JP6191568B2 - Method for producing grain-oriented electrical steel sheet - Google Patents

Description

  The present invention relates to a method for producing a grain-oriented electrical steel sheet, and more specifically, to a method for producing a grain-oriented electrical steel sheet having excellent magnetic properties and coating properties.

The grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetic properties, particularly low iron loss. For this purpose, crystal grains in the steel sheet are highly aligned in the [110] <001> orientation (so-called Goth orientation) by secondary recrystallization annealing. In this secondary recrystallization annealing, since the temperature is raised to about 1200 ° C. in a long time of about 10 days with the subsequent purification annealing, the annealing is usually performed in a batch furnace while being wound around the coil.
During this secondary recrystallization annealing, a forsterite film is formed on the surface of the steel sheet, which is composed of a subscale mainly composed of SiO ₂ formed on the surface of the steel sheet during decarburization annealing, and a decarburization annealing. An annealing separator mainly composed of MgO applied later is formed as a forsterite film by a reaction formula of 2MgO + SiO ₂ → Mg ₂ SiO ₄ .

  Forsterite coatings are required to have uniform and high adhesion for improving magnetic properties by applying tensile stress to the steel sheet and for insulation and corrosion resistance. Various techniques have been proposed for improvement.

  For example, Patent Document 1 discloses that Al is dissolved in forsterite particles, and the concentration of the solid solution Al in the forsterite particles in contact with the ground iron is increased toward the ground iron side, whereby the adhesion of the coating is increased. A method for improving the property and the effect of imparting tension has been proposed.

Patent Document 2 discloses a method for obtaining suitable magnetic characteristics and film characteristics by forming the forsterite film from Mg ₂ SiO ₄ , FeAl ₂ O ₄ , and TiN.

Further, Patent Document 3 discloses a technique for improving magnetic properties by adding cordierite in an annealing separator and Patent Document 4 by adding RAl ₂ O ₄ type spinel complex oxide.

Japanese Patent No. 3952606 Japanese Patent No. 3562433 Japanese Patent Laid-Open No. 5-140637 JP-A-4-74871

However, in the method of Patent Document 1, it is extremely difficult to condition that Al is dissolved in the forsterite particles and the concentration of the solid solution Al in the forsterite particles in contact with the ground iron is increased toward the ground iron side. It was difficult to achieve this condition with the full length of the entire coil even if it was possible in a part of the coil. Also, the method of Patent Document 2, although the formation of FeAl ₂ O _4, is unstable in the temperature range of FeAl ₂ O ₄ is the final annealing, easily changed in MgAl ₂ O _4, which coil full length full width It was difficult to generate.

  On the other hand, in the method of Patent Document 3, cordierite is added to the separating agent, and this is transferred to the film during finish annealing to enhance the tension effect. The method of Patent Document 4 reacts with the spinel compound and Ti. However, it was difficult to achieve this over the entire length of the coil due to the non-uniformity of the interlayer atmosphere of the coil during finish annealing.

  The present invention has been made in view of the problems of the prior art, and by adding an appropriate Al compound to the annealing separator, the direction in which the magnetic characteristics and the film characteristics are uniformly improved over the entire length of the coil. It aims at proposing the manufacturing method which can obtain an electrical property electrical steel sheet.

  Inventors repeated earnest examination in order to solve the said problem. As a result, while adding a large amount of an Al compound to the annealing separator, it does not migrate into the forsterite film, but retains it in the annealing separator so that the magnetic properties and the film can be uniformly distributed over the entire length of the coil. We found a way to improve the characteristics.

That is, the gist configuration of the present invention is as follows.
1. As a component, it is mass%, C: 0.002 to 0.10%, Si: 2.0 to 8.0%, Mn: 0.005 to 1.0%, the steel material consisting of Fe and inevitable impurities as the balance is hot-rolled and heated. Decarburization that also serves as the primary recrystallization annealing by forming a rolled sheet and subjecting it to hot-rolled sheet annealing as necessary, followed by cold rolling of the final sheet thickness by cold rolling at least once with intermediate annealing In the manufacturing method of grain-oriented electrical steel sheet consisting of a series of steps of applying annealing separator to the steel sheet surface and performing finish annealing after annealing.
As the above annealing separator, Mg compound with 90% cumulative diameter in the range of 2-10μm: Al compound with 50% cumulative diameter of 1.5μm or more and Vickers hardness of 16GPa or less for 100 parts by mass is converted to Al ₂ O ₃ A method for producing a grain-oriented electrical steel sheet, comprising 20 to 150 parts by mass.

2. In addition to the component composition of the steel material, mass: Al: 0.010 to 0.050% and N: 0.003 to 0.020%, or Al: 0.010 to 0.050%, N: 0.003 to 0.020%, Se: The method for producing a grain-oriented electrical steel sheet according to 1 above, comprising 0.003% to 0.030% and / or S: 0.002% to 0.03%.

3. 2. Production of grain-oriented electrical steel sheet according to 1 above, in addition to the component composition of the steel material, in mass%, Se: 0.003-0.030% and / or S: 0.002-0.03% Method.

4). In addition to the component composition of the steel material, in mass%, Al: less than 0.01% and N: less than 0.0050%, Se: less than 0.003% and S: less than 0.002%, The manufacturing method of the grain-oriented electrical steel sheet according to 1 above.

5. In addition to the component composition of the steel materials described in 1-4 above, in mass%, Ni: 0.010-1.50%, Cr: 0.01-0.50%, Cu: 0.01-0.50%, P: 0.005-0.50%, Sb : 0.005-0.50%, Sn; 0.005-0.50%, Bi: 0.005-0.50%, Mo: 0.005-0.100%, B: 0.0002-0.0025%, Te: 0.0005-0.0100%, Nb: 0.0010-0.0100%, V: One or two or more types selected from 0.001 to 0.010% and Ta: 0.001 to 0.010% are contained.

  According to the present invention, excellent magnetic properties and coating properties are imparted over the entire length of the entire coil by adding a large amount of an Al compound whose particle size distribution and hardness are optimized in the annealing separator.

It is the figure which plotted the addition amount of aluminum hydroxide, and the minimum value and maximum value of the iron loss of a coil.

Hereinafter, the present invention will be specifically described.
First, an experiment that triggered the development of the present invention will be described.
<Experiment 1>
Steel containing C: 0.065 mass%, Si: 3.44 mass%, Mn: 0.08 mass%, made into a steel slab by continuous casting method, heated to 1410 ° C, hot-rolled, and plate thickness: 2.4mm hot-rolled sheet, after 1050 ° C x 60 seconds hot-rolled sheet annealing, primary cold rolled to an intermediate sheet thickness of 1.8mm, after 1120 ° C x 80-second intermediate annealing, A cold rolled sheet having a final thickness of 0.23 mm was obtained by warm rolling at 200 ° C.

Next, decarburization annealing was performed in a wet atmosphere of 50 vol% H ₂ -50 vol% N ₂ and a dew point of 55 ° C. held at 840 ° C. for 100 seconds.
Thereafter, 100 parts by mass of MgO, 5 parts by mass of titanium oxide, 3 parts by mass of strontium hydroxide and 0.01 parts by mass of potassium hydroxide were fixed, and aluminum hydroxide was variously changed in the range of 0 to 200 parts by mass. An annealing separator was applied to the steel sheet surface and dried. The average particle diameter of aluminum hydroxide used at this time is 4.5 μm, the Vickers hardness is 9 GPa, and the cumulative 90% diameter of MgO is 5.0 μm.

After this, it is wound into a coil, subjected to secondary recrystallization annealing and finish annealing including purification at 1200 ° C for 7 hours in a hydrogen atmosphere, then the unreacted annealing separator is removed, the coating is applied, and the coating is applied. The product coil was obtained by performing the flattening annealing at 800 ° C. for 30 seconds while baking. And the iron loss of this coil was continuously measured in the longitudinal direction, and the minimum value and the maximum value were obtained respectively.
The result is shown in FIG.

  From the figure, it can be seen that by setting the addition amount of aluminum hydroxide to 20 to 150 parts by mass with respect to 100 parts by mass of MgO, good magnetic characteristics are stably obtained. When the amount of aluminum hydroxide added was small, the best magnetic properties in the coil were good, but the difference from the worst value was large. In addition, when the amount of aluminum hydroxide added is too large, characteristics tend to deteriorate both in the best value and the worst value. Thus, in order to investigate the mechanism of why the variation in magnetic properties is reduced by adding a large amount of aluminum hydroxide, the component analysis of the surface coating on the steel sheet after finish annealing was performed under the condition of adding aluminum hydroxide. .

As a result, it was confirmed that even when aluminum hydroxide was added to the annealing separator, the aluminum contained therein did not migrate into the coating. Moreover, when the unreacted annealing separator after the finish annealing was investigated, MgAl ₂ O ₄ was formed in the unreacted separating agent.

From the above points, the inventors considered the effect of improving variation in magnetic properties by adding an aluminum compound as follows.
In general, finish annealing is performed in a state in which a steel sheet is wound in a coil shape, and thus a temperature distribution is generated in the outer coil winding portion and the middle winding portion. This increases the surface pressure inside the coil and narrows the gap between the layers. As a result, the gas flowability of the interlayer atmosphere is suppressed, and the magnetic characteristics may be deteriorated.

However, when an aluminum compound is added to the annealing separator, spinel (MgAl ₂ O ₄ ) is synthesized in the annealing separator during finish annealing. Since this spinel has a lower density than magnesia, the spinel has a function of discharging hydrated water and the like without hindering the circulation of the interlayer atmosphere due to coil tightening during annealing. As a result, since the precipitates inside the steel sheet are not decomposed by oxidation and the crystal grain growth inhibitory force is maintained, the magnetic properties are improved.

In addition, what is important in the above annealing separator is to keep the cumulative 50% diameter of the Al compound to 1.5 μm or more and to keep the cumulative 90% diameter of MgO as low as 2 to 10 μm.
The reason why the cumulative 50% diameter of the Al compound is increased is to prevent migration of Al into the coating. When the particle size is small, the diffusion of Al ions in the compound proceeds excessively and diffuses into the coating, and the purpose of securing the interlayer between the steel sheets cannot be obtained.

On the other hand, the reason why the cumulative 90% diameter of MgO is lowered is to secure a gap between the steel sheets of the coil wound by increasing the thickness of the annealing separator. That is, if this value is too large, fine MgO particles and Al compound particles enter the gaps between the coarse MgO particles, and the annealing separation agent is densely filled and the gaps are narrowed. By maintaining the particle size balance of MgO and Al compound, a gap between the steel plates can be secured.
Here, the cumulative 90% diameter and the cumulative 50% diameter are the particle diameters corresponding to 90% cumulative and 50% cumulative particle diameters counted from the smallest of the particle diameters measured with a laser diffraction particle size distribution meter. It is. The 50% cumulative diameter corresponds to the average particle diameter.

Next, the component composition that the steel material (slab) of the method electrical steel sheet to which the present invention is applied should have and a preferable component composition will be described. In addition, the remainder of the steel plate component shown below consists of Fe and an unavoidable impurity.
C: 0.002 to 0.10 mass%
If C is less than 0.002 mass%, the grain boundary strengthening effect due to C is lost, and defects such as cracks in the slab are produced. On the other hand, if it exceeds 0.10 mass%, it will be difficult to reduce to 0.005 mass% or less where demagnetization annealing does not cause magnetic aging. Therefore, C is preferably in the range of 0.002 to 0.10 mass%. More preferably, it is the range of 0.010-0.080 mass%.

Si: 2.0-8.0mass%
Si is an element necessary for increasing the specific resistance of steel and reducing iron loss. If the effect is less than 2.0 mass%, it is not sufficient. On the other hand, if it exceeds 8.0 mass%, the workability deteriorates and it becomes difficult to produce by rolling. Therefore, Si is preferably in the range of 2.0 to 8.0 mass%. More preferably, it is the range of 2.5-4.5 mass%.

Mn: 0.005 to 1.0 mass%
Mn is an element necessary for improving the hot workability of steel. If the effect is less than 0.005 mass%, it is not sufficient. On the other hand, if it exceeds 1.0 mass%, the magnetic flux density of the product plate decreases. Therefore, Mn is preferably in the range of 0.005 to 1.0 mass%. More preferably, it is the range of 0.02-0.20 mass%.

About components other than the said Si, C, and Mn, in order to produce secondary recrystallization, it is divided into the case where an inhibitor is utilized, and the case where it does not.
First, in the case of using an inhibitor to cause secondary recrystallization, for example, when using an AlN-based inhibitor, Al and N are Al: 0.010 to 0.050 mass%, N: 0.003 to 0.020 mass%, respectively. It is preferable to make it contain in the range. Moreover, when utilizing a MnS * MnSe type | system | group inhibitor, it is preferable to contain 1 type or 2 types of Mn of the amount mentioned above, and S: 0.002-0.030mass% and Se: 0.003-0.030mass%. . If the added amount is less than the above lower limit value, the inhibitor effect cannot be sufficiently obtained, whereas if the upper limit value is exceeded, the inhibitor component remains undissolved during slab heating, resulting in a decrease in magnetic properties. is there. AlN and MnS / MnSe inhibitors may be used in combination within the above ranges.

  On the other hand, when an inhibitor is not used to cause secondary recrystallization, the contents of Al, N, S and Se, which are the above-described inhibitor forming components, are reduced as much as possible, Al: less than 0.01 mass%, N: It is preferable to use a steel material reduced to less than 0.0050 mass%, S: less than 0.002 mass%, and Se: less than 0.003 mass%.

  In addition to the above components in the grain-oriented electrical steel sheet of the present invention, Ni: 0.010-1.50 mass%, Cr: 0.01-0.50 mass%, Cu: 0.01-0.50 mass%, P: 0.005-0.50 for the purpose of improving magnetic properties. mass%, Sb: 0.005-0.50 mass%, Sn: 0.005-0.50 mass%, Bi: 0.005-0.50 mass%, Mo: 0.005-0.100 mass%, B: 0.0002-0.0025 mass%, Te: 0.0005-0.0100 mass% Nb: 0.0010 to 0.0100 mass%, V: 0.001 to 0.010 mass%, and Ta: 0.001 to 0.010 mass% may be added as appropriate.

Next, the manufacturing method of the grain-oriented electrical steel sheet of this invention is demonstrated.
After melting the steel having the above-described component composition by a conventional refining process, a steel material (slab) may be produced by a conventionally known ingot-bundling rolling method or continuous casting method, or A thin cast slab having a thickness of 100 mm or less may be manufactured by direct casting to produce a steel material. The slab, etc., according to a conventional method, for example, when containing an inhibitor component, is heated to about 1400 ° C., whereas when not containing an inhibitor component, after heating to a temperature of 1300 ° C. or less, hot rolling To serve. In addition, when not containing an inhibitor component, you may hot-roll immediately after casting, without heating. In the case of a thin slab, hot rolling may be performed, or hot rolling may be omitted and the subsequent process may be performed as it is.

  Next, the hot-rolled sheet obtained by hot rolling is subjected to hot-rolled sheet annealing as necessary. In order to obtain good magnetic properties, the annealing temperature of hot-rolled sheet annealing in the case of performing hot-rolling annealing is preferably in the range of 800 to 1150 ° C. If it is less than 800 degreeC, the band structure formed by hot rolling will remain, it will become difficult to obtain the primary recrystallized structure of grain size, and the development of secondary recrystallization will be inhibited. On the other hand, when the temperature exceeds 1150 ° C., the grain size after the hot-rolled sheet annealing is excessively coarsened, so that it becomes difficult to obtain a primary recrystallized structure of sized particles.

  The hot-rolled sheet after hot-rolling or after hot-rolled sheet annealing is subjected to one or more cold rollings or two or more cold-rolling sandwiching the intermediate annealing to form a cold-rolled sheet having a final thickness. The annealing temperature of the intermediate annealing is preferably in the range of 900 to 1200 ° C. When the temperature is lower than 900 ° C., the recrystallized grains after the intermediate annealing tend to be finer, and the Gos nuclei in the primary recrystallized structure tend to decrease and the magnetic characteristics of the product plate tend to decrease. On the other hand, when the temperature exceeds 1200 ° C., the crystal grains become too coarse as in the case of hot-rolled sheet annealing, and it becomes difficult to obtain a primary recrystallized structure of grain size.

  In addition, cold rolling (final cold rolling) with a final sheet thickness is performed by increasing the steel plate temperature during cold rolling to 100 to 300 ° C, or at a temperature of 100 to 300 ° C during the cold rolling. In order to improve the primary recrystallization texture and to improve the magnetic properties, it is effective to apply the aging treatment once or plural times.

  The cold-rolled sheet having the final thickness is then subjected to decarburization annealing that also serves as primary recrystallization annealing. The temperature is 700 to 900 ° C. and the time is 30 to 300 seconds. If it is less than 700 ° C or less than 30 seconds, decarburization will be insufficient or the primary recrystallized grain size will be too small and the magnetic properties will deteriorate. Becomes too large, and the magnetic characteristics deteriorate.

An annealing separator is applied after decarburization annealing, and it is the most important point of the present invention to devise this annealing separator.
That is, in the annealing separator, an Al compound having a cumulative 50% diameter of 1.5 μm or more and a Vickers hardness of 16 GPa or less is 20 to 20% in terms of Al ₂ O ₃ with respect to 100 parts by mass of MgO having a cumulative 90% diameter of 2 to 10 μm. The addition of 150 parts by mass is the greatest feature of the present invention.

If the amount of Al compound added is less than 20 parts by mass, the effect of the present invention cannot be obtained. On the other hand, if it exceeds 150 parts by mass, the relative amount of MgO becomes too small, resulting in poor film formation. This is because the magnetic characteristics are also deteriorated.
Also, if the 50% cumulative diameter of Al compound is less than 1.5μm, Al will infiltrate into the coating or Al compound will enter the gaps between MgO particles, the filling rate of Al compound will be too high, and finish annealing It may become impossible to secure a gap between the inner layers. Therefore, the 50% cumulative diameter of the Al compound is set to 1.5 μm or more. Although the upper limit of the 50% cumulative diameter of the Al compound is not particularly limited, it is about 50 μm industrially.

  Also, if the cumulative 90% diameter of MgO particles is less than 2 μm, the particle size is too fine and the particle size distribution becomes too narrow, causing MgO to flocculate and lower the filling rate before finish annealing. However, the sintering of MgO particles occurs during annealing, and the final filling rate becomes rather high. On the other hand, when the cumulative 90% diameter of MgO particles exceeds 10 μm, the Al compound enters the gaps between the coarse grains, the Al compound filling rate increases, and it becomes impossible to secure the gaps during finish annealing.

  The Vickers hardness of the Al compound in the present invention is 16 GPa or less. This is because if it exceeds 16 GPa, it will cause the steel sheet to be pressed with surface pressure during finish annealing. Although the lower limit of the Vickers hardness of the Al compound is not particularly limited, it is industrially about 1 GPa.

  In addition to MgO and Al compounds, various conventionally known additives can be used for the annealing separator. For example, Ca, Sr, Ba, Ti, Mn, Mo, Fe, Cu, Zn, Ni and Al oxides, hydroxides, sulfates, carbonates, nitrates, borates, chlorides, sulfides, etc. is there. These can be used either alone or in combination.

After the annealing separator is applied, finish annealing is performed in a state where the steel sheet is wound in a coil shape, and a secondary recrystallized structure highly accumulated in the Goss orientation is developed and a forsterite film is formed.
The annealing temperature of the finish annealing is preferably performed at 800 ° C. or more for the purpose of achieving secondary recrystallization and to 1100 ° C. for completing the secondary recrystallization. Thereafter, in order to form a forsterite film, it is preferable that the temperature is subsequently increased to about 1200 ° C.

  The steel plate coil after the finish annealing is then subjected to flattening annealing after performing water washing, brushing, pickling, etc. to remove the unreacted annealing separator adhering to the steel plate surface to obtain a final product.

  In order to further reduce the iron loss, it is preferable to perform a magnetic domain refinement process. As a processing method, a method of forming a groove in a final product plate or introducing a thermal strain or a shock strain in a linear or dotted manner by laser irradiation or plasma irradiation, which is generally performed, a final plate For example, a method of forming a groove by etching the steel sheet surface in an intermediate process, such as a steel sheet cold-rolled to a thickness, can be used.

[Example 1]
C: 0.070mass%, Si: 3.43mass%, Mn: 0.08mass%, Al: 0.025mass%, Se: 0.025mass% and N: 0.01mass% Containing steel slab consisting of the remainder Fe and inevitable impurities Manufactured by a casting method, heated to a temperature of 1420 ° C, hot-rolled to a hot-rolled sheet with a thickness of 2.4 mm, subjected to hot-rolled sheet annealing at 1000 ° C for 50 seconds, and then primary cold After rolling to an intermediate thickness of 1.8 mm by rolling and intermediate annealing at 1100 ° C. for 20 seconds, a final cold rolled sheet with a final thickness of 0.23 mm was finished by secondary cold rolling and decarburized annealing. Decarburization annealing was held at 840 ° C. for 100 seconds in a humid atmosphere of 50 vol% H ₂ -50 vol% N ₂ , dew point: 55 ° C.

Next, with respect to 100 parts by mass of MgO having a cumulative 90% diameter as an annealing separator, 5 parts by mass of TiO ₂ and various amounts of added Al compounds are changed into a slurry form on the steel sheet surface. After coating and drying, finish annealing accompanied by a purification treatment at 1200 ° C. for 10 hours was further performed. The atmosphere of the finish annealing was H ₂ when kept at 1200 ° C. for purification, and N ₂ when raising and lowering the temperature.
Table 1 shows the measurement results of the magnetic properties at this time.

  From the table, it can be seen that by applying the present invention, good magnetic characteristics can be achieved uniformly without variation.

[Example 2]
A steel slab having the composition shown in Table 2 and the balance consisting of Fe and inevitable impurities is manufactured by a continuous casting method, heated to a temperature of 1380 ° C., and then hot-rolled to obtain a sheet thickness of 2.0 mm. A hot-rolled sheet was subjected to hot-rolled sheet annealing at 1030 ° C. for 10 seconds, followed by cold rolling to finish a cold-rolled sheet having a final sheet thickness of 0.23 mm. Thereafter, decarburization annealing was performed. Decarburization annealing was held at 840 ° C. for 100 seconds in a humid atmosphere of 50 vol% H ₂ -50 vol% N ₂ and dew point: 55 ° C. Next, MgO with a cumulative 90% diameter of 5.0 μm: 100 parts by mass of strontium sulfate and 2 parts by mass of lithium hydroxide, cumulative 50% diameter (average particle diameter): 3.2 μm, Vickers hardness of 1 GPa An annealing separator containing 2 parts by mass or 80 parts by mass of Al (OH) ₃ was applied to the surface of the steel sheet and dried, followed by a final annealing with a purification treatment at 1220 ° C. for 4 hours. Note that the atmosphere of the finish annealing was H _{2 at} the time of 1220 ° C. in which the purification treatment was performed, and Ar at the time of temperature increase and decrease.
The magnetic properties of the finish annealing coil obtained as described above were evaluated in the same manner as in Example 1.
The evaluation results are also shown in Table 2.

  It can be seen from the table that the coil having the components satisfying the present invention can obtain excellent magnetic characteristics without variation by adding an Al compound having an appropriate particle size and hardness to the annealing separator.

Claims (5)

As a component, it is mass%, C: 0.002 to 0.10%, Si: 2.0 to 8.0%, Mn: 0.005 to 1.0%, the steel material consisting of Fe and inevitable impurities as the balance is hot-rolled and heated. Decarburization that also serves as the primary recrystallization annealing by forming a rolled sheet and subjecting it to hot-rolled sheet annealing as necessary, followed by cold rolling of the final sheet thickness by cold rolling at least once with intermediate annealing In the manufacturing method of grain-oriented electrical steel sheet consisting of a series of steps of applying annealing separator to the steel sheet surface and performing finish annealing after annealing.
As the above annealing separator, Mg compound with 90% cumulative diameter in the range of 2-10μm: Al compound with 50% cumulative diameter of 1.5μm or more and Vickers hardness of 16GPa or less for 100 parts by mass is converted to Al ₂ O ₃ A method for producing a grain-oriented electrical steel sheet, comprising 20 to 150 parts by mass.   In addition to the component composition of the steel material, mass: Al: 0.010 to 0.050% and N: 0.003 to 0.020%, or Al: 0.010 to 0.050%, N: 0.003 to 0.020%, Se: The method for producing a grain-oriented electrical steel sheet according to claim 1, comprising 0.003 to 0.030% and / or S: 0.002 to 0.03%.   The grain-oriented electrical steel sheet according to claim 1, further comprising, in addition to the component composition of the steel material, mass%, Se: 0.003-0.030% and / or S: 0.002-0.03%. Production method.   In addition to the component composition of the steel material, in mass%, Al: less than 0.01% and N: less than 0.0050%, Se: less than 0.003% and S: less than 0.002%, The manufacturing method of the grain-oriented electrical steel sheet according to claim 1. In addition to the composition of the steel material, mass: Ni: 0.010 to 1.50%, Cr: 0.01 to 0.50%, Cu: 0.01 to 0.50%, P: 0.005 to 0.50%, Sb: 0.005 to 0.50%, Sn: 0.005 to 0.50%, Bi: 0.005 to 0.50%, Mo: 0.005 to 0.100%, B: 0.0002 to 0.0025%, Te: 0.0005 to 0.0100%, Nb: 0.0010 to 0.0100%, V: 0.001 to 0.010% and Ta The method for producing a grain-oriented electrical steel sheet according to any one of claims 1 to 4, further comprising one or more selected from 0.001 to 0.010%.

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