sheet,
　after the hot rolled sheet annealing, a step of obtaining a cold rolled steel sheet by performing cold rolling,
　the cold-rolled and performing decarburization annealing of the steel sheet
　after said decarburization annealing, an annealing separating agent containing MgO is coated, and performing finish annealing,
has a
　step of performing the hot rolling, the finish temperature and performing rough rolling to 1200 ° C. or less, the start temperature of 1000 ° C. or higher, and a step of performing finish rolling in which the end temperature of 950 ° C. ~ 1100 ° C.,
　in the hot rolling, the rough rolling the finish rolling start within 300 seconds from the start,
　the finish rolling Exit from begins cooling the cooling rate is not less than 50 ° C. / sec within 10 seconds,
　the holding temperature of the hot-rolled sheet annealing, when the termination temperature of the finish rolling was set to Tf, 950 ℃ ~ (Tf + 100) ℃ and then,
　the molten steel is the
　mass%,
　C: 0.015% ~
　0.10%, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12%,
　acid-soluble Al:
　%
　~ 0.065 0.010%, N: 0.0040% ~ 0.0100%, Cu:
　0.10% ~ 1.00%, Cr: 0% ~
　0.3%, P: 0% ~ 0 .5%,
　Ni: 0% - 1%,
　S or Se, or both: 0.005% to 0.050% in
　total, Sb or Sn or both: 0.000% to 0.3% in
　total, Y, Te, La, Ce, Nd, Hf, Ta, Pb or Bi, or any combination thereof: 0.0000% to 0.01% in total, and
　balance: Fe and impurities,
　in that it has a chemical composition expressed method for producing a grain-oriented electrical steel sheet characterized by.
[0013]
　(6)
　the step of performing the casting, in a region where the thickness of one side of the solidified shell becomes 25% or more of the thickness of the slab, characterized by having a step of performing a magnetic stirring of the molten steel (5) method for producing oriented electrical steel sheet according to.
[0014]
　(7)
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any combinations: 0.0005% to 0.01% in total
production method of the grain-oriented electrical steel sheet according to at least one of is possible, characterized in that filled (5) or (6).
[0015]
　(8)
　obtaining a slab subjected to continuous casting of molten steel,
　and obtaining a hot rolled steel sheet by performing hot rolling of the slab heated to a temperature range of 1300 ° C. ~ 1490 ° C.,
　the hot-rolled steel sheet 600 ° C., the step of winding at a temperature range
having a
　step of performing the hot rolling, and performing rough rolling to the finishing temperature and 1200 ° C. or less, the start temperature of 1000 ° C. or more, a termination temperature and a step of performing the finish rolling and 950 ° C. ~ 1100 ° C.,
　in the hot rolling, the finish rolling begins within 300 seconds from the start of the rough rolling,
　within 10 seconds from the end of the finish rolling cooling rate starts cooling over 50 ° C. / sec,
　the molten steel is the
　mass%,
　C: 0.015% ~ 0.10%, Si: 2.0% ~
　5.0%, Mn: 0. 0.3% to 0.12%
　acid-soluble Al: 0.010% - 0.0
　% 65,
　N: 0.0040% ~
　0.0100%, Cu: 0.10% ~ 1.00%,
　Cr: 0% ~ 0.3%, P: 0% ~
　0.5%, Ni: 0 % 1%,
　S or Se, or both: 0.005% to 0.050% in
　total, Sb or Sn or both: 0.000%
　to 0.3% in total, Y, Te, La , Ce, Nd, Hf, Ta, Pb, or Bi, or any combination thereof: 0.0000% to 0.01% in total, and
　balance: Fe and impurities,
　Method for manufacturing a hot-rolled steel sheets for grain-oriented electrical steel sheet characterized by having a chemical composition expressed in.
[0016]
　(9)
　the step of performing the casting, in a region where the thickness of one side of the solidified shell becomes 25% or more of the thickness of the slab, characterized by having a step of performing a magnetic stirring of the molten steel (8) method for manufacturing a hot-rolled steel sheets for grain-oriented electrical steel sheet according to.
[0017]
　(10)
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any 0.0005% to 0.01% in total: the combination of
the manufacturing method of hot-rolled steel sheets for grain-oriented electrical steel sheet according to at least one of is possible, characterized in that filled (8) or (9).
Effect of the invention
[0018]
　According to the present invention, the fine precipitation in the solution and the hot rolling of the precipitates which act as inhibitors can be made uniform over the entire length of the slab, with a low iron loss over the entire length of the coil, the variation is less good magnetic properties it is possible to obtain.
BRIEF DESCRIPTION OF THE DRAWINGS
[0019]
[1] Figure 1, Cu content is an image showing the case of 0.4% crystal structure.
FIG. 2 is, Cu content is an image showing the case of 0.01% crystal structure.
DESCRIPTION OF THE INVENTION
[0020]
　It will be described in detail embodiments of the present invention.
[0021]
　First described molten steel having a chemical composition used in the hot-rolled steel sheet and manufacturing for grain-oriented electrical steel sheet according to the embodiment of the present invention. Although details will be described later, the hot-rolled steel sheets for grain-oriented electrical steel sheet according to the embodiment of the present invention is manufactured through continuous casting and hot rolling and the like of the molten steel. Therefore, the chemical composition of the hot-rolled steel sheet and the molten steel for grain-oriented electrical steel sheet, not only the properties of the hot-rolled steel sheet is obtained by considering these processes. In the following description, a unit of content of each element contained in the hot-rolled steel sheet or the molten steel for the grain-oriented electrical steel sheet "%" is especially meant to "mass%" unless otherwise specified. Hot-rolled steel sheets for grain-oriented electrical steel sheet according to the present embodiment, C: 0.015% ~ 0.10%, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12 %, acid-soluble Al: 0.010% ~ 0.065%, N: 0.0040% ~ 0.0100%, Cu: 0.10% ~ 1.00%, Cr: 0% ~ 0.3%, P: 0% ~ 0.5%, Ni: 0% ~ 1%, S or Se, or both: 0.005% to 0.050% in total, Sb or Sn or both: 0 in total. 000% ~ 0.3%, Y, Te, La, Ce, Nd, Hf, Ta, Pb, or Bi, or any combination thereof: 0.0000% to 0.01% in total, and balance: Fe and impurities in has a chemical composition represented. As the impurity, those included in raw materials such as ores and scrap, intended to be included in the manufacturing process, is exemplified.
[0022]
　(C: 0.015% ~ 0.10%)
　C stabilizes secondary recrystallization. The C content is less than 0.015%, secondary recrystallization becomes unstable. Therefore, C content is 0.015% or more. Further, to stabilize the secondary recrystallization, C content is preferably 0.04% or more. The C content of 0.10 percent, the time required for decarburization annealing is made economically disadvantageous long. Therefore, C content is not more than 0.10%, preferably not more than 0.09%.
[0023]
　(Si: 2.0% ~
　5.0%) Si is higher resistivity increases high content reduces the eddy current loss of the product. Si content is less than 2.0%, an eddy current loss becomes large. Therefore, Si content is 2.0% or more. Si content cracking easily occurs in cold rolling the more, Si content is 5.0 percent, cold rolling becomes difficult. Therefore, Si content is at most 5.0%. To further reduce the iron loss of the product, Si content is preferably 3.0% or more. To prevent reduction in the yield due to cracking during manufacture, Si content is preferably not more than 4.0%.
[0024]
　(Mn: 0.03% ~
　0.12%) Mn enhances the inhibitor to form S, and Se precipitates. The Mn content is less than 0.03%, its effect is small. Therefore, Mn content is 0.03% or more. The Mn content of 0.12 percent, undissolved Mn is produced in slab heating, uniform MnS or MnSe in a subsequent hot rolling, and can not be finely precipitated. Therefore, Mn content is at most 0.12%.
[0025]
　(Acid-soluble Al: 0.010% ~
　0.065%) Al forms AlN, acts as an inhibitor. The Al content is less than 0.010%, its effect can not be exhibited. Therefore, Al content is 0.010% or more. Further, to stabilize the secondary recrystallization, Al content is preferably 0.020% or more. The Al content 0.065 percent, not work effectively as inhibitors. Therefore, Al content is set to 0.065% or less. Further, to stabilize the secondary recrystallization, Al content is preferably to 0.040% or less.
[0026]
　(N: 0.0040% ~ 0.0100%)
　N forms AlN, acts as an inhibitor. The N content is less than 0.0040%, its effect can not be exhibited. Therefore, N content is 0.0040% or more. N content is 0.0100% greater, surface defects called blisters occur. Therefore, N content is 0.0100% or less. Further, to stabilize the secondary recrystallization, N content is, preferably 0.0060% or more.
[0027]
　(Cu: 0.10% ~
　1.00%) Cu is to reduce the temperature dependence of the precipitation of MnS and MnSe in MnS and the solution and the hot rolling of MnSe in the slab heating, uniform MnS and MnSe, and to be finely precipitated. The Cu content is less than 0.10%, its effect is small. Therefore, Cu content is 0.10% or more. In order to obtain this effect more reliably, Cu content is preferably 0.30 percent. Cu content is 1.00 percent is not economical become edge cracking likely to occur during hot rolling. Therefore, Cu content is at most 1.00%. To more reliably suppress edge cracking, Cu content is preferably to 0.80%.
[0028]
　(S or Se, or both: 0.005% to 0.050% in total)
　S and Se is effective for strengthening the inhibitors, to improve the magnetic properties. It is less than 0.005% content of S or Se, or both of these in total, inhibitor is weak, the magnetic characteristics are deteriorated. Therefore, the content of S or Se or both are a total of 0.005% or more. Further, to stabilize the secondary recrystallization, the content of S or Se or both are preferably a total of 0.020% or more. In 0.050 percent content of S or Se, or both of these in total, edge cracking is likely to occur in hot rolling. Therefore, the content of S or Se or both shall be 0.050% or less in total. Further, to stabilize the secondary recrystallization, the content of S or Se, or both are, preferably 0.040% or less in total.
[0029]
　Sb, Sn, Y, Te, La, Ce, Nd, Hf, Ta, Pb and Bi is not an essential element, may optionally be contained in limits a predetermined amount of hot-rolled sheet for grain-oriented electrical steel sheet it is an optional element.
[0030]
　(Sb or Sn or both: 0.000% to 0.3% in
　total) Sb and Sn are strongly inhibitor. Therefore, Sb or Sn may be contained. In order to obtain the advantageous effects sufficiently, Sb or Sn or the content of both of which, preferably the total 0.003% or more. In 0.3 percent Sb or Sn or the content of both of these in total, operational effects can be obtained not economical. Therefore, Sb or Sn or the content of both of these is 0.3% or less in total.
[0031]
　(Y, Te, La, Ce , Nd, Hf, Ta, Pb or Bi, or any combination thereof:
　0.0000% to 0.01% in total) Y, Te, La, Ce, Nd, Hf, Ta , Pb and Bi are strong inhibitors. Thus, Y, Te, La, Ce , Nd, Hf, Ta, Pb or Bi, or any combination thereof may be contained. In order to obtain the advantageous effects sufficiently, Y, Te, La, Ce , Nd, Hf, Ta, Pb or Bi or the content of any combination thereof is preferably the total 0.0005% or more. Further, to stabilize the secondary recrystallization, Y, Te, La, Ce , Nd, Hf, Ta, Pb or Bi, or the content of any combination of these, 0.0010% and more preferably in a total and more. Y, Te, La, Ce, Nd, Hf, Ta, Pb content or Bi or any combination 0.01 percent in total, operational effects can be obtained not economical. Accordingly, Y, Te, La, Ce, Nd, Hf, Ta, Pb or Bi or the content of any of these combinations are 0.01% or less in total.
[0032]
　(Others)
　Further in accordance with the known purpose, hot-rolled steel sheets for grain-oriented electrical steel sheet according to the present embodiment is Cr: 0% ~ 0.3%, P: 0% ~ 0.5% and Ni: 0% it may contain ~ 1%.
[0033]
　Hot-rolled steel sheets for grain-oriented electrical steel sheet according to the embodiment of the present invention, the circle equivalent diameter are dispersed following MnS or MnSe or both 50 nm, Cu 2 S are not substantially precipitated. Cu 2 S is thermally unstable precipitates as compared with MnS and MnSe, the effect as an inhibitor is little. Rather, Cu 2 in the case of producing a hot rolled steel sheet under the condition that S is not generated, the state of dispersion of MnS and MnSe is satisfactory, the magnetic properties of the product is improved. Confirmation of the presence state of these precipitates form a thin film sample by focused ion beam (FIB), it is made in the transmission electron microscope (TEM). In identifying the composition of the fine precipitates dispersed in the steel energy dispersive spectroscopy by (EDS), components contained in the matrix not only components constituting the precipitates are also detected. Therefore, in the present invention, when the diameter is sulfides 30 nm ~ 50 nm and Se compounds 10 was EDS analysis, Cu content was quantitatively analyzed, including the matrix phase is less than 1%, Cu 2 S is substantially and it is determined not to have to precipitation. If sulfide or Se compound is not spherical, the circle equivalent diameter D and the diameter of the precipitates. The area S of the precipitate was measured by TEM observation, "S = [pi] D 2 can be determined from / 4".
[0034]
　Next, a description will be given chemical composition of the grain-oriented electrical steel sheet according to the embodiment of the present invention. Although details will be described later, oriented electrical steel sheet according to the embodiment of the present invention, the casting of molten steel, hot rolling, hot-rolled sheet annealing, cold rolling, is produced through application of annealing separator, and finishing annealing, etc. that. Therefore, the chemical composition of the grain-oriented electrical steel sheet, not only the properties of the grain-oriented electrical steel sheet, is taken into consideration these processes. In the following description, a unit of content of each element contained in the grain-oriented electrical steel sheet "%" is especially meant to "mass%" unless otherwise specified. Oriented electrical steel sheet according to the present embodiment, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12%, Cu: 0.10% ~ 1.00%, Sb or Sn or both of: 0.000% to 0.3% in total, Cr: 0% ~ 0.3%, P: 0% ~ 0.5%, Ni: 0% ~ 1%, and balance: Fe and It has a chemical composition represented by the impurities. As the impurity, those included in raw materials such as ores and scrap, intended to be included in the manufacturing process, is exemplified.
[0035]
　(Si: 2.0% ~
　5.0%) Si is higher resistivity increases high content reduces the eddy current loss of the product. Si content is less than 2.0%, an eddy current loss becomes large. Therefore, Si content is 2.0% or more. Si content cracking easily occurs in cold rolling the more, Si content is 5.0 percent, cold rolling becomes difficult. Therefore, Si content is at most 5.0%. To further reduce the iron loss of the product, Si content is preferably 3.0% or more.
[0036]
　(Mn: 0.03% ~
　0.12%) Mn enhances the inhibitor to form precipitates with S or Se. The Mn content is less than 0.03%, its effect is small. Therefore, Mn content is 0.03% or more. The Mn content of 0.12 percent, undissolved Mn is produced in slab heating, uniform MnS or MnSe in a subsequent hot rolling, and can not be finely precipitated. Therefore, Mn content is at most 0.12%.
[0037]
　(Cu: 0.10% ~
　1.00%) Cu is to reduce the temperature dependence of the solution of MnS and MnSe in the hot-rolling temperature region, the MnS or MnSe uniform, is finely precipitated. The Cu content is less than 0.10%, its effect is small. Therefore, Cu content is 0.10% or more. In order to obtain this effect more reliably, Cu content is preferably 0.30 percent. Cu content is 1.00 percent is not economical become edge cracking likely to occur during hot rolling. Therefore, Cu content is at most 1.00%. To more reliably suppress edge cracking, Cu content is preferably to 0.80%.
[0038]
　Sb and Sn is not an essential element, a good optional elements may optionally be contained in limits a predetermined amount in the grain-oriented electrical steel sheet.
[0039]
　(Sb or Sn or both: 0.000% to 0.3% in
　total) Sb and Sn are strongly inhibitor. Therefore, Sb or Sn may be contained. In order to obtain the advantageous effects sufficiently, Sb or Sn or the content of both of which, preferably the total 0.003% or more. In 0.3 percent Sb or Sn or the content of both of these in total, operational effects can be obtained not economical. Therefore, Sb or Sn or the content of both of these is 0.3% or less in total.
[0040]
　(Others)
　Further in accordance with the known purpose-oriented electrical steel sheet according to the present embodiment is Cr: 0% ~ 0.3%, P: 0% ~ 0.5% and Ni: containing from 0% to 1% it may be.
[0041]
　C, acid-soluble Al, N, Cr, P, Ni, S, and Se are in the process of manufacturing the oriented electrical steel sheet, the crystal orientation {110} <001> to control the Goss texture was integrated in the orientation is utilized, it may not be included in the grain-oriented electrical steel sheet. Although details will be described later, these elements, in purification annealing contained in the final annealing, is discharged out of the system. In particular C, N, S, lowering the concentration of the acid-soluble Al and Se is remarkable, it becomes 50ppm or less. If the condition of a normal purification annealing, 9 ppm or less, more 6ppm or less, if sufficiently performed purification annealing, reaches a degree that can not be detected (1 ppm or less) in the general analysis. Accordingly, it is intended to C, N, S, even as the acid-soluble Al and Se is left in the grain-oriented electrical steel sheet as an impurity.
[0042]
　The oriented electrical steel sheet according to the embodiment of the present invention, L-direction average diameter in parallel direction L in the rolling direction of the crystal grains observed in the surface of the steel sheet is, in the C direction average diameter in perpendicular direction C to the rolling direction 3 it is 2.0 times or more. In the following description, the ratio of the L-direction average diameter to the C direction average diameter (L direction mean diameter / C direction average diameter) may be referred to as "particle size ratio". Crystal structure oriented electrical steel sheet of the present embodiment is characteristic due to its own inhibitor control. Although the mechanism of tissue formation is not clear, probably it is inferred that there is a correlation between the dispersion state of an inhibitor MnS and MnSe. When the particle diameter ratio is 3.0 or more, the magnetoresistance effect of the crystal grain boundary is reduced, and since the magnetic domain width is reduced, the magnetic properties is improved. Therefore, the particle size ratio of the crystal grains observed in the surface of the steel sheet is set to 3.0 or higher, preferably 3.5 or more.
[0043]
　Next, a method for manufacturing the hot-rolled steel sheets for grain-oriented electrical steel sheet according to the embodiment of the present invention. In the method for producing hot-rolled steel sheets for grain-oriented electrical steel sheet according to the present embodiment, the molten steel continuous casting, performing hot rolling and the like.
[0044]
　First, in the continuous casting and hot rolling of the molten steel, by performing the continuous casting of molten steel used in the production of the hot-rolled steel sheet to form a slab, heat and hot rolling of the slab.
[0045]
　In continuous casting, in a region where the thickness of one side of the solidified shell is 25% or more of the thickness of the slab, it is preferable to perform the electromagnetic stirring of the molten steel. Is less than 25% ratio of one side of the solidified shell thickness to the slab thickness, Cu 2 S is easily deposited, the effect of improving the magnetic properties because hardly obtained. Thus, the ratio of one side of the solidified shell thickness to the slab thickness is preferably 25% or more. Electromagnetic stirring of such molten steel, an effect of suppressing the formation of sulfide containing Cu. Even if a magnetic stir only solidified shell ratio of thickness of 33% greater than the area of one side with respect to the slab thickness, the effect is not sufficiently obtained. Thus, the ratio of one side of the solidified shell thickness to the slab thickness is preferably not more than 33%. By performing electromagnetic stirring on one side of the solidified shell ratio of thickness of 25% to 33% area with respect to the slab thickness, subjected to magnetic stirring ratio of one side of the solidified shell thickness with more than 33% of the region to the slab thickness it may be. By performing electromagnetic stirring of molten steel, Cu to the hot-rolled steel sheet 2 S is less likely to be precipitated, the crystal grains of particle size ratio to be observed at the surface of grain-oriented electromagnetic steel sheet as a final product tends to be 3.5 or more . This is because the sulfide by hot rolling is dispersed more finely precipitated.
[0046]
　The slab heating temperature is less than 1300 ° C., a large variation in the magnetic flux density of the product. Accordingly, the slab heating temperature, and 1300 ° C. or higher. Slab heating temperature in the 1490 ° C. greater than the slab is melted. Accordingly, the slab heating temperature, and 1490 ° C. or less.
[0047]
　In hot rolling, it carried out rough rolling to the finishing temperature and 1200 ° C. or less, the start temperature of 1000 ° C. or more, performing finish rolling termination temperature was set to 950 ℃ ~ 1100 ℃. The end temperature is 1200 ° C. than the rough rolling, MnS or MnSe precipitation in the rough rolling is not promoted, Cu in the finishing rolling 2 S ends up generating, magnetic properties of the product are deteriorated. Therefore, the end temperature of the rough rolling is set to 1200 ° C. or less. Is less than the finish rolling start temperature is 1000 ° C., below the 950 ° C. Exit temperature of the finish rolling, Cu 2 S is easily precipitated, the magnetic properties of the product is not stable. Therefore, the starting temperature of finish rolling is set to 1000 ° C. or higher. The end temperature is lower than 950 ° C. of finish rolling, Cu 2 S is easily precipitated, the magnetic characteristics are not stable. Further, when the temperature difference between the slab heating temperature is too large, it is difficult to adjust the temperature history of hot-rolled coils entire length, it is difficult to build in homogeneous inhibitor over the entire length of the hot-rolled coil. Therefore, the end temperature of finish rolling is set to 950 ° C. or higher. The end temperature is 1100 ° C. than the finish rolling can not be controlled to be dispersed MnS and MnSe fine. Therefore, the end temperature of finish rolling is set to 1100 ° C. or less.
[0048]
　From the start of the rough rolling finishing within 300 seconds to start rolling. The time is 300 seconds more than the start of rough rolling to the start of the finish rolling, 50 nm or less of MnS or MnSe which acts as an inhibitor is not dispersed, the secondary recrystallization grain diameter control and finish annealing the decarburization annealing becomes difficult, magnetic characteristics are deteriorated. Therefore, the time from the start of rough rolling to the start of the finish rolling is within 300 seconds. The lower limit of the time is not particularly necessary to set if normal rolling. In less than 30 seconds until the start of the finish rolling from the start of rough rolling, the precipitation amount of MnS or MnSe is not sufficient, the secondary recrystallized grains may become difficult to develop during finish annealing.
[0049]
　The rear end of the hot-rolled steel sheet has a long residence time of the start of the finish rolling from the start of rough rolling than the center portion of the hot-rolled steel sheet, MnS tends coarsened were precipitated. The tip of the hot-rolled steel sheet, because the starting temperature of the rough rolling is high, MnS is easily coarsened. By Cu is contained, it is possible to suppress the coarsening of MnS, resulting in effective in reducing the variation in magnetic properties in the coil.
[0050]
　From the end of finish rolling within 10 seconds, the cooling rate starts to cool over 50 ° C. / sec. The time is more than 10 seconds from the end of finish rolling until the start of cooling, Cu 2 S is easily precipitated, the magnetic properties of the product is not stable. Therefore, the time from the end of finish rolling until the start of cooling to a maximum of 10 seconds, preferably within 2 seconds. If it is less than finish rolling after the cooling rate is 50 ° C. / sec, Cu 2 S is easily precipitated, the magnetic properties of the product is not stable. Therefore, the cooling rate after the finish rolling is set to 50 ° C. / sec or higher.
[0051]
　Then, they wound up in a temperature range of 600 ℃ or less. The coiling temperature is 600 ° C. greater, Cu 2 S is easily precipitated, the magnetic properties of the product is not stable. Therefore, the coiling temperature is set to 600 ° C. or less.
[0052]
　In this way, it is possible to manufacture a hot-rolled steel sheets for grain-oriented electrical steel sheet according to the present embodiment.
[0053]
　Next, a method for manufacturing a grain-oriented electrical steel sheet according to the embodiment of the present invention. In the method of manufacturing the oriented electrical steel sheet according to the present embodiment will be molten steel continuous casting, hot rolling, hot-rolled sheet annealing, cold rolling, decarburization annealing, coating of an annealing separating agent, the final annealing and the like. For continuous casting and hot rolling of the molten steel can be performed similarly to the manufacturing method of the hot-rolled steel sheet for the grain-oriented electrical steel sheet.
[0054]
　Performing hot-rolled sheet annealing the resulting hot-rolled steel sheet. When the termination temperature of finish rolling was Tf, the holding temperature of the hot-rolled sheet annealing 950 ℃ ~ (Tf + 100) to ° C.. Holding temperature is less than 950 ° C., can not be homogeneous inhibitor over the entire length of the hot-rolled coils, the magnetic properties of the product is not stable. Therefore, the holding temperature is set to 950 ° C. or higher. The holding temperature is (Tf + 100) ℃ greater, MnS which is finely precipitated in the hot rolled grows rapidly, the secondary recrystallization becomes unstable. Therefore, the holding temperature is set to (Tf + 100) ℃ or less. By performing appropriately hot-rolled sheet annealing, it is possible to suppress the coarse growth of MnS during finish annealing. The mechanism by which coarse growth is suppressed, be inferred as follows. And interface Cu segregation of MnS and matrix, is believed to work inhibitory to the growth of MnS. Too high a holding temperature of hot-rolled sheet annealing, Cu tends to interface disappears segregated with the growth of MnS, the effect can not be sufficiently obtained. Furthermore, in order to obtain the effect of such Cu is, Cu in the hot-rolled steel sheet 2 S is assumed that substantially precipitated is possible not favor. P, Sn, may also exhibit the same action easily segregated elements such as Sb and Bi.
[0055]
　Next, obtain a cold-rolled steel sheet performed twice or more cold rolling sandwiching the rolling or intermediate annealing between single cold. Thereafter, decarburization annealing of the cold-rolled steel sheet, coated with annealing separator containing MgO, performing finish annealing. Annealing separator contains MgO, the proportion of MgO in the annealing separator agent is, for example, 90 mass% or more. In the finish annealing, after the completion of secondary recrystallization, it may be subjected to purification annealing. Cold rolling, decarburization annealing, coating of an annealing separating agent, and finish annealing may be performed by a general method.
[0056]
　In this way, it is possible to manufacture a grain-oriented electrical steel sheet according to the present embodiment. After finish annealing, it may form an insulating coating by coating and baking.
[0057]
　The manufacturing conditions in the manufacturing method of the hot-rolled steel sheet and grain-oriented electrical steel sheet for grain-oriented electrical steel sheet according to the embodiment of the present invention, Cu 2 S is a difficult condition precipitates. Such particle size ratio of the crystal grains hot-rolled steel sheet with that observed in the surface of the produced grain-oriented electrical steel sheet becomes 3.0 or more. This mechanism is as follows. MnS as the inhibitor, it had been understood to uniformly dispersed by hot rolling, Cu 2 when suppress the precipitation of S,
[0058]
　From the above, according to the manufacturing method of the hot-rolled steel sheet and grain-oriented electrical steel sheet for grain-oriented electrical steel sheet according to the embodiment of the present invention, the fine precipitation in the solution and the hot rolling of the precipitates which act as inhibitors can be made uniform over the entire length of the slab, the magnetic characteristics over the entire length of the coil can be obtained hot rolled steel sheets for grain-oriented electrical steel sheet and grain-oriented electrical steel sheet excellent in little variation low iron loss.
[0059]
　Having described in detail preferred embodiments of the present invention, the present invention is not limited to such an example. It would be appreciated by those skilled in the relevant field of technology of the present invention, within the scope of the technical idea described in the claims, it is intended to cover various changes and modifications , also such modifications are intended to fall within the technical scope of the present invention.
Example
[0060]
　Next, the hot-rolled steel sheet and grain-oriented electrical steel sheet for grain-oriented electrical steel sheet according to the embodiment of the present invention will be specifically described below showing Examples. Examples shown below are only just examples of the hot-rolled steel sheet and grain-oriented electrical steel sheet for grain-oriented electrical steel sheet according to the embodiment of the present invention, the hot-rolled steel sheet and the direction for grain-oriented electrical steel sheet according to the present invention sex electromagnetic steel sheet is not limited to the following examples.
[0061]
　(Example 1)
　by casting the steels B and C shown in Table 1 to prepare a slab, the slab subjected to hot rolling six passes, the plate thickness was obtained hot rolled steel sheets of 2.3 mm. The front three-pass interpass time is a rough rolling of 5 seconds to 10 seconds, subsequent 3 between the path path time has a finish rolling of less than 2 seconds. Underlined in Table 1 indicates that the value is out of range of the present invention. The casting of the molten steel was subjected to magnetic stirring under the conditions shown in Table 2. Conditions of slab heating temperatures and hot rolling are also shown in Table 2. After hot rolling completion, immediately cooled to 550 ° C. over a water spray, heat treatment was performed for winding equivalent by holding for 1 hour at the temperature shown in Table 2 in an air furnace. Also shown in Table 2 for cooling conditions. For hot-rolled steel sheet thus obtained was confirmed by TEM the existing state of the sulfide. The results are shown in Table 2. Then, the hot rolled steel sheet was annealed at a temperature shown in Table 2, the thickness in the cold rolling and 0.225 mm, subjected to decarburization annealing at 840 ° C., then coated with an annealing separator mainly comprised of MgO, perform finish annealing of 1170 ° C., to produce a variety of grain-oriented electrical steel sheet. The resulting directional grain size ratio observed on the surface of the electrical steel sheet was obtained. The results are shown in Table 2. Underlined in Table 2 indicates that the value is out of range of the present invention.
[0062]
[Table 1]

[0063]
[Table 2]

[0064]
　As shown in Table 2, Sample No. 1 ~ No. 8 and sample No. 21 ~ No. In 28, the slab heating temperature, hot rolling condition, cooling conditions, the coiling temperature, the holding temperature of the hot-rolled sheet annealing are within the scope of the present invention, good results of the particle size ratio is 3.0 times or more obtained. Of these samples, sample No. 1, No. 2, No. 21 and No. In 22, for performing a magnetic stir when molten steel casting, excellent results that the particle size ratio is 3.5 or more was obtained.
[0065]
　Sample No. 9 and No. In 29, since the slab heating temperature is too low, it was small particle size ratio. Sample No. 10 and No. In 30, since the slab heating temperature is too high, it was not possible to carry out the subsequent hot rolling. Sample No. 11 and No. In 31, for completion temperature of the rough rolling it was too high, was small particle size ratio. Sample No. 12 and No. In 32, because the time from the start of rough rolling to the start of the finish rolling was too long, it was small particle size ratio. Sample No. 13 and No. In 33, for completion temperature of the starting temperature and finish rolling of the finish rolling it was too low, was small particle size ratio. Sample No. 14 and No. In 34, for termination temperature of finish rolling it was too low, was small particle size ratio. Sample No. 15 and No. In 35, for termination temperature of finish rolling it was too high, was small particle size ratio. Sample No. 16 and No. In 36, since the time until cooling start from the end of finish rolling it was too long, was small particle size ratio. Sample No. 17 and No. In 37, the cooling rate after finish rolling was too late, was small particle size ratio. Sample No. 18 and No. In 38, since the coiling temperature is too high, it was small particle size ratio. Sample No. 19 and No. In 39, for holding the temperature of the hot-rolled sheet annealing it was too low, was small particle size ratio. Sample No. 20 and No. In 40, for holding the temperature of the hot-rolled sheet annealing it was too high, was small particle size ratio.
[0066]
　(Example 2-1)
　was cast steels A ~ N shown in Table 1 to prepare a slab, the slab 1350 ° C., then heated for 30 minutes, 2.3 mm is thickness performing hot rolling of 6 paths to obtain a hot-rolled steel sheet. The front three-pass interpass time is a rough rolling of 5 seconds to 10 seconds, subsequent 3 between the path path time has a finish rolling of less than 2 seconds. The time from the rough rolling start to finish rolling start, was 40 seconds to 180 seconds. The end temperature of the rough rolling and 1120 ℃ ~ 1160 ℃, and the starting temperature of finish rolling and 1000 ℃ ~ 1140 ℃. The end temperature Tf of the hot rolling (finish rolling) was set to 900 ℃ ~ 1060 ℃. After hot rolling completion (after finish rolling end), immediately cooled to 550 ° C. over a water spray, 550 ° C. in an air furnace, a heat treatment was carried out winding equivalent by holding for 1 hour. After the end of the final rolling, the time to start cooling is 0.7 seconds to 1.7 seconds, and the cooling rate after the finish rolling to a 70 ° C. / sec or more. The resulting hot-rolled steel sheets were annealed at 900 ° C. ~ 1150 ° C., the plate thickness by cold rolling and 0.225 mm, subjected to decarburization annealing at 840 ° C., coated with an annealing separator composed mainly of MgO then, it was finished annealing of 1170 ℃. After washing with water, then sheared to 60mm width × 300 mm length, after stress relief annealing at 850 ° C., and subjected to magnetic measurements. The results of magnetic measurements shown in Table 3. Underlined in Table 3 indicates that the numerical value is outside the scope of the present invention. Cu: 0.4% when the crystal structure shown in FIG. 1, Cu: 2 to the case of the 0.01% crystal structure.
[0067]
[table 3]

[0068]
　From Table 3, the absolute value improvement of characteristics due to the Cu is contained is shown. Experimental conditions of this example, the starting temperature of the rough rolling is high, since the residence time is short to the start of the finish rolling from the start of rough rolling, near and conditions at the tip of the hot-rolled steel sheet, the tip of the hot-rolled steel sheet and also it indicated the possibility of improving the characteristic degradation in the rear end. Magnetic properties was confirmed to improve by high Cu content.
[0069]
　As shown in Table 3, Sample No. B1, No. C1, No. C2, No. D1, No. D4, No. D5, No. E1, No. F1, No. G1, No. H1, No. J1, No. K1, No. L1, No. M1, and No. In N1, since the hot-rolling conditions, the holding temperature of the hot-rolled sheet annealing, the chemical composition is within the scope of the present invention, the particle size ratio is 3.0 times or more, good magnetic properties were obtained. Of these samples, sample No. D1, No. D4, No. D5, No. G1, and No. In H1, since a high Cu content, it was obtained excellent magnetic properties.
[0070]
　Sample No. In A1, since Cu content was too low, it was small particle size ratio. Sample No. A2 and No. In A3, low Cu content, since the holding temperature hot-rolled sheet annealing was too high, was small particle size ratio. Sample No. B2, No. B3, No. C3, No. D2, No. D3, No. E2, and No. In E3, for holding the temperature of hot-rolled sheet annealing it was too high, was small particle size ratio. Sample No. In D6, for holding the temperature of the hot-rolled sheet annealing it was too low, was small particle size ratio. Sample No. In I1, low end temperature of the finish rolling, since the holding temperature of the hot-rolled sheet annealing was too low, Cu 2 S was precipitated. Sample No. O1 and No. In O2, high S content, Cu content for a relatively high is within the scope of the present invention, Cu 2 S was precipitated. Sample No. P1 and No. In P2, since Cu content was too high, Cu 2 S was precipitated. Sample No. In Q1, low end temperature of the finish rolling, since the holding temperature of the hot-rolled sheet annealing was too low, Cu 2 S was precipitated.
[0071]
　(Example 2-2)
　during casting of molten steel, except for performing electromagnetic stirring under the conditions shown in Table 4, was performed in the same manner as in Example 2-1. The results of the particle size ratio and magnetic measurements are shown in Table 4. Underlined in Table 4 indicates that the numerical value is outside the scope of the present invention.
[0072]
[Table 4]

[0073]
　As shown in Table 4, Sample No. B4, No. C4, No. C5, No. D7, No. D10, No. D11, No. E4, No. F2, No. G2, No. H2, No. J2, No. K2, No. L2, No. M2, and No. In N2, hot rolling conditions, in the range of holding temperature, the chemical composition present invention hot-rolled sheet annealing, for performing a magnetic stir when the molten steel of the casting, and the particle size ratio is 3.5 or more, excellent magnetic properties were obtained.
[0074]
　Sample No. In A4, since Cu content was too low, it was small particle size ratio. Sample No. A5 and No. In A6, low Cu content, since the holding temperature hot-rolled sheet annealing was too high, was small particle size ratio. Sample No. B5, No. B6, No. C6, No. D8, No. D9, No. E5, and No. In E6, for holding the temperature of hot-rolled sheet annealing it was too high, was small particle size ratio. Sample No. In D12, for holding the temperature of the hot-rolled sheet annealing it was too low, was small particle size ratio. Sample No. In I2, low end temperature of the finish rolling, since the holding temperature of the hot-rolled sheet annealing was too low, Cu 2 S was precipitated. Sample No. O3 and No. In O4, high S content, Cu content for a relatively high is within the scope of the present invention, Cu 2 S was precipitated. Sample No. P3 and No. In P4, since the Cu content is too high, Cu 2 S was precipitated. Sample No. In Q2, low end temperature of the finish rolling, since the holding temperature of the hot-rolled sheet annealing was too low, Cu 2 S was precipitated.
[0075]
　(Example 3-1)
　steel type A shown in Table 1, B, C, and cast H to prepare a slab, the slab 1350 ° C., then heated for 30 minutes, plate thickness by performing hot rolling of 6 paths There was obtained a hot-rolled steel sheet of 2.3mm. The front three-pass interpass time is a rough rolling of 5 seconds to 10 seconds, subsequent 3 between the path path time has a finish rolling of less than 2 seconds. Front three-pass predetermined time coercive heated to 1100 ° C. or more after rolling, the time from the start of rough rolling to the start of the finish rolling (the waiting time) were adjusted as shown in Table 5. The end temperature Tf of the hot rolling (finish rolling) was two 1000 ° C. and 1060 ° C.. After hot rolling end (finish rolling after the end), and cooled to immediately 550 ℃ over the water spray. Others, hot-rolled conditions were as follows. That is, the end temperature of the rough rolling and 1120 ° C.-1160 ° C., and the starting temperature of finish rolling and 1000 ° C.-1140 ° C., the time from after the end of finish rolling to the start cooled to 0.7 seconds to 1.7 seconds the cooling rate after the finish rolling to a 70 ° C. / sec, and the coiling temperature 550 ° C. (simulated by heat treatment atmosphere furnace 1 hour hold). The resulting hot-rolled steel sheets were annealed at 1080 ° C. ~ 1100 ° C., the plate thickness by cold rolling and 0.225 mm, subjected to decarburization annealing at 840 ° C., an annealing separator composed mainly of MgO coating then, it was finished annealing of 1170 ℃. After washing with water, then sheared to 60mm width × 300 mm length, after stress relief annealing at 850 ° C., and subjected to magnetic measurements. The results of magnetic measurements shown in Table 5. Underlined in Table 5 indicates that the number is out of range of the present invention.
[0076]
[table 5]

[0077]
　As shown in Table 5, Sample No. B7 ~ No. B9, No. C7 ~ No. C9, No. H3, and No. In H4, since the hot-rolling conditions, the holding temperature of the hot-rolled sheet annealing, the chemical composition is within the scope of the present invention, good results of the particle size ratio is 3.0 times or more was obtained. If the time from the start of rough rolling to the start of the finish rolling is within 300 seconds, stable and good magnetic properties were obtained.
[0078]
　Sample No. A7 ~ No. In A9, since Cu content was too low, it was small particle size ratio. Sample No. In H5, because the time from the start of rough rolling to the start of the finish rolling was too long, magnetic properties were inferior.
[0079]
　(Example 3-2)
　during casting of molten steel, except for performing electromagnetic stirring under the conditions shown in Table 6, were conducted in the same manner as in Example 3-1. The results of the particle size ratio and magnetic measurements are shown in Table 6. Underlined in Table 6 indicates that the numerical value is outside the scope of the present invention.
[0080]
[Table 6]

[0081]
　As shown in Table 6, Sample No. B10 ~ No. B12, No. C10 ~ No. C12, No. H6, and No. In H7, hot rolling conditions, in the range of holding temperature, the chemical composition present invention hot-rolled sheet annealing, for performing a magnetic stir when the molten steel of the casting, and the particle size ratio is 3.5 or more, excellent magnetic properties were obtained.
[0082]
　Sample No. A10 ~ No. In A12, since Cu content was too low, it was small particle size ratio. Sample No. In H8, because the time from the start of rough rolling to the start of the finish rolling was too long, magnetic properties were inferior.

claims

[Claim 1]Bymass%,Si: 2.0% ~5.0%, Mn: 0.03% ~0.12%, Cu: 0.10% ~
　1.00%, Sb or Sn or both: total
　% ~ 0.3 0.000%,
　Cr: 0% ~ 0.3%, P: 0%
　~ 0.5%, Ni: 0% ~ 1%, and
　balance: Fe and impurities,
　in represented by chemical has a composition,
　L-direction average diameter in parallel direction L in the rolling direction of the crystal grains observed in the surface of the steel sheet is, that in the vertical direction C to the rolling direction is the direction C average diameter of 3.0 times or more oriented electrical steel sheet characterized.
[Claim 2]
　Oriented electrical steel sheet according to claim 1, wherein the L direction average diameter is more than 3.5 times the C direction average diameter.
[Claim 3]
　By
　mass%,
　C: 0.015% ~
　0.10%, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12%,
　acid-soluble Al: 0.010% ~ 0
　% .065,
　N: 0.0040% ~
　0.0100%, Cu: 0.10% ~ 1.00%,
　Cr: 0% ~ 0.3%, P: 0% ~
　0.5%, Ni: 0% 1%,
　S or Se, or both: 0.005% to 0.050% in
　total, Sb or Sn or both: 0.000% to
　total,0.3% Y, Te, la, Ce, Nd, Hf, Ta, Pb , or Bi, or any combination thereof: 0.0000% to 0.01% in total, and
　balance: Fe and impurities,
　have in a chemical composition represented,
　the circle equivalent and diameter dispersed following MnS or MnSe or both 50 nm, Cu 2 S is the actual Hot-rolled steel sheets for grain-oriented electrical steel sheet characterized in that not qualitatively precipitated.
[Claim 4]
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any combination thereof: 0.0005% to 0.01% in total
hot rolled steel sheets for grain-oriented electrical steel sheet according to claim 3, characterized in that at least one of is satisfied.
[Claim 5]
　Obtaining a slab subjected to continuous casting of molten steel,
　1300 ° C. obtaining a hot rolled steel sheet by performing hot rolling of the slab is heated to a temperature range of ~ 1490 ° C.,
　the following 600 ° C. the hot-rolled steel sheet a step of winding the temperature range,
　and performing hot-rolled sheet annealing of the hot-rolled steel sheet,
　after the hot rolled sheet annealing, a step of obtaining a cold rolled steel sheet by performing cold rolling,
　de of the cold-rolled steel sheet and performing charcoal annealing,
　after the decarburization annealing, an annealing separating agent containing MgO is coated, and performing finish annealing,
has a
　step of performing the hot rolling, 1200 ° C. or less end temperature and that the step of performing rough rolling, the starting temperature and 1000 ° C. or more and, and a step of performing finish rolling in which the end temperature of 950 ° C. ~ 1100 ° C.,
　in the hot rolling, 300 from the start of the rough rolling the finish rolling start within seconds,
　the end of the finish rolling Cooling rate within 10 seconds will start cooling over 50 ° C. / sec,
　a holding temperature of the hot-rolled sheet annealing, a finish temperature of the finish rolling when the Tf, and 950 ℃ ~ (Tf + 100) ℃,
　the molten steel is the
　mass%,
　C: 0.015% ~
　0.10%, Si: 2.0% ~ 5.0%, Mn: 0.03% ~ 0.12%,
　acid-soluble Al: 0.
　%
　~ 0.065 010%, N: 0.0040% ~
　0.0100%, Cu: 0.10% ~ 1.00%, Cr: 0%
　~ 0.3%, P: 0% ~ 0.5
　Pasento, Ni: 0 Pasento ～ 1 Pasento,
　S or Se or both: 0.005% to 0.050% in
　total, Sb or Sn or both:
　0.000% to 0.3% in total, Y, Te, La, Ce, Nd, hf, Ta, Pb or Bi, or any combination thereof: 0.0000% to 0.01% in total, and
　balance: Fe and impurities,
　grain-oriented electrical steel sheet characterized by having a in chemical composition represented the method of production.
[Claim 6]
　The step of performing the casting, in a region where the thickness of one side of the solidified shell becomes 25% or more of the thickness of the slab, according to claim 5, characterized in that it comprises a step of performing a magnetic stirring of the molten steel method for producing a grain-oriented electrical steel sheet.
[Claim 7]
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any combination thereof: 0.0005% to 0.01% in total
production method of the grain-oriented electrical steel sheet according to claim 5 or 6, characterized in that at least one of is satisfied.
[8.]
　Obtaining a slab subjected to continuous casting of molten steel,
　1300 ° C. obtaining a hot rolled steel sheet by performing hot rolling of the slab is heated to a temperature range of ~ 1490 ° C.,
　the following 600 ° C. the hot-rolled steel sheet a step of winding in a temperature range,
has a
　step of performing rolling the heat and performing rough rolling to the finishing temperature and 1200 ° C. or less, the start temperature of 1000 ° C. or higher, 950 ° C. ~ Exit temperature and a step of performing the finish rolling and 1100 ° C.,
　in the hot rolling, the finish rolling begins within 300 seconds from the start of the rough rolling,
　the cooling rate from the end of the finish rolling within 10 seconds start cooling over 50 ° C. / sec,
　the molten steel is the
　mass%,
　C: 0.015% ~ 0.10%, Si: 2.0%
　~ 5.0%, Mn: 0.03% ~ 0.12%,
　acid-soluble Al: 0.010% ~ 0.065% ,
　N:
　0.0040%
　~ 0.0100%, Cu: 0.10% ~
　1.00%, Cr: 0% ~ 0.3%, P: 0% ~
　0.5%, Ni: 0% ~ 1%,
　S or Se, or both: 0.005% to 0.050% in
　total, Sb or Sn or both:
　0.000% to 0.3% in total, Y, Te, La, Ce , Nd, Hf, Ta, Pb, or Bi, or any combination thereof: 0.0000% to 0.01% in total, and
　balance: Fe and impurities,
　Method for manufacturing a hot-rolled steel sheets for grain-oriented electrical steel sheet characterized by having a chemical composition expressed in.
[Claim 9]
　The step of performing the casting, in a region where the thickness of one side of the solidified shell becomes 25% or more of the thickness of the slab, according to claim 8, characterized in that it comprises a step of performing a magnetic stirring of the molten steel method for manufacturing a hot-rolled steel sheets for grain-oriented electrical steel sheet.
[Claim 10]
　In the above chemical
　composition, Sb or Sn or both: 0.003% to 0.3% in total, and
　Y, Te, La, Ce, Nd, Hf, Ta, Pb , or Bi, or any combination thereof: 0.0005% to 0.01% in total
production process of hot-rolled steel sheets for grain-oriented electrical steel sheet according to claim 8 or 9, characterized in that at least one of is satisfied.