WO2016056501A1 - 低鉄損方向性電磁鋼板およびその製造方法 - Google Patents
低鉄損方向性電磁鋼板およびその製造方法 Download PDFInfo
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- WO2016056501A1 WO2016056501A1 PCT/JP2015/078173 JP2015078173W WO2016056501A1 WO 2016056501 A1 WO2016056501 A1 WO 2016056501A1 JP 2015078173 W JP2015078173 W JP 2015078173W WO 2016056501 A1 WO2016056501 A1 WO 2016056501A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 110
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000000034 method Methods 0.000 title description 48
- 238000000137 annealing Methods 0.000 claims abstract description 128
- 238000005096 rolling process Methods 0.000 claims abstract description 90
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- 238000010438 heat treatment Methods 0.000 claims abstract description 46
- 238000005097 cold rolling Methods 0.000 claims abstract description 27
- 238000000576 coating method Methods 0.000 claims abstract description 13
- 239000011248 coating agent Substances 0.000 claims abstract description 12
- 229910001224 Grain-oriented electrical steel Inorganic materials 0.000 claims description 39
- 238000011282 treatment Methods 0.000 claims description 36
- 229910052839 forsterite Inorganic materials 0.000 claims description 17
- HCWCAKKEBCNQJP-UHFFFAOYSA-N magnesium orthosilicate Chemical compound [Mg+2].[Mg+2].[O-][Si]([O-])([O-])[O-] HCWCAKKEBCNQJP-UHFFFAOYSA-N 0.000 claims description 17
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- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- 229910052787 antimony Inorganic materials 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims description 6
- 229910052715 tantalum Inorganic materials 0.000 claims description 6
- 229910052718 tin Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052797 bismuth Inorganic materials 0.000 claims description 5
- 229910052796 boron Inorganic materials 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052714 tellurium Inorganic materials 0.000 claims description 5
- 229910000976 Electrical steel Inorganic materials 0.000 claims description 4
- 238000004458 analytical method Methods 0.000 claims description 4
- 229910052759 nickel Inorganic materials 0.000 claims description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 abstract description 24
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- 238000005121 nitriding Methods 0.000 description 7
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
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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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- 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
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- 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
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- 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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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1233—Cold rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- 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
- C21D8/1261—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 following hot rolling
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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- 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
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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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
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
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- 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
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- C—CHEMISTRY; METALLURGY
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- 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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
Definitions
- the present invention relates to a grain-oriented electrical steel sheet that is suitable for use in iron core materials such as transformers, and that is excellent in magnetic properties, particularly iron loss properties, and a method for producing the same.
- Oriented electrical steel sheets are magnetic materials mainly used as iron core materials for transformers, generators, rotating machines, etc., and are required to have low energy loss (iron loss) generated inside the iron core by excitation.
- the crystal grain Goss orientation ( ⁇ 110 ⁇ ⁇ 001>) is highly aligned in one direction toward the rolling direction of the steel sheet, realizing high magnetic permeability.
- This technique utilizes a phenomenon called secondary recrystallization in which crystal grains having a specific orientation, that is, Goss orientation, grow coarsely while phagocytosing crystal grains in other orientations. Since the ⁇ 001> orientation, which is the easy axis of magnetization, faces the rolling direction, the permeability in the rolling direction is remarkably improved and the hysteresis loss is reduced.
- Patent Document 1 discloses that the deviation angle ⁇ of the entire secondary recrystallized grain with the axis in the direction perpendicular to the rolling surface (ND, thickness direction) from the ⁇ 110 ⁇ ⁇ 001> ideal orientation is sharpened to an appropriate value or less.
- Patent Document 3 discloses a technique for reducing iron loss by irradiating laser on the surface of a grain-oriented electrical steel sheet after finish annealing to subdivide magnetic domains
- Patent Document 4 describes a directionality after finish annealing.
- a technique for reducing the iron loss by applying pressure to the magnetic steel sheet to form grooves in the base iron portion to subdivide the magnetic domain and then performing strain relief annealing is disclosed in Patent Document 5 as secondary re-generation.
- Patent Document 5 There has been proposed a technique for improving the iron loss characteristics by performing a magnetic domain refinement process after the crystal grain size is set to 10 mm or more and the average value of ⁇ angles is highly sharpened to 2 ° or less.
- JP 2001-192785 A Japanese Patent No. 2983128 Japanese Patent No. 4510757 Japanese Examined Patent Publication No. 62-053579 JP 2013-077380 A
- the iron loss characteristics of grain-oriented electrical steel sheets have been greatly improved by applying the technology for imparting grooves and strain regions to the steel sheet surface to refine the magnetic domain.
- the cost of improving the iron loss characteristics by the above technology is not yet sufficient, and further improvement is required.
- the present invention has been made in view of the above-mentioned problems of the prior art, and the object thereof is to stably provide a grain-oriented electrical steel sheet having better iron loss characteristics, and to provide an advantageous manufacturing method thereof. It is to propose.
- the magnetic domain refinement technology that gives grooves and strain regions to the steel sheet surface reduces the width of the main magnetic domain in order to alleviate the high energy state that occurs in the locally introduced grooves and strain regions, resulting in eddy current loss. This is to utilize the reduction. That is, when a groove is introduced, a magnetic pole is generated in the groove portion, and when a strained region is introduced, a magnetic domain structure called a reflux magnetic domain is generated in the strained region, resulting in a high energy state. Therefore, in order to alleviate this, the phenomenon of reducing the width of the main magnetic domain is used.
- the technique of refining secondary recrystallized grains can be considered to subdivide the magnetic domain using the grain boundary as a magnetic pole generation site.
- the effect of magnetic domain refinement treatment that imparts grooves and strain regions is the same as that of secondary recrystallized grains, and magnetic domain refinement treatment that imparts grooves and strain regions to a steel sheet is performed.
- the secondary recrystallized grains are considered to be coarse, and the secondary recrystallized grains have not been refined.
- the plate width direction from the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains is the axis. It has been found that better magnetic properties (iron loss properties) can be stably obtained by controlling the average value [ ⁇ ] of the deviation angle ⁇ to an appropriate range, and the present invention has been developed.
- the present invention contains Si in a content of 2.5 to 5.0 mass% and Mn: 0.01 to 0.8 mass%, and the balance is composed of Fe and inevitable impurities.
- Continuous or intermittent linear grooves or linear strain regions on both sides are formed in a direction intersecting the rolling direction with a spacing d in the rolling direction of 1 to 10 mm, and a forsterite film is formed on both surfaces of the steel plate.
- the area ratio S ⁇ 6.5 occupying the surface of the steel sheet with recrystallized grains is 90% or more, and the absolute value of the deviation angle ⁇ about the plate width direction from the ⁇ 110 ⁇ ⁇ 001> ideal orientation is less than 2.5 °.
- Area occupied by secondary recrystallized grains on steel plate surface S Beta2.5 is not less than 75%, and an average length in the rolling direction of the secondary recrystallized grains [L] (mm) and the average value of the beta [beta] (°) is the following (1) and (2) Formula; 15.63 ⁇ [ ⁇ ] + [L] ⁇ 44.06 (1) [L] ⁇ 20 (2) It is a grain-oriented electrical steel sheet characterized by satisfying
- the grain-oriented electrical steel sheet of the present invention further includes Cr: 0.01 to 0.50 mass%, Cu: 0.01 to 0.50 mass%, P: 0.005 to 0.50 mass%.
- the present invention also relates to a method for producing the grain-oriented electrical steel sheet described above, wherein C: 0.002 to 0.10 mass%, Si: 2.5 to 5.0 mass%, Mn: 0.01 to 0.00.
- a steel slab containing 8 mass%, Al: 0.010 to 0.050 mass%, and N: 0.003 to 0.020 mass%, the balance being composed of Fe and unavoidable impurities is hot-rolled to heat After the hot-rolled sheet annealing or without performing the hot-rolled sheet annealing, it is made a cold-rolled sheet with the final thickness by one or more cold rollings sandwiching the intermediate annealing, and the primary recrystallization annealing.
- the method of manufacturing a grain-oriented electrical steel sheet comprising a series of steps in which an annealing separator is applied to the steel sheet surface, finish annealing is performed, and a tension-imparting film is formed, in the heating process of the primary recrystallization annealing.
- the steel sheet after the primary recrystallization annealing is heated from the temperature T to 700 ° C. at a heating rate of 80 ° C./s or more.
- the steel slab used in the method for producing the grain-oriented electrical steel sheet according to the present invention may further include Se: 0.003-0.030 mass% and S: 0.002-0.030 mass%. It contains one or two kinds selected.
- the steel slab used in the method for producing the grain-oriented electrical steel sheet according to the present invention in addition to the above component composition, Cr: 0.01 to 0.50 mass%, Cu: 0.01 to 0.50 mass%, P: 0.005 to 0.50 mass%, Ni: 0.010 to 1.50 mass%, Sb: 0.005 to 0.50 mass%, Sn: 0.005 to 0.50 mass%, Bi: 0.005 to 0.50 mass%, Mo: 0.005 to 0.10 mass%, B: 0.0002 to 0.0025 mass%, Te: 0.0005 to 0.010 mass%, Nb: 0.0010 to 0.010 mass%, V : One or more selected from 0.001 to 0.010 mass% and Ta: 0.001 to 0.010 mass%.
- the grain size and crystal orientation of secondary recrystallized grains can be controlled within an appropriate range when a linear groove or strain region is added to the surface of a grain-oriented electrical steel sheet to perform magnetic domain refinement.
- the effect of improving the iron loss characteristics due to the magnetic domain subdivision can be exhibited to the maximum, so that it becomes possible to provide a grain oriented electrical steel sheet having a lower iron loss than before.
- the average value [ ⁇ ] of the misalignment angle ⁇ around the plate width direction from the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains and the average length [L] of the secondary recrystallized grains in the rolling direction are iron. It is a graph which shows the influence which it has on loss W17 / 50 . It is a graph which shows the relationship between the area ratio S ( alpha) 6.5 of the secondary recrystallized grain whose deviation angle (alpha) is less than 6.5 degrees, and iron loss W17 / 50 . It is a graph which shows the relationship between the area ratio S ( beta) 2.5 of the secondary recrystallized grain whose shift
- the shift angle ⁇ is smaller than 6.5 ° secondary recrystallized grains of the area ratio S ⁇ 6.5, the area ratio S Beta2.5 of secondary recrystallized grains deviation angle ⁇ is less than 2.5 °, It is a graph which shows the influence which acts on iron loss W17 / 50 .
- the method for determining the ratio of the maximum value I max and the minimum value I min (I max / I min ) in the Si depth direction of the intensity profile of light emission is a diagram for explaining.
- the grain-oriented electrical steel sheet of the present invention is applied to a linear groove or a linear strain region on one side or both sides of a steel sheet and subjected to a magnetic domain refinement treatment. It is necessary to be. Any linear grooves or strain regions imparted to the steel sheet surface for magnetic domain refinement are introduced in a direction intersecting at an angle close to 90 ° with respect to the rolling direction. If this crossing angle is reduced, the effect of improving the iron loss due to the magnetic domain fragmentation is reduced, so it is desirable to set the angle within the range of 90 to 60 °.
- channel may be provided as a continuous linear form, or may be provided as an intermittent linear form which repeats a specific unit like a broken line or a point sequence.
- the interval d in the steel sheet rolling direction between the linear groove or the linear strain region when performing the magnetic domain subdivision treatment needs to be in the range of 1 to 10 mm. If it exceeds 10 mm, the effect of magnetic domain fragmentation cannot be obtained sufficiently. On the other hand, if it is less than 1 mm, the proportion of the groove and strained region in the steel sheet increases, the apparent magnetic flux density decreases, and hysteresis loss Will increase. The range of 2 to 8 mm is preferable.
- the grain-oriented electrical steel sheet of the present invention requires that the grain size and crystal orientation of secondary recrystallized grains be controlled within an appropriate range described below. .
- On one surface of a grain-oriented electrical steel sheet containing 3.4 mass% of Si continuous linear grooves of width 80 ⁇ m ⁇ depth 25 ⁇ m are crossed at a crossing angle of 70 ° with respect to the rolling direction and spaced at a distance of 3.5 mm in the rolling direction.
- a test piece having a width of 100 mm and a length of 300 mm with the rolling direction as the length direction was cut out from various directional electrical steel sheets formed of d and having a forsterite film and a phosphate glass tension imparting film formed on both surfaces of the steel sheet.
- the deviation angle ⁇ with the axis perpendicular to the rolling surface from the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains, and the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains were measured.
- the iron loss W 17/50 is an iron loss value measured by the method described in JIS C2556 for each test piece.
- the deviation angle ⁇ and deviation angle ⁇ are measured over the entire surface at a pitch of 2 mm in the width direction and length direction of the test piece using a general-purpose X-ray diffractometer, and the secondary recrystallized grains at each position are measured.
- the deviation angle ⁇ with the axis perpendicular to the rolling plane from the ⁇ 110 ⁇ ⁇ 001> ideal orientation and the deviation angle ⁇ with the axis in the plate width direction from the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains. was measured, and the average value of each was determined.
- the average length [L] in the rolling direction of the secondary recrystallization is such that, after removing the coating on the surface of the test piece after the iron loss measurement, a straight line extending in the rolling direction is drawn at a pitch of 5 mm in the width direction.
- the number of grain boundaries crossing the straight line is the average grain size in the rolling direction obtained by dividing the length of the straight line.
- FIG. 1 shows the influence of the average value [ ⁇ ] of the deviation angle ⁇ and the average diameter [L] in the rolling direction of secondary recrystallization on the iron loss W 17/50 .
- the test piece showing good characteristics with an iron loss W 17/50 of less than 0.71 W / kg is the average length [L] (mm) in the rolling direction of the secondary recrystallized grains and the average of ⁇
- the value [ ⁇ ] (°) is the following formula (1) and formula (2); 15.63 ⁇ [ ⁇ ] + [L] ⁇ 44.06 (1) [L] ⁇ 20 (2) It turns out that it is the thing of the range which satisfy
- test pieces having an iron loss W 17/50 of 0.71 W / kg or more are mixed in the above range. Accordingly, the relationship between the area fraction S ⁇ 6.5 of the crystal grains having a deviation angle ⁇ of 6.5 ° or less and the iron loss W 17/50 , and the area of the crystal grains having a deviation angle ⁇ of 2.5 ° or less.
- the relationship between the fraction S ⁇ 2.5 and the iron loss W 17/50 was investigated, and the results are shown in FIG. 2 and FIG.
- the area fraction S ⁇ 6.5 and the area fraction S ⁇ 2.5 are deviations when each point measured at a pitch of 2 mm over the entire surface of the test piece is regarded as a measurement point of one crystal grain.
- the iron loss W 17/50 correlates with the area fraction S ⁇ 6.5 and the area fraction S ⁇ 2.5, and the higher the area fraction, the lower the iron loss. I understand. Therefore, the test piece in the range where the average length [L] in the rolling direction of the secondary recrystallized grains and the average value [ ⁇ ] of the deviation angle ⁇ shown in FIG. 1 satisfy the expressions (1) and (2) described above.
- the relationship between the iron loss W 17/50 , the area fraction S ⁇ 6.5 and the area fraction S ⁇ 2.5 is shown in FIG. From this figure, the test piece showing good characteristics with an iron loss W 17/50 of less than 0.71 W / kg has an area fraction S ⁇ 6.5 of 90% or more and an area fraction S ⁇ 2.5 of 75%. It turns out that it is the above.
- the average length [L] of the secondary recrystallized grains in the rolling direction and the average value [ ⁇ ] of the deviation angle ⁇ are described above (1 )
- the range satisfying the formula (2) it is necessary that the area fraction S ⁇ 6.5 is 90% or more and the area fraction S ⁇ 2.5 is 75% or more. It was.
- the value of the right side of equation (1) is 40 or less
- the value of the right side of equation (2) is 18 or less
- the area fraction S ⁇ 6.5 is 93% or more
- S ⁇ 2.5 is 80%. That's it.
- the grain-oriented electrical steel sheet subjected to the magnetic domain refinement treatment has a magnetic domain refinement effect due to grain boundaries as long as the secondary recrystallization is sufficiently larger than the repeated interval d in the rolling direction of the applied linear groove or strain region. Hardly appears.
- the grain boundaries intersecting the rolling direction begin to show the same effect as having undergone additional magnetic domain refinement, Eddy current loss is further reduced and iron loss is reduced.
- the above-described effect is manifested in the magnetic domain refinement process in which the process interval d in the rolling direction is in the range of 1 to 10 mm.
- the average length [L] of the secondary recrystallized grains in the rolling direction is 20 mm or less, That is, it is considered that the time when the expression (2) is satisfied.
- the above effect cannot be obtained by simply narrowing the interval d in the rolling direction of the magnetic domain refinement process.
- the domain (grooves and strained regions) subjected to the magnetic domain refinement processing has a larger total volume than the grain boundaries, and in the case of grooves, there is no iron, and in the case of strained regions, the rolling direction depends on the strain. This is considered to be because the apparent magnetic flux density is lowered and the hysteresis loss is increased because the magnetic permeability is reduced.
- the magnetic domain refinement effect obtained by the grain boundaries intersecting with the rolling direction is weakened. Need to compensate by sharpening. That is, by reducing the deviation angle ⁇ about the plate width direction from the ⁇ 110 ⁇ ⁇ 001> ideal orientation of the secondary recrystallized grains, the hysteresis loss is reduced, and the lancet magnetic domain ( ⁇ angle is several degrees). It is possible to reduce the eddy current loss by reducing the magnetic domain width generated in order to reduce the magnetostatic energy generated in the case of deviation and suppressing the increase of the magnetic domain width. Therefore, as the average length [L] in the rolling direction of the secondary recrystallized grains increases, it is necessary to decrease the average value [ ⁇ ] of the deviation angle ⁇ according to the equation (1).
- deviation angle ⁇ is 6.5 ° or less of secondary recrystallized grains of area fraction S Arufa6.5
- deviation angle ⁇ is 2.5 ° or less of secondary recrystallized grains of the area fraction S Beta2.5
- each has a lower limit is considered as follows. Even if the average ⁇ angle [ ⁇ ] and the average ⁇ angle [ ⁇ ] are small values, if the secondary recrystallized grains contain more than a certain number of crystal grains having an orientation greatly deviating from the Goss orientation, The magnetic properties are deteriorated and the iron loss of the entire steel sheet is increased.
- the primary recrystallization annealing in order to reduce the average length “L” in the rolling direction of the secondary recrystallized grains, also serves as primary recrystallization annealing or decarburization annealing. It is effective to increase the heating rate.
- the heating process of the primary recrystallization annealing is rapidly heated, the number of primary recrystallized grains having Goss orientation increases in the steel sheet structure after the primary recrystallization annealing. This is because the diameter can be reduced.
- the rapid heat treatment suppresses the development of the ⁇ 111> // ND orientation in the recrystallization texture, and the generation of Goss orientation grains ( ⁇ 110 ⁇ ⁇ 001>) serving as nuclei for secondary recrystallization.
- Goss orientation grains ⁇ 110 ⁇ ⁇ 001>
- the steel sheet reaches a high temperature in a short time, so that the accumulated strain energy is relatively low, and even when the Goss orientation is higher than the ⁇ 111> // ND orientation grains, Crystallization occurs, and the ⁇ 111> // ND orientation after recrystallization relatively decreases, and the number of Goss orientation grains ( ⁇ 110 ⁇ ⁇ 001>) increases.
- the number of Goss orientation grains increases, many Goss orientation grains appear in secondary recrystallization, so that the secondary recrystallization grains become finer and iron loss is reduced.
- it is necessary to heat the heating process in the section of 500 to 700 ° C. at a heating rate of 80 ° C./s or more.
- it is 120 degrees C / s or more.
- the cold rolling is a warm rolling, which promotes the introduction of a deformation band (shear band) into the crystal grains by rolling, and the Goss azimuth angle surrounded by a strained region in the deformation band. This is effective for making secondary recrystallized grains finer.
- the crystal orientation of the secondary recrystallized grains is sharpened so that the average value [ ⁇ ] of the above [L] and the deviation angle ⁇ satisfies the expressions (1) and (2), and the area fraction S
- the inhibitor one or more selected from well-known AlN, MnS, MnSe and the like can be used, but are not limited thereto.
- the secondary recrystallization orientation In order to sharpen the secondary recrystallization orientation, it is also effective to increase the reduction ratio of the final cold rolling.
- the rolling reduction of the final cold rolling is increased, the ⁇ 111 ⁇ ⁇ 112> orientation and ⁇ 12.4 1 ⁇ ⁇ 148> which are one of the ⁇ 111> // ND orientations in the texture after primary recrystallization.
- the degree of integration in the direction increases. Since the crystal grain boundary between the crystal grain having these two orientations and the Goss orientation grain is higher in mobility than the other crystal grain boundaries, the preferential growth of the Goss orientation grain is promoted in the finish annealing. As a result, the sharpness of the secondary recrystallization orientation to the Goss orientation is improved.
- the rolling reduction in the final cold rolling is in the range of 85 to 94%. Preferably it is 87 to 92% of range.
- the secondary recrystallized grains become coarse.
- the grain size and crystal orientation of secondary recrystallized grains must be kept in an appropriate balance, and coarsening is not preferable.
- the rapid heating in the primary recrystallization annealing described above is effective.
- a temperature of 500 to 700 ° C it is difficult to secure a sufficient number of Goss-oriented grains simply by regulating the rate of temperature rise in the region.
- a holding process is performed for holding for 1 to 10 seconds at any temperature T in the section of 250 to 600 ° C. in the heating process. It is necessary to heat the section from the processing temperature T to 700 ° C. at a temperature increase rate of 80 ° C./s or more.
- the reason is as follows.
- the ⁇ 111> // ND orientation with a high strain energy is preferentially recovered. . Therefore, the driving force that causes recrystallization of the ⁇ 111> // ND orientation resulting from the rolled structure of the ⁇ 111> // ND orientation selectively decreases, and other orientations cause recrystallization.
- the number of Goss orientation grains after primary recrystallization relatively increases.
- the retention treatment temperature is less than 250 ° C. or the retention time is less than 1 second, the recovery amount is insufficient and the above effect cannot be obtained.
- the retention treatment temperature exceeds 600 ° C. or the holding time exceeds 10 seconds
- recovery occurs in a wide range, so that the recovered structure remains as it is without recrystallization.
- the structure is different from the primary recrystallization texture described above and has a great adverse effect on the secondary recrystallization, so that the iron loss characteristic is deteriorated. Therefore, in the present invention, it is necessary to perform a holding treatment for holding for 1 to 10 seconds at any temperature between 250 to 600 ° C. in the heating process of the temporary recrystallization annealing.
- the present invention requires heating the 500 to 700 ° C. section of the heating process at a heating rate of 80 ° C./s or more in order to increase the number of Goss oriented grains.
- the processing temperature T (any temperature from 250 to 600 ° C.) is a temperature lower than 700 ° C. Therefore, it is necessary to set the heating rate to 80 ° C./s even in the section from the holding treatment temperature T to 700 ° C. Preferably it is 120 degrees C / s or more.
- the above method alone is not sufficient, and the secondary recrystallization orientation
- the average rate of temperature increase from 700 ° C. to soaking in the heating process of the primary recrystallization annealing is 15 ° C. / S or less
- the oxygen potential P H2O / P H2 of the atmosphere in the section from 700 ° C. to soaking is in the range of 0.2 to 0.4
- the oxygen potential P H2O / PH2 needs to be in the range of 0.3 to 0.5.
- an internal oxide layer mainly composed of SiO 2 is usually formed on the steel sheet surface layer by keeping the atmosphere oxidizing.
- This internal oxide layer becomes a base for forming a forsterite film by reacting with an annealing separator mainly composed of MgO during the subsequent finish annealing, and nitrogen in the atmosphere in the steel plate during the finish annealing. It has the effect of preventing nitriding that penetrates and suppresses the decomposition of AlN as an inhibitor.
- the decomposition of AlN is prevented by nitriding, selective secondary recrystallization only in the Goss orientation is prevented, and grains having an orientation shifted from the Goss orientation are also secondary recrystallized.
- the effect of suppressing nitriding is greatly affected by the structure of the internal oxide layer. That is, the structure of the internal oxide layer effective in suppressing nitrogen intrusion is such that SiO 2 is layered or fine spherical and concentrated at a specific depth position of the internal oxide layer (Si is concentrated). ) Structure and having such an internal oxide layer effectively prevents nitrogen intruding from the steel sheet surface layer from diffusing into the steel sheet during finish annealing, thereby suppressing nitriding.
- the internal oxide layer having the above structure can be judged from the concentration level of Si in the oxide layer. Specifically, the surface of the steel sheet after the primary recrystallization annealing is analyzed by a glow discharge emission analyzer GDS to obtain a concentration distribution (emission intensity profile) in the depth direction of Si, and Si in the emission intensity profile of Si is obtained.
- the maximum emission intensity of I max is I max and the minimum emission intensity of Si appearing at a position deeper than the maximum emission intensity I max is I min , the larger the ratio of both intensities (I max / I min ), the larger the oxide layer.
- the concentration of Si is advanced, and it is considered that the structure is suitable for suppressing nitrogen intrusion. According to the investigation by the inventors, the value of (I max / I min ) of the internal oxide layer effective in suppressing nitriding is 1.5 or more. A preferable value of (I max / I min ) is 1.55 or more.
- the surface of the steel sheet after the primary recrystallization annealing is measured using a high-frequency glow discharge emission spectrometer, the Si emission intensity is measured from the outermost surface of one side of the sample to a sufficiently deep region in the direction toward the thickness center, and the obtained Si profile From this, the maximum emission intensity I max of Si and the minimum emission intensity I min of Si appearing at a position deeper than the maximum emission intensity I max are obtained, and I max / I min is calculated.
- the emission intensity distribution in the depth direction from the surface of the steel sheet is also measured for Fe simultaneously with Si, and the Fe deficient layer existing in the surface layer portion is measured.
- I Fe (t) is the Fe emission intensity at the measurement time t in a deeper region and the Fe emission intensity increases and converges to a constant value, and the Fe emission intensity I at the measurement time 2t when Fe (2t) has a t 0 the minimum time within a range of ⁇ 3% relative to the emission intensity I Fe (t) described above, more than twice the time of the t 0, to continue the measurement Say.
- the atmosphere in a temperature range of 700 ° C. or higher where the internal oxide layer starts to be formed is made relatively low oxidizing and then gradually heated.
- the oxygen potential P H2O / P H2 of the atmosphere between 700 ° C. and the soaking temperature is set in the range of 0.2 to 0.4, and the rate of temperature increase between the above is set to 15 ° C./s or less. Is desirable.
- the oxygen potential P H2O / P H2 of the atmosphere exceeds 0.4 because it is too high, or when the temperature rising rate exceeds 15 ° C./s and reaches a high temperature in a short time, the formation of the internal oxide layer rapidly occurs.
- the SiO 2 structure changes from a layered or fine sphere to a coarse sphere or dendrite, and Si concentration decreases.
- the oxygen potential P H2O / P H2 of the atmosphere is less than 0.2, the internal oxide layer is not sufficiently formed until the soaking is reached, and the formation of the internal oxide layer proceeds rapidly during the soaking. After all, it becomes a rough spherical shape or dendritic shape.
- the oxygen potential P H2O / P H2 of the atmosphere in the section is in the range of 0.25 to 0.35, and the temperature increase rate in the section is 10 ° C./s or less.
- the oxidizability of the soaking atmosphere is also important, and the oxygen potential P H2O / P H2 of the soaking atmosphere needs to be in the range of 0.3 to 0.5.
- the oxygen potential P H2O / P H2 is less than 0.3, the formation of the internal oxide layer does not proceed, so that Si concentration does not occur.
- it exceeds 0.5 the formation of the oxide layer proceeds rapidly, and in any case, an internal oxide layer with appropriate Si concentration cannot be formed.
- a preferable oxygen potential P H2O / P H2 at the time of soaking is in the range of 0.35 to 0.45.
- the grain-oriented electrical steel sheet of the present invention needs to have a forsterite film and a tension-imparting film (insulating film) on both surfaces of the steel sheet.
- the forsterite film can be formed by applying and drying an annealing separator mainly composed of MgO on the surface of the steel sheet after decarburization annealing and then performing finish annealing.
- This forsterite film has an insulating property and also has a function of applying a tensile stress acting in the rolling direction to the steel sheet surface to narrow the magnetic domain width and reduce eddy current loss.
- the tension-imparting coating (insulating coating) is obtained by applying a coating solution containing, for example, phosphate-chromate-colloidal silica to the surface of the steel sheet after finish annealing and baking at a temperature of about 800 ° C.
- a coating solution containing, for example, phosphate-chromate-colloidal silica to the surface of the steel sheet after finish annealing and baking at a temperature of about 800 ° C.
- it has the function of reducing the eddy current loss by narrowing the magnetic domain width by increasing the insulation of the steel sheet surface and applying a tensile stress acting in the rolling direction to the steel sheet surface.
- the tension applied to the steel sheet surface by these coatings is preferably in the range of 4.8 to 36 MPa per one surface of the steel sheet from the viewpoint of effectively reducing eddy current loss.
- the magnitude of the applied tension can be measured from the amount of warpage of the steel sheet when the coating on one side of the steel sheet is removed by pickling after forming the tension coat.
- the forsterite film is formed from a sub-scale mainly composed of silica formed on the steel sheet surface during decarburization annealing during finish annealing, so that the forsterite film has insulating properties and adhesion to the steel sheet.
- an appropriate amount of subscales must be formed.
- the oxygen basis weight is 0.30 g / m 2
- the subscale is too small, and the amount of forsterite film produced becomes insufficient, and the insulation and adhesion of the film are lowered.
- it exceeds 0.75 g / m 2 the amount of forsterite produced becomes excessive, resulting in a decrease in the space factor when the steel plates are laminated.
- the oxygen basis weight after decarburization annealing it is preferable to limit the oxygen basis weight after decarburization annealing to a range of 0.30 to 0.75 g / m 2 . More preferably, it is in the range of 0.40 to 0.60 g / m 2 .
- the grain-oriented electrical steel sheet of the present invention is a hot-rolled sheet obtained by hot-rolling a steel material (slab) adjusted to a predetermined component composition, which will be described later, and subjected to hot-rolled sheet annealing or hot-rolled sheet annealing. Without cold rolling at least once with intermediate or intermediate annealing, the final sheet thickness is cold-rolled and subjected to primary recrystallization annealing that also serves as primary recrystallization annealing or decarburization annealing, and then the steel sheet surface is annealed. A separator is applied, finish annealing is performed, an insulating film is formed, and a magnetic domain refinement process is performed in any step after the cold rolling.
- the steel material (slab) used for manufacturing the grain-oriented electrical steel sheet of the present invention contains 2.5 mass% or more of Si in order to increase the specific resistance of the product plate (steel plate after finish annealing) and reduce eddy current loss. It is necessary. If it is less than 2.5 mass%, eddy current loss is not reduced, and good iron loss characteristics cannot be obtained. On the other hand, when it contains exceeding 5 mass%, it will become difficult to cold-roll, and risks, such as a plate fracture, will increase. Therefore, Si is set in the range of 2.5 to 5 mass%. Preferably, it is in the range of 2.8 to 4.3 mass%.
- the slab used in the present invention contains C and Mn in the range of C: 0.002 to 0.10 mass% and Mn: 0.01 to 0.8 mass%, respectively.
- C has an effect of strengthening grain boundaries and suppressing slab cracking, and therefore needs to contain 0.002 mass% or more.
- C in order not to cause magnetic aging, it is necessary that C is reduced to 0.0050 mass% or less at the stage of the product plate, but the C content of the steel material exceeds 0.1 mass%. And there is a possibility that decarburization and annealing cannot be sufficiently performed.
- the preferable C content of the steel material is in the range of 0.01 to 0.09 mass%.
- Mn needs to contain 0.01 mass% or more in order to prevent hot brittleness and to ensure favorable hot workability. However, if it exceeds 0.8 mass%, the above effect is saturated and the magnetic flux density is reduced. A preferable Mn content is in the range of 0.02 to 0.5 mass%.
- the slab used for the material of the grain-oriented electrical steel sheet of the present invention causes secondary recrystallization and increases the degree of integration in the Goss orientation. It is necessary to contain in the range of 0.010 to 0.050 mass%, N: 0.003 to 0.020 mass%. If Al is less than 0.050 mass% or N is less than 0.003 mass%, the formation of AlN becomes insufficient and the degree of integration in the Goss orientation decreases. On the other hand, if Al exceeds 0.050 mass%, or if N exceeds 0.02 mass%, the amount of AlN formed becomes excessive, and secondary recrystallization in the Goss orientation is hindered. Therefore, the content of Al and N needs to be in the above range.
- N when using AlN as an inhibitor may contain an amount necessary for secondary recrystallization when melting steel, or any of from cold rolling to secondary recrystallization in finish annealing.
- nitriding treatment may be performed to contain the amount necessary for secondary recrystallization.
- examples of the inhibitor that can be used in the present invention include MnSe and MnS.
- Se and S are Se: 0.003 to 0.030 mass, respectively.
- %, S It is preferable to contain in the range of 0.002 to 0.03 mass%. More preferably, the range is Se: 0.005 to 0.025 mass%, and S: 0.002 to 0.01 mass%.
- the MnSe and MnS inhibitors are preferably used in combination with AlN. Further, MnSe and MnS may be used alone or in combination.
- one or more selected from Cr, Cu and P are used: Cr: 0.01 to 0.50 mass%, Cu: 0.01 to You may contain in the range of 0.50 mass% and P: 0.005-0.50 mass%.
- one or more selected from Ni, Sb, Sn, Bi, Mo, B, Te, Nb, V and Ta are used.
- the slab is preferably manufactured by a conventional ingot-bundling rolling method or a continuous casting method after melting the steel having the above-mentioned composition by a conventional refining process. Then, according to a conventional method, it is reheated to a temperature of about 1400 ° C. and hot rolled. However, when AlN is used as the inhibitor and nitriding is performed in the middle of the manufacturing process, the reheating temperature can be made lower than the above.
- the hot-rolled sheet obtained by hot rolling is subjected to hot-rolled sheet annealing as necessary.
- the temperature of this hot-rolled sheet annealing is preferably in the range of 800 to 1150 ° C. in order to obtain good magnetic properties. If it is less than 800 degreeC, the band structure formed by hot rolling will remain, it will become difficult to obtain the primary recrystallized structure of a sized grain, and the growth of a secondary recrystallized grain will be inhibited. On the other hand, when the temperature exceeds 1150 ° C., the grain size after the hot-rolled sheet annealing is excessively coarsened, so that it becomes difficult to obtain a primary recrystallized structure of sized particles.
- the steel sheet that has been subjected to hot-rolled sheet annealing is made into a cold-rolled sheet having a final thickness by one or more cold rollings or two or more cold rollings with intermediate annealing.
- the annealing temperature of the intermediate annealing is preferably in the range of 900 to 1200 ° C.
- the temperature is lower than 900 ° C.
- the recrystallized grains after the intermediate annealing become finer, and the Goss nuclei in the primary recrystallized structure are reduced to deteriorate the magnetic properties of the product plate.
- the temperature exceeds 1200 ° C. the crystal grains become too coarse as in the hot-rolled sheet annealing, and it becomes difficult to obtain a primary recrystallized structure of the sized grains.
- the cold rolling (final cold rolling) with the final sheet thickness controls the grain size and crystal orientation of the secondary recrystallized grains within an appropriate range, so that the rolling reduction is 85 to 94%. It is necessary to be in the range. Preferably it is 87 to 92% of range.
- the cold-rolled sheet having the final thickness is then subjected to primary recrystallization annealing that also serves as decarburization annealing.
- the annealing temperature in the primary recrystallization annealing is preferably in the range of 800 to 900 ° C. from the viewpoint of promptly proceeding the decarburization reaction when decarburization annealing is involved. Therefore, even in the case of C: 0.005 mass% or less that does not require decarburization, annealing in the above atmosphere is necessary to secure a subscale layer necessary for forming forsterite.
- C in the steel sheet after decarburization annealing needs to be 0.0050 mass% or less from the viewpoint of preventing magnetic aging. Preferably it is 0.0030 mass% or less.
- a holding treatment is performed by holding at any temperature T between 250 and 600 ° C. for 1 to 10 seconds, and then It is necessary to heat at a temperature increase rate of 80 ° C./s or more between the holding temperature T and 700 ° C.
- the holding temperature in the holding process is not necessarily constant, and if the temperature change is ⁇ 10 ° C./s or less, the same effect as the holding can be obtained, and can be considered constant.
- the primary recrystallization annealing it is necessary to form an internal oxide layer effective for suppressing nitridation during finish annealing.
- the surface of the steel sheet after the primary recrystallization annealing is subjected to glow discharge emission analysis (GDS). ),
- GDS glow discharge emission analysis
- the ratio (I max / I min ) between the maximum value I max in the emission intensity profile of Si in the depth direction and the minimum value I min appearing at a position deeper than the maximum value I max is 1.5 or more. It is necessary to form an internal oxide layer.
- heating is performed at a temperature increase rate of 15 ° C./s or less in an atmosphere in which the oxygen potential P H2O / PH2 is in the range of 0.2 to 0.4 from 700 ° C. to the soaking temperature. Furthermore, it is necessary to set the oxygen potential P H2O / P H2 at the time of soaking in the range of 0.3 to 0.5.
- the steel sheet that has undergone primary recrystallization annealing is coated with an annealing separator mainly composed of MgO, dried, and then subjected to finish annealing.
- finish annealing it is preferable to raise the temperature to about 1200 ° C. in order to carry out purification treatment after maintaining and maintaining at 800 to 1050 ° C. for 20 hours or longer to develop and complete secondary recrystallization.
- the steel sheet that has been subjected to finish annealing is then washed with water, brushed, pickled, etc. to remove unreacted annealing separator adhering to the steel sheet surface, and then flattened and annealed to correct the shape. It is effective for reduction. This is because the finish annealing is normally performed in a coil state, and the characteristics may be deteriorated when measuring the iron loss due to coil winding.
- the steel plate of the present invention needs to be coated with an insulating film on the surface of the steel plate before or after the above-described flattening annealing.
- the insulating film needs to be a tension-imparting film that applies tension to the steel sheet.
- the above-described insulating film composed of phosphate-chromate-colloidal silica is applied. preferable.
- the steel sheet of the present invention needs to be subjected to magnetic domain subdivision treatment in order to further reduce iron loss.
- the groove width is preferably 20 to 250 ⁇ m, and the groove depth is preferably in the range of 2 to 15% of the plate thickness. If the width is too narrow or the depth is too shallow, the magnetic domain refinement effect cannot be obtained sufficiently.
- the method for forming the groove is not particularly limited. For example, in any step after the final cold rolling to obtain the final plate thickness, one or both surfaces of the steel plate surface are etched, knurled by a gear roll, or laser irradiation. Etc. can be used.
- the method for introducing the strain region is not particularly limited.
- laser irradiation, electron beam irradiation, plasma jet spraying, ion beam A method such as thermal spraying can be used.
- the strain region introduced by these methods is recovered by annealing at a high temperature, and the magnetic domain refinement effect is lost. Therefore, the strain region is preferably applied after finish annealing.
- the magnetic domain has been subdivided by introducing the groove or strain region can be confirmed by the fact that a reflux magnetic domain extending along the linear direction is formed in the linear portion of the strained steel plate surface. it can.
- the reflux magnetic domain can be easily observed without removing the coating on the surface of the steel sheet by using a bitter method in which a magnetic colloid solution is dropped on the surface of the steel sheet, or a commercially available magnet viewer using the magnetic colloid solution.
- an observation method such as a Kerr effect microscope using a magneto-optical effect, a transmission electron microscope using electrons as a probe, or a spin-polarized scanning electron microscope may be used.
- a steel slab was produced by a continuous casting method, reheated to a temperature of 1415 ° C. by induction heating, and then hot-rolled to obtain a hot rolled sheet having a thickness of 2.5 mm. Next, the hot-rolled sheet was subjected to hot-rolled sheet annealing at 1000 ° C. for 50 seconds, then cold-rolled to an intermediate thickness of 1.9 mm, subjected to intermediate annealing at 1100 ° C.
- the retention treatment conditions performed at the temperature T during the heating process and the temperature increase rate from the retention treatment temperature T to 700 ° C. were variously changed. Furthermore, between 700 ° C. and a soaking temperature of 850 ° C., heating is performed at a heating rate of 10 ° C./s in an atmosphere with an oxygen potential of P H2O / P H2 : 0.30, and a soaking process (decarburization annealing). The oxygen potential of the atmosphere was set to P H2O / P H2 : 0.39.
- a sample is taken from the center of the plate width of the steel sheet after the primary recrystallization annealing, and from the outermost surface of one side of the sample to the center of the plate thickness using a high-frequency glow discharge emission spectrometer GDS (System 3860 manufactured by Rigaku Corporation).
- the light emission intensity of Si was measured in the direction to go, and I max / I min was determined by the method described above from the light emission intensity profile of the obtained Si in the plate thickness direction.
- all the steel plates after the primary recrystallization annealing had a value of I max / I min in the range of 1.6 to 1.7.
- the GDS analysis and the method of obtaining I max / I min were the same as described above.
- the surface of the steel sheet after the primary recrystallization annealing is coated with an annealing separator mainly composed of MgO, dried, further subjected to secondary recrystallization, and then subjected to a purification treatment at 1200 ° C. for 10 hours. Annealed.
- the atmosphere of the above-mentioned finish annealing was set to H 2 at the time of 1200 ° C. holding for the purification treatment, and N 2 at the time of temperature increase and temperature decrease.
- a tension-imparting insulating film mainly composed of magnesium phosphate containing colloidal silica is applied at a basis weight of 5 g / m 2 per side and baked to obtain a product coil. did.
- a steel slab is manufactured by a continuous casting method, reheated to a temperature of 1400 ° C. by induction heating, and then hot-rolled to a hot-rolled sheet having a thickness of 2.6 mm. After performing cold rolling to an intermediate thickness of 1.8 mm, an intermediate annealing at 1100 ° C. for 30 seconds is performed, and then final cold rolling with a reduction ratio of 89.4% is performed to obtain a cold sheet having a thickness of 0.23 mm. Finished in a sheet.
- the said cold-rolled sheet was subjected to primary recrystallization annealing that also served as decarburization annealing at 840 ° C. for 120 seconds.
- a holding treatment is performed for 1.5 seconds at a temperature of 400 ° C. during the heating process, and after that, heating is performed at a temperature increase rate of 150 ° C./s between 400 to 700 ° C. heating rate until 840 ° C. is, the oxygen potential P H2O / P H2 of between ambient and the oxygen potential P H2O / P H2 atmosphere in the soaking process in the various conditions shown in Table 2 Changed.
- the steel sheet after the primary recrystallization annealing samples were taken from the plate width center to determine the I max / I min in the same manner as in Example 1.
- the surface of the steel sheet after the primary recrystallization annealing is coated with an annealing separator mainly composed of MgO, dried, further subjected to secondary recrystallization, and then subjected to a purification treatment at 1200 ° C. for 10 hours. Annealed.
- the atmosphere of the finish annealing was H 2 at the time of maintaining at 1200 ° C. for the purification treatment, and N 2 at the time of temperature increase and temperature decrease.
- a tension-imparting insulating film mainly composed of magnesium phosphate containing colloidal silica was applied to both surfaces of the steel plate after the finish annealing at a basis weight of 5 g / m 2 per side and baked.
- a CO 2 laser is applied at an intersecting angle of 80 ° with respect to the rolling direction at an output of 100 W, a beam condensing diameter of 210 ⁇ m, and a scanning speed of 10 m / s, and an interval d in the rolling direction.
- Continuous irradiation was performed at 6 mm, a linear strain region was added, and magnetic domain refinement treatment was performed to obtain a product coil.
- the magnetic domain structure on the steel plate surface was observed using the bitter method, and it confirmed that the reflux magnetic domain was formed in the laser irradiation part.
- the cold-rolled sheet was subjected to primary recrystallization annealing that also served as decarburization annealing at 845 ° C. for 100 seconds.
- heating is performed at a temperature increase rate of 200 ° C./s between 500 to 700 ° C., and a soaking temperature of 845 from 700 ° C.
- a tension-imparting insulating film mainly composed of magnesium phosphate containing colloidal silica is applied at a basis weight of 5 g / m 2 per side and baked to obtain a product coil. did.
- a CO 2 laser is applied to one surface of the product coil at an intersection angle of 80 ° with respect to the rolling direction under the conditions of an output of 120 W, a beam focusing diameter of 220 ⁇ m, and a scanning speed of 12 m / s, The distance d in the rolling direction was changed as shown in Table 3, and continuous irradiation was performed to introduce linear strain on the steel sheet surface.
- an intersection angle of 80 ° with respect to the rolling direction at an acceleration voltage of 70 kV and a beam current of 15 mA in a vacuum of 0.1 Pa is applied to one surface of the product coil using an electron beam accelerator.
- the distance d in the rolling direction was changed as shown in Table 3, and the electron beam was continuously irradiated in a linear shape to introduce linear strain on the steel sheet surface.
- the magnetic domain structure on the surface of the steel sheet was observed using the pitter method after the magnetic domain subdivision process, and it was confirmed that a reflux magnetic domain was formed in the laser irradiation part. .
- Si-containing steel slabs having various composition shown in Table 4 are manufactured by a continuous casting method, heated by induction heating to a temperature of 1420 ° C., and then hot-rolled to obtain a hot-rolled sheet having a thickness of 2.4 mm. After hot-rolled sheet annealing at 1100 ° C. ⁇ 40 seconds, it was cold-rolled to a thickness of 1.7 mm, and after intermediate annealing at 1100 ° C. ⁇ 25 seconds, the final cold rolling reduction ratio was 86.4%. And finished into a cold rolled sheet having a final sheet thickness of 0.23 mm.
- a continuous groove having a width of 75 ⁇ m and a depth of 25 ⁇ m is formed on one surface of the cold-rolled sheet by electrolytic etching at an angle of 75 ° from the rolling direction and a distance d in the rolling direction of 3 mm, and then 850 ° C. ⁇ 170
- a primary recrystallization annealing was performed which also served as a second decarburization annealing.
- the atmosphere of the finish annealing was H 2 at the time of maintaining at 1200 ° C. for the purification treatment, and N 2 at the time of temperature rise and time including the secondary recrystallization.
- an insulating tension coating mainly composed of magnesium phosphate containing colloidal silica was applied and baked on both sides of the steel plate after finish annealing at a basis weight of 5 g / m 2 per one side of the steel plate.
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Abstract
Description
鋼板表面に溝や歪領域を付与する磁区細分化処理技術は、局所的に導入された溝部分や歪領域部分に生じる高エネルギー状態を緩和するために主磁区の幅が小さくなり、渦電流損が低減することを利用したものである。すなわち、溝を導入した場合には、溝部分に磁極が発生して、また、歪領域を導入した場合には、歪領域部分に還流磁区と呼ばれる磁区構造が発生して、高エネルギー状態となるため、これを緩和するために主磁区の幅が小さくなる現象を利用したものである。一方、二次再結晶粒を細粒化する技術は、粒界を磁極の発生部位として磁区を細分化するものであると考えることができる。
そのため、従来は、溝や歪領域を付与する磁区細分化処理の効果は、二次再結晶粒の細粒化効果と同じであり、鋼板に溝や歪領域を付与する磁区細分化処理を施す場合には、二次再結晶粒は粗大であってもよいと考えられ、二次再結晶粒を細粒化することは行われていなかった。
15.63×[β]+[L]<44.06 ・・・(1)
[L]≦20 ・・・(2)
を満たすことを特徴とする方向性電磁鋼板である
Siを3.4mass%含有する方向性電磁鋼板の片側表面に、幅80μm×深さ25μmの連続した線状溝を圧延方向に対して70°の交差角で、圧延方向に3.5mmの間隔dで形成され、鋼板両面にフォルステライト被膜と燐酸塩系ガラス張力付与被膜が形成された種々の方向性電磁鋼板から、圧延方向を長さ方向とする幅100mm×長さ300mmの試験片を切り出し、該試験片について、二次再結晶粒の{110}<001>理想方位からの圧延面垂直方向を軸とするずれ角α、二次再結晶粒の{110}<001>理想方位からの板幅方向を軸とするずれ角β、二次再結晶の圧延方向の平均長さ[L]および鉄損W17/50を測定した。
また、上記ずれ角αおよびずれ角βは、汎用のX線回折装置を用いて、試験片の幅方向および長さ方向に2mmピッチで全面にわたって測定し、各々の位置における二次再結晶粒の{110}<001>理想方位からの圧延面垂直方向を軸とするずれ角α、および、二次再結晶粒の{110}<001>理想方位からの板幅方向を軸とするずれ角βを測定し、それぞれの平均値を求めた。
また、上記二次再結晶の圧延方向の平均長さ[L]は、上記鉄損測定後の試験片表面の被膜を除去した後、圧延方向に伸びる直線を幅方向に5mmピッチで描き、上記直線を横切る粒界の数で、直線の長さを除して求めた圧延方向の平均粒径である。
15.63×[β]+[L]<44.06 ・・・(1)
[L]≦20 ・・・(2)
を満たす範囲のものであることがわかる。
ここで、面積分率Sα6.5および面積分率Sβ2.5とは、前述した試験片全面にわたって2mmピッチで測定した各点を1つの結晶粒の測定点と見做したときの、ずれ角αが6.5°以下の測定点の割合(%)およびずれ角βが2.5°以下の測定点の割合(%)である。
磁区細分化処理を施した方向性電磁鋼板は、付与した線状の溝あるいは歪領域の圧延方向の繰り返し間隔dに比して二次再結晶が十分に大きければ、粒界による磁区細分化効果はほとんど現れない。しかし、二次再結晶の大きさが、間隔dにある程度近づいてくると、圧延方向と交差する粒界は、追加の磁区細分化処理を施したことと同様の効果を示し始め、これにより、渦電流損がさらに低減されて鉄損が低減する。そして、前述した圧延方向の処理間隔dが1~10mmの範囲とする磁区細分化処理において上記効果が発現するのは、二次再結晶粒の圧延方向の平均長さ[L]が20mm以下、すなわち、(2)式を満たすときであると考えられる。
平均α角[α]や平均β角[β]が小さい値であっても、二次再結晶粒中にGoss方位から大きく外れた方位を持つ結晶粒が一定数以上含まれると、その部分で磁気特性が劣化し、鋼板全体の鉄損が増大する。そのため、二次再結晶粒の圧延方向平均長さ[L]およびずれ角βの平均値[β]が上記した(1)式および(2)式を満たしていても、面積分率Sα6.5や面積分率Sβ2.5が低いと、図2~図4のように、良好な鉄損特性が得られなくなる。
したがって、二次再結晶粒のずれ角αおよびずれ角βは、圧延方向にある程度以上先鋭化されている必要があり、その臨界点がSα6.5は90%、Sβ2.5は75%であると考えている。
先述した急速加熱の途中の回復が起こる温度域(250~600℃)に所定時間保持する保定処理を施した場合には、歪エネルギーが高い<111>//ND方位が優先的に回復を起こす。そのため、<111>//ND方位の圧延組織から生じる<111>//ND方位が再結晶を起こす駆動力が選択的に低下し、それ以外の方位が再結晶を起こすようになる。その結果、一次再結晶後のGoss方位粒の数が相対的に増大する。ただし、保定処理温度が250℃未満であったり、保持時間が1秒未満あったりすると、回復量が不足し、上記効果が得られない。一方、保定処理温度が600℃超えであったり、保持時間が10秒を超えたりすると、回復が広い範囲で起こるため、再結晶が起こらずに回復組織がそのまま残存するようになる。その結果、上記の一次再結晶集合組織とは異なった組織になり、二次再結晶に大きな悪影響を与えるため、鉄損特性が低下する。そこで、本発明では、一時再結晶焼鈍の加熱過程における250~600℃間のいずれかの温度で1~10秒間保持する保定処理を施す必要がある。
一次再結晶焼鈍の高温域、とりわけ、700℃以上の温度域では、通常、雰囲気を酸化性に保つことで鋼板表層にSiO2を主体とする内部酸化層を形成させている。この内部酸化層は、続く仕上焼鈍中に、MgOを主体とする焼鈍分離剤と反応してフォルステライト被膜を形成するための下地となるとともに、仕上焼鈍の途中で雰囲気中の窒素が鋼板中に侵入し、インヒビターであるAlNの分解を抑制する浸窒を防止する効果を有する。浸窒によってAlNの分解が妨げられると、Goss方位のみの選択的二次再結晶が妨げられ、Goss方位からずれた方位を持つ粒も二次再結晶してしまう。
一次再結晶焼鈍後の鋼板表面を、高周波グロー放電発光分析装置を用いてサンプルの片側最表面から板厚中心へ向かう方向に十分深い領域までSiの発光強度を測定し、得られたSiのプロファイルから、Siの最大発光強度Imaxと、上記最大発光強度Imaxよりも深い位置に現れるSiの最小発光強度Iminを求め、Imax/Iminを算出する。ここで、上記の十分深い領域まで測定するとは、図5に示したように、Siと同時にFeについても鋼板表面から深さ方向の発光強度分布を測定し、表層部に存在するFeの欠乏層よりも深く、かつ、Feの発光強度が上昇して一定の値に収束していく領域における測定時間tでのFeの発光強度をIFe(t)とし、測定時間2tにおけるFeの発光強度IFe(2t)が前述した発光強度IFe(t)に対して±3%の範囲内にある最小の時間をt0としたとき、上記t0の2倍以上の時間、測定を継続することをいう。
フォルステライト被膜は、脱炭焼鈍後の鋼板表面に、MgOを主体とする焼鈍分離剤を塗布・乾燥した後、仕上焼鈍を施すことで形成することができる。このフォルステライト被膜は、絶縁性を有するとともに、鋼板表面に圧延方向に働く引張応力を付与して、磁区幅を狭め、渦電流損を低減する働きを有する。
本発明の方向性電磁鋼板は、後述する所定の成分組成に調整した鋼素材(スラブ)を熱間圧延して熱延板とし、熱延板焼鈍を施した後または熱延板焼鈍を施すことなく、1回または中間焼鈍を挟む2回以上の冷間圧延により最終板厚の冷延板とし、一次再結晶焼鈍あるいは脱炭焼鈍を兼ねた一次再結晶焼鈍を施した後、鋼板表面に焼鈍分離剤を塗布し、仕上焼鈍を施し、絶縁被膜を被成するとともに、上記の冷間圧延後のいずれかの工程で、磁区細分化処理を施すことで製造する。
Cは、粒界を強化し、スラブ割れを抑制する効果があるため0.002mass%以上の含有を必要とする。一方、磁気時効を起こさないためには、製品板の段階で、Cが0.0050mass%以下に低減されていることが必要であるが、鋼素材のC量が0.1mass%を超えていると、脱炭焼鈍でも十分に脱炭できないおそれがある。好ましい鋼素材のC含有量は0.01~0.09mass%の範囲である。
また、Mnは、熱間脆性を防止し、良好な熱間加工性を確保するために0.01mass%以上の含有を必要とする。しかし、0.8mass%を超えると、上記効果が飽和する他、磁束密度の低下を招く。好ましいMn含有量は、0.02~0.5mass%の範囲である。
この一次再結晶焼鈍における焼鈍温度は、脱炭焼鈍を伴う場合は、脱炭反応を速やかに進行させる観点から、800~900℃の範囲とするのが好ましい。したがって、脱炭が不要なC:0.005mass%以下の場合でも、フォルステライト形成に必要なサブスケール層を確保するため、上記雰囲気での焼鈍が必要である。ここで、上記脱炭焼鈍後の鋼板中のCは、磁気時効を防止する観点から、0.0050mass%以下であることが必要である。好ましくは0.0030mass%以下である。なお、一次再結晶焼鈍と脱炭焼鈍を別々に行ってもよい。
次いで、上記冷延板の片表面に、電解エッチングで幅70μm×深さ28μmの連続する線状の溝を、圧延方向に対して75°の交差角で圧延方向の間隔dを3mmとして形成した。
次いで、上記冷延板に850℃で120秒間均熱する脱炭焼鈍を兼ねた一次再結晶焼鈍を施した。この際、加熱過程途中の温度Tにおいて行う保定処理条件、および、該保定処理温度Tから700℃までの間の昇温速度を表1に示したように種々に変化させた。さらに、700℃から均熱温度850℃までの間は、酸素ポテンシャルPH2O/PH2:0.30とした雰囲気下で、昇温速度10℃/sで加熱し、均熱過程(脱炭焼鈍時)の雰囲気の酸素ポテンシャルはPH2O/PH2:0.39とした。
最後に、上記仕上焼鈍後の鋼板両面に、コロイダルシリカを含有するリン酸マグネシウムを主成分とする張力付与絶縁被膜を、片面当たり5g/m2の目付量で塗布し、焼き付けて、製品コイルとした。
また、X線回折装置を用いて、上記鉄損測定後の試験片について、二次再結晶粒の結晶方位を、板幅方向、圧延方向ともに2mmピッチで全面にわたって測定し、ずれ角βの平均値[β]、および、ずれ角αが6.5°以下の結晶粒の面積分率Sα6.5およびずれ角βが2.5°以下の結晶粒の面積分率Sβ2.5を求めた。
また、上記鉄損測定後の試験片表面の絶縁被膜およびフォルステライト被膜を除去して結晶粒界を現出させた後、圧延方向に伸びる直線を幅方向に対して5mmピッチで描き、上記直線を横切る粒界の数を測定して、二次再結晶粒の圧延方向の平均長さ[L]を求めた。
上記の測定の結果を表1に併記した。この表から、一次再結晶焼鈍の加熱途中における保定処理条件(温度T、時間)およびその後の保定処理温度T~700℃までの間の昇温速度を適正化し、二次再結晶粒の圧延方向の平均長さ[L]および結晶方位([β]、Sα6.5、Sβ2.5)を本発明の条件を満たすように制御した方向性電磁鋼板は、いずれも鉄損特性に優れていることがわかる。
次いで、上記冷延板に840℃×120秒の脱炭焼鈍を兼ねた一次再結晶焼鈍を施した。この際、加熱過程途中の400℃の温度で1.5秒間保持する保定処理を施し、その後、400~700℃間を150℃/sの昇温速度で加熱した後、700℃から均熱温度である840℃までの間の昇温速度、その間の雰囲気の酸素ポテンシャルPH2O/PH2、および、均熱過程での雰囲気の酸素ポテンシャルPH2O/PH2を表2に示した種々の条件に変化させた。また、上記一次再結晶焼鈍後の鋼板について、板幅中心部からサンプルを採取し、実施例1と同様の方法でImax/Iminを求めた。
次いで、上記一次再結晶焼鈍後の鋼板表面に、MgOを主体とする焼鈍分離剤を塗布し、乾燥した後、さらに、二次再結晶させた後、1200℃×10時間の純化処理を行う仕上焼鈍を施した。なお、仕上焼鈍の雰囲気は、純化処理する1200℃保定時はH2、昇温時および降温時はN2とした。
次いで、上記仕上焼鈍後の鋼板両面に、コロイダルシリカを含有するリン酸マグネシウムを主成分とする張力付与絶縁被膜を、片面当たり5g/m2の目付量で塗布し、焼き付けた。
最後に、上記鋼板の片表面に、CO2レーザを、出力100W、ビーム集光径210μm、走査速度10m/sの条件で圧延方向に対して80°の交差角で、圧延方向の間隔dを6mmとして連続照射し、線状の歪領域を付与して磁区細分化処理を施し、製品コイルとした。なお、上記磁区細分化処理後、ビッター法を用いて鋼板表面の磁区構造を観察し、レーザ照射部に還流磁区が形成されていることを確認した。
上記の測定結果を表2に併記した。この表から、Imax/Imin、二次再結晶粒の圧延方向の平均長さ[L]および結晶方位([β]、Sα6.5、Sβ2.5)が本発明の条件を満たす方向性電磁鋼板は、いずれも鉄損特性に優れていることがわかる。
次いで、上記冷延板に、845℃×100秒の脱炭焼鈍を兼ねた一次再結晶焼鈍を施した。この際、加熱過程途中の500℃の温度で3秒間保持する保定処理を施した後、500~700℃間を200℃/sの昇温速度で加熱し、さらに、700℃から均熱温度845℃までの間を、酸素ポテンシャルPH2O/PH2:0.24とした雰囲気下で、昇温速度8℃/s以下で加熱し、酸素ポテンシャルPH2O/PH2:0.33とした雰囲気下で均熱処理を施した。上記一次再結晶焼鈍後の鋼板について、板幅中心部からサンプルを採取し、実施例1と同様の方法でImax/Iminを求めたところ、1.68であった。
次いで、上記一次再結晶焼鈍後の鋼板表面に、MgOを主体とする焼鈍分離剤を塗布し、乾燥した後、さらに、二次再結晶させた後、1200℃×10時間の純化処理を行う仕上焼鈍を施した。なお、上記仕上焼鈍の雰囲気は、純化処理する1200℃保定時はH2、二次再結晶を含む昇温時および降温時はN2とした。
最後に、上記仕上焼鈍後の鋼板両面に、コロイダルシリカを含有するリン酸マグネシウムを主成分とする張力付与絶縁被膜を、片面当たり5g/m2の目付量で塗布し、焼き付けて、製品コイルとした。
また、X線回折装置を用いて、上記鉄損測定後の試験片について、二次再結晶粒の結晶方位を、板幅方向、圧延方向ともに2mmピッチで全面にわたって測定し、ずれ角βの平均値[β]、および、ずれ角αが6.5°以下の結晶粒の面積分率Sα6.5およびずれ角βが2.5°以下の結晶粒の面積分率Sβ2.5を求めた。
また、上記鉄損測定後の試験片表面の絶縁被膜およびフォルステライト被膜を除去して結晶粒界を現出させた後、圧延方向に伸びる直線を幅方向に対して5mmピッチで描き、上記直線を横切る粒界の数を測定して、二次再結晶粒の圧延方向の平均長さ[L]を求めた。
上記の測定結果を表3に併記した。この表から、磁区細分化処理の圧延方向の間隔dを本発明の条件を満たす範囲とした方向性電磁鋼板は、いずれも鉄損特性に優れていることがわかる。
次いで、上記冷延板の片表面に、電解エッチングで幅75μm×深さ25μmの連続する溝を、圧延方向から75°の角度で圧延方向の間隔dを3mmとして形成した後、850℃×170秒の脱炭焼鈍を兼ねた一次再結晶焼鈍を施した。この際、加熱過程途中の300℃の温度で2秒間保持する保定処理を施した後、700℃までを昇温速度100℃/sで加熱し、さらに、700℃から均熱温度である850℃までの間を、酸素ポテンシャルPH2O/PH2を0.25とした雰囲気下で、昇温速度5℃/sで加熱した後、酸素ポテンシャルPH2O/PH2を0.35とした雰囲気下で均熱処理を施した。なお、一次再結晶焼鈍後の鋼板について、板幅中心部からサンプルを採取し、実施例1と同様の方法でImax/Iminを求めたところ1.65であった。
次いで、MgOを主体とする焼鈍分離剤を鋼板表面に塗布、乾燥した後、さらに、二次再結晶させた後、1200℃×10時間の純化処理を行う仕上焼鈍を施した。仕上焼鈍の雰囲気は、純化処理する1200℃保定時はH2、二次再結晶を含む昇温時および降温時はN2とした。次いで、仕上焼鈍後の鋼板両面にコロイダルシリカを含有するリン酸マグネシウムを主成分とする絶縁張力コーティングを、鋼板片面当たり5g/m2の目付量で塗布、焼き付けた。
また、上記鉄損測定後の試験片について、X線回折装置を用いて、二次再結晶粒の結晶方位を、板幅方向、圧延方向ともに2mmピッチで全面にわたって測定し、ずれ角βの平均値[β]、および、ずれ角αが6.5°以下の結晶粒の面積分率Sα6.5およびずれ角βが2.5°以下の結晶粒の面積分率Sβ2.5を求めた。
また、上記鉄損測定後の試験片表面の絶縁被膜およびフォルステライト被膜を除去して結晶粒界を現出させた後、圧延方向に伸びる直線を幅方向に対して5mmピッチで描き、上記直線を横切る粒界の数を測定して、二次再結晶粒の圧延方向の平均長さ[L]を求めた。
上記の測定結果を表4に併記した。この表から、鋼スラブの成分、Imax/Imin、二次再結晶粒の圧延方向の平均長さ[L]および結晶方位([β]、Sα6.5、Sβ2.5)が本発明の条件を満たす方向性電磁鋼板は、いずれも鉄損特性に優れていることがわかる。
Claims (5)
- Siを2.5~5.0mass%およびMn:0.01~0.8mass%を含有し、残部がFeおよび不可避的不純物からなる成分組成を有し、鋼板の片面または両面に連続したまたは断続した線状の溝あるいは線状の歪領域が、圧延方向と交差する方向に、圧延方向の間隔dを1~10mmとして形成され、かつ、鋼板両表面にフォルステライト被膜と張力付与被膜が形成されてなる方向性電磁鋼板であって、
{110}<001>理想方位からの圧延面垂直方向を軸とするずれ角αの絶対値が6.5°未満である二次再結晶粒の鋼板表面に占める面積率Sα6.5が90%以上、
{110}<001>理想方位からの板幅方向を軸とするずれ角βの絶対値が2.5°未満である二次再結晶粒の鋼板表面に占める面積率Sβ2.5が75%以上であり、かつ、
二次再結晶粒の圧延方向の平均長さ[L](mm)と上記βの平均値[β](°)が下記(1)式および(2)式を満たすことを特徴とする方向性電磁鋼板。
15.63×[β]+[L]<44.06 ・・・(1)
[L]≦20 ・・・(2) - 上記成分組成に加えてさらに、Cr:0.01~0.50mass%、Cu:0.01~0.50mass%、P:0.005~0.50mass%、Ni:0.010~1.50mass%、Sb:0.005~0.50mass%、Sn:0.005~0.50mass%、Bi:0.005~0.50mass%、Mo:0.005~0.10mass%、B:0.0002~0.0025mass%、Te:0.0005~0.010mass%、Nb:0.0010~0.010mass%、V:0.001~0.010mass%およびTa:0.001~0.010mass%のうちから選ばれる1種または2種以上を含有することを特徴とする請求項1に記載の方向性電磁鋼板。
- 請求項1に記載の方向性電磁鋼板の製造方法であって、C:0.002~0.10mass%、Si:2.5~5.0mass%、Mn:0.01~0.8mass%、Al:0.010~0.050mass%およびN:0.003~0.020mass%を含有し、残部がFeおよび不可避的不純物からなる成分組成を有する鋼スラブを熱間圧延して熱延板とし、熱延板焼鈍を施した後または熱延板焼鈍を施すことなく、1回または中間焼鈍を挟む2回以上の冷間圧延により最終板厚の冷延板とし、一次再結晶焼鈍を施した後、鋼板表面に焼鈍分離剤を塗布し、仕上焼鈍を施し、張力付与被膜を被成する一連の工程からなる方向性電磁鋼板の製造方法において、
上記一次再結晶焼鈍の加熱過程における250~600℃の区間内のいずれかの温度Tで1~10秒間保持する保定処理を施した後、上記温度Tから700℃までを昇温速度80℃/s以上で加熱するとともに、一次再結晶焼鈍後の鋼板表面をグロー放電発光分析したときのSiの深さ方向の発光強度プロファイルにおける最大値Imaxと、該最大値Imaxより深い位置に現れる最小値Iminとの比(Imax/Imin)を1.5以上とし、さらに、
上記冷間圧延後のいずれかの工程で、鋼板の片面または両面に連続したまたは断続した線状の溝あるいは線状の歪領域を、圧延方向と交差する方向に圧延方向の間隔dを1~10mmとして形成することを特徴とする方向性電磁鋼板の製造方法。 - 上記鋼スラブは、上記成分組成に加えてさらに、Se:0.003~0.030mass%およびS:0.002~0.030mass%のうちから選ばれる1種または2種を含有することを特徴とする請求項3に記載の方向性電磁鋼板の製造方法。
- 上記鋼スラブは、上記成分組成に加えてさらに、Cr:0.01~0.50mass%、Cu:0.01~0.50mass%、P:0.005~0.50mass%、Ni:0.010~1.50mass%、Sb:0.005~0.50mass%、Sn:0.005~0.50mass%、Bi:0.005~0.50mass%、Mo:0.005~0.10mass%、B:0.0002~0.0025mass%、Te:0.0005~0.010mass%、Nb:0.0010~0.010mass%、V:0.001~0.010mass%およびTa:0.001~0.010mass%のうちから選ばれる1種または2種以上を含有することを特徴とする請求項3また4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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JPWO2016056501A1 (ja) | 2017-04-27 |
KR101959646B1 (ko) | 2019-03-18 |
CN107109552A (zh) | 2017-08-29 |
RU2674502C2 (ru) | 2018-12-11 |
US20220170131A1 (en) | 2022-06-02 |
JP6319605B2 (ja) | 2018-05-09 |
EP3205738B1 (en) | 2019-02-27 |
CN107109552B (zh) | 2018-12-28 |
EP3205738A1 (en) | 2017-08-16 |
US20170298467A1 (en) | 2017-10-19 |
KR20170043658A (ko) | 2017-04-21 |
RU2017115765A (ru) | 2018-11-13 |
EP3205738A4 (en) | 2017-08-30 |
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