JPH09118920A - Stable manufacture of grain-oriented magnetic steel sheet excellent in magnetic property - Google Patents

Abstract

PROBLEM TO BE SOLVED: To obtain good magnetic properties even when Ti content is varied in the manufacture of a grain-oriented magnetic steel sheet. SOLUTION: A slab consisting of, by weight, 0.025-0.075% C, 2.5-4.0% Si, 0.020-0.038% acid-sol. Al, 0.0050-0.0095% N, 0.0050-0.0150% at least one kind of S and Se, 0.05-0.8% Mn, 0.002-0.012% Ti and the balance Fe with inevitable impurities is heated at less than 1,280 deg.C and hot-rolled. As necessary, the hot rolled sheet is annealed, made into a prescribed thickness by cold rolling of more than one times, nitriding treatment is executed in the state where the strip is made to run after decarburization annealing and a separation agent for annealing essentially composed of MgO is applied. The content of N in the melting stage is defined as 0.0050+14/48 Ti <=N <=0.0095+14/48 Ti (%), the average grain diameter of a primarily recrystallized grain after completion of decarburization annealing till start of the final finish annealing is defined as 19-26μm. In this way, the range restriction of Ti of an impurity element is expanded, thereby actual production is facilitated.

Description

Detailed Description of the Invention

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for manufacturing a grain-oriented electrical steel sheet used as an iron core of a transformer or the like.

[0002]

2. Description of the Related Art Unidirectional electrical steel sheets are mainly used as iron core materials for transformers and other electric equipment, and are excellent in magnetic characteristics such as excitation characteristics and iron loss characteristics. Required for reduced energy loss. As a characteristic value representing the excitation characteristics, magnetic flux density B ₈ in the strength of 800A / m of the magnetic field standardized by JIS it is normally used. Further, as the characteristic value indicating the energy loss, the energy loss (iron loss) W _17/50 per kg of the steel sheet when magnetized at a frequency of 50 Hz to 1.7 Tesla (T) is also JI.
Standardized by S.

[0003] The magnetic flux density is the largest controlling factor of iron loss. Generally, the higher (larger) the magnetic flux density, the better the iron loss characteristics. In general, as the magnetic flux density increases, the size of the secondary recrystallized grains increases, and iron loss may deteriorate. In this case, as already widely known, by controlling the magnetic domain, the iron loss can be improved irrespective of the grain size of the secondary recrystallization.

This unidirectional electrical steel sheet has a so-called Goss structure having {110} on the surface of the steel sheet and <001> axis in the rolling direction by causing secondary recrystallization in the final finishing annealing step. In order to obtain good magnetic properties, it is necessary that <001>, which is the axis of easy magnetization, be highly aligned in the rolling direction.

A technique for producing such a high magnetic flux density unidirectional electrical steel sheet has been developed for a long time, and in Japan, a method of using MnS or AlN as a so-called inhibitor (Japanese Patent Laid-Open No. 4-496).
0-15644), a method using MnS, MnSe, Sb and the like (JP-A-51-13469). In these cases, complete solid solution of the inhibitor at the hot rolled sheet stage is required, and in actual hot rolling, steel ingot (slab)
It is necessary to set the heating temperature of 1350 ° C. or higher.

There are a number of disadvantages and inconveniences in heating at this high temperature. For this reason, attempts have been made to lower the heating temperature of the steel ingot (slab) during hot rolling. JP-A-59-56522 discloses one of them. A number of inventions have been made as a development of this technology, and a method of performing nitridation in the process of increasing the temperature from decarburizing annealing to final finish annealing to form inhibitors (Japanese Patent Application Laid-Open Nos. 62-45285 and 60-179855). ), And a method of performing a nitriding treatment using a mixed gas of hydrogen, nitrogen and ammonia while the strip is running (JP-A-2-77525, JP-A-1-82400, JP-A-3-180).
No. 460, JP-A-1-317592).

Further, a method of controlling the primary recrystallized grain size at an intermediate stage after completion of primary recrystallization during decarburization annealing and before completion of secondary recrystallization during final annealing (JP-A-3-294425).
JP, JP-A-2-96275, JP-A-2-59
No. 020, and Japanese Patent Laid-Open No. 1-82393) are also disclosed. However, in these methods, Ti is treated as an unavoidable impurity, and the content thereof is 0.003% or less, preferably 0.0020% or less.

Japanese Patent Publication No. 6-86632 discloses a technique for producing grain-oriented electrical steel sheet by using a low ingot heating temperature, which positively utilizes Ti. This method discloses a method for producing a grain-oriented electrical steel sheet having a high magnetic flux density by containing 0.0020 to 0.0150% of Ti and nitriding it before the start of secondary recrystallization in final annealing. . In this case, good magnetic properties can be obtained, but since nitriding is performed by high temperature finish annealing (box annealing), nitriding tends to be non-uniform, and secondary recrystallization is stable (B ₈ = 1.94 T). The formation of the glass film may become unstable.

[0009]

The main characteristics that the grain-oriented electrical steel sheet should have are good magnetic properties (low iron loss, high magnetic flux density) and good coating properties (coating tension, adhesion, appearance). is there. In this respect, the technique disclosed in Japanese Patent Publication No. 6-86632 has room for further improvement. By the way, in the conventional method for producing a grain-oriented electrical steel sheet, when a large amount of Ti is present, the secondary recrystallization becomes unstable as is widely known. For example, it is possible to re-crystallize a high Ti material by the method disclosed in Japanese Patent Laid-Open No. 5-295442,
Also in this case, it is necessary to carefully control the hot rolling conditions, and the Ti content is limited to 80 ppm.

The cause of Ti in the molten steel is considered to be contamination as impurities from Fe-Si alloy iron, contamination from sand iron into molten pig iron for stable operation of the blast furnace, contamination from scrap and the like. That is, the hot rolling temperature of the high Ti slab is set to 128
The present invention produced by heating at 0 ° C. or lower and nitriding after decarburization annealing has a great difficulty in the production in any case.

In the first place, the grain-oriented electrical steel sheet has an S of about 3%.
It contains i and uses a large amount of Fe-Si alloy iron.
For this reason, a high-grade Fe-Si alloy containing few impurities, especially containing less Ti, has been used. However, when the present invention is applied, the magnetic characteristics are improved, and
Further, it becomes possible to reduce the quality of the ferroalloy, and the cost can be reduced.

The present invention is a further development of the technique disclosed in Japanese Examined Patent Publication No. 6-86632.
An object of the present invention is to provide a technique capable of obtaining the film characteristics and reducing the above cost. B ₈ of the grain-oriented electrical steel sheet strongly depends on the degree of integration of Goss orientation. Furthermore, it is known that the degree of integration of Goss orientation depends on the texture during primary recrystallization (Yoshitomi et al., The Japan Institute of Metals, 5
8 (1994), 882). Since the primary recrystallization texture does not change with the addition of Ti, only the effect of the inhibitor has to be considered.

The present inventor has filed an application for Japanese Patent Application No. 7-82984 in order to solve these problems. With this technique, the primary recrystallized grains are as large as about 27 μm, and the secondary recrystallized grains are therefore secondary. Since the recrystallized grains become large, magnetic domain control becomes necessary.

[0014]

Means for Solving the Problems The inventors of the present invention have made earnest studies and found that the technique disclosed in Japanese Patent Publication No. 6-86632 and the steps up to decarburization annealing are the same, but the nitriding is carried out by running strips. The nitriding amount and B
A unidirectional electrical steel sheet with a good primary coating (glass coating) without controlling the nitrogen partial pressure in the atmosphere in AF (final finish annealing: box-type annealing for forming primary coating and secondary recrystallization) Completed the technology to manufacture.

Specifically, in the present invention in which the hot rolling heating temperature is 1280 ° C. or lower, the initial amounts of Al and N are defined to control the primary recrystallized grain size during decarburization annealing, and Since the inhibitor for recrystallization is performed by nitriding after decarburization annealing, it was found that the Ti content in the molten steel stage has little influence on the secondary recrystallization.

That is, it was found that it is necessary to add the amount of N combined with Ti (14/48 × Ti) in the melting stage in order to secure the amount of N combined with Al.
Further, in this case, it was also found that the Ti equivalent of N in the steel sheet is stably present, so that even if N is added in excess, it does not adversely affect the formation of the primary coating.

[0017]

DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below in detail.
The inventors of the present invention heated an electromagnetic steel slab having a relatively high Ti content at a low heating temperature of 1280 ° C. or lower, and annealed the hot rolled sheet using the obtained hot rolled sheet, if necessary, once or more. Stable production of unidirectional electrical steel sheet with excellent magnetic properties and coating properties, which can be produced by a method of forming an inhibitor by nitriding while running the strip after decarburization annealing after cold rolling. Repeated research and development on possible processes.

First, the reasons for limiting the component composition of the electromagnetic steel slab used as the starting material in the present invention are as follows. C: C was set to 0.025 to 0.075%. In the conventional invention, if 0.025% or less, so-called 3% Si-Fe is used.
The material (basic component of grain-oriented electrical steel sheet) has no transformation phase. If it exceeds 0.075%, 30ppm in the decarburization annealing process
For the following, productivity will be hindered because it takes too much time. Si: If the content of Si is less than 2.5%, good iron loss cannot be obtained. On the other hand, if it exceeds 4.5%, it becomes difficult to perform steel sheet processing such as cold rolling at room temperature due to brittleness.

S and Se: S and Se are 0.015%
Hereafter, it is preferably 0.010% or less. 1280 ° C
Producing hot-rolled sheet at the following slab heating temperature, then hot-rolled sheet annealing, after cold rolling, in the unidirectional electrical steel sheet produced by the incorporation of inhibitors after the decarburization annealing step such as strip nitriding This is because a large amount of S and Se hinders the grain growth of primary recrystallized grains and is harmful. If it is less than 0.005%, grain growth of primary recrystallized grains may occur due to unavoidable fluctuation factors in operation during hot rolling (temperature history difference on and between skids, fluctuation in hot rolling temperature due to acceleration of rolling speed, etc.). It is difficult to manufacture the product industrially in a stable manner due to local variations.

Ti and N: Ti and N form a thermodynamically stable and strong compound. The present invention is a method for producing a grain-oriented electrical steel sheet without controlling the Ti content very strictly, and the Ti content is 0.002 to 0.012%. The lower limit of 0.002% is 14/48 × Ti ≦ 0.0006% when the Ti content is less than this, and N
This is because the process capability is within the component control range. TiN
Is a considerably large precipitate, but when it is present in a certain amount or more, an inhibitor effect occurs, and other elements Al, S, Mn, etc. are precipitated by using TiN as a nucleus, and the original inhibitor effect is impaired. Therefore, secondary recrystallization becomes unstable, so the upper limit of Ti is made 0.012%.

N is important because it mainly bonds with Si and Al and acts as an inhibitor for primary recrystallization grain growth control and secondary recrystallization. However, since it binds to Ti as described above, it is necessary to additionally add the Ti content equivalent in order to obtain the inhibitor effect, and the amount is 14/48 × Ti.
(%). If it is 0.0050% or less, secondary recrystallization failure occurs, and if it exceeds 0.0095%, bubbles (blister: surface defect of steel sheet) occur. However, the additional amount of N equivalent to the Ti equivalent of the present invention does not cause this blister. The reason is that Ti combines with N to form stable TiN, so that excess N does not become excess.

Al: Al is added together with nitrogen to control the primary recrystallized grain growth during decarburization annealing. 128
AlN has an appropriate solubility even when the slab is heated below 0 ° C. 0.020-0.03 for effective AlN formation
It is necessary to set it to 8%. If the amount of Al is too large, the film formation and the inhibitor are affected by the atmosphere during finish annealing, and the magnetic properties are deteriorated. Therefore, the upper limit is 0.038%. The lower limit is required to be 0.02% or more to secure secondary recrystallization. Mn: If Mn is small, secondary recrystallization becomes unstable, and if Mn is large, B ₈ becomes high, but if a certain amount or more is added, the cost becomes high. Therefore, it is set to 0.05 to 0.8%.

Sn and Sb: Desirably added to reduce the size of secondary recrystallized grains. If the amount is too small, the effect is small, and if the amount is too large, the glass coating is deteriorated or the decarburization tends to be poor, which is not desirable. Therefore, when adding it,
It is set to 0.03 to 0.3%. Cr: Cr is added to improve the glass coating. The range is preferably 0.03 to 0.3%.

Cu: Cu is 0.05 to 0.3%.
Cu is added to remarkably improve the magnetic characteristics. Its effect lies in the enhancement of the inhibitor of secondary recrystallization. If the addition amount is less than 0.05%, there is no effect and 0.3
If it exceeds%, defects frequently occur during hot rolling. Although the reason is not clear, if Cu is added, the primary coating (glass coating)
Tend to be improved. In addition, addition of P or the like for facilitating the formation of the glass coating and improving the texture does not impair the gist of the present invention.

Although AlN, MnS, MnSe, TiN and the like are effective for controlling the grain growth of the primary recrystallized grain growth after decarburization annealing, in the present invention, the contents of S and Se are in the conventional direction. The effect of MnS and MnSe is small because it is less than that of the magnetic electrical steel sheet, but the effect of TiN and AlN is large. As described above, the amounts of Al, N, and Ti act as grain growth control of primary recrystallized grain growth and as an inhibitor for secondary recrystallization, so that the interrelationship is important.

When Ti is contained, TiN is preferentially formed as described above, so that N consumed by AlN is reduced and it becomes necessary to compensate. As a method for compensating for this, there are various methods such as adding TiN equivalent in the melting stage, increasing the strip nitriding amount, and increasing the nitrogen partial pressure in the BAF to prevent denitrification. The present invention defines the amount of N added in excess.

Next, processing conditions such as melting, casting and hot rolling will be described. Melting and casting according to the present invention are carried out by a known ordinary method. That is, for melting, a converter or an electric furnace is used, and hot metal may be used as a main raw material or scrap. The components are usually adjusted with a vacuum degassing device, but this is not necessary as long as the components are within the range. Casting is performed by a continuous casting machine, but an ingot method may also be used.

The subsequent slabbing is adopted in consideration of the balance between the finish thickness of hot rolling and the ability of the hot rolling machine (reduction). The hot rolling is performed by a normal continuous hot rolling machine, but a so-called reversible Steckel mill may be used. Maximum slab heating temperature during hot rolling is 1280
° C. This is because the strip is made to run on the same line or another line after decarburization annealing as in the present invention.
Heating above this temperature is not necessary for solutionizing.
Further, the lower the cost, the better from the viewpoint of reducing the energy cost and defects such as edge cracks of the hot rolled sheet.

The process after hot rolling is not particularly limited, but the final cold rolling rate is preferably 80 to 95%. If necessary, cold rolling is performed once or more with intermediate annealing. The hot-rolled sheet annealing is performed as necessary to alleviate the non-uniformity of hot-rolling and control the precipitation form of AlN, and the treatment conditions are not particularly limited, but the maximum temperature is 11
It is desirable that the cooling rate be 60 ° C., and the cooling rate be optimized depending on the amount of AlN and the balance of Si / C.

Decarburization annealing is carried out by a conventional method, and the carbon level is decarburized to 0.0030% or less in order to prevent magnetic aging of the product. Further, an oxide layer is formed in order to form a good glass film. Nitriding is performed in a mixed gas of hydrogen, nitrogen and ammonia under the condition that the strip is run on the same line as the decarburization annealing equipment or on a different line.

The primary recrystallized grains from the end of decarburization annealing to the start of final finish annealing are 19 to 26 in order to obtain good magnetic properties without the need for magnetic domain control after secondary recrystallization.
μm. In order to achieve this grain size, there are methods such as adjusting the temperature of decarburization annealing.

Then, an annealing separator containing MgO as a main component is applied. Secondary recrystallization occurs at the subsequent elevated temperature of finish annealing. If the nitrogen partial pressure is less than 5%, the AlN in the steel sheet is easily decomposed, and TiN is the only inhibitor, resulting in poor secondary recrystallization. On the other hand, if it exceeds 90%, it becomes difficult to form a good glass film, so that the atmospheric pressure is 5 to 9%.
It is extremely desirable to set it to 0%.

In summary, the most important point of the present invention is that in the grain-oriented electrical steel sheet manufacturing method for lowering the heating temperature of a steel ingot, the content of N is changed in consideration of the amount of Ti in the melting stage to change the AlN content. The effect of combined inhibitor of TiN and TiN, uniform AlN formation by strip nitriding, specification of nitriding conditions unique to Ti-containing component system, and prevention of AlN decomposition and glass coating improvement effect by specifying N ₂ partial pressure during finish annealing. Good magnetic properties (B ₈ =
1.95T) and the film properties, and the Ti regulation range is expanded.

[0034]

【Example】

(Example 1) C: 0.052%, Si: 3.23%, M
n: 1.01%, S: 0.010%, P: 0.025
%, Cr: 0.10%, acid-soluble Al: 0.028%,
The amount of Ti is 0.002, 0.005, 0.007, 0.
009, 0.011, 0.015%, and N
About 0.0085% and 14/48 × Ti (%) are additionally added, and a molten steel made of the balance Fe and inevitable impurities is continuously cast by a usual method to obtain a slab.
1. After heating at 50 ° C., start hot rolling at 1080 ° C.
It was taken up as 6 mm at 560 ° C.

Thereafter, hot-rolled sheet annealing was performed at 1120 ° C. for 2 minutes, pickling, and then warm rolling at 185 to 210 ° C. to 0.2.
Cold rolled to 85 mm. Then, N ₂ : 25 at 830 ° C.
%, H ₂ : 150% in 75% atmospheric gas with a dew point of 65 ° C.
Second annealing, decarburization, primary recrystallization and oxide film formation were performed.
Furthermore, 0.0110 to 0.0120% in strip state
After nitriding, an annealing separator containing MgO as a main component was applied. In the subsequent finish annealing, the temperature rising rate was 15 ° C./hour, the atmosphere was N ₂ : 25%, H ₂ : 75%, and 1200 ° C.
Heated up.

After that, purification annealing was carried out at 1200 ° C. for 30 hours in a dry atmosphere of H ₂ : 100%. Finally, an aluminum phosphate-based tension-imparting insulating coating was applied and the shape was corrected, sheared to Epstein size, strain relief annealing was performed, and the magnetic properties were measured. Table 1 shows the results.

[0037]

[Table 1]

As described above, under the conditions of each step of Example 1, when the amount of Ti is large, the secondary recrystallization defect occurs unless the equivalent amount of N is added. In No. 12, the magnetic properties were not good even though the N equivalent was compensated by Ti equivalent and the secondary recrystallization was good, because the primary recrystallized grain growth was insufficient due to the formation of TiN. It is thought that it was because there was. In Nos. 1 and 2, although not according to the present invention, the Ti content is small, so that good magnetic properties are obtained.

(Example 2) C: 0.045%, Si:
3.0%, Mn: 0.12%, S: 0.007%, acid-soluble Al: 0.030%, Ti content of 0.002, 0.
006, 0.008, 0.012, 0.015% and N about 0.0065% and 14/48 × T
i (%) is additionally added, and molten steel made of Cr: 0.12%, the balance Fe and inevitable impurities is continuously cast by a usual method to obtain a slab, which is heated at 1150 ° C. and then 10
Hot rolling was started at 75 ° C., and the film was wound at 550 ° C. with 2.8 mm.

Then, after pickling, 0.33 is applied by a tandem rolling mill.
Cold rolled to 5 mm. Then, at 845 ° C., N ₂ : 25
%, H ₂ : 200% at a dew point of 62 ° C. in an atmosphere gas of 75%
Second annealing, decarburization, primary recrystallization and oxide film formation were performed. Furthermore, 0.0110 to 0.012 in the strip state
Nitriding was performed at 0%, and then an annealing separator containing MgO as a main component was applied. In the subsequent finish annealing, the temperature rising rate was 15 ° C./hour, the atmosphere was N ₂ : 50%, H ₂ : 50%, and 120
Heated to 0 ° C.

Thereafter, purification annealing was performed at 1200 ° C. for 30 hours in a dry atmosphere of H ₂ : 100%. Finally, an aluminum phosphate tension-applying insulating coating was applied and the shape was corrected, sheared to Epstein size, strain relief annealing was performed, and the magnetic properties were measured. Table 2 shows the results.
Shown in As can be seen from Table 2, using the present invention, T
Good magnetic properties were obtained even with a large i content.

[0042]

[Table 2]

(Example 3) C: 0.058%, Si:
3.51%, Mn: 0.09%, Se: 0.009%,
P: 0.05%, Cu: 0.10%, Cr: 0.11.
%, Sn: 0.10%, acid-soluble Al: 0.029%,
N: 0.0082% and addition of the following Ti content, T
i: 0.001, 0.005, 0.008, 0.01
1, 0.015%, molten steel made of the balance Fe and unavoidable impurities is continuously cast by a usual method to obtain a slab, which is heated at 1150 ° C. and then hot rolling is started at 1085 ° C. Then, it was rolled up to 2.3 mm at 560 ° C.

Thereafter, the temperature was maintained at 1120 ° C. for 30 seconds, subsequently stored at 900 ° C. for 30 seconds, cooled from 750 ° C. to 30 ° C./second to room temperature, pickled, warm-rolled at 185 to 220 ° C., and 0 Cold rolled to 0.22 mm.

Then, at 830 ° C., N ₂ : 25%, H ₂ :
Annealing was performed for 120 seconds at a dew point of 63 ° C. in a 75% atmosphere gas to perform decarburization, primary recrystallization, and oxide film formation. Further, 0.110 to 0.120% of nitriding was performed in a strip state, and subsequently, an annealing separator containing MgO as a main component was applied. In the subsequent finish annealing, a temperature rising rate of 13 ° C./hour and an atmosphere of N ₂ : 4
The mixture was heated to 1200 ° C. with 0% and H ₂ : 60%.

Thereafter, purification annealing was carried out at 1200 ° C. for 20 hours in a dry atmosphere of H ₂ : 100%. Finally, an aluminum phosphate tension-applying insulating coating was applied and the shape was corrected, sheared to Epstein size, strain relief annealing was performed, and the magnetic properties were measured. Table 3 shows the results.

[0047]

[Table 3]

[0048]

According to the present invention, good magnetic characteristics can be stably obtained even if the Ti content is large.

 ─────────────────────────────────────────────────── ─── Continuation of the front page (72) Hisawa Kitagawa No. 1-1 Tobata-cho, Tobata-ku, Kitakyushu City Inside the Hachiman Works, Nippon Steel Co., Ltd. (72) Ikuo Miyamoto No. 1 Tobita-cho, Tobata-ku, Kitakyushu No. 1 Nippon Steel Yawata Works Co., Ltd.

Claims (4)

[Claims] 1. A weight ratio of C: 0.025 to 0.075.
%, Si: 2.5 to 4.0%, acid-soluble Al: 0.020 to 0.038%, N: 0.0050 to 0.0095%, S, Se at least one kind is 0.0050 to 0. .015
0%, Mn: 0.05 to 0.8%, Ti: 0.002 to 0.012%, and 0.0050 + 14/48 Ti ≦ N ≦ 0.0095 + 14/48
A slab containing Ti (%) and the balance of Fe and inevitable impurities is 1280
Heating at a temperature of less than ℃, hot rolling, hot-rolled sheet annealing, cold rolling at least once with intermediate annealing sandwiched between hydrogen, nitrogen and ammonia under conditions that allow strips to run after decarburization annealing. Nitriding is performed in a mixed gas, and the average grain size of the primary recrystallized grains after the decarburization annealing is finished and before the final finish annealing is 19 to
A stable manufacturing method of a grain-oriented electrical steel sheet having excellent magnetic properties, characterized by applying an annealing separator having a thickness of 26 μm and containing MgO as a main component, and performing final finishing annealing. 2. A weight ratio of C: 0.025 to 0.075.
%, Si: 2.5 to 4.0%, acid-soluble Al: 0.020 to 0.038%, N: 0.0050 to 0.0095%, S, Se at least one kind is 0.0050 to 0. .015
0%, Mn: 0.05 to 0.8%, Ti: 0.002 to 0.012%, and 0.0050 + 14/48 Ti ≦ N ≦ 0.0095 + 14/48
A slab containing Ti (%) and the balance of Fe and inevitable impurities is 1280
It is heated at a temperature of less than ℃, hot-rolled, hot-rolled sheet is not annealed, cold-rolling is performed once or more with an intermediate anneal, and hydrogen, nitrogen, and ammonia are run under the conditions that allow the strip to run after decarburization annealing. The average grain size of the primary recrystallized grains after the decarburization annealing is completed until the final finishing annealing is started is 19 to
A stable manufacturing method of a grain-oriented electrical steel sheet having excellent magnetic properties, characterized by applying an annealing separator having a thickness of 26 μm and containing MgO as a main component, and performing final finishing annealing. 3. Stability of the grain-oriented electrical steel sheet with excellent magnetic properties according to claim 1 or 2, further containing 0.03 to 0.30% of at least one of Sn, Sb and Cr. Production method. 4. The method for stable production of a grain-oriented electrical steel sheet having excellent magnetic properties according to claim 1, 2 or 3, further containing Cu in an amount of 0.05 to 0.30%.