METHOD FOR PRODUCING GRAIN-ORIENTED ELECTRICAL STEEL SHEET

Abstract

Excellent magnetic properties can be stably obtained in grain-oriented electrical steel sheets produced from thin slabs without using inhibitor forming components. Provided is a method for producing a grain-oriented electrical steel sheet comprising: subjecting a molten steel to continuous casting to form a slab with 25 to 100 mm in thickness, the molten steel having a chemical composition containing, in mass %, C: 0.002 to 0.100%, Si: 2.00 to 8.00%, Mn: 0.005 to 1.000%, Al: <0.0100%, N: <0.0050%, S: <0.0050% and Se: <0.0050%, and the balance being Fe and inevitable impurities; heating and then hot rolling the slab to form a hot-rolled steel sheet; wherein the step of heating the slab is performed at 1000 to 1300 C. for 10 to 600 seconds.

Claims

1. A method for producing a grain-oriented electrical steel sheet, comprising: subjecting a molten steel to continuous casting to form a slab with a thickness of 25 mm or more and 100 mm or less, the molten steel having a chemical composition containing, in mass %, C in an amount of 0.002% or more and 0.100% or less, Si in an amount of 2.00% or more and 8.00% or less, Mn in an amount of 0.005% or more and 1.000% or less, Al in an amount of less than 0.0100%, N in an amount of less than 0.0050%, S in an amount of less than 0.0050% and Se in an amount of less than 0.0050%, with the balance being Fe and inevitable impurities; heating and then hot rolling the slab to form a hot-rolled steel sheet; cold rolling the hot-rolled steel sheet once or cold rolling the hot-rolled steel sheet twice or more with an intermediate annealing in between, to form a cold-rolled steel sheet having a final sheet thickness; performing a primary recrystallization annealing to the cold-rolled steel sheet; performing a secondary recrystallization annealing to the cold-rolled steel sheet after the primary recrystallization annealing; wherein the step of heating the slab is performed at a temperature of 1000 C. or more and 1300 C. or less for a time of 10 seconds or more and 600 seconds or less.

2. The method for producing a grain-oriented electrical steel sheet according to claim 1, wherein the slab is heated with being conveyed along a casting direction at a rate of 10 m/min. or more in the step of heating the slab.

3. The method for producing a grain-oriented electrical steel sheet according to claim 1, wherein the chemical composition contains, in mass %, S in an amount of less than 0.0030% and Se in an amount of less than 0.0030%.

4. The method for producing a grain-oriented electrical steel sheet according to claim 1, wherein the chemical composition further contains, in mass %, one or more selected from the group consisting of Cr in an amount of 0.01% or more and 0.50% or less, Cu in an amount of 0.01% or more and 0.50% or less, P in an amount of 0.005% or more and 0.50% or less, Ni in an amount of 0.001% or more and 0.50% or less, Sb in an amount of 0.005% or more and 0.50% or less, Sn in an amount of 0.005% or more and 0.50% or less, Bi in an amount of 0.005% or more and 0.50% or less, Mo in an amount of 0.005% or more and 0.100% or less, B in an amount of 0.0002% or more and 0.0025% or less, Nb in an amount of 0.0010% or more and 0.0100% or less and V in an amount of 0.0010% or more and 0.0100% or less.

5. The method for producing a grain-oriented electrical steel sheet according to claim 1, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

6. The method for producing a grain-oriented electrical steel sheet according to claim 2, wherein the chemical composition contains, in mass %, S in an amount of less than 0.0030% and Se in an amount of less than 0.0030%.

7. The method for producing a grain-oriented electrical steel sheet according to claim 2, wherein the chemical composition further contains, in mass %, one or more selected from the group consisting of Cr in an amount of 0.01% or more and 0.50% or less, Cu in an amount of 0.01% or more and 0.50% or less, P in an amount of 0.005% or more and 0.50% or less, Ni in an amount of 0.001% or more and 0.50% or less, Sb in an amount of 0.005% or more and 0.50% or less, Sn in an amount of 0.005% or more and 0.50% or less, Bi in an amount of 0.005% or more and 0.50% or less, Mo in an amount of 0.005% or more and 0.100% or less, B in an amount of 0.0002% or more and 0.0025% or less, Nb in an amount of 0.0010% or more and 0.0100% or less and V in an amount of 0.0010% or more and 0.0100% or less.

8. The method for producing a grain-oriented electrical steel sheet according to claim 3, wherein the chemical composition further contains, in mass %, one or more selected from the group consisting of Cr in an amount of 0.01% or more and 0.50% or less, Cu in an amount of 0.01% or more and 0.50% or less, P in an amount of 0.005% or more and 0.50% or less, Ni in an amount of 0.001% or more and 0.50% or less, Sb in an amount of 0.005% or more and 0.50% or less, Sn in an amount of 0.005% or more and 0.50% or less, Bi in an amount of 0.005% or more and 0.50% or less, Mo in an amount of 0.005% or more and 0.100% or less, B in an amount of 0.0002% or more and 0.0025% or less, Nb in an amount of 0.0010% or more and 0.0100% or less and V in an amount of 0.0010% or more and 0.0100% or less.

9. The method for producing a grain-oriented electrical steel sheet according to claim 6, wherein the chemical composition further contains, in mass %, one or more selected from the group consisting of Cr in an amount of 0.01% or more and 0.50% or less, Cu in an amount of 0.01% or more and 0.50% or less, P in an amount of 0.005% or more and 0.50% or less, Ni in an amount of 0.001% or more and 0.50% or less, Sb in an amount of 0.005% or more and 0.50% or less, Sn in an amount of 0.005% or more and 0.50% or less, Bi in an amount of 0.005% or more and 0.50% or less, Mo in an amount of 0.005% or more and 0.100% or less, B in an amount of 0.0002% or more and 0.0025% or less, Nb in an amount of 0.0010% or more and 0.0100% or less and V in an amount of 0.0010% or more and 0.0100% or less.

10. The method for producing a grain-oriented electrical steel sheet according to claim 2, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

11. The method for producing a grain-oriented electrical steel sheet according to claim 3, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

12. The method for producing a grain-oriented electrical steel sheet according to claim 4, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

13. The method for producing a grain-oriented electrical steel sheet according to claim 6, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

14. The method for producing a grain-oriented electrical steel sheet according to claim 7, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

15. The method for producing a grain-oriented electrical steel sheet according to claim 8, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

16. The method for producing a grain-oriented electrical steel sheet according to claim 9, wherein at least a part of the heating is performed by an induction heating in the step of heating the slab.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0052] In the accompanying drawings:

[0053] FIG. 1 is a graph illustrating a relationship between the heating temperature and the heating time in the heating process and the magnetic flux density B.sub.8.

DETAILED DESCRIPTION

[0054] [Chemical Composition]

[0055] A grain-oriented electrical steel sheet and a method for producing thereof according to one of the disclosed embodiments are described below. Firstly, reasons for limiting chemical composition of steel are described. In the description, % representing content (amount) of each component element denotes mass % unless otherwise noted.

[0056] C: 0.002% or more and 0.100% or less

[0057] The amount of C is limited to 0.100% or less. This is because, if the content of C exceeds 0.100%, it would be difficult to reduce the content to 0.005% or less where no magnetic aging occurs after a decarburization annealing. Meanwhile, if the content of C is less than 0.002%, an effect of grain boundary strengthening by C would be lost to cause defects, such as cracks occurred in slabs, that impede operability. Therefore, the amount of C should be 0.002% or more and 0.100% or less. The amount of C is preferably 0.010% or more. And the amount of C is preferably 0.050% or less.

[0058] Si: 2.00% or more and 8.00% or less

[0059] Si is an element necessary for increasing specific resistance of steel and improving iron loss properties. For that purpose, the content of Si of 2.00% or more is required. Meanwhile, if the content of Si exceeds 8.00%, workability of steel degrades to make the rolling difficult. Therefore, the amount of Si should be 2.00% or more and 8.00% or less. The amount of Si is preferably 2.50% or more. And the amount of Si is preferably 4.50% or less.

[0060] Mn: 0.005% or more and 1.000% or less

[0061] Mn is an element necessary for providing favorable hot workability. For that purpose, the content of Mn of 0.005% or more is required. Meanwhile, if the content of Mn exceeds 1.000%, magnetic flux density of product sheets decreases. Therefore, the amount of Mn should be 0.005% or more and 1.000% or less. The amount of Mn is preferably 0.040% or more. And the amount of Mn is preferably 0.200% or less.

[0062] As mentioned above, the content of Al, N, S and Se as the inhibitor forming components is to be reduced as much as possible. Specifically, each amount should be limited to Al: less than 0.0100%, N: less than 0.0050%, S: less than 0.0050% and Se: less than 0.0050%. The amount of Al is preferably less than 0.0080%. The amount of N is preferably less than 0.0040%. The amount of S is preferably less than 0.0030%. And the amount of Se is preferably less than 0.0030%.

[0063] Our basic component is as described above, and the balance is Fe and inevitable impurities. Such inevitable impurities include impurities that inevitably contaminate from raw materials, production lines and so forth. In addition to the above, the following other elements can be also appropriately contained.

[0064] For the purpose of improving the magnetic property, the present disclosure can appropriately contain one or more selected from among, Cr in an amount of 0.01% or more, Cr in an amount of 0.50% or less, Cu in an amount of 0.01% or more, Cu in an amount of 0.50% or less, P in an amount of 0.005% or more, P in an amount of 0.50% or less, Ni in an amount of 0.001% or more, Ni in an amount of 0.50% or less, Sb in an amount of 0.005% or more, Sb in an amount of 0.50% or less, Sn in an amount of 0.005% or more, Sn in an amount of 0.50% or less, Bi in an amount of 0.005% or more, Bi in an amount of 0.50% or less, Mo in an amount of 0.005% or more, Mo in an amount of 0.100% or less, B in an amount of 0.0002% or more, B in an amount of 0.0025% or less, Nb in an amount of 0.0010% or more, Nb in an amount of 0.0100% or less, V in an amount of 0.0010% or more and V in an amount of 0.0100% or less. There is no effect of improving the magnetic property when the addition amount of each chemical composition is less than the lower limit. And the magnetic property degrades due to suppression of development of secondary recrystallized grains when the addition amount of each chemical composition is more than the upper limit.

[0065] Secondly, our method for producing a grain-oriented electrical steel sheet will be described.

[0066] [Slab Thickness]

[0067] A slab is produced through a continuous casting process from a molten steel having the aforementioned chemical composition. Thickness of the produced slab is designed to be 100 mm or less in order for cost reduction. Meanwhile, the thickness of the slab is designed to be 25 mm or more. This is because the thinner the thickness of the slab is, the faster solidification reaches to a center of the slab when cooled, leaving the slab more difficult to be adjusted afterward. The thickness of the slab is preferably 40 mm or more. And the thickness of the slab is preferably 80 mm or less.

[0068] [Heating]

[0069] The slab produced from the molten steel is heated in a heating process prior to a hot rolling. As illustrated in the aforementioned experimental result of FIG. 1, heating temperature of 1000 C. or more and 1300 C. or less, as well as heating time of 10 seconds or more and 600 seconds or less, are essential as heating conditions.

[0070] An annealing at a high temperature for a long time for dissolving inhibitors is not necessary for the aforementioned heating process. Therefore, the heating temperature is preferably 1250 C. or less, and the heating time is preferably 300 seconds or less, both from the viewpoint of cost reduction. Further, the heating temperature is preferably 1110 C. or more, and the heating temperature is preferably 1200 C. or less, both from the viewpoint of the magnetic property. And the heating time is preferably 10 seconds or more, and the heating time is preferably 200 seconds or less, both from the viewpoint of the magnetic property as well. In addition, at least a part of the heating may be performed by an induction heating in the heating process. The induction heating is a method to heat with self-heating, for example, by applying an alternating magnetic field to a slab.

[0071] In the heating method, it is preferable to maintain heated during conveyance with using an apparatus, in which a conveyance table and a heating furnace are integrated, called a tunnel furnace. Fluctuation of the temperature within the slab can be suppressed by this method.

[0072] Here, in a conventional method of slab heating, it is common that the heating furnace has a skid and the slab is conveyed in a direction of the slab width with the slab being lifted intermittently by a walking beam and so forth during the heating. However, when using the thin slabs, a problem arises that the slab droops due to its thinness upon lifted in the furnace. Moreover, considerable drop in temperature at a skid part directly affects the magnetic degradation at a corresponding part of a product sheet. Therefore, the above method is inappropriate when using the thin slabs. For these reasons, a method of heating while conveying the slab in parallel to a casting direction of the slab, such as a tunnel furnace method, is desirable in the present disclosure. Even in such a case, it is concerned that the drooping of the slab between rolls may occur to cause surface defects and the like as the slab is normally conveyed on the table rolls. For this reason and in order to be able to suppress the drooping of the slab as well as to prevent heat release from the rolls, conveyance rate of 10 m/min. or more is desirable when conveying the slab while heating.

[0073] [Hot Rolling]

[0074] A hot rolling is performed after the aforementioned heating. Given that the slab is thin, it is desirable to omit a rough rolling and only perform a finish rolling through a tandem mill from the viewpoint of cost. When rolling, it is preferable to start the hot rolling within 100 seconds after the previous heating process has been performed from the viewpoint of suppressing variation in temperature. More preferably, the hot rolling is started at an elapsed time of more than 30 seconds. And more preferably, the hot rolling is started within an elapsed time of 70 seconds or less.

[0075] As temperature of the hot rolling, a start temperature of 900 C. or more as well as a finish temperature of 700 C. or more are desirable, both for obtaining favorable final magnetic property in the inhibitor-less chemical component. However, the finish temperature is desirably 1000 C. or less as a shape after the rolling tends to be unfavorable when the finish temperature is too high.

[0076] [Hot Band Annealing]

[0077] A hot band annealing is performed as needed to a hot-rolled steel sheet obtained through the hot rolling. In order to obtain favorable magnetic property, temperature of the hot band annealing is preferably 800 C. or more, and the temperature of the hot band annealing is preferably 1150 C. or less. When the temperature of the hot band annealing is less than 800 C., band texture from the hot rolling remains to make it difficult to achieve a primary recrystallized microstructure with uniformly-sized grains, resulting in impeding development of a secondary recrystallization. When the temperature of the hot band annealing exceeds 1150 C., grain size after the hot band annealing grows too coarse to make it extremely disadvantageous for achieving the primary recrystallized microstructure with uniformly-sized grains. The temperature of the hot band annealing is desirably 950 C. or more. And the temperature of the hot band annealing is desirably 1080 C. or less. Annealing time is preferably 10 seconds or more. And the annealing time is preferably 200 seconds or less. The band texture tends to remain when the annealing time is less than 10 seconds. When the annealing time exceeds 200 seconds, a concern arises that segregate-able elements and so forth segregate to grain boundaries so that defects such as cracks and the like may occur easily during a subsequent cold rolling.

[0078] [Cold Rolling]

[0079] After the hot rolling or the hot band annealing, a cold rolling is performed once or more with an intermediate annealing(s) in between, as needed, to form a cold-rolled steel sheet having a final sheet thickness. Temperature of the intermediate annealing is preferably 900 C. or more. And the temperature of the intermediate annealing is preferably 1200 C. or less. When the temperature of the intermediate annealing is less than 900 C., the recrystallized grains become finer and the primary recrystallized microstructure has less Goss nuclei, resulting in the magnetic degradation. Meanwhile, when the temperature of the intermediate annealing exceeds 1200 C., the grain size grows too coarse to make it extremely disadvantageous for achieving the primary recrystallized microstructure with uniformly-sized grains, as with the hot band annealing.

[0080] Further, the temperature of the intermediate annealing is more preferably in an approximate range from 900 C. to 1150 C. In a final cold rolling, performing the cold rolling with an increased temperature to 100 C. to 300 C. is effective, and performing an aging treatment once or more within a temperature range from 100 C. to 300 C. during the cold rolling is also effective, both in order for improving the magnetic property by changing recrystallized texture.

[0081] [Primary Recrystallization Annealing]

[0082] A primary recrystallization annealing is performed after the aforementioned cold rolling. The primary recrystallization annealing may also serve as a decarburization annealing. An annealing temperature of 800 C. or more is effective, and the annealing temperature of 900 C. or less is also effective, both from the viewpoint of decarburization. An atmosphere is desirably wet from the viewpoint of decarburization. Moreover, annealing time is preferably in an approximate range from 30 seconds to 300 seconds. However, these will not apply to a case with C contained only in an amount of 0.005% or less where the decarburization is unnecessary.

[0083] [Applying Annealing Separator]

[0084] An annealing separator is applied, as needed, to a steel sheet after the aforementioned primary recrystallization annealing. At this point, in a case of forming a forsterite film as making much account of iron loss, the forsterite film is formed while a secondary recrystallized microstructure is developed by applying the annealing separator mainly containing MgO followed by performing a secondary recrystallization annealing which also serves as a purification annealing. In a case of not forming the forsterite film as making much account of blanking workability, the annealing separator will not be applied, or even if applied, silica, alumina and so forth are used instead of MgO as MgO forms the forsterite film. When applying these annealing separators, an electrostatic coating and the like which does not introduce water is effective. Heat resistant inorganic material sheets, for example, silica, alumina and mica, may also be used.

[0085] [Secondary Recrystallization Annealing]

[0086] A secondary recrystallization annealing is performed after the aforementioned primary recrystallization annealing or applying the annealing separator. The secondary recrystallization annealing may also serve as a purification annealing. The secondary recrystallization annealing, serving as the purification annealing as well, is desirably performed at a temperature of 800 C. or more in order to generate a secondary recrystallization. Further, it is desirable to retain the temperature at 800 C. or more for 20 hours or more in order to complete the secondary recrystallization. On one hand, in the aforementioned case of not forming the forsterite film as making much account of the blanking property, it is also possible to finish the annealing with the retention of the temperature in a range from 850 C. to 950 C. since only the secondary recrystallization has to be completed. On the other hand, in the aforementioned case of forming the forsterite film as making much account of the iron loss or in order to reduce noise from a transformer, it is desirable to heat up to a temperature of about 1200 C.

[0087] [Flattening Annealing]

[0088] A flattening annealing may further be performed after the aforementioned secondary recrystallization annealing. At such point, adhered annealing separator will be removed by water washing, brushing and/or acid cleaning in a circumstance where the annealing separator was applied. It is effective to subsequently adjust shape by performing the flattening annealing in order to reduce iron loss. Preferable temperature of the flattening annealing is in an approximate range from 700 C. to 900 C. from the viewpoint of shape adjustment.

[0089] [Insulation Coating]

[0090] In a circumstance where stacked steel sheets are used, applying an insulation coating on the surface of steel sheets before or after the flattening annealing is effective in order to improve iron loss properties. Coatings that can impart tension to the steel sheets are desirable for reducing the iron loss. It is preferable to adopt coating methods such as a tension coating via a binder, as well as a physical vapor deposition and a chemical vapor deposition to deposit inorganic substances onto the surface layer of steel sheets. This is because these methods are excellent in a coating adhesion property and allow to obtain an effect of considerable reduction of the iron loss.

[0091] [Magnetic Domain Refining Treatment]

[0092] A magnetic domain refining treatment can be performed after the aforementioned flattening annealing in order to reduce iron loss. The treatment methods include, for example, methods that are commonly practiced such as grooving a steel sheet after final annealing; introducing a linear thermal strain or impact strain by laser or electron beam; and grooving beforehand an intermediate product such as a cold-rolled sheet with a final sheet thickness.

[0093] The other production conditions may be according to those for general grain-oriented electrical steel sheets.

EXAMPLES

Example 1

[0094] A slab having a thickness of 60 mm was produced by continuous casting from a molten steel containing, in mass %, C: 0.015%, Si: 3.25%, Mn: 0.040%, Al: 0.0020%, N: 0.0009% and S: 0.0012%, with the balance being Fe and inevitable impurities. As a heating process prior to a hot rolling, a heating treatment was performed in a tunnel furnace of regenerative burner heating type under the conditions described in Table 1. After 45 seconds of this, a hot rolling was performed to finish to a thickness of 2.2 mm. A hot band annealing was then performed at a temperature of 975 C. for 30 seconds, followed by a cold rolling to finish to a sheet thickness of 0.23 mm.

[0095] After this, a primary recrystallization annealing, which also serves as a decarburization annealing, was performed under soaking conditions of at 840 C. for 60 seconds in an atmosphere of 50% H.sub.2+50% N.sub.2 with a dew point of 55 C., followed by applying an annealing separator mainly containing MgO. Then a secondary recrystallization annealing, which also serves as a purification annealing, was performed with retaining a temperature at 1200 C. for 10 hours in a H.sub.2 atmosphere. After this, a flattening annealing, which also serves as formation of a tension imparting coating mainly containing magnesium phosphate and chromic acid, was performed under conditions of at 820 C. for 15 seconds. Magnetic flux density B.sub.8 of thus obtained sample was measured according to a method described in JIS C 2550 and the result thereof is also described in Table 1. As is apparent from Table 1, the steel sheets obtained according to the present disclosure have favorable magnetic properties.

TABLE-US-00001 TABLE 1 Heating process prior to hot rolling Heating Heating Magnetic flux temperature time density B.sub.8 No. ( C.) (sec.) (T) Remarks 1 900 10 1.558 Comparative example 2 900 300 1.585 Comparative example 3 950 10 1.794 Comparative example 4 950 300 1.807 Comparative example 5 1000 2 1.902 Comparative example 6 1000 10 1.929 Example 7 1000 100 1.928 Example 8 1000 300 1.917 Example 9 1000 600 1.910 Example 10 1000 1000 1.898 Comparative example 11 1150 2 1.900 Comparative example 12 1150 10 1.932 Example 13 1150 100 1.933 Example 14 1150 300 1.919 Example 15 1150 600 1.915 Example 16 1150 1000 1.899 Comparative example 17 1300 2 1.894 Comparative example 18 1300 10 1.917 Example 19 1300 100 1.917 Example 20 1300 300 1.916 Example 21 1300 600 1.912 Example 22 1300 1000 1.888 Comparative example 23 1350 10 1.577 Comparative example 24 1350 300 1.567 Comparative example

Example 2

[0096] A slab having a thickness of 45 mm was produced by continuous casting from a molten steel containing the chemical composition described in Table 2 with the balance being Fe and inevitable impurities. As a heating process prior to a hot rolling, the slab was passed through a tunnel furnace in which a temperature is retained at 1200 C., and the temperature was continuously retained at 1200 C. for 150 seconds. After 65 seconds from this, a hot rolling was performed to finish to a thickness of 3.0 mm. A slab conveyance rate during the heating process in the tunnel furnace was set to 25 m/min. Moreover, heating up to a temperature of 700 C. was performed by an induction heating, while the further heating and heat retention was performed by a gas burner. A hot band annealing was then performed at a temperature of 1000 C. for 60 seconds, followed by a cold rolling to a sheet thickness of 0.9 mm. In addition, an intermediate annealing was performed at a temperature of 1000 C. for 100 seconds, followed by a cold rolling to finish to a thickness of 0.23 mm.

[0097] After this, a primary recrystallization annealing, which also serves as a decarburization annealing, was performed under soaking conditions of at 820 C. for 20 seconds in an atmosphere of 50% H.sub.2+50% N.sub.2 with a dew point of 55 C., followed by applying an annealing separator mainly containing MgO. Then a secondary recrystallization annealing, which also serves as a purification annealing, was performed with retaining a temperature at 1150 C. for 3 hours in a H.sub.2 atmosphere. After this, a flattening annealing, which also serves as formation of a tension imparting coating mainly containing magnesium phosphate and chromic acid, was performed under conditions of at 850 C. for 10 seconds. Magnetic flux density B.sub.8 of thus obtained sample was measured according to a method described in JIS C 2550 and the result thereof is also described in Table 2. As is apparent from Table 2, the steel sheets obtained according to the present disclosure have favorable magnetic properties.

TABLE-US-00002 TABLE 2 Magnetic flux density Chemical composition (mass %) B.sub.8 No. C Si Mn sol. Al N S Se Others (T) Remarks 1 0.011 3.41 0.050 0.0012 0.0008 0.0010 0.0010 1.915 Example 2 0.095 4.56 0.840 0.0089 0.0045 0.0028 1.912 Example 3 0.001 3.25 0.060 0.0020 0.0013 0.0008 0.0030 1.565 Comparative example 4 0.124 3.31 0.060 0.0018 0.0010 0.0010 1.591 Comparative example 5 0.020 1.56 0.770 0.0021 0.0011 0.0012 1.584 Comparative example 6 0.013 10.50 0.050 0.0010 0.0010 0.0011 1.580 Comparative example 7 0.055 3.39 0.004 0.0020 0.0015 0.0007 0.0010 1.599 Comparative example 8 0.074 3.24 1.040 0.0046 0.0009 0.0021 1.602 Comparative example 9 0.026 2.58 0.190 0.0130 0.0011 0.0012 1.783 Comparative example 10 0.015 3.86 0.140 0.0019 0.0094 0.0012 0.0020 1.845 Comparative example 11 0.018 3.15 0.040 0.0016 0.0010 0.0120 1.867 Comparative example 12 0.020 3.02 0.050 0.0020 0.0008 0.0015 0.0100 1.564 Comparative example 13 0.015 3.25 0.050 0.0019 0.0012 0.0015 0.0010 Sb: 0.18, P: 0.013 1.934 Example 14 0.021 3.46 0.130 0.0055 0.0009 0.0035 Cr: 0.02, Cu: 0.02, Sb: 0.008, Sn: 0.015 1.920 Example 15 0.048 5.51 0.360 0.0019 0.0014 0.0013 0.0020 Ni: 0.42, Sn: 0.38, Mo: 0.009 1.921 Example 16 0.008 3.59 0.210 0.0017 0.0042 0.0007 Nb: 0.0015, V: 0.0015, Cr: 0.43, Ni: 0.02 1.918 Example 17 0.014 3.20 0.230 0.0064 0.0010 0.0048 0.0050 Cu: 0.45, Bi: 0.008, Mo: 0.075 1.920 Example 18 0.033 2.88 0.040 0.0011 0.0008 0.0008 P: 0.31, Sb: 0.43, B: 0.0005, V: 0.0070 1.925 Example 19 0.015 3.04 0.070 0.0022 0.0028 0.0015 Bi: 0.33, B: 0.0022, Nb: 0.0094 1.925 Example 20 0.002 3.31 0.04 0.0028 0.0016 0.0014 1.917 Example 21 0.014 3.11 0.97 0.0048 0.0010 0.0007 0.0010 1.910 Example 22 0.021 3.48 0.2 0.0018 0.0015 0.0012 0.0070 1.877 Comparative example 23 0.035 2.46 0.09 0.0017 0.0064 0.0012 1.872 Comparative example

INDUSTRIAL APPLICABILITY

[0098] The present disclosure does not only allow to stably obtain excellent magnetic properties in grain-oriented electrical steel sheets produced from thin slabs without using inhibitor forming components, but is also applicable to stainless steels having a single-phase structure same as that of the grain-oriented electrical steel sheets.