WO2012017690A1 - 方向性電磁鋼板およびその製造方法 - Google Patents
方向性電磁鋼板およびその製造方法 Download PDFInfo
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- WO2012017690A1 WO2012017690A1 PCT/JP2011/004473 JP2011004473W WO2012017690A1 WO 2012017690 A1 WO2012017690 A1 WO 2012017690A1 JP 2011004473 W JP2011004473 W JP 2011004473W WO 2012017690 A1 WO2012017690 A1 WO 2012017690A1
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- tension
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 59
- 239000010959 steel Substances 0.000 title claims abstract description 59
- 238000004519 manufacturing process Methods 0.000 title claims description 20
- 239000011248 coating agent Substances 0.000 claims abstract description 59
- 238000000576 coating method Methods 0.000 claims abstract description 59
- 238000005096 rolling process Methods 0.000 claims abstract description 54
- 229910052839 forsterite Inorganic materials 0.000 claims abstract description 50
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 claims abstract description 50
- 239000013078 crystal Substances 0.000 claims abstract description 26
- 230000005381 magnetic domain Effects 0.000 claims abstract description 25
- 238000000137 annealing Methods 0.000 claims description 84
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 claims description 33
- 238000000034 method Methods 0.000 claims description 32
- 238000001816 cooling Methods 0.000 claims description 16
- 238000004804 winding Methods 0.000 claims description 13
- 238000005097 cold rolling Methods 0.000 claims description 12
- 238000005261 decarburization Methods 0.000 claims description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 abstract description 90
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- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 2
- 229910052787 antimony Inorganic materials 0.000 description 2
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- GVALZJMUIHGIMD-UHFFFAOYSA-H magnesium phosphate Chemical compound [Mg+2].[Mg+2].[Mg+2].[O-]P([O-])([O-])=O.[O-]P([O-])([O-])=O GVALZJMUIHGIMD-UHFFFAOYSA-H 0.000 description 2
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Images
Classifications
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
- H01F1/18—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets with insulating coating
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1283—Application of a separating or insulating coating
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1288—Application of a tension-inducing coating
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1255—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest with diffusion of elements, e.g. decarburising, nitriding
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
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- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
- Y10T428/24479—Structurally defined web or sheet [e.g., overall dimension, etc.] including variation in thickness
- Y10T428/2457—Parallel ribs and/or grooves
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
- Y10T428/24479—Structurally defined web or sheet [e.g., overall dimension, etc.] including variation in thickness
- Y10T428/24612—Composite web or sheet
Definitions
- the present invention relates to a grain-oriented electrical steel sheet used for a core material such as a transformer and a manufacturing method thereof.
- the grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetization characteristics, particularly low iron loss.
- it is important to highly align the secondary recrystallized grains in the steel sheet in the (110) [001] orientation (so-called Goth orientation) and to reduce impurities in the product steel sheet.
- control of crystal orientation and reduction of impurities are limited in view of the manufacturing cost.
- a technique for reducing the iron loss by introducing non-uniform strain to the surface of the steel sheet by a physical method and subdividing the width of the magnetic domain has been developed, that is, a magnetic domain refinement technique.
- Patent Document 1 proposes a technique for reducing the iron loss of a steel sheet by irradiating a final product plate with a laser, introducing a high dislocation density region into the steel sheet surface layer, and narrowing the magnetic domain width.
- Patent Document 2 a steel sheet that has been subjected to finish annealing is formed with a groove having a depth of more than 5 ⁇ m in the base iron portion under a load of 882 to 2156 MPa (90 to 220 kgf / mm 2 ), and then 750
- Patent Document 3 a linear groove extending in a direction substantially orthogonal to the rolling direction of the plate is provided on the surface of the ground iron, and the surface of the other ground iron is directed from the bottom surface of the linear groove in the thickness direction.
- a technique for causing a continuous crystal grain boundary or a fine crystal grain region having a grain size of 1 mm or less has been proposed.
- the technology for performing magnetic domain subdivision processing by the groove formation described above has less iron loss reduction effect than the magnetic domain subdivision technology that introduces a high dislocation density region by laser irradiation or the like, and when assembled in an actual transformer, Even if the iron loss is reduced by subdividing the magnetic domain, the iron loss of the actual transformer is hardly improved, that is, the building factor (BF) is extremely bad.
- the present invention has been developed in view of the above situation, and further reduces the iron loss of the material formed with the grooves for magnetic domain subdivision, and obtains excellent low iron loss characteristics when assembled in an actual transformer. It is an object of the present invention to provide a grain-oriented electrical steel sheet that can be manufactured together with its advantageous manufacturing method.
- the gist configuration of the present invention is as follows. 1.
- a grain-oriented electrical steel sheet having a forsterite film and a tension coating on the steel sheet surface, and having grooves for controlling magnetic domain subdivision on the steel sheet surface, Forsterite film thickness at the bottom of the groove is 0.3 ⁇ m or more,
- the groove frequency which is the abundance ratio of grooves having crystal grains having a grain difference of 10 ⁇ m or more and a grain size of 5 ⁇ m or more, directly below the groove from the Goss orientation is 20% or less
- the total tension imparted to the steel sheet by the forsterite coating and the tension coating is 10.0 MPa or more in the rolling direction, 5.0 MPa or more in the direction perpendicular to the rolling direction, and these total tensions have the relationship of the following formula: Satisfied grain-oriented electrical steel sheet.
- B Total tension by forsterite film and tension coating perpendicular to rolling
- decarburization annealing is performed, and then the steel sheet surface is coated with an annealing separator mainly composed of MgO, and then the final finish annealing is performed.
- a method for producing a grain-oriented electrical steel sheet to which a tension coating is applied (1) The groove for magnetic domain subdivision is formed before the final finish annealing to form the forsterite film.
- the basis weight of the annealing separator is 10.0 g / m 2 or more.
- the coil winding tension after application of the annealing separator is in the range of 30 to 150 N / mm 2 .
- the average cooling rate up to 700 ° C in the cooling process of final finish annealing is in the range of 50 ° C / h or less.
- the flow rate of the atmospheric gas in a temperature range of at least 900 ° C. is 1.5 Nm 3 / h ⁇ ton or less.
- a method for producing grain-oriented electrical steel sheets in which the ultimate temperature during final finish annealing is 1150 ° C or higher.
- the slab for grain-oriented electrical steel sheet is hot-rolled and then subjected to hot-rolled sheet annealing as necessary, and then subjected to one or more cold rollings or two or more cold rollings sandwiching intermediate annealing, and finally 3.
- the iron loss reduction effect in the steel sheet formed with grooves and subjected to the magnetic domain subdivision treatment is effectively maintained even in the actual transformer, it exhibits excellent low iron loss characteristics in the actual transformer.
- a grain-oriented electrical steel sheet can be obtained.
- Forsterite film thickness at the bottom of the groove 0.3 ⁇ m or more
- the reason for the introduction effect of the magnetic domain refinement is that the amount of magnetic pole introduced is small Due to that.
- the amount of magnetic pole introduced when the groove was formed was examined. As a result, it was found that there is a correlation between the thickness of the forsterite film at the groove forming portion and the amount of magnetic pole. Therefore, the relationship between the coating thickness and the magnetic pole amount was investigated in more detail, and it was found that increasing the coating thickness at the groove forming portion was effective in increasing the magnetic pole amount.
- the thickness of the forsterite film necessary for increasing the magnetic pole amount and enhancing the magnetic domain refinement effect is 0.3 ⁇ m or more, preferably 0.6 ⁇ m or more.
- the upper limit of the forsterite film thickness is preferably about 5.0 ⁇ m because if the film is too thick, the adhesion to the steel sheet is lowered and the forsterite film is easily peeled off.
- the inventors consider as follows. That is, there is a correlation between the coating thickness and the tension applied to the steel sheet by the coating, and the coating tension at the groove bottom increases as the coating thickness increases. This increase in tension increases the internal stress of the steel sheet at the bottom of the groove, and as a result, the amount of magnetic poles is considered to have increased.
- the exciting magnetic flux is only the component in the rolling direction. Therefore, in order to improve the iron loss, the tension in the rolling direction may be increased.
- the excitation magnetic flux has not only a rolling direction component but also a rolling perpendicular direction component. For this reason, not only the rolling direction but also the tension in the direction perpendicular to the rolling affects the iron loss. Therefore, in the present invention, the optimum tension ratio is determined by the ratio of the rolling direction component and the rolling perpendicular direction component of the excitation magnetic flux. Specifically, the relationship of the following formula (1) is satisfied.
- the total tension A in the rolling direction is not particularly limited as long as the steel sheet is within the range where plastic deformation does not occur. Preferably it is 200 MPa or less.
- the total tension of the forsterite film and the tension coating is determined as follows.
- a sample of 280 mm in the rolling direction ⁇ 30 mm in the direction perpendicular to the rolling is measured, and when measuring the tension in the direction perpendicular to the rolling, a sample of 280 mm in the direction perpendicular to the rolling and 30 mm in the rolling direction is cut out. .
- the forsterite film on one side and the tension coating are removed, and the amount of warpage obtained by measuring the amount of warpage of the steel sheet before and after the removal is converted into tension by the following conversion formula (2).
- the tension obtained by this method is the tension applied to the surface from which the forsterite film and the tension coating have not been removed. Since the tension is applied to both sides of the sample, two samples are prepared for measurement in the same direction of the same product, the tension for each side is obtained by the above method, and the average value in the present invention is the tension applied to the sample. did.
- the method for determining the thickness of the forsterite film at the bottom of the groove is as follows. As shown in FIG. 1, the forsterite film present at the bottom of the groove is observed with a SEM in a cross section along the direction in which the groove extends, the area of the forsterite film is obtained by image analysis, and the area is determined by the measurement distance. By dividing, the forsterite film thickness of the steel sheet was determined. The measurement distance at this time was 100 mm.
- the groove frequency which is the ratio of grooves having crystal grains having an orientation difference of 10 ° or more from the Goss orientation and a grain size of 5 ⁇ m or more immediately below the groove, is important. In the present invention, it is important that the groove frequency is 20% or less. Hereinafter, the groove frequency will be specifically described.
- the groove frequency In order to improve the building factor, in addition to the above-mentioned definition of the tension of the forsterite film, it is important that there are as few crystal grains as possible as far as possible from the Goss orientation.
- Patent Document 2 and Patent Document 3 it is stated that the material iron loss is further improved when fine grains are present directly under the groove.
- the inventors manufactured an actual transformer using a material that does not have fine grains directly below the groove and a material that does not exist, the material iron loss is inferior to the material that does not have fine grains immediately below the groove, The transformer iron loss was good, that is, the building factor was good. Therefore, further investigation was made in detail on the material having fine grains directly under the groove, and the value of the groove frequency, which is the ratio of the groove with fine grains immediately below the groove and the groove without fine grains immediately below the groove, is important. I found out. A specific method for obtaining the groove frequency is described below, but a groove frequency of 20% or less showed a good building factor. Therefore, the groove frequency of the present invention is 20% or less.
- the fine grain is defined as a crystal grain having an azimuth difference of 10 ° or more from the Goss orientation and a grain size of 5 ⁇ m or more, which is a target for deriving the groove frequency.
- the upper limit of the particle size is about 300 ⁇ m.
- the method for obtaining the crystal grain size, crystal orientation difference, and groove frequency of the crystal grains immediately below the groove is as follows.
- the crystal grain size of the crystal grains is obtained by performing cross-sectional observation in 100 directions in a direction perpendicular to the groove portion, and when crystal grains exist, the crystal grain size is obtained with a circular equivalent diameter.
- the crystal orientation difference is obtained as a deviation angle from the Goss orientation by measuring the crystal orientation of the crystal at the bottom of the groove using EBSP (Electron Back Scattering Pattern).
- the groove frequency is a ratio obtained by dividing the groove in which the crystal grains defined in the present invention are present among the above-mentioned 100 measurement points by the number 100 of the measurement points.
- the component composition of the slab for grain-oriented electrical steel sheet may be a component composition that causes secondary recrystallization.
- the magnetic flux density B 8 that is an index of the degree of integration is preferably 1.90 T or more.
- an inhibitor for example, when using an AlN-based inhibitor, Al and N, and when using an MnS / MnSe-based inhibitor, an appropriate amount of Mn and Se and / or S should be contained. Good. Of course, both inhibitors may be used in combination.
- the preferred contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, S: 0.005 to 0.03 mass%, and Se: 0.005 to 0.03 mass%, respectively. .
- the present invention can also be applied to grain-oriented electrical steel sheets in which the contents of Al, N, S, and Se are limited and no inhibitor is used.
- the amounts of Al, N, S and Se are preferably suppressed to Al: 100 mass ppm or less, N: 50 mass ppm or less, S: 50 mass ppm or less, and Se: 50 mass ppm or less, respectively.
- C 0.08 mass% or less
- the burden of reducing C to 50 massppm or less where no magnetic aging occurs during the manufacturing process increases. Therefore, the content is preferably 0.08% by mass or less.
- the lower limit since a secondary recrystallization is possible even for a material not containing C, it is not particularly necessary to provide it.
- Si 2.0-8.0% by mass Si is an element effective for increasing the electrical resistance of steel and improving iron loss, and its content of 2.0% by mass or more is particularly effective for reducing iron loss. On the other hand, when it is 8.0% by mass or less, particularly excellent workability and magnetic flux density can be obtained. Accordingly, the Si content is preferably in the range of 2.0 to 8.0% by mass.
- Mn 0.005 to 1.0 mass%
- Mn is an element advantageous for improving the hot workability, but if the content is less than 0.005% by mass, the effect of addition is poor. On the other hand, if it is 1.0 mass% or less, the magnetic flux density of a product board will become especially favorable. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
- Ni 0.03-1.50 mass%
- Sn 0.01-1.50 mass%
- Sb 0.005-1.50 mass%
- Cu 0.03-3.0 mass%
- P 0.03-0.50 mass%
- Mo 0.005-0.10 mass%
- Cr At least one Ni selected from 0.03 to 1.50 mass% is an element useful for further improving the hot rolled sheet structure and further improving the magnetic properties.
- the content is less than 0.03% by mass, the effect of improving the magnetic properties is small.
- the amount of Ni is preferably in the range of 0.03 to 1.50% by mass.
- Sn, Sb, Cu, P, Mo, and Cr are elements that are useful for further improving the magnetic properties, but if any of them is less than the lower limit of each component, the effect of improving the magnetic properties is small.
- the amount is not more than the upper limit amount of each component described above, the development of secondary recrystallized grains is the best. For this reason, it is preferable to make it contain in said range, respectively.
- the balance other than the above components is inevitable impurities and Fe mixed in the manufacturing process.
- the slab having the above-described component composition is heated and subjected to hot rolling according to a conventional method, but may be immediately hot rolled after casting without being heated.
- hot rolling may be performed, or the hot rolling may be omitted and the process may proceed as it is.
- hot-rolled sheet annealing is performed as necessary.
- the main purpose of hot-rolled sheet annealing is to eliminate the band structure generated by hot rolling and to make the primary recrystallized structure sized, thereby further developing the goth structure and improving the magnetic properties in the secondary recrystallization annealing. That is.
- the hot rolled sheet annealing temperature is preferably in the range of 800 to 1100 ° C.
- the hot-rolled sheet annealing temperature is less than 800 ° C, the band structure in hot rolling remains, making it difficult to achieve a sized primary recrystallized structure and obtaining the desired secondary recrystallization improvement. I can't.
- the hot-rolled sheet annealing temperature exceeds 1100 ° C., the grain size after the hot-rolled sheet annealing becomes too coarse, and it becomes difficult to realize a sized primary recrystallized structure.
- decarburization annealing (also used for recrystallization annealing) is performed, and an annealing separator is applied. .
- a final finish annealing is performed for the purpose of secondary recrystallization and forsterite film formation.
- the annealing separator is preferably composed mainly of MgO in order to form forsterite.
- MgO as a main component means that it may contain a known annealing separator component or property improving component other than MgO as long as it does not inhibit the formation of the forsterite film that is the object of the present invention. To do.
- the groove formation according to the present invention is performed in any step after the final cold rolling and before the final finish annealing.
- an insulating coating is applied to the steel sheet surface before or after planarization annealing.
- this insulating coating means a coating (hereinafter referred to as tension coating) capable of imparting tension to a steel sheet in order to reduce iron loss.
- the tension coating include silica-containing inorganic coating, physical vapor deposition, and ceramic coating by chemical vapor deposition.
- the tension in the rolling direction can be controlled by adjusting the coating amount of the tension coating. That is, in the tension coating, the coating liquid is usually applied and baked in a baking furnace in a state where the steel sheet is pulled in the rolling direction. Therefore, in the rolling direction, the coating material is baked in a state where the steel plate is extended and the steel plate is thermally expanded. When unloaded and cooled after baking, the steel sheet shrinks more than the coating material due to shrinkage due to unloading and the difference in thermal expansion coefficient between the steel sheet and the coating material, and the coating material pulls the steel sheet. A tension
- tensile_strength is provided to a steel plate by becoming a state.
- the following control items are provided as manufacturing conditions. That is, (a) The basis weight of the annealing separator is 10.0 g / m 2 or more, (b) The coil winding tension after application of the annealing separator is in the range of 30 to 150 N / mm 2 . (c) The average cooling rate up to 700 ° C in the cooling process of the final finish annealing process is 50 ° C / h or less, That is.
- An annealing separator releases moisture, CO 2 and the like during annealing, and its volume decreases compared to the time of application.
- the decrease in volume means that voids are created there, and as a result, it is understood that it is effective for stress relaxation.
- the basis weight of the annealing separator is small, the gap is insufficient, so the basis weight is limited to 10.0 g / m 2 or more.
- the basis weight of the annealing separator is not particularly limited as long as there is no inconvenience in the production process (coil winding deviation or the like during final finish annealing). If inconvenience such as winding deviation occurs, it is preferably 50 g / m 2 or less.
- a range of 30 to 150 N / mm 2 is defined as a winding tension condition that relieves the stress caused by temperature unevenness during cooling and does not collapse the coil.
- the cooling rate during the final finish annealing is reduced, the temperature distribution in the steel sheet is reduced, so that the stress in the coil is relaxed.
- the slower the cooling rate the better from the viewpoint of stress relaxation, but it is not preferable from the viewpoint of production efficiency.
- the upper limit is allowed up to 50 ° C./h.
- the stress is alleviated by controlling the basis weight of the annealing separator, the winding tension and the cooling rate, and as a result, the tension of the forsterite film in the direction perpendicular to the rolling can be improved.
- the present invention it is important to form a forsterite film on the groove bottom with a certain thickness or more.
- a forsterite film on the bottom of the groove it is necessary to form a groove before forming the forsterite film for the following reason. That is, when a groove is formed using a pressurizing means such as a gear-type roll after the forsterite film is formed, unnecessary strain is introduced into the steel sheet surface, so that it was introduced by pressing after the formation of the groove. High temperature annealing is required to remove the strain. When such high-temperature annealing is performed, fine grains are formed immediately below the grooves. However, since it is extremely difficult to control the crystal orientation of the fine grains, it causes deterioration of iron loss characteristics of the actual transformer. In such a case, the above-described fine grains can be eliminated by performing high-temperature and long-time annealing such as final finish annealing. However, such additional processing causes a decrease in productivity and costs. Invite up.
- the grooves are formed by chemical polishing such as electrolytic etching after the final finish annealing and forming the forsterite film, the forsterite film at the bottom of the groove will be removed during chemical polishing. In order to satisfy the coating amount, it is necessary to form a forsterite coating again, resulting in an increase in cost.
- the atmospheric gas flow rate in the temperature range of at least 900 ° C. or higher in the final finish annealing is 1.5 Nm 3 / h ⁇ ton or less. This is because, even when the coil is tightly wound, a large gap exists in the groove portion, so that the atmosphere flowability becomes very high as compared with the layers other than the groove portion.
- the atmosphere flowability is too high, oxygen and other gases released from the annealing separator during the final finish annealing are less likely to stay between the layers, so the amount of additional oxidation of the steel sheet generated during the final finish annealing is reduced.
- the disadvantage that the forsterite film becomes thinner is incurred.
- the atmospheric flowability between layers is low except for the groove portion, the influence of the atmospheric gas flow rate is small, and there is no particular problem even if the atmospheric gas flow rate is limited as described above.
- the lower limit of the atmospheric gas flow rate it is generally 0.01 Nm 3 / h ⁇ ton or more.
- channel is formed in the steel plate surface of a grain-oriented electrical steel sheet in one of the processes before final finish annealing.
- the iron loss improvement by the subdividing effect is expressed more effectively, and a sufficient magnetic domain subdividing effect is obtained.
- a driving force for secondary recrystallization occurs due to the size effect, and the primary recrystallized grains are engulfed by the secondary recrystallized grains.
- the strain formation is performed by a chemical method that does not introduce strain, such as electrolytic etching, instead of a mechanical method such as a protruding roll, the coarsening of the primary recrystallized grains can be suppressed, and the residual remains efficiently. Since the frequency of fine particles can be reduced, a chemical method such as electrolytic etching is more suitable as the groove forming means.
- the shape of the groove in the present invention is not particularly limited as long as the magnetic domain width can be subdivided, but a linear form is desirable.
- the groove formation in the present invention includes a conventionally known groove formation method, for example, a local etching method, a scribing method with a blade, a rolling method using a roll with protrusions, etc., and the most preferable method.
- a local etching method for example, a local etching method, a scribing method with a blade, a rolling method using a roll with protrusions, etc.
- the most preferable method is used in this method.
- an etching resist is attached to the steel sheet after the final cold rolling by printing or the like, and then a groove is formed in the non-attached region by a process such as electrolytic etching.
- the groove formed on the surface of the steel sheet has a width of 50 to 300 ⁇ m, a depth of 10 to 50 ⁇ m and a spacing of about 1.5 to 10.0 mm in the case of a linear groove, with respect to the direction perpendicular to the rolling direction of the linear groove.
- the deviation is preferably within ⁇ 30 °.
- “linear” includes not only a solid line but also a dotted line and a broken line.
- a conventionally known method for manufacturing a grain-oriented electrical steel sheet in which grooves are formed and magnetic domain subdivision processing is performed may be applied.
- an etching resist is applied by gravure offset printing, and then a linear groove having a width of 150 ⁇ m and a depth of 20 ⁇ m is formed by 10 ° with respect to the direction perpendicular to the rolling direction by electrolytic etching and resist stripping in an alkaline solution. They were formed at intervals of 3 mm at an inclination angle.
- the coating amount of the annealing separator and the winding tension after application of the annealing separator were changed.
- the ultimate temperature was 1200 ° C, and the gas flow rate at 900 ° C or higher and the average cooling rate in the cooling process in the temperature region of 700 ° C or higher were changed.
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Abstract
Description
そのためには、鋼板中の二次再結晶粒を、(110)[001]方位(いわゆる、ゴス方位)に高度に揃えることや、製品鋼板中の不純物を低減することが重要である。しかしながら、結晶方位の制御や、不純物を低減することは、製造コストとの兼ね合い等で限界がある。そこで、鋼板の表面に対して物理的な手法で不均一歪を導入し、磁区の幅を細分化して鉄損を低減する技術、すなわち磁区細分化技術が開発されている。
上記した磁区細分化技術の開発により、鉄損特性が良好な方向性電磁鋼板が得られるようになってきている。
1.鋼板表面にフォルステライト被膜および張力コーティングをそなえ、該鋼板表面に磁区細分化を司る溝を有する方向性電磁鋼板であって、
該溝の底部におけるフォルステライト被膜厚みが0.3μm以上で、
該溝直下にGoss方位から10°以上の方位差で、かつ粒径が5μm以上の結晶粒を有する溝の存在比率である溝頻度が20%以下で、
該フォルステライト被膜および該張力コーティングにより、鋼板に付与する合計張力が、圧延方向で10.0MPa以上、圧延方向に対して直角方向で5.0MPa以上で、かつこれらの合計張力が、下記式の関係を満足する方向性電磁鋼板。
記
1.0 ≦ A/B ≦ 5.0
A: 圧延方向のフォルステライト被膜および張力コーティングによる合計張力
B: 圧延方向に対して直角方向のフォルステライト被膜および張力コーティングによる合計張力
(1) 磁区細分化用の溝の形成を、フォルステライト被膜を形成する最終仕上げ焼鈍前に実施する、
(2) 焼鈍分離剤の目付け量を10.0g/m2以上とする、
(3) 焼鈍分離剤塗布後のコイル巻き取り張力を30~150N/mm2の範囲とする、
(4) 最終仕上げ焼鈍の冷却過程における700℃までの平均冷却速度を50℃/h以下の範囲とする、
(5) 最終仕上げ焼鈍において、少なくとも900℃以上の温度域における雰囲気ガスの流量を1.5Nm3/h・ton以下とする、
(6) 最終仕上げ焼鈍時の到達温度を1150℃以上とする
方向性電磁鋼板の製造方法。
本発明では、磁区細分化用の溝形成を行ったフォルステライト被膜(Mg2SiO4を主体とする被膜)をそなえる方向性電磁鋼板の素材鉄損特性の改善、およびその方向性電磁鋼板を使用した実機トランスにおけるビルディングファクターの劣化を防止するために、溝底部に形成されるフォルステライト被膜の厚み、鋼板に付与する張力、および溝直下に存在する結晶粒について以下のとおり規定した。
高転位密度領域を導入する磁区細分化手法に比べて、溝を形成する磁区細分化による溝の導入効果が低い理由は、導入される磁極量が少ないことに起因する。まず、溝を形成した時の導入される磁極量について検討した。その結果、溝形成部のフォルステライト被膜厚みと磁極量とに相関があることが分かった。そこで、被膜厚みと磁極量との関係をさらに詳細に調査したところ、溝形成部の被膜厚みを厚くすることが磁極量の増加に有効であることが究明された。
この結果より、磁極量を増加させ、磁区細分化効果を高めるのに必要なフォルステライト被膜厚みは、0.3μm以上、好ましくは0.6μm以上である。
一方、上記フォルステライト被膜厚みの上限は、厚くなりすぎると鋼板との密着性が低下し、フォルステライト被膜が剥離しやすくなるため、5.0μm程度が好ましい。
そこで、本発明では、励磁磁束の圧延方向成分と圧延直角方向成分の割合で最適張力比を定めることにした。具体的には次式(1)の関係を満足させることである。
1.0 ≦ A/B ≦ 5.0 … (1)
好ましくは、1.0≦ A/B ≦3.0 である。
A: 圧延方向のフォルステライト被膜および張力コーティングによる合計張力
B: 圧延直角方向のフォルステライト被膜および張力コーティングによる合計張力
製品(張力コーティング塗布材)より、圧延方向の張力を測定する場合は圧延方向280mm×圧延直角方向30mm、圧延直角方向の張力を測定する場合は圧延直角方向280mm×圧延方向30mmのサンプルをそれぞれ切り出す。その後、片面のフォルステライト被膜と張力コーティングを除去し、その除去前後の鋼板反り量を測定して得られた反り量を、以下の換算式(2)にて張力換算する。この方法で求めた張力は、フォルステライト被膜と張力コーティングを除去しなかった面に付与されている張力である。張力はサンプル両面に付与されているので、同一製品の同一方向の測定について2サンプルを用意し、上記方法で片面毎の張力を求め、本発明ではその平均値をサンプルに付与されている張力とした。
図1に示すように、溝の底部に存在するフォルステライト被膜を、溝の延びる方向に沿った断面にてSEMにより観察し、画像解析にてフォルステライト被膜の面積を求め、面積を測定距離で割ることにより、その鋼板のフォルステライト被膜厚みを求めた。このときの測定距離は100mmとした。
本発明では、溝直下に、Goss方位から10°以上の方位差で、かつ粒径が5μm以上の結晶粒を有する溝の存在割合である溝頻度が重要である。本発明では、この溝頻度を20%以下とすることが肝要である。
以下、溝頻度について具体的に説明する。
ビルディングファクターの改善には、上記したようなフォルステライト被膜の張力の規定に加えて、溝形成部の直下にGoss方位からのずれが大きい結晶粒をなるべく存在させないことが重要である。
ここに、特許文献2や特許文献3では溝直下に微細粒が存在する場合、素材鉄損がより改善すると述べられている。しかしながら、発明者らが溝直下に微細粒が存在する素材と存在しない素材を用いて実機トランスを製造したところ、溝直下に微細粒を存在しない素材の方が、素材鉄損は劣るものの、実機トランス鉄損は良好、すなわち、ビルディングファクターが良好であるという結果を得た。
そこで、さらに、溝直下に微細粒が存在する素材を詳細に調査したところ、溝直下に微細粒が存在する溝と溝直下に微細粒が存在しない溝の比率である溝頻度の値が重要であることが分かった。溝頻度の具体的な求め方は以下に記載するが、溝頻度が20%以下のものがビルディングファクターが良好な結果を示していた。従って、本発明の溝頻度は20%以下とする。
従って、本発明で微細粒とは、Goss方位から10°以上の方位差で、かつ粒径が5μm以上の結晶粒であって、溝頻度を導出する際の対象となる結晶粒と定義する。なお、粒径の上限は、300μm程度である。粒径がこのサイズ以上になると、素材鉄損も劣化するので、微細粒を有する溝頻度をある程度低減しても実機鉄損を改善する効果が乏しくなるからである。
結晶粒の結晶粒径は、図2に示すように、溝部に直交する方向での断面観察を100箇所行い、結晶粒が存在した場合は円相等径にて結晶粒径を求める。また、結晶方位差は、EBSP(Electron BackScattering Pattern)を用いて溝底部の結晶の結晶方位を測定し、Goss方位からのずれ角として求める。さらに、溝頻度とは、上記の100箇所の測定箇所の内、本発明で規定する結晶粒が存在した溝を、測定箇所の数100で割った比率のことである。
本発明において、方向性電磁鋼板用スラブの成分組成は、二次再結晶が生じる成分組成であればよい。なお、結晶粒の<100>方向への集積度が高いほど、磁区細分化による鉄損低減効果は大きくなるので、集積度の指標となる磁束密度B8が1.90T以上であることが好ましい。
また、インヒビターを利用する場合、例えばAlN系インヒビターを利用する場合であればAlおよびNを、またMnS・MnSe系インヒビターを利用する場合であればMnとSeおよび/またはSを適量含有させればよい。勿論、両インヒビターを併用してもよい。この場合におけるAl、N、SおよびSeの好適含有量はそれぞれ、Al:0.01~0.065質量%、N:0.005~0.012質量%、S:0.005~0.03質量%、Se:0.005~0.03質量%である。
この場合には、Al、N、SおよびSe量はそれぞれ、Al:100質量ppm以下、N:50質量ppm以下、S:50質量ppm以下、Se:50質量ppm以下に抑制することが好ましい。
C:0.08質量%以下
Cは、熱延板組織の改善のために添加をするが、0.08質量%を超えると製造工程中に磁気時効の起こらない50質量ppm以下までCを低減する負担が増大するため、0.08質量%以下とすることが好ましい。なお、下限に関しては、Cを含まない素材でも二次再結晶が可能であるので特に設ける必要はない。
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であり、含有量が2.0質量%以上でとくに鉄損低減効果が良好である。一方、8.0質量%以下の場合、とくに優れた加工性や磁束密度を得ることができる。従って、Si量は2.0~8.0質量%の範囲とすることが好ましい。
Mnは、熱間加工性を良好にする上で有利な元素であるが、含有量が0.005質量%未満ではその添加効果に乏しい。一方1.0質量%以下とすると製品板の磁束密度がとくに良好となる。このため、Mn量は0.005~1.0質量%の範囲とすることが好ましい。
Ni:0.03~1.50質量%、Sn:0.01~1.50質量%、Sb:0.005~1.50質量%、Cu:0.03~3.0質量%、P:0.03~0.50質量%、Mo:0.005~0.10質量%およびCr:0.03~1.50質量%のうちから選んだ少なくとも1種
Niは、熱延板組織をさらに改善して磁気特性を一層向上させるために有用な元素である。しかしながら、含有量が0.03質量%未満では磁気特性の向上効果が小さく、一方1.50質量%以下ではとくに二次再結晶の安定性が増し、磁気特性がさらに改善される。そのため、Ni量は0.03~1.50質量%の範囲とするのが好ましい。
なお、上記成分以外の残部は、製造工程において混入する不可避的不純物およびFeである。
焼付け後、除荷されるとともに冷却されると、除荷による収縮や鋼板とコーティング材の熱膨張率の差により、コーティング材に比べて鋼板がより収縮することになり、コーティング材が鋼板を引っ張る状態となることで鋼板に張力が付与される。
すなわち、
(a) 焼鈍分離剤の目付け量を10.0g/m2以上とする、
(b) 焼鈍分離剤塗布後のコイル巻き取り張力を30~150N/mm2の範囲とする、
(c) 最終仕上げ焼鈍工程の冷却過程における700℃までの平均冷却速度を50℃/h以下とする、
ことである。
従って、被膜へのダメージを抑制するためには、鋼板間に少しの空隙を与えることで、鋼板に発生する応力を低減すること、および冷却速度を低減して、コイル内の温度差を低減することが有効なのである。
焼鈍分離剤は、焼鈍中に水分やCO2などを放出し、塗布時より体積が減少する。体積が減少するということは、そこに空隙が生まれることを意味しており、その結果として応力緩和に有効であることが分かる。ここに、焼鈍分離剤の目付け量が少ないと空隙が不十分であることから、目付け量を10.0g/m2以上に限定する。なお、焼鈍分離剤の目付け量は、生産工程に不都合(最終仕上げ焼鈍時のコイルの巻きずれ等)のない限り、とくに上限はない。前記巻きずれなどの不都合が生じるようであれば、50g/m2以下とすることが好ましい。
このように、焼鈍分離剤目付け量、巻き取り張力および冷却速度のそれぞれの制御によって、応力が緩和され、結果として圧延直角方向のフォルステライト被膜の張力を向上させることが可能になるのである。
すなわち、フォルステライト被膜を形成した後に歯車型ロールなどの加圧手段を用いて溝を形成した場合は、鋼板表面に不要な歪が導入されるため、溝の形成後、加圧によって導入された歪みを除去するための高温焼鈍が必要となる。このような高温焼鈍が施された場合、溝直下に微細粒が形成されるが、この微細粒の結晶方位制御は極めて困難であるため、実機トランスの鉄損特性劣化を招く原因となる。このような場合、さらに、最終仕上げ焼鈍のような高温かつ長時間の焼鈍を行うことで、上記した微細粒を消滅させることができるが、このような追加処理は生産性の低下を招き、コストアップを招来する。
ここに、雰囲気流通性が高すぎると、最終仕上げ焼鈍時に焼鈍分離剤から放出される酸素などのガスが層間に滞留しにくくなるため、最終仕上げ焼鈍時に発生する鋼板の追加酸化量が減少して、フォルステライト被膜が薄くなるという不利が招来する。なお、溝部以外では、層間の雰囲気流通性が低いため、雰囲気ガス流量の影響は小さく、雰囲気ガス流量を上記のように制限しても特に問題にはならない。なお、雰囲気ガス流量の下限をとくに限定する必要は無いが、一般には0.01Nm3/h・ton以上である。
ここで、最終仕上げ焼鈍時に、サイズ効果により二次再結晶の駆動力が生じて、一次再結晶粒は二次再結晶粒に蚕食される。しかしながら、一次再結晶が正常粒成長によって粗大化した場合、二次再結晶粒と一次再結晶粒の粒径差が小さくなる。従って、サイズ効果が低下して一次再結晶粒は蚕食されにくくなり、一部の一次再結晶粒はそのまま残ってしまう。これが、結晶方位の悪い微細粒である。溝形成時に溝周辺部に歪みが導入される場合、その歪によって溝周辺部の一次再結晶粒は粗大化しやすくなり、微細粒の残留頻度が増加する。このような結晶方位の悪い微細粒頻度を低下させ、ひいてはそのような微細粒を有する溝頻度を低下させるためには、最終仕上げ焼鈍時の到達温度を1150℃以上にする必要がある。
なお、本発明における溝の形状は、磁区幅を細分化できれば特に限定はされないが、線状の形態が望ましい。
表1に示す成分組成になる鋼スラブを連続鋳造にて製造し、1400℃に加熱後、熱間圧延により板厚:2.2 mmの熱延板としたのち、1020℃で180秒の熱延板焼鈍を施した。ついで、冷間圧延により中間板厚:0.55mmとし、酸化度PH2O/PH2=0.25、温度:1050℃、時間:90秒の条件で中間焼鈍を実施した。その後、塩酸酸洗により表面のサブスケールを除去したのち、再度、冷間圧延を実施して、板厚:0.23mmの冷延板とした。
ついで、酸化度PH2O/PH2=0.55、均熱温度:825℃で200秒保持する脱炭焼鈍を施したのち、MgOを主成分とする焼鈍分離剤を塗布した。このとき表2に示すように、焼鈍分離剤塗布量と焼鈍分離剤塗布後の巻き取り張力を変化させた。その後、二次再結晶と純化を目的とした最終仕上げ焼鈍をN2:H2=60:40の混合雰囲気中にて1250℃、10hの条件で実施した。
この最終仕上げ焼鈍では、到達温度を1200℃とし、900℃以上でのガス流量と700℃以上の温度領域の冷却過程における平均冷却速度を変化させた。そして、830℃、30秒保持する条件で、鋼板形状を整える平坦化焼鈍を行い、50%のコロイダルシリカとリン酸マグネシウムからなる張力コーティングを付与して製品とし、磁気特性および被膜張力を評価した。なお、圧延方向の張力は張力コーティングの塗布量を変化させることで調整した。また、比較例として、最終仕上げ焼鈍後に上述した方法で溝形成を行なった製品も作製した。ここで、溝形成タイミング以外の製造条件は上記と同じとした。次いで、各製品を斜角せん断し、500kVAの三相トランスを組み立て、50Hz、1.7Tで励磁した状態での鉄損を測定した。
上記した鉄損測定結果を表2に併記する。
表1に示す成分組成になる鋼スラブについて、実施例1と同様の手順、条件を用いて、冷間圧延まで行なった。その後、突起付きロールを用いて鋼板表面を局所的に加圧し、幅:150μm、深さ:20μmの線状溝を、圧延方向と直交する向きに対し10°の傾斜角度にて3mm間隔で形成した。ついで、酸化度PH2O/PH2=0.50、均熱温度:840℃で300秒保持する脱炭焼鈍を施したのち、MgOを主成分とする焼鈍分離剤を塗布した。このとき表3に示すように、焼鈍分離剤塗布量と焼鈍分離剤塗布後の巻き取り張力を変化させた。その後、二次再結晶と純化を目的とした最終仕上げ焼鈍をN2:H2=30:70の混合雰囲気中にて1230℃、100hの条件で実施した。
この最終仕上げ焼鈍では、900℃以上でのガス流量と700℃以上の温度領域の冷却過程における平均冷却速度および到達温度を変化させた。そして、820℃、100秒保持する条件で、鋼板形状を整える平坦化焼鈍を行い、50%のコロイダルシリカとリン酸マグネシウムからなる張力コーティングを付与して製品とし、磁気特性および被膜張力を評価した。なお、圧延方向の張力は張力コーティングの塗布量を変化させることで調整した。また、比較例として、最終仕上げ焼鈍後に上述した方法で溝形成を行なった製品も作製した。ここで、溝形成タイミング以外の製造条件は上記と同じとした。次いで、各製品を斜角せん断し、500kVAの三相トランスを組み立て、50Hz、1.7Tで励磁した状態での鉄損を測定した。
上記した鉄損測定結果を表3に併記する。
Claims (3)
- 鋼板表面にフォルステライト被膜および張力コーティングをそなえ、該鋼板表面に磁区細分化を司る溝を有する方向性電磁鋼板であって、
該溝の底部におけるフォルステライト被膜厚みが0.3μm以上で、
該溝直下にGoss方位から10°以上の方位差で、かつ粒径が5μm以上の結晶粒を有する溝の存在比率である溝頻度が20%以下で、
該フォルステライト被膜および該張力コーティングにより、鋼板に付与する合計張力が、圧延方向で10.0MPa以上、圧延方向に対して直角方向で5.0MPa以上で、かつこれらの合計張力が、下記式の関係を満足する方向性電磁鋼板。
記
1.0 ≦ A/B ≦ 5.0
A: 圧延方向のフォルステライト被膜および張力コーティングによる合計張力
B: 圧延方向に対して直角方向のフォルステライト被膜および張力コーティングによる合計張力 - 方向性電磁鋼板用スラブを圧延して最終板厚に仕上げたのち、脱炭焼鈍を施し、ついで鋼板表面にMgOを主成分とする焼鈍分離剤を塗布してから、最終仕上げ焼鈍を行った後、張力コーティングを施す方向性電磁鋼板の製造方法であって、
(1) 磁区細分化用の溝の形成を、フォルステライト被膜を形成する最終仕上げ焼鈍前に実施する、
(2) 焼鈍分離剤の目付け量を10.0g/m2以上とする、
(3) 焼鈍分離剤塗布後のコイル巻き取り張力を30~150N/mm2の範囲とする、
(4) 最終仕上げ焼鈍の冷却過程における700℃までの平均冷却速度を50℃/h以下の範囲とする、
(5) 最終仕上げ焼鈍において、少なくとも900℃以上の温度域における雰囲気ガスの流量を1.5Nm3/h・ton以下とする、
(6) 最終仕上げ焼鈍時の到達温度を1150℃以上とする
方向性電磁鋼板の製造方法。 - 方向性電磁鋼板用スラブを、熱間圧延し、ついで必要に応じて熱延板焼鈍を施したのち、1回の冷間圧延または中間焼鈍を挟む2回以上の冷間圧延を施して、最終板厚に仕上げる請求項2に記載の方向性電磁鋼板の製造方法。
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Also Published As
Publication number | Publication date |
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JP5853352B2 (ja) | 2016-02-09 |
RU2013109940A (ru) | 2014-09-20 |
EP2602346A4 (en) | 2017-06-07 |
CN103069032B (zh) | 2015-04-08 |
BR112013002008B1 (pt) | 2019-07-02 |
KR20130049806A (ko) | 2013-05-14 |
KR101421392B1 (ko) | 2014-07-18 |
CA2807447A1 (en) | 2012-02-09 |
JP2012036446A (ja) | 2012-02-23 |
MX2013001344A (es) | 2013-03-22 |
CN103069032A (zh) | 2013-04-24 |
EP2602346A1 (en) | 2013-06-12 |
CA2807447C (en) | 2015-10-27 |
MX344369B (es) | 2016-12-14 |
US9406437B2 (en) | 2016-08-02 |
EP2602346B1 (en) | 2018-12-12 |
RU2537059C2 (ru) | 2014-12-27 |
US20130129984A1 (en) | 2013-05-23 |
BR112013002008A2 (pt) | 2016-05-31 |
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