JP6819646B2 - Electromagnetic steel sheet and its manufacturing method - Google Patents

Description

The present invention relates mainly to an electromagnetic steel sheet having excellent high frequency characteristics and magnetic flux density suitable for use in an iron core for a rotating machine such as a motor or a generator, and a method for manufacturing the same.

The amount of electric power consumed by motors and generators is enormous, and it is necessary to reduce the loss of the iron core used in these devices from the viewpoint of reducing energy consumption.

In addition, the rotation speed of rotating machines is increasing in order to reduce the size and weight of electric vehicles, hybrid electric vehicles, and household electric devices. In order to effectively reduce the loss generated in the iron core of a high-speed electric motor, it is necessary to reduce the high-frequency loss of the iron core. For that purpose, the thickness of the electromagnetic steel sheet used as the iron core material is reduced and the electrical resistivity is increased. Is an effective means.

As an electromagnetic steel sheet used for the above-mentioned applications, a material steel sheet is made into a sufficiently thin base material by a rolling method, Si is vapor-deposited on the surface of the steel sheet by a chemical vapor deposition silica method, and Si is further diffused inside the steel sheet. A method for producing an electromagnetic steel sheet containing a high Si content of 5% by mass or more by homogenization has been established, and it is known to be effective in improving high-frequency magnetic characteristics.

However, the magnetic steel sheet obtained by this method has a low saturation magnetization due to its high Si content, and there is a problem that the magnetic flux density (B ₅₀ ) at a magnetic field strength of 5000 A / m required by many rotating machines cannot be increased. There was a point. If the B _{50 of the} electrical steel sheet used as the iron core of the rotating machine is low, sufficient torque cannot be obtained, and if an increase in the current value is attempted to compensate for this, there arises a problem that copper loss increases.

In addition, although it is effective to reduce the plate thickness in order to improve the high-frequency iron loss of the electromagnetic steel sheet, it is difficult to stably manufacture an electromagnetic steel sheet with a plate thickness of 0.1 mm or less, including the plate thickness accuracy. There was a problem that the cost was high and the cost increased. Therefore, as a practical method for improving the high frequency characteristics, it can be said that it is effective to sufficiently increase the Si content after achieving a certain degree of thinning.

Tokukousho 35-2657 Gazette Japanese Unexamined Patent Publication No. 4-362132 Japanese Patent No. 4123629 Japanese Unexamined Patent Publication No. 7-173542 Japanese Patent Application Laid-Open No. 6-128642

By the way, in order to prevent the decrease of the magnetic flux density B ₅₀ when 5% by mass or more of Si is added, the inventors can improve the crystal orientation of the steel sheet according to the decrease of the saturation magnetization due to the increase of the amount of Si. I came to have the idea that it might not be effective.

It is known that in the development of ordinary electrical steel sheets, the improvement of texture is effective in improving the magnetic flux density, while the increase in Si content contributes to the improvement of iron loss through the increase in electrical resistivity. , These are usually pursued independently, and a technique for using both of them in a complementary manner as in the present invention has not been proposed.

For example, a high Si steel sheet with a Si content of around 6.5% by mass is ideal in terms of electrical resistivity, magnetic permeability, iron loss, and hysteresis loss characteristics, but has the problem that the magnetic flux density in the high magnetic field region is inferior. Has a point.

On the other hand, the present invention improves the decrease in magnetic flux density in the high magnetic field region by using the positive cube orientation {100} <001> or the in-plane non-directional orientation {100} <uvw> as the texture of the steel sheet. With this in mind, it was developed after repeated experiments and studies in order to obtain such a steel sheet.

Integrating the <001> direction, which is the easy magnetization direction of the electrical steel sheet, in the plate surface is effective in improving the magnetic flux density obtained at a magnetic field strength of about 1000 to 10000 A / m in the magnetization process. It is possible to improve B ₅₀ , which is used as a representative value of the magnetic flux density of. As a method for highly accumulating the <001> orientations in the surface of the steel sheet, a method for developing the normal cube orientation {100} <001> or the in-plane non-directional orientation {100} <uvw> is known.

As a method for improving the positive cube orientation {100} <001>, for example, there is a technique described in Patent Document 1. In Patent Document 1, after cold rolling in one direction, cold rolling is further added in a direction intersecting the cold rolling direction, and short-time annealing and high-temperature annealing at 900 to 1300 ° C. are performed, so-called cross rolling. Utilizing this, a method of secondary recrystallization of {100} <001> oriented grains using an inhibitor is disclosed.

Further, in Patent Document 2, cold rolling is performed in a direction perpendicular to the hot rolling direction at a reduction rate of 50 to 90%, and then annealing is performed for the purpose of primary recrystallization, and then purification is performed as secondary recrystallization. Disclosed is a method of performing final finish annealing for the purpose of secondary recrystallization of {100} <001> oriented grains using AlN as an inhibitor.
Since all of these methods use cross rolling, which is significantly different from normal cold rolling, if the Si content of the base metal is extremely high, problems such as cracks during rolling will occur, resulting in industrial production. Is virtually impossible.

Further, in Patent Document 3, C: 0.003 to 0.08 wt%, Si: 2.0 to 8.0 wt%, Mn: 0.005 to 3.0 wt% and Al: 0.0010 to 0.012 wt% are contained, and Se, S, O and N are contained. The slab is made of molten steel, which is reduced to 30 ppm or less, and the balance is composed of Fe and unavoidable impurities. Then, after hot rolling, hot-rolled sheet is annealed as necessary, and then one or intermediate annealing is performed. An electromagnetic steel plate consisting of a series of steps in which cold rolling is performed two or more times to finish the final plate thickness, then recrystallization annealing is performed, and then an annealing separator is applied as necessary, and then final finish annealing is performed. In the manufacturing method, a manufacturing method in which the average crystal grain size before final cold rolling is 100 μm or more and 650 μm or less is disclosed.
In the case of this method, since it is necessary to make the grain size before rolling coarse, cracks are likely to occur during rolling. In particular, when the Si content is increased, the occurrence of cracks is further promoted, so that it is difficult to produce a material having a high Si content.

Further, as a method for producing a steel sheet having an in-plane non-directional orientation {100} <uvw>, Patent Document 4 describes C of 1.0% by mass or less, Si of 0.2 to 6.5% by mass, and Mn of 0.05 to 3% by mass. When the contained steel sheet is finally annealed in a tight coil state or a laminated state, it is annealed using a substance that promotes decarburization as an annealing separator, or a substance that promotes decarburization and a substance that promotes demineralization. The method is disclosed.
Also in this method, in order to obtain a high Si material, it is necessary to cold-roll the base material having a high Si content, and it is difficult to make the Si content 4% by mass or more.

Further, in Patent Document 5, in mass%, molten steel composed of 4.0% <Si ≤ 8.0%, Al ≤ 2.0%, balance Fe and unavoidable impurities is solidified by the surface of a cooling body that moves and renews to form a cast steel strip. Then, in the method for producing a high silicon-containing non-oriented electrical steel sheet which is cold-rolled to a predetermined thickness and then finish-annealed, the rolling ratio is set to 5% or more and less than 40% during cold rolling. A method for manufacturing a non-oriented electrical steel sheet having an in-plane non-directional orientation is disclosed.
In this method, a steel strip having a predetermined thickness is obtained by casting and then cold-rolled to obtain the desired plate thickness. Therefore, the cold rolling ratio can be lowered, but the steel strip after quenching casting. Since uneven structure and defects are likely to occur at the edges and inside, cracks during cold rolling are more likely to occur than in normal rolling, and it is also possible to stably obtain high Si material with a well-developed texture. It can be said that it is difficult.

In the production of the above-mentioned bidirectional electrical steel sheet or in-plane non-oriented electrical steel sheet, if the Si content is increased to 5% or more at the steelmaking stage, cold rolling becomes difficult, so that a desired product can be obtained. There is a problem that it cannot be done.

On the other hand, in the base metal stage before cold rolling, the Si content is set within the range that can be manufactured by cold rolling, and after obtaining a steel strip with a sufficiently developed texture, Si is placed inside the steel sheet by the CVD method or the like. By injecting it, it is possible to stably manufacture high-Si electromagnetic steel sheets even when the sheet thickness is sufficiently thin, and it is possible to realize low loss and high efficiency when applied as an iron core for rotating machines. Is.
The present invention has been completed after various experiments and studies based on the above findings.

That is, the gist structure of the present invention is as follows.
1. 1. By mass%, Si: contains 4.0% or less, the balance being Fe and unavoidable impurities, the rolling direction of the B ₅₀ at least 1.80T, perpendicular to the rolling direction of the B ₅₀ has a magnetic characteristic of more than 1.75T Manufacture of an electromagnetic steel sheet characterized by uniformly containing 5.0 to 7.0% Si in the plate thickness direction by injecting Si from the outside into a base steel sheet having a sheet thickness of 0.25 mm or less and diffusing it. Method.

2. 2. The method for producing an electromagnetic steel sheet according to 1, wherein the average crystal grain size of the base steel sheet is 200 μm or more.

3. 3. The base steel sheet is mass%, and Mn: 0.005 to 2.0%, Sn: 0.01 to 0.50%, Sb: 0.005 to 0.50%, Mo: 0.005 to 0.50%, Cr: 0.05 to 1.50%, Ni: 0.005 to The method for producing an electromagnetic steel sheet according to 1 or 2 above, wherein the composition contains at least one selected from 2.0% and P: 0.005 to 0.5%.

4. An electromagnetic steel sheet containing 5.0 to 7.0% by mass of Si uniformly in the plate thickness direction, the balance of which is composed of Fe and unavoidable impurities, and the plate thickness is 0.25 mm or less, and the B _{50 in} the rolling direction is 1.60 T. As described above, the electromagnetic steel sheet characterized in that B _{50 in the} direction perpendicular to rolling is 1.55 T or more.

5. The weight of the electrical steel sheet is Mn: 0.005 to 2.0%, Sn: 0.01 to 0.50%, Sb: 0.005 to 0.50%, Mo: 0.005 to 0.50%, Cr: 0.05 to 1.50%, Ni: 0.005 to 2.0. % And P: The electromagnetic steel sheet according to 4 above, wherein the composition contains at least one selected from 0.005 to 0.5%.

By using the electromagnetic steel sheet obtained by the present invention as an iron core material for a rotating machine such as a motor or a generator used under high rotation and high frequency conditions, both iron loss and copper loss can be improved. It is possible to achieve higher motor efficiency than.

Hereinafter, a method for manufacturing an electromagnetic steel sheet according to the present invention and each constituent requirement of the obtained electromagnetic steel sheet will be specifically described. In addition, "%" regarding a component shall mean mass% unless otherwise specified.
(1) Si content of base steel sheet before Si injection: 4.0% or less (remaining is unavoidable impurities)
If the Si content of the base steel sheet before Si injection manufactured by cold rolling exceeds 4.0%, the load of cold rolling becomes excessive and the frequency of cracking of the steel strip increases, resulting in normal industrial production. Since it will be difficult to manufacture with equipment, the amount of Si in the base steel sheet is limited to 4.0% or less.

(2) Magnetic characteristics of base steel sheet before Si injection: B _{50 in the} rolling direction is 1.80 T or more, B _{50 in the} direction perpendicular to rolling is 1.75 T or more.
Considering the decrease in saturation magnetization after Si injection, it is necessary to use a steel sheet with a sufficiently high directional integration before Si injection. Even if Si is injected into a base steel sheet having a B _{50 in the} rolling direction of less than 1.80 T to increase the Si content to 5% or more, the B ₅₀ in the rolling direction cannot be 1.60 T or more. Further, if the B _{50 in the} direction perpendicular to the rolling of the base steel sheet is less than 1.75 T, even if Si is injected to increase the Si content to 5% or more, B ₅₀ of 1.60 T or more cannot be obtained.

(3) Si content (product) with a plate thickness of 0.25 mm or less and a uniform 5.0 to 7.0% in the plate thickness direction
To improve the high-frequency magnetic characteristics, the plate thickness shall be 0.25 mm or less, and the Si content shall be 5.0 to 7.0%. If the plate thickness exceeds 0.25 mm, the high-frequency magnetic characteristics cannot be sufficiently improved even if the Si content is increased. If the Si content is less than 5.0%, the eddy current loss increases and the iron loss increases. On the other hand, if the Si content exceeds 7.0%, the embrittlement of the steel sheet becomes remarkable, so the content is limited to 7.0% or less.
As for the plate thickness, it is more desirable to set the plate thickness to 0.20 mm or less because the thinner the plate, the higher the Si content and the more effective the effect.

(4) Si injection Easy rolling Si content: A high Si electromagnetic steel sheet can be stably produced by injecting Si after cold rolling into a base steel sheet with a Si content of 4.0% or less. ..
Various methods can be applied as the method of injecting Si, but after temporarily increasing the amount of Si on the surface of the steel sheet by the chemical vapor deposition silencing method, the Si distribution is increased in the plate thickness direction by annealing at high temperature. The method of homogenization is industrially established and suitable for application to the present invention.

(5) Average crystal grain size of the base steel sheet before Si injection treatment: 200 μm or more As shown in Nos. 29 to 36 of Table 1 described later, the average crystal grain size of the base steel sheet before Si injection treatment is 200 μm. By doing so, the decrease of B ₅₀ due to the Si injection process is prevented, and high motor efficiency can be obtained when used as a motor iron core. Since the Si diffusion treatment is performed at a high temperature of up to 1200 ° C., there is a possibility that {111} texture, which is disadvantageous for increasing B ₅₀ , may develop in the process of primary grain growth during the diffusion treatment, but before the Si injection treatment. It is considered that if the particle size of is increased, the development of the {111} textured structure accompanying the primary grain growth during the diffusion treatment is suppressed.
Therefore, in the present invention, it is preferable that the B ₅₀ in the rolling direction is 1.80 T or more and the B ₅₀ in the direction perpendicular to rolling is 1.75 T or more, and at the same time, the primary particle size is 200 μm or more in the steel sheet before the Si injection treatment. .. In order to obtain such a base steel sheet, it is preferable that the hot-rolled sheet annealing temperature is about 1080 ° C. or higher, the cold rolling is about 180 ° C. or higher, and the annealing temperature after cold rolling is 1080 ° C. or higher. Further, it is suitable to measure the average crystal grain size (primary recrystallization grain size) of the base steel sheet in a cross section cut by a plane orthogonal to the plate thickness direction.

(6) B _{50 in the} rolling direction is 1.60 T or more, B _{50 in the} direction perpendicular to rolling is 1.55 T or more (product)
By setting the B _{50 in} the rolling direction of the product to 1.60 T or more and the B _{50 in the} rolling direction perpendicular to 1.55 T or more, not only is it possible to obtain a sufficiently high torque when used as a rotating machine, but also copper. It is possible to prevent an increase in loss. Further, when used as a split iron core, better characteristics can be obtained by setting the teeth direction in which the magnetic flux density is high as the rolling direction. Therefore, it is advantageous to increase the magnetic flux density in the rolling direction as compared with the rolling perpendicular direction from the viewpoint of improving the characteristics of the actual machine.
If an additional trying to increase efficiency of the rotating machine, by increasing the orientation integration degree of the base material steel plate before Si implantation, or 1.65T the rolling direction of the B ₅₀ in the product, 1.60T a direction perpendicular to the rolling direction of the B ₅₀ It is desirable to do the above.

Next, optional additive components other than Si will be described.
Mn: 0.005 to 2.0%
Mn is an element useful for improving hot workability, but if the content is less than 0.005%, it will not be effective, while if it exceeds 2.0%, it will be difficult to form an texture, so Mn is contained. The amount is preferably in the range of 0.005 to 2.0%.

Sn: 0.01 to 0.50%
Addition of Sn of 0.01% or more contributes to the improvement of the orientation integration of the positive cube directional steel sheet or the in-plane non-directional steel sheet by improving the texture structure, but if it exceeds 0.5%, the effect is saturated and the cost increases. The upper limit is preferably 0.5%.

Sb: 0.005 to 0.50%
Like Sn, Sb is an element that is effective in improving the magnetic flux density. However, if the content is less than 0.005%, the effect of addition is poor, while if it exceeds 0.50%, the effect reaches saturation. Therefore, the Sb content is preferably 0.005 to 0.50%.

Mo: 0.005 to 0.50%
Mo is an element that prevents defects on the surface of steel sheets during hot rolling and is effective in reducing iron loss by suppressing surface oxidation. However, if the content is less than 0.005%, the effect of addition is poor, while if it exceeds 0.50%, carbides are formed and iron loss increases, so the Mo content can be set to 0.005 to 0.50%. preferable.

Cr: 0.05 to 1.50%
Cr is an element that has the effect of reducing eddy current loss by increasing the electrical resistivity of the steel sheet together with Si. However, if the addition amount is less than 0.05%, such an effect cannot be obtained, while if the addition amount exceeds 1.50%, carbides are formed and the magnetic properties are deteriorated. Therefore, the Cr content is in the range of 0.05 to 1.50%. Is preferable.

Ni: 0.005 to 2.0%
It is presumed that Ni is also a ferromagnetic element and contributes to the improvement of magnetic flux density. However, if the addition amount is less than 0.005%, the improvement amount of the magnetic characteristics is small, while if it exceeds 2.0%, the texture formation becomes unstable and the magnetic characteristics deteriorate. Therefore, the Ni addition amount is set to 0.005 to 2.0%. Is preferable.
Each of the above components contributes to the formation of texture by being added to the base steel sheet, and has the effect of improving the magnetic properties by being present in the base iron of the product.

P: 0.005 to 0.5%
P has an texture improving effect, and this effect is expressed at 0.005% or more. On the other hand, if it is added in excess of 0.5%, it causes embrittlement of the steel sheet. Therefore, the P content is preferably in the range of 0.005 to 0.5%.

In addition to the above, C: 0.002 to 0.10% and Al: 0.0010 to 0.015% may be contained as components after slab casting in order to produce a base steel sheet before the Si injection treatment in which the texture is properly controlled. It is advantageous in forming an texture having a high magnetic flux density in the rolling direction and the direction perpendicular to rolling.
C: 0.002 to 0.10%
C promotes local deformation in crystal grains in cold rolling, promotes the development of {100} <001> structure, and effectively contributes to improving the magnetic properties. However, if the content in the steel before cold rolling is less than 0.002%, the effect of producing {100} <001> grains becomes small, which causes a decrease in the magnetic flux density. On the other hand, if the amount of C exceeds 0.10%, not only is it difficult to remove by decarburization annealing, but also γ transformation is partially caused during hot rolling sheet annealing, making it difficult to form an texture. Therefore, the C content is preferably 0.002 to 0.10%.

Al: 0.0010 to 0.015%
Al has an action of appropriately developing {100} <001> grains during annealing for forming a texture to obtain a base steel sheet. If the Al amount is less than 0.0010%, the degree of integration of the {100} <001> direction decreases and a good magnetic flux density cannot be obtained. On the other hand, if the Al amount exceeds 0.015%, the {100} <001> direction is also achieved. Not only does the degree of integration decrease, but the {110} <001> orientation increases, leading to deterioration of the average magnetic characteristics in the rolled surface. Therefore, the Al content should be in the range of 0.0010 to 0.015%.

Next, typical production conditions of the present invention will be described.
In order to produce the steel sheet of the present invention, a steel slab containing 4.0% or less of Si and, if necessary, containing Mn, Sn, Sb, Mo, Cr, Ni, P, C and Al is hot-rolled. After making a hot-rolled sheet with a plate thickness of 1.5 to 3.5 mm, hot-rolled sheet is annealed at a temperature of 1080 ° C to 1170 ° C as necessary, then pickled and then cold once or twice or more with intermediate annealing in between. A base steel sheet is obtained by rolling to a final sheet thickness of 0.25 mm or less and then annealing one or more times.
After that, Si is concentrated on the surface of the steel sheet by methods such as CVD, electrodeposition coating, and plating (Si injection from the outside), and then diffused into the steel by annealing at a high temperature of 1150 ° C or higher to obtain the desired steel sheet. obtain. Here, it is desirable that the cold rolling is performed under the condition that the maximum temperature of the steel sheet reaches a temperature of 180 ° C. or higher at least once. Further, it is preferable to perform decarburization annealing to bring the C content in the steel to 5 ppm or more and 60 ppm or less before concentrating Si on the surface of the steel sheet, and then to perform box annealing at 900 ° C. or higher for 8 hours or longer.
In this series of annealing, by remaining in the steel a predetermined C after decarburization annealing, the subsequent box annealing, the rolling direction of the B ₅₀ at least 1.80T, perpendicular to the rolling direction of B ₅₀ is 1.75T The formation of an organization that achieves the above is promoted. In this box annealing, by keeping the temperature at 900 ° C. or higher for 8 hours or longer, coarse crystal grains can be obtained by secondary recrystallization. Therefore, high-temperature annealing for silencing does not cause grain growth, and the magnetic flux density is reduced. It becomes possible to prevent it.

A slab having a composition containing the “component before Si injection treatment” shown in Table 1 and C: 0.015% and Al: 0.0030% is produced by continuous casting, heated at 1100 ° C. for 20 minutes, and then hot-rolled. Finished to a thickness of 2.5 mm. Then, hot-rolled sheet annealing and cold rolling (maximum temperature in rolling) were performed under the conditions shown in Table 1, and then cold rolling was also performed to finish the final sheet thickness to 0.20 to 0.30 mm.
Then, in an atmosphere of hydrogen: 75%, nitrogen: 25%, dew point: 50 ° C., annealing was performed at the annealing temperature shown in Table 1 with a soaking time of 20 seconds for both recrystallization and decarburization annealing. C was reduced to 10 ppm. Then, finish annealing was performed at 950 ° C. for 35 hours in a nitrogen atmosphere. C: 8 ppm and Al: 0.0015% remained as impurities in the ground iron after finish annealing.

After collecting Epstein test pieces for evaluation of magnetic properties in the rolling direction and the direction perpendicular to the rolling from the steel sheet after finish annealing described above, strain relief annealing is performed in an Ar atmosphere at 800 ° C. for 3 hours, and the rolling direction and the direction perpendicular to the rolling direction. The magnetic flux density B ₅₀ was measured.
Subsequently, the Si concentration on the surface of the steel sheet is concentrated by the chemical vapor phase immersion silice method on the steel strip after the finish annealing, and then annealed at 1200 ° C. for 10 minutes to obtain the Si distribution of the total plate thickness. After homogenization, a coating liquid containing a mixture of aluminum dichromate, emulsion resin, and ethylene glycol was applied and baked at 300 ° C. to obtain an electromagnetic steel sheet product. An Epstein test piece was cut out from this product, and the magnetic flux density B ₅₀ in the rolling direction and the direction perpendicular to the rolling was measured.

Subsequently, using the obtained electrical steel sheet, an 8-pole IPMSM motor (distributed winding) having a rated capacity of 3 kW was manufactured, and the motor efficiency at a torque of 2 Nm and a rotation speed of 10000 rpm was evaluated.
The results obtained are shown in Table 2.

As shown in Table 2, by using the electromagnetic steel sheet of the present invention, higher motor efficiency than conventional materials is obtained.
In particular, when the average crystal grain size of the base steel sheet is 200 μm or more (No. 29 to 36) and an appropriate amount of an arbitrary component is added (No. 31 to 36), high motor efficiency is obtained.

Claims (5)

By mass%, Si: containing 4% or less, the balance being Fe and unavoidable impurities, the rolling direction of the B ₅₀ at least 1.80T, perpendicular to the rolling direction of the B ₅₀ has a magnetic characteristic of more than 1.75T Manufacture of an electromagnetic steel sheet characterized by uniformly containing 5.0 to 7.0% Si in the plate thickness direction by injecting Si from the outside into a base steel sheet having a sheet thickness of 0.25 mm or less and diffusing it. Method. The method for producing an electromagnetic steel sheet according to claim 1, wherein the average crystal grain size of the base steel sheet is 200 μm or more. The base steel sheet is mass%, and further, Mn: 0.005 to 2.0%, Sn: 0.01 to 0.50%, Sb: 0.005 to 0.50%, Mo: 0.005 to 0.50%, Cr: 0.05 to 1.50%, Ni: 0.005 to The method for producing an electromagnetic steel sheet according to claim 1 or 2, wherein the composition contains at least one selected from 2.0% and P: 0.005 to 0.5%. An electromagnetic steel sheet containing 5.0 to 7.0% by mass of Si uniformly in the plate thickness direction, the balance of which is composed of Fe and unavoidable impurities, and the plate thickness is 0.25 mm or less, and the B _{50 in} the rolling direction is 1.60 T. As described above, the electromagnetic steel sheet characterized in that B _{50 in the} direction perpendicular to rolling is 1.55 T or more. The weight of the electrical steel sheet is Mn: 0.005 to 2.0%, Sn: 0.01 to 0.50%, Sb: 0.005 to 0.50%, Mo: 0.005 to 0.50%, Cr: 0.05 to 1.50%, Ni: 0.005 to 2.0. % And P: The electromagnetic steel sheet according to claim 4, wherein the composition contains at least one selected from 0.005 to 0.5%.