WO2019156220A1 - 方向性電磁鋼板 - Google Patents
方向性電磁鋼板 Download PDFInfo
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- WO2019156220A1 WO2019156220A1 PCT/JP2019/004656 JP2019004656W WO2019156220A1 WO 2019156220 A1 WO2019156220 A1 WO 2019156220A1 JP 2019004656 W JP2019004656 W JP 2019004656W WO 2019156220 A1 WO2019156220 A1 WO 2019156220A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K26/00—Working by laser beam, e.g. welding, cutting or boring
- B23K26/36—Removing material
- B23K26/362—Laser etching
- B23K26/364—Laser etching for making a groove or trench, e.g. for scribing a break initiation groove
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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
- C21D8/1277—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
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- 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
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
- C21D10/005—Modifying the physical properties by methods other than heat treatment or deformation by laser shock processing
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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
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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
- C22C38/002—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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- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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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- 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
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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
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- 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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
- C21D8/1216—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
- C21D8/1222—Hot rolling
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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
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- 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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- 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
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2202/00—Physical properties
- C22C2202/02—Magnetic
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
Definitions
- the present invention relates to a grain-oriented electrical steel sheet. This application claims priority based on Japanese Patent Application No. 2018-021104 for which it applied to Japan on February 8, 2018, and uses the content here.
- a grain-oriented electrical steel sheet is a steel sheet in which the orientation of crystal grains in the steel sheet is highly accumulated in the ⁇ 110 ⁇ ⁇ 001> orientation and the easy axis of magnetization is aligned in the longitudinal direction. Since the easy magnetization axes are aligned in the longitudinal direction, it refers to an electrical steel sheet having the characteristics of low iron loss and excellent magnetism.
- This grain-oriented electrical steel sheet has a structure in which a plurality of magnetic domains (striped magnetic domains) whose magnetization is oriented in the rolling direction are arranged with a domain wall in between, and many of these domain walls are 180 ° domain walls. The electromagnetic steel sheet is easily magnetized in the rolling direction.
- the magnetic flux density is high and the iron loss is low at a relatively small constant magnetizing force. Therefore, the grain-oriented electrical steel sheet is very excellent as a transformer core material.
- W17 / 50 [W / kg] is used as an index of iron loss.
- W17 / 50 is a value of iron loss generated in the grain-oriented electrical steel sheet when AC excitation is performed so that the maximum magnetic flux density is 1.7 T at a frequency of 50 Hz. If this W17 / 50 is reduced, a more efficient transformer can be manufactured.
- the grain-oriented electrical steel sheet is given a strain substantially perpendicular to the rolling direction (conveying direction) and at a constant period (a constant interval), the iron loss further decreases.
- a reflux type magnetic domain whose magnetization is orthogonal to the rolling direction is formed by local strain, and the domain wall interval of the substantially rectangular stripe domain is narrowed by using the energy increment there (the width of the stripe domain is reduced). Smaller). Since the iron loss (W17 / 50) has a positive correlation with the interval between the 180 ° domain walls, the iron loss is reduced by this principle.
- the method for reducing the iron loss of the grain-oriented electrical steel sheet using the local strain is a strain relief annealing (for about 2 hours at 800 ° C.) to eliminate the deterioration of the iron loss due to the processing strain of the wound core. The effect is lost by annealing.
- a method of introducing periodic grooves in a direction crossing the rolling direction is generally used as a method in which the effect of reducing iron loss is not lost even when strain relief annealing is performed.
- Patent Document 1 discloses that the iron loss is improved by introducing linear wrinkles into the grain-oriented electrical steel sheet before finish annealing.
- Patent Document 2 discloses that the iron loss is reduced by forming grooves on the surface of the electromagnetic steel sheet with high power efficiency by irradiating a continuous wave laser beam having a limited wavelength.
- the electromagnetic steel sheet is a very hard steel sheet containing about 3% Si, and thus the tooth mold is likely to be worn and damaged. Since the groove depth varies when the tooth mold is worn, the iron loss improvement effect becomes non-uniform.
- the method by laser irradiation (referred to as a laser method) has an advantage that high-speed grooving can be performed by a high-power density focused laser beam. Further, since the laser method is non-contact processing, stable and uniform groove processing can be performed by controlling the laser power and the like.
- a CO 2 laser that can easily obtain a relatively high power is used as a laser light source.
- the wavelength of the CO 2 laser is in a 9 to 11 ⁇ m band, and the laser light having this wavelength is processed at a processing point. It is greatly absorbed by metal vapor and plasma generated at (processing position). Therefore, the reaching power of the laser beam to the steel sheet surface is reduced and the processing efficiency is lowered. Further, the plasma and metal vapor heated and expanded by absorbing the laser beam act as a secondary heat source and melt around the end (shoulder) of the groove. , The increase in melt projections) is worsened.
- the grain-oriented electrical steel sheet according to one aspect of the present invention is a grain-oriented electrical steel sheet having a steel plate surface provided with a groove, and is an area that extends from the groove width direction end of the groove toward the outside in the groove width direction.
- the surface protrusions protruding from the surface of the steel sheet extend along the groove longitudinal direction of the groove, and the average protrusion height of the surface protrusion is more than 5 ⁇ m and not more than 10 ⁇ m.
- the total length in the groove longitudinal direction of the portion having a height of 50% or more of the height of the peak point appearing in the contour line of the surface protrusion is the surface. It is 30% or more of the total length of the protrusion in the groove longitudinal direction.
- a magnetic domain control effect greater than the groove introduction type magnetic domain control effect is obtained due to the linear elastic stress caused by the protrusions of the directional electrical steel sheet when the directional electrical steel sheet is laminated in the manufacture of the iron core. Therefore, the iron loss of the iron core can be reduced.
- the grain-oriented electrical steel sheet according to the present embodiment (hereinafter abbreviated as the present magnetic steel sheet) is a grain-oriented electrical steel sheet having a steel sheet surface provided with grooves.
- the present magnetic steel sheet surface protrusions that bulge from the steel sheet surface extend in the groove longitudinal direction of the groove in a region that extends from the groove width direction end of the groove toward the outer side in the groove width direction.
- the average protrusion height of the surface protrusion is more than 5 ⁇ m and not more than 10 ⁇ m.
- a portion having a height of 50% or more of the height of the peak point appearing in the contour line of the surface protrusion when the surface protrusion is seen in a cross section including the groove longitudinal direction and the normal direction of the steel sheet surface The total length in the groove longitudinal direction is 30% or more of the total length of the surface protrusions in the groove longitudinal direction.
- the laser beam is absorbed on the surface of the steel sheet, the metal (base metal) of the steel sheet melts and fine molten droplets scatter, or the base metal on the surface of the steel sheet heated to the boiling point evaporates. As a result, a groove is formed.
- the melt on the surface of the steel plate is scattered by high-temperature metal vapor or plasma pressure at the processing point (laser beam irradiation point).
- the melt cannot be completely scattered, and the melt adheres to the periphery of the formed groove and surface protrusions (protrusions, melt protrusions, etc.) are generated. .
- a region that protrudes from the end of the groove width direction toward the outside in the groove width direction (periphery of the groove) is 20 ⁇ m or more that protrudes from the steel plate surface.
- Surface protrusions (protrusions, melted protrusions, etc.) having a height of approximately 40% were observed in the magnetic measurement (pressed Epstein measurement) with a compressive force applied to the steel sheet surface, leading to practical use. There wasn't.
- the groove width of the groove formed on the surface of the steel sheet is small, so that the occurrence of protrusions at the focal position can be substantially suppressed.
- the distance between the surface and the laser irradiation device varies and enters a defocused state, the occurrence of protrusions on the surface of the steel sheet becomes significant.
- the groove-introducing SRA-resistant magnetic domain control technology using a laser when the laser is out of focus, the protrusions generated in the form of rising from the steel sheet surface at the periphery of the groove become large.
- This protrusion may cause a short-circuit between layers, an increase in core loss due to stress acting when forming the laminated core, and a reduction in laminated space factor.
- SRA magnetic domain control by laser groove formation if the protrusions around the groove due to laser groove formation are too large, iron loss deterioration is caused by local elastic deformation in the electromagnetic steel sheet due to the steel sheet surface compression force when the iron core is laminated. It is thought to occur.
- the present inventors are similar to the laser magnetic domain control of strain introduction type in the grain-oriented electrical steel sheet at the time of forming the laminated iron core.
- the average protrusion height of the surface protrusion is more than 5 ⁇ m and not more than 10 ⁇ m.
- Condition 2 When the surface protrusion is viewed in a cross section including the groove longitudinal direction and the normal direction of the steel sheet surface, the groove length of the portion having a height of 50% or more of the peak point height appearing on the contour line of the surface protrusion The total length in the direction is 30% or more of the total length in the groove longitudinal direction of the surface protrusion.
- the magnetic steel sheet has a base steel plate, and may have a coating on the surface of the base steel plate as necessary.
- the coating include a glass coating and a tension insulating coating.
- the base steel plate is a steel plate in which the orientation of crystal grains in the base steel plate is highly accumulated in the ⁇ 110 ⁇ ⁇ 001> orientation, and has excellent magnetic properties in the rolling direction.
- the chemical composition of the mother steel sheet is not particularly limited, and can be appropriately selected from chemical compositions known as grain-oriented electrical steel sheets.
- the chemical composition of the mother steel plate is not limited thereto.
- the base steel plate has a chemical composition of mass%, Si: 0.8% to 7%, C: more than 0% and 0.085% or less, acid-soluble Al: 0% to 0.065%, N: 0 % To 0.012%, Mn: 0% to 1%, Cr: 0% to 0.3%, Cu: 0% to 0.4%, P: 0% to 0.5%, Sn: 0% to 0.3%, Sb: 0% to 0.3%, Ni: 0% to 1%, S: 0% to 0.015%, Se: 0% to 0.015%, with the balance being Fe and It is preferable to consist of impurities.
- the chemical composition of the mother steel plate is a preferable chemical component for controlling the Goss texture in which the crystal orientation is accumulated in the ⁇ 110 ⁇ ⁇ 001> orientation.
- Si and C are basic elements
- acid-soluble Al, N, Mn, Cr, Cu, P, Sn, Sb, Ni, S, and Se are selective elements. Since these selective elements may be contained according to the purpose, there is no need to limit the lower limit value, and it may not be contained substantially. Moreover, even if these selective elements are contained as impurities, the effects of the present invention are not impaired.
- the balance of the basic element and the selective element is composed of Fe and impurities.
- the “impurity” means an element that is inevitably mixed from ore as a raw material, scrap, or a manufacturing environment when the mother steel plate is industrially manufactured.
- grain oriented electrical steel sheets undergo purification annealing during secondary recrystallization.
- the inhibitor forming elements are discharged out of the system.
- the decrease in the concentration is remarkable, and it becomes 50 ppm or less.
- the purification annealing is sufficiently performed, it reaches a level that cannot be detected by general analysis (1 ppm or less).
- the chemical composition of the mother steel plate may be measured using ICP-AES (Inductively Coupled Plasma-Atomic Emission Spectrometry). Specifically, for example, a 35 mm square test piece is obtained from the center position of the mother steel plate after removal of the coating, and the condition is based on a calibration curve prepared in advance by ICPS-8100 manufactured by Shimadzu Corporation (measurement device). It can be specified by measuring. C and S may be measured using a combustion-infrared absorption method, and N may be measured using an inert gas melting-thermal conductivity method.
- the chemical component of the base steel plate is a component obtained by analyzing a component of a steel plate obtained by removing a glass coating and a coating containing phosphorus described below from a grain-oriented electrical steel plate by a method described below.
- the manufacturing method of a base steel plate is not specifically limited, The manufacturing method of a conventionally well-known grain-oriented electrical steel plate can be selected suitably.
- the production method for example, after C is 0.04 to 0.1% by mass, and the others are subjected to hot rolling by heating a slab having the above chemical composition of the base steel plate to 1000 ° C. or more Then, hot-rolled sheet annealing is performed as necessary, and then cold-rolled steel sheet is formed by cold rolling at least once with one or more intermediate annealings, and the cold-rolled steel sheet is 700, for example, in a wet hydrogen-inert gas atmosphere. Examples include a method of heating to ⁇ 900 ° C.
- the thickness of the mother steel plate is not particularly limited, but may be 0.10 mm or more and 0.50 mm or less, or 0.15 mm or more and 0.35 mm or less.
- glass coating examples include a coating having at least one oxide selected from forsterite (Mg 2 SiO 4), spinel (MgAl 2 O 4), and cordierite (Mg 2 Al 4 Si 5 O 16).
- the method for forming the glass coating is not particularly limited, and can be appropriately selected from known methods.
- a method of performing the finish annealing after applying an annealing separator mainly composed of magnesia (MgO) to the cold-rolled steel plate can be mentioned.
- the annealing separator has an effect of suppressing sticking between steel plates during finish annealing.
- finish annealing is performed by applying an annealing separator containing magnesia
- a glass coating containing forsterite (Mg2SiO4) is formed on the surface of the base steel plate by reacting with silica contained in the base steel plate.
- the film thickness of the glass coating is not particularly limited, but may be 0.5 ⁇ m or more and 3 ⁇ m or less.
- FIG. 1 is a plan view schematically showing an example of a groove pattern provided on the steel sheet surface of the electromagnetic steel sheet.
- FIG. 2 is a schematic view of a groove (for example, the groove 11) and surface protrusions existing in the periphery thereof in a cross section perpendicular to the groove longitudinal direction.
- FIG. 3 is a schematic view of the surface protrusions present on the periphery of the groove (for example, the groove 11) in a cross section including the groove longitudinal direction and the normal direction of the steel sheet surface.
- the rolling direction of the electromagnetic steel sheet 1 is the X-axis direction
- the width direction of the electromagnetic steel sheet 1 (the direction perpendicular to the rolling direction in the same plane)
- the Y-axis direction is the direction perpendicular to the rolling direction in the same plane
- the electromagnetic steel sheet 1 The plate thickness direction (direction orthogonal to the XY plane, that is, the normal direction of the steel plate surface) is defined as the Z-axis direction.
- a linear groove 10 and an intermittent line-shaped groove 11 are provided on the steel plate surface (surface of the mother steel plate) so as to extend along the plate width direction Y.
- the longitudinal direction of the grooves 10 and 11 coincides with the plate width direction Y.
- the grooves 10 and 11 need only be provided so as to intersect the rolling direction X, and the groove longitudinal direction and the rolling direction X do not necessarily have to be orthogonal to each other. That is, the groove longitudinal direction and the plate width direction Y do not have to coincide.
- surface protrusions 12 protruding from the steel plate surface extend in the peripheral portion 100 of the groove 11 along the groove longitudinal direction
- the steel plate surface Surface protrusions 13 protruding from the reference plane BL
- the groove width direction of the groove 11 coincides with the rolling direction X.
- a region (region between a and b in FIG. 2) that extends from the groove width direction one end portion a of the groove 11 toward the outer side in the groove width direction is defined as the peripheral portion 100.
- the groove width direction one end portion a of the groove 11 and the groove width direction other end portion a ′ of the groove 11 are the intersections of the contour line (cross-sectional curve) of the groove 11 and the reference plane BL, respectively. is there.
- Point b is an intersection of the contour line (cross-sectional curve) of the surface protrusion 12 and the reference plane BL, and is a point away from the groove width direction one end a to the groove width direction outer side.
- Point b ′ is an intersection of the contour line (cross-sectional curve) of the surface protrusion 13 and the reference plane BL, and is a point away from the other end portion a ′ in the groove width direction to the outside in the groove width direction.
- the non-grooved region (non-grooved surface) of the grain-oriented electrical steel sheet 1 is set to the reference plane BL (including the reference height and the surface of the steel sheet before groove formation) in the thickness direction. ing.
- the reference plane BL including the reference height and the surface of the steel sheet before groove formation
- the groove width W of the groove 11 is a linear distance between the groove width direction one end a and the groove width direction other end a ′.
- the groove depth D of the groove 11 is the depth from the reference plane BL to the groove bottom (distance in the plate thickness direction Z).
- a point on the contour line of the groove 11 and present at the deepest position in the thickness direction Z is defined as a groove bottom.
- the projection height T12 of the surface projection 12 is the height (distance in the plate thickness direction Z) from the reference plane BL to the tip of the surface projection 12.
- the protrusion height T13 of the surface protrusion 13 is the height (distance in the plate thickness direction Z) from the reference surface BL to the tip of the surface protrusion 13.
- the protrusion width of the surface protrusion 12 is a linear distance between the groove width direction one end a and the point b.
- the protrusion width of the surface protrusion 13 is a linear distance between the groove width direction other end a ′ and the point b ′. For various dimensions, a statistically sufficient number of measurements (for example, 50 measurements) are performed.
- grooves having a predetermined length extending in a direction intersecting the rolling direction X by a heat source such as a laser are formed at predetermined intervals on the surface of the electromagnetic steel sheet 1.
- the direction intersecting with the rolling direction X includes a direction orthogonal to the rolling direction X in the XY plane (that is, the plate width direction Y), and between this plate width direction Y and the groove longitudinal direction.
- the angle may be within a range of ⁇ 45 °, or may be within a range of ⁇ 30 °.
- the shape of the groove may be a linear shape extending in the plate width direction Y when the electromagnetic steel sheet 1 is viewed in plan, or may be an intermittent line shape.
- the linear shape may be a rectangular shape, an elliptical shape or the like when enlarged and observed.
- the interval between adjacent grooves in the plate width direction Y may be 1 ⁇ m to 1000 ⁇ m.
- the interval between adjacent grooves in the rolling direction X may be 1 to 10 mm, 3 to 6 mm, or 4 to 5 mm.
- channel is the 2nd nearest distance from the edge part (peripheral part) of the 1st groove
- the average groove depth of the electrical steel sheet 1 may be 8 to 30 ⁇ m or 15 to 25 ⁇ m.
- the average groove depth is an average value of the measured values of the groove depth D of 50 grooves for the grooves formed on the steel plate surface.
- the measuring method of the groove depth D is as follows. First, a sample is taken from the steel plate to be measured so that a cross section perpendicular to the groove longitudinal direction is exposed. By polishing the cross section of the sample, a cross section including the groove and its peripheral portion as shown in FIG. 2 appears, and then the cross section is observed with an optical microscope or a scanning microscope to obtain a groove depth D ( For example, the linear distance from the reference plane BL to the groove bottom in FIG. 2 is measured. Such groove depth D is measured for each of 50 locations of the steel sheet to be measured. The average groove depth is a value obtained by averaging the measurement results of these 50 groove depths D.
- the average groove width of the groove width W may be 1 to 200 ⁇ m.
- the average groove width is an average value of the measured values of the groove width W of 50 grooves with respect to the grooves formed on the steel plate surface.
- the method for measuring the groove width W is as follows. First, a sample is taken from the steel plate to be measured so that a cross section perpendicular to the groove longitudinal direction is exposed. By polishing the cross section of the sample, a cross section including the groove and its peripheral portion as shown in FIG. 2 is revealed, and then the cross section is observed with an optical microscope or a scanning microscope to obtain a groove width W (for example, The linear distance between aa ′ in FIG. 2 is measured. Such a groove width W is measured for each of 50 locations of the steel plate to be measured. The average groove width is a value obtained by averaging the measurement results of these 50 groove widths W.
- the average protrusion height of the surface protrusion is more than 5 ⁇ m and not more than 10 ⁇ m.
- the average protrusion height of the surface protrusions is preferably 5.8 ⁇ m or more, and more preferably 6.0 ⁇ m or more. If the average protrusion height of the surface protrusions exceeds 10 ⁇ m, it is not preferable because the tendency for the insulation between the laminated steel sheets to deteriorate increases. Therefore, the upper limit of the average protrusion height of the surface protrusion is 10 ⁇ m.
- the average protrusion height of the surface protrusion is preferably 7.3 ⁇ m or less.
- the average protrusion height of the surface protrusions is an average value of measured values of 50 protrusion heights (for example, T12 and T13 in FIG. 2) for the surface protrusions formed on the surface of the steel sheet.
- the method for measuring the height of the protrusion is as follows. First, a sample is taken from the steel plate to be measured so that a cross section perpendicular to the groove longitudinal direction is exposed. By polishing the cross section of the sample, a cross section including the groove and its peripheral portion as shown in FIG. 2 is revealed, and then the cross section is observed with an optical microscope or a scanning microscope to form a peripheral portion of the groove.
- the height of the existing surface protrusion (for example, T12 and T13 in FIG. 2) is measured. Such a projection height is measured for each of 50 locations of the steel plate to be measured.
- the average protrusion height is a value obtained by averaging the measurement results of these 50 protrusion heights.
- the shape of the surface projection is not particularly limited, and the shape of the projection with a pointed tip when the section of the grain-oriented electrical steel sheet cut along a predetermined direction (plate width direction, rolling direction, etc.) perpendicular to the steel plate surface is viewed from the front. It may be a bank with a flat tip.
- the average protrusion width of the surface protrusion is not particularly limited, but may be 1 to 10 ⁇ m.
- the average protrusion width is an average value of measured values of protrusion widths at 50 locations for protrusions formed on the steel sheet surface.
- the method for measuring the protrusion width is as follows. First, a sample is taken from the steel plate to be measured so that a cross section perpendicular to the groove longitudinal direction is exposed. By polishing the cross section of the sample, a cross section including the groove and its peripheral portion as shown in FIG.
- the protrusion width of the existing surface protrusion (for example, the linear distance between ab and the linear distance between a ′ and b ′ in FIG. 2) is measured.
- Such a protrusion width is measured at each of 50 locations of the steel plate to be measured.
- the average protrusion width is a value obtained by averaging the measurement results of these 50 protrusion widths.
- the measurement result obtained by the surface roughness meter uses a method in which a cross-section obtained by cutting a grain-oriented electrical steel sheet along the rolling direction perpendicular to the steel sheet surface is polished and observed with an optical microscope or a scanning microscope. If the measurement result is the same as this, the groove depth (groove depth dimension) can be determined from the length dimension of the groove in the thickness direction (distance from the reference surface to the tip of the groove). Good. Similarly, the protrusion height may be determined from the height dimension (distance in the plate thickness direction) from the reference surface to the tip of the surface protrusion.
- the surface protrusion 12 (or 13) is seen in a cross section including the groove longitudinal direction (plate width direction Y) and the plate thickness direction Z, the contour of the surface protrusion 12.
- the peak having the peak point P3 and the peak having the peak point P4 are 50% or more of the height of the peak point P3 existing at a higher position. It is connected gently in this area.
- the mountain having the peak point P3 and the mountain having the peak point P4 are regarded as one mountain, and the height of 50% or more of the height of the highest peak point P3 in this one mountain.
- the length in the longitudinal direction of the groove having the thickness is LP3. Since the peak points P1, P2, and P5 do not apply to the above case, the length in the groove longitudinal direction may be obtained for each peak point. That is, in the mountain having the peak point P1, the length in the groove longitudinal direction of a portion having a height of 50% or more of the height of the peak point P1 is LP1.
- the length in the groove longitudinal direction of the portion having a height of 50% or more of the height of the peak point P2 is defined as LP2.
- the length in the groove longitudinal direction of the portion having a height of 50% or more of the height of the peak point P5 is LP5.
- the ratio represented by (Lsum ⁇ 100) / L is defined as the protrusion continuity index. That is, in the electromagnetic steel sheet 1, the shape of the surface protrusion is controlled so that the protrusion continuity index is 30% or more.
- the protrusion continuity index satisfies the condition of 30% or more (the condition that the length Lsum is 30% or more of the length L).
- the iron loss reduction effect of the iron core is significantly increased.
- the protrusion continuity index is preferably 50% or more.
- the upper limit of the protrusion continuity index is not particularly limited. The upper limit of the protrusion continuity index is mathematically 100%, but it is difficult to actually set the protrusion continuity index to 100%.
- the method for measuring the protrusion continuity index is as follows. Using a device capable of measuring the three-dimensional shape of the steel plate surface to be measured, such as a laser microscope, the steel plate surface image including the groove portion is measured, and the protruding portion at a position higher than the reference surface BL is identified in the groove peripheral portion. A protrusion continuity index is obtained from the length extending to the groove portion at the contour line position indicating a value of 50% or more of the height value at the peak position of the continuous portion among the protrusion portions.
- a laser irradiation method (see Japanese Patent Application Laid-Open No. 6-57335 and International Publication No. 2016/171124) in which grooves are formed by irradiating a laser on the surface of the steel sheet is used.
- the laser output is 200 to 3000 W
- the focused spot diameter (diameter including 86% of the laser output) in the laser rolling direction is 10 to 100 ⁇ m
- the desired groove shape can be obtained by appropriately adjusting these laser irradiation conditions within the above range.
- a continuous-wave laser (wavelength capable of continuous oscillation) having a wavelength of 1.0 to 2.1 ⁇ m and high condensing property
- lasers include fiber lasers and thin disk solid-state lasers containing YAG.
- the laser beam having a wavelength range of 1.0 to 2.1 ⁇ m is difficult to be absorbed by metal ion plasma or metal vapor generated at a processing point.
- a continuous wave laser there is no iron loss improvement deterioration due to the gap between the holes in the point sequence groove, which is generated in the pulsed laser.
- a laser in which various laser media (excitation atoms) are doped in the core of a fiber that is an oscillation medium may be used.
- a fiber laser doped with Yb (yttrium) in the core has an oscillation wavelength of 1.07 to 1.08 ⁇ m
- a fiber laser doped with Er (erbium) in the core has an oscillation wavelength of 1.55 ⁇ m and Tm
- the oscillation wavelength is 1.70 to 2.10 ⁇ m.
- a YAG laser which is a high-power laser in the same wavelength range, has an oscillation wavelength of 1.06 ⁇ m. In the method using these fiber laser and YAG laser, the influence of laser absorption into plasma or metal vapor at the processing point is small.
- the diameter of the condensing spot may be 100 ⁇ m or less.
- the fiber laser can condense up to the same diameter as the core diameter, and a fiber laser having a core diameter of 100 ⁇ m or less is suitable for ensuring higher condensing performance.
- a solid-state laser such as a YAG laser
- a thin disk laser whose oscillation medium is a thin disk type crystal has a large crystal surface area and is easy to cool. Is less likely to occur, and it is possible to easily collect minute light of 100 ⁇ m or less. Note that the diameter of the focused spot and the groove width do not necessarily match.
- the surface of the steel plate may be irradiated with the laser beam by shifting (defocusing) the focal position of the laser beam in order to form a surface protrusion with a desired height.
- Defocusing may be set within a range of ⁇ 1.2 mm from the focal position.
- an assist gas such as air or an inert gas is sprayed onto a portion of the surface of the steel plate irradiated with the laser beam.
- an assist gas plays a role of removing components melted or evaporated from the steel sheet by laser irradiation.
- the assist gas By spraying the assist gas, the laser beam reaches the steel plate surface without being hindered by the above-described molten or evaporated components, so that the grooves are stably formed.
- the inventors have changed the flow rate of the assist gas at a flow rate of 0 to 100 (liters / minute) at a time interval of 0.02 to 0.2 msec, so that the average protrusion height of the surface protrusion is more than 5 ⁇ m and 10 ⁇ m. It has been found that a characteristic protrusion form of the electrical steel sheet 1 can be obtained which is as follows and the protrusion continuity index is 30% or more. For example, as disclosed in International Application Publication (WO2016 / 171130), a method of blowing assist gas at a constant flow rate set within a range of 10 to 1000 (liters / minute) is known.
- the method of increasing or decreasing the flow rate of the assist gas at a specific time interval is a novel method that is not known at all.
- the present inventors introduced linear elastic strain similar to the strain-introducing type laser magnetic domain control into the electromagnetic steel sheet during the formation of the laminated core.
- the iron core can be reduced in iron loss.
- the present inventors have intensively studied a method that can achieve both stable formation of grooves and low iron loss of the iron core, and as a result, have found a method for increasing and decreasing the flow rate of the assist gas at specific time intervals. It was.
- the flow rate of the assist gas may be varied between the minimum value A1 and the maximum value A2 included in the range of 0 to 100 (liters / minute).
- FIG. 4 is a schematic diagram showing an example of a manufacturing apparatus including a laser light source and a laser beam irradiation apparatus used in the present embodiment.
- the irradiation position of the laser beam irradiated on the grain-oriented electrical steel sheet (steel sheet) 1 is also shown.
- a fiber laser doped with Yb as a laser medium is used as a laser light source will be described.
- a steel plate 1 is a directional electromagnetic steel plate having a plate width of 1000 mm after secondary recrystallization, and a glass coating is formed on the surface of the ground iron.
- the steel plate 1 is passed at a constant speed in the line direction (rolling direction, transport direction) L at a line speed VL.
- the laser device 2 is a commercially available fiber laser having a maximum output of 2000 W.
- the fiber core is doped with Yb as a laser medium, and its oscillation wavelength is 1.07 to 1.08 ⁇ m.
- the diameter of the core is about 15 ⁇ m, and the laser oscillation mode of the output beam is a substantially basic Gaussian mode.
- the continuous wave (CW) laser beam output from the laser device 2 is transmitted through the optical fiber 3 and reaches the laser irradiation device 4.
- the laser irradiation device 4 includes a collimator 5, a icosahedron rotating polygon mirror 6, and an f ⁇ lens 7 having a focal length of 200 mm.
- the collimator 5 adjusts the diameter of the laser beam LB output from the transmission fiber 3.
- the rotating polygon mirror 6 deflects the laser beam LB to scan the steel plate 1 at a high speed in the substantially plate width direction C, and the f ⁇ lens 7 condenses the laser beam LB.
- the beam scanning speed V on the steel plate 1 can be adjusted in the range of 2 to 50 m / s by adjusting the rotation speed of the rotating polygon mirror 6.
- the scanning width of the focused beam on the steel plate 1 in the plate width direction is about 150 mm.
- the focused beam diameter (diameter including 86% of energy) d can be adjusted to 10 to 100 ⁇ m by changing the output beam diameter by the collimator 5.
- a focus mechanism (not shown) is disposed between the rotating polygon mirror 6 and the f ⁇ lens 7 having a focal length of 200 mm, and the distance between the f ⁇ lens 7 and the steel plate can be adjusted by this focus mechanism.
- a laser beam is scanned on the steel plate 1 by one surface of the rotating polygon mirror 6 to rotate, and one groove of a predetermined length (for example, the total length in the plate width direction) is formed in the substantially width direction on the steel plate 1.
- the interval between adjacent grooves in the L direction that is, the irradiation pitch PL in the rolling direction (conveying direction) can be changed by adjusting the line speed VL and the polygon rotation speed.
- PL irradiation pitch, groove interval
- the flow rate of the assist gas at the time of laser irradiation is controlled so as to fluctuate at a time interval of 0.02 to 0.2 msec at a flow rate of 0 to 100 (liters / minute).
- the steel plate 1 after the laser beam irradiation is coated with an insulating coating that imparts electrical insulation and tension to the surface by a coating apparatus (not shown).
- the present invention is not limited to the above embodiment.
- the above-described embodiment is an exemplification, and any device that has substantially the same configuration as the technical idea of the present invention and exhibits the same function and effect is included in the scope of the present invention.
- Examples 1 and 2 Comparative Examples 1 to 7
- the magnetic flux density B8 is 40 ⁇ m in the rolling direction and 100 ⁇ m in the sheet width direction.
- a linear groove having a width of about 50 ⁇ m and a depth of about 20 ⁇ m was formed at intervals of 5 mm in the rolling direction at a scanning speed of 20 m / s using a 3 kW fiber laser having a beam shape of 1 mm.
- Example 1 was a position close to 0.8 mm ( ⁇ 0.8 mm) from the focal position
- Example 2 was a position 0.9 mm far from the focal position (+0.9 mm). Is a focal position ( ⁇ 0 mm)
- Comparative Example 2 is a position near 0.4 mm ( ⁇ 0.4 mm)
- Comparative Example 3 is a position 0.5 mm away from the focal position (+0.5 mm)
- Comparative Example 4 is a focal point.
- Comparative Example 7 A position 1.1 mm away from the position (+1.1 mm), Comparative Example 5 is a position 1.2 mm closer to the focal position ( ⁇ 1.2 mm), Comparative Example 6 is a position 0.8 mm farther from the focal position (+0.8 mm), In Comparative Example 7, irradiation was performed at a position close to 1.1 mm ( ⁇ 1.1 mm) from the focal position. Furthermore, the assist gas flow rate was increased or decreased at specific time intervals under the conditions shown in Table 1 (minimum value A1 and maximum value A2 of the assist gas flow rate, and the variation time interval of the assist gas flow rate).
- Comparative Examples 1 to 5 show an example in which the minimum value A1 and the maximum value A2 of the assist gas flow rate are equal and the assist gas flow rate is not changed with time, that is, an example in which the assist gas flow rate is controlled to be constant.
- Table 1 shows the measurement results of the average groove width, average groove depth, average protrusion height, protrusion continuity index, magnetic flux density, and iron loss of the obtained grain-oriented electrical steel sheet.
- the iron loss of the grain-oriented electrical steel sheet was evaluated by a single plate measurement method after taking a single plate (W100 mm ⁇ L500 mm) and subjecting it to strain relief annealing at 800 ° C. for 2 hours.
- W17 / 50 is an iron loss value at 1.7 T / 50 Hz.
- the magnetic flux density B8 is defined by the magnetic flux density [T] generated when the magnetizing force H is 800 A / m.
- B8 is the magnetic flux density when the steel sheet is magnetized in the rolling direction.
- the projection continuity index using a device capable of measuring the three-dimensional shape of the steel plate surface to be measured, such as a laser microscope, the steel plate surface image including the groove portion is measured, and the protrusion at a position higher than the reference plane BL in the groove peripheral portion. After the portion was identified, the protrusion continuity index was measured from the length extending to the groove portion at the contour line position showing a value of 50% or more of the height value at the peak position of the continuous portion among the protrusion portions.
- the flow rate of the assist gas is controlled so as to fluctuate at a time interval of 0.02 to 0.2 msec at a flow rate of 0 to 100 (liters / minute).
- the average protrusion height and protrusion continuity index can be controlled within the scope of the present invention. That is, in Examples 1 and 2, the average protrusion height could be controlled in the range of more than 5 ⁇ m to 10 ⁇ m and the protrusion continuity index could be controlled to 30% or more.
- the flow rate of the assist gas was not appropriately controlled. As a result, one or both of the average protrusion height and the protrusion continuity index could not be controlled within the scope of the present invention.
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Abstract
Description
本願は、2018年2月8日に日本に出願された特願2018-021104号に基づき優先権を主張し、その内容をここに援用する。
この方向性電磁鋼板は、圧延方向に磁化が向いた磁区(縞状磁区)が、磁壁を挟んで複数配列した構造を有し、これら磁壁のうちの多くは、180°磁壁であり、方向性電磁鋼板は、圧延方向に磁化し易い。そのため、比較的小さな一定の磁化力において、磁束密度が高く、鉄損が低い。
したがって、方向性電磁鋼板は、トランスの鉄心材料として非常に優れている。
鉄損の指標には、一般にW17/50[W/kg]が用いられる。W17/50は、周波数50Hzにおいて最大磁束密度が1.7Tになるように交流励磁したときに、方向性電磁鋼板に発生する鉄損の値である。このW17/50を小さくすると、より効率の高いトランスが製造できる。
方向性電磁鋼板は、圧延方向(搬送方向)に略垂直、且つ一定周期(一定間隔)の歪みを付与すると、更に鉄損が低下する。この場合、局所的な歪みによって圧延方向と磁化が直交する還流型の磁区が形成され、そこでのエネルギー増分を源にして略長方形の縞状磁区の磁壁間隔が狭くなる(縞状磁区の幅が小さくなる)。鉄損(W17/50)は、180°磁壁の間隔に正の相関を有するため、この原理によって鉄損が低下する。ところで、この局所的な歪を利用する方向性電磁鋼板の鉄損の低下方法は、巻鉄心の加工歪による鉄損の悪化を解消するために実施する歪取り焼鈍(800℃で2時間程度の焼鈍)によって、その効果が失われてしまう。歪取り焼鈍を行った時でも、低鉄損化の効果が失われない方法としては、圧延方向と交差する方向に、周期的な溝を導入する方法が一般的に用いられる。
また、特許文献2には、波長を限定した連続波レーザビームを照射することにより、高パワー効率で電磁鋼板表面に溝を形成して鉄損を低減する旨開示されている。
本発明は上記実情に鑑みてなされたものであり、鉄心の鉄損を低減することができる方向性電磁鋼板を提供することを目的とする。
すなわち、本発明の一態様に係る方向性電磁鋼板は、溝が設けられた鋼板表面を有する方向性電磁鋼板であって、前記溝の溝幅方向端部から溝幅方向外側に向かって広がる領域において、前記鋼板表面から隆起する表面突起が前記溝の溝長手方向に沿って延在し、前記表面突起の平均突起高さが5μm超10μm以下であり、前記溝長手方向及び前記鋼板表面の法線方向を含む断面で前記表面突起をみた場合に、前記表面突起の輪郭線に現れるピーク点の高さの50%以上の高さを有する部分の前記溝長手方向の合計長さが、前記表面突起の前記溝長手方向の全長に対して30%以上の長さである。
本実施形態に係る方向性電磁鋼板(以下、本電磁鋼板と略称する)は、溝が設けられた鋼板表面を有する方向性電磁鋼板である。本電磁鋼板では、溝の溝幅方向端部から溝幅方向外側に向かって広がる領域において、鋼板表面から隆起する表面突起が溝の溝長手方向に沿って延在する。表面突起の平均突起高さは5μm超10μm以下である。
また、本電磁鋼板において、溝長手方向及び鋼板表面の法線方向を含む断面で表面突起をみた場合に、表面突起の輪郭線に現れるピーク点の高さの50%以上の高さを有する部分の溝長手方向の合計長さが、表面突起の溝長手方向の全長に対して30%以上の長さである。
CO2パルスレーザ(照射径大)を使用したレーザ溝形成試験では、溝の溝幅方向端部から溝幅方向外側に向かって広がる領域(溝の周辺部)に、鋼板表面から隆起する20μm以上の高さを有する表面突起(突起、溶融突起等)が発生し、鋼板表面に圧縮力をかけた磁気測定(加圧エプスタイン測定)では40%程度の鉄損劣化が見られ、実用化に至らなかった。
連続照射のレーザ(照射径小)を使用したレーザ溝形成技術では、鋼板表面に形成される溝の溝幅が小さいため、焦点位置での突起の発生は、ほぼ抑制することができるが、鋼板表面とレーザ照射装置との距離が変動して、デフォーカス状態になると、鋼板表面での突起の発生が顕著となる。
レーザでの溝導入型耐SRA磁区制御技術において、レーザのフォーカスがずれた場合、溝の周辺部において鋼板表面から隆起する形で発生する突起が大きくなる。この突起は、層間短絡、積層鉄心形成時に働く応力によるコア損失の増加、及び積層占積率の低下などを引き起こす原因となる可能性がある。
また、レーザ溝形成による耐SRA磁区制御においては、レーザ溝形成による溝の周辺部の突起が大き過ぎると鉄心積層時の鋼板表面圧縮力により電磁鋼板内の局部的な弾性変形によって鉄損劣化が生じると考えられる。
一方、本発明者らは、溝の周辺部に形成される表面突起の形態が以下の2つの条件を満たす場合に、積層鉄心形成時に方向性電磁鋼板内に歪導入型のレーザ磁区制御と同様な線状の弾性歪が導入され、より低鉄損化が図れることを見出した。
(条件1)表面突起の平均突起高さが5μm超10μm以下である。
(条件2)溝長手方向及び鋼板表面の法線方向を含む断面で表面突起をみた場合に、表面突起の輪郭線に現れるピーク点の高さの50%以上の高さを有する部分の溝長手方向の合計長さが、表面突起の溝長手方向の全長に対して30%以上の長さである。
以下、本電磁鋼板の各構成について説明する。
本電磁鋼板は、母鋼板を有し、必要に応じ、母鋼板の表面に被膜を有していてもよい。被膜としては、例えば、グラス被膜及び張力絶縁被膜などが挙げられる。
母鋼板の化学組成は、特に限定されず、方向性電磁鋼板として公知の化学組成の中から、適宜選択して用いることができる。以下、好ましい母鋼板の化学組成の一例について説明するが、母鋼板の化学組成はこれに限定されない。
なお、本実施形態において、「不純物」とは、母鋼板を工業的に製造する際に、原料としての鉱石、スクラップ、または製造環境等から不可避的に混入する元素を意味する。
また、方向性電磁鋼板では二次再結晶時に純化焼鈍を経ることが一般的である。純化焼鈍においてはインヒビター形成元素の系外への排出が起きる。特にN、Sについては濃度の低下が顕著で、50ppm以下になる。通常の純化焼鈍条件であれば、9ppm以下、さらには6ppm以下、純化焼鈍を十分に行えば、一般的な分析では検出できない程度(1ppm以下)にまで達する。
母鋼板の化学成分は、鋼の一般的な分析方法によって測定すればよい。例えば、母鋼板の化学成分は、ICP-AES(Inductively Coupled Plasma-Atomic Emission Spectrometry)を用いて測定すればよい。具体的には、例えば、被膜除去後の母鋼板の中央の位置から35mm角の試験片を取得し、島津製作所製ICPS-8100等(測定装置)により、予め作成した検量線に基づいた条件で測定することにより特定できる。なお、CおよびSは燃焼-赤外線吸収法を用い、Nは不活性ガス融解-熱伝導度法を用いて測定すればよい。なお、母鋼板の化学成分は、方向性電磁鋼板から後述の方法により後述のグラス被膜およびリンを含有する被膜等を除去した鋼板を母鋼板としてその成分を分析した成分である。
母鋼板の板厚は特に限定されないが、0.10mm以上0.50mm以下であってもよく、0.15mm以上0.35mm以下であってもよい。
グラス被膜の膜厚は特に限定されないが、0.5μm以上3μm以下であってもよい。
図1は、本電磁鋼板の鋼板表面に設けられた溝のパターン例を模式的に示す平面図である。
図2は、溝長手方向に直交する断面で溝(例えば溝11)とその周辺部に存在する表面突起をみた模式図である。
図3は、溝長手方向及び鋼板表面の法線方向を含む断面で溝(例えば溝11)の周辺部に存在する表面突起をみた模式図である。
なお、図1~図3において、本電磁鋼板1の圧延方向をX軸方向、本電磁鋼板1の板幅方向(同一平面内で圧延方向に直交する方向)をY軸方向、本電磁鋼板1の板厚方向(XY平面に直交する方向、すなわち鋼板表面の法線方向)をZ軸方向と定義する。
図1に示すように、線状の溝10及び、断続線状の溝11が、板幅方向Yに沿って延びるように鋼板表面(母鋼板の表面)に設けられている。言い換えれば、本実施形態において、溝10及び溝11の溝長手方向は、板幅方向Yと一致する。溝10及び溝11の周辺部12には、表面突起が存在する。
なお、溝10及び11は、圧延方向Xと交差するように設けられていればよく、必ずしも、溝長手方向と圧延方向Xとが直交している必要はない。すなわち、溝長手方向と板幅方向Yとが一致している必要はない。
ここで、溝11の溝幅方向一端部aから溝幅方向外側に向かって広がる領域(図2中のa-b間の領域)を周辺部100と定義する。また、溝11の溝幅方向他端部a’から溝幅方向外側に向かって広がる領域(図2中のa’-b’間の領域)を周辺部110と定義する。図2に示すように、溝11の溝幅方向一端部aと、溝11の溝幅方向他端部a’は、それぞれ、溝11の輪郭線(断面曲線)と基準面BLとの交点である。点bは、表面突起12の輪郭線(断面曲線)と基準面BLとの交点であって且つ溝幅方向一端部aから溝幅方向外側へ離れている点である。点b’は、表面突起13の輪郭線(断面曲線)と基準面BLとの交点であって且つ溝幅方向他端部a’から溝幅方向外側へ離れている点である。
また、図2においては、方向性電磁鋼板1の非溝形成領域(非溝形成処理面)を板厚方向における基準面BL(基準高さ、溝形成前の鋼板の表面を含む)に設定している。
図2に示すように、溝11は、溝幅方向一端部aから溝幅方向他端部a’までの区間において、基準面BLから溝形成処理により本電磁鋼板1の母鋼板の一部が除去されることで形成された領域である。
また、溝11の溝幅Wは、溝幅方向一端部aと溝幅方向他端部a’との間の直線距離である。そして、溝11の溝深さDは、基準面BLから溝底までの深さ(板厚方向Zの距離)である。溝11の輪郭線上の点であって且つ板厚方向Zの最も深い位置に存在する点を溝底とする。
また、表面突起12の突起高さT12は、基準面BLから表面突起12の先端までの高さ(板厚方向Zの距離)である。表面突起13の突起高さT13は、基準面BLから表面突起13の先端までの高さ(板厚方向Zの距離)である。
表面突起12の突起幅は、溝幅方向一端部aと点bとの間の直線距離である。表面突起13の突起幅は、溝幅方向他端部a’と点b’との間の直線距離である。
なお、各種の寸法については、統計的に十分な回数の測定(例えば、50回の測定)を行う。
本実施形態において、圧延方向Xと交差する方向とは、XY平面内において圧延方向Xに直交する方向(つまり板幅方向Y)を含んでおり、この板幅方向Yと溝長手方向との間の角度が±45°の範囲内であってもよく、または±30°の範囲内であってもよい。
溝の形状が断続線状である場合、板幅方向Yにおいて隣り合う溝の間隔は、1μm~1000μmであってもよい。
一方、圧延方向Xにおいて隣り合う溝の間隔は、1~10mmであってもよく、3~6mmであってもよく、または4~5mmであってもよい。
なお、本実施形態において溝の間隔とは、所定の方向(板幅方向Y、圧延方向X等)における1つ目の溝の端部(周辺部)から、最も近い距離にある2つ目の溝の端部(周辺部)までの最短距離である。
平均溝深さは、鋼板表面に形成された溝について、50か所の溝の溝深さDの測定値の平均値である。
溝深さDの測定方法は、以下の通りである。まず、被測定鋼板から、溝長手方向に直交する断面が露出するようにサンプルを採取する。そのサンプル断面を研磨することにより、図2に示すような溝とその周辺部を含む断面を現出させた後、その断面を光学顕微鏡または走査型顕微鏡で観察することにより、溝深さD(例えば図2中の基準面BLから溝底までの直線距離)を測定する。このような溝深さDを、被測定鋼板の50か所のそれぞれについて測定する。平均溝深さは、これら50個の溝深さDの測定結果を平均して得られる値である。
平均溝幅は、鋼板表面に形成された溝について、50か所の溝の溝幅Wの測定値の平均値である。
溝幅Wの測定方法は、以下の通りである。まず、被測定鋼板から、溝長手方向に直交する断面が露出するようにサンプルを採取する。そのサンプル断面を研磨することにより、図2に示すような溝とその周辺部を含む断面を現出させた後、その断面を光学顕微鏡または走査型顕微鏡で観察することにより、溝幅W(例えば図2中のa-a’間の直線距離)を測定する。このような溝幅Wを、被測定鋼板の50か所のそれぞれについて測定する。平均溝幅は、これら50個の溝幅Wの測定結果を平均して得られる値である。
表面突起の平均突起高さが10μmを超えると、積層された鋼板間の絶縁性が劣化する傾向が強まるので好ましくない。従って、表面突起の平均突起高さの上限は10μmである。表面突起の平均突起高さは7.3μm以下であることが好ましい。
表面突起の平均突起高さとは、鋼板表面に形成された表面突起について、50か所の突起高さ(例えば図2中のT12及びT13など)の測定値の平均値である。
突起高さの測定方法は、以下の通りである。まず、被測定鋼板から、溝長手方向に直交する断面が露出するようにサンプルを採取する。そのサンプル断面を研磨することにより、図2に示すような溝とその周辺部を含む断面を現出させた後、その断面を光学顕微鏡または走査型顕微鏡で観察することにより、溝の周辺部に存在する表面突起の突起高さ(例えば図2中のT12及びT13など)を測定する。このような突起高さを、被測定鋼板の50か所のそれぞれについて測定する。平均突起高さは、これら50個の突起高さの測定結果を平均して得られる値である。
表面突起の形状は特に限定されず、方向性電磁鋼板を鋼板面に垂直に所定の方向(板幅方向、圧延方向等)に沿って切断した断面を正面視した時に、先端が尖った突起状であってもよく、先端が平坦な土手状であってもよい。
上記のように、(Lsum×100)/Lで表される比率を突起連続性指標と定義する。すなわち、本電磁鋼板1において、突起連続性指標が30%以上となるように表面突起の形態が制御されている。
レーザ顕微鏡等、被測定鋼板面の三次元形状を測定できる装置を用いて、溝部を含む鋼板面画像を測定して、溝周辺部で基準面BLより高い位置の突起部分を同定する。この突起部分の内、連続する部分のピーク位置での高さ値の50%以上の値を示す等高線位置の溝部に延伸する長さから突起連続性指標を求める。
レーザ照射法の場合の照射条件としては、一般的には、レーザ出力を200~3000Wに、レーザの圧延方向における集光スポット径(レーザ出力の86%を含む直径)を10~100μmに、レーザの板幅方向における集光スポット径を10~1000μmに、レーザ走査速度を5~100m/sに、レーザ走査ピッチ(間隔)を2~10mmに設定することが好ましい。所望の溝形状は、これらのレーザ照射条件を上記範囲で適宜調整することで得ることが出来る。
例えば、このようなレーザとして、ファイバレーザ、YAGを含む薄ディスク型固体レーザ等が挙げられる。上記1.0~2.1μmの波長域のレーザ光は、加工点で発生する金属イオンのプラズマや金属蒸気に吸収されにくい。さらに、連続波レーザを用いることにより、パルス発振レーザで生じる、点列溝の穴間のギャップによる鉄損改善劣化もない。
また、同様の波長域の高出力レーザであるYAGレーザでは、発振波長が1.06μmである。これらのファイバレーザ及びYAGレーザを使用する方法では、加工点でのプラズマ或いは金属蒸気へのレーザの吸収の影響が少ない。
ファイバレーザは、コア直径と同程度まで集光可能であり、より高い集光性を確保するためには、100μm以下のコア径を有するファイバレーザが適する。
また、YAGレーザ等の固体レーザにおいて、発振媒体が薄ディスク型の結晶である薄ディスクレーザでは、結晶の表面積が大きく冷却が容易であるため、高出力動作においても結晶の熱歪みによる集光性の劣化が生じにくく、100μm以下の微小集光も容易に行える。
なお、この集光スポットの径と溝幅とは、必ずしも一致しない。例えば、パワー密度が大きく、ビーム走査速度Vが小さいと、溝幅が、集光スポットの径よりも大きくなる。
また、上記のような精度の高いレーザを用いる場合、所望の高さの表面突起形成のために、レーザビームの焦点位置をずらして(デフォーカスして)、鋼板表面にレーザを照射してもよい。デフォーカスは、焦点位置から±1.2mmの範囲で設定してもよい。
以上のことから、集光ビーム径等を制御して、溝断面積、すなわち、溶融物の除去量を制御すること等により、突起を発生させる成分量を制御でき、突起高さを制御することができる。
本発明者らは、アシストガスの流量を0~100(リットル/分)間の流量で0.02~0.2msecの時間間隔で変動させることにより、表面突起の平均突起高さが5μm超10μm以下であり、且つ突起連続性指標が30%以上であるという本電磁鋼板1の特徴的な突起形態が得られることを見出した。例えば国際出願公報(WO2016/171130)に開示されているように、アシストガスを10~1000(リットル/分)の範囲内で設定された一定の流量で吹き付ける方法は知られているが、上記のように、アシストガスの流量を特定の時間間隔で増減させる方法は全く知られていない新規の方法である。
本発明者らは、特定の条件を満たす表面突起を鋼板表面に形成することにより、積層鉄心形成時に電磁鋼板内に歪導入型のレーザ磁区制御と同様な線状の弾性歪が導入され、その結果、鉄心の低鉄損化を実現できることを見出した。この知見を基に、本発明者らは、溝の安定的な形成と鉄心の低鉄損化を両立できる方法を鋭意研究した結果、アシストガスの流量を特定の時間間隔で増減させる方法を見出したのである。
なお、アシストガスの流量は、0~100(リットル/分)の範囲内に含まれる最小値A1と最大値A2との間で変動させればよい。
図4は、本実施形態で用いるレーザ光源及びレーザビーム照射装置を備える製造装置の一例を示す模式図である。なお、この図4には、方向性電磁鋼板(鋼板)1に照射されるレーザ光の照射位置についても示されている。レーザ媒質としてYbがドープされたファイバレーザをレーザ光源として用いた例を説明する。
図4において、鋼板1は、二次再結晶後の板幅1000mmの方向性電磁鋼板であり、地鉄表面にグラス被膜が形成されている。鋼板1は、ライン速度VLでライン方向(圧延方向、搬送方向)Lに一定速度で通板される。
コアの直径は、約15μmであり、出力ビームのレーザ発振モードは、略基本ガウスモードである。
レーザ装置2から出力された連続波(CW)のレーザ光は、光ファイバ3を伝送され、レーザ照射装置4に到達する。
このレーザ照射装置4は、コリメータ5と、20面体の回転ポリゴンミラー6と、焦点距離200mmのfθレンズ7とを備える。
コリメータ5は、伝送ファイバ3から出力したレーザビームLBの直径を調整する。
また、回転ポリゴンミラー6は、レーザビームLBを偏向させて鋼板1上を高速で略板幅方向Cに走査し、fθレンズ7は、このレーザビームLBを集光する。
鋼板1上における集光ビームの板幅方向の走査幅は、約150mmである。
集光ビーム径(エネルギーの86%が含まれる直径)dを、コリメータ5による出力ビーム径の変更によって10~100μmに調整できる。
なお、図示されないフォーカス機構を、回転ポリゴンミラー6と焦点距離200mmのfθレンズ7との間に配置しており、このフォーカス機構によってfθレンズ7と鋼板との距離が調整できる。回転する回転ポリゴンミラー6の1面によりレーザビームが鋼板1上に走査されて、鋼板1上に所定の長さ(例えば、板幅方向の全長)の1本の溝が略幅方向に形成される。L方向に隣接する溝の間隔、すなわち圧延方向(搬送方向)の照射ピッチPLは、ライン速度VL及びポリゴン回転速度の調整により変更可能である。
また、上述したように、レーザ照射時のアシストガスの流量は、0~100(リットル/分)間の流量で0.02~0.2msecの時間間隔で変動するように制御される。
レーザビーム照射後の鋼板1には、図示されないコーティング装置により表面に電気的絶縁及び張力を付与する絶縁被膜コーティングを施す。
800A/mでの磁束密度B8の値が1.94Tである高磁束密度の方向性電磁鋼板(板厚0.23mm)に対して、鋼板の圧延方向に40μm、板幅方向に100μmの楕円形状のビーム形状で3kWのファイバレーザを用いて20m/sの走査速度で圧延方向に5mm間隔で幅約50μm、深さ約20μmの線状の溝を形成した。
その際、レーザビームが鋼板面で、実施例1は焦点位置から0.8mm近い位置(-0.8mm)、実施例2は焦点位置から0.9mm遠い位置(+0.9mm)、比較例1は焦点位置(±0mm)、比較例2は焦点位置から0.4mm近い位置(-0.4mm)、比較例3は焦点位置から0.5mm遠い位置(+0.5mm)、比較例4は焦点位置から1.1mm遠い位置(+1.1mm)、比較例5は焦点位置から1.2mm近い位置(-1.2mm)、比較例6は焦点位置から0.8mm遠い位置(+0.8mm)、比較例7は焦点位置から1.1mm近い位置(-1.1mm)での照射を行った。
さらに、表1に示す条件(アシストガス流量の最小値A1及び最大値A2、アシストガス流量の変動時間間隔)で、アシストガスの流量を特定の時間間隔で増減させた。なお、比較例1~5は、アシストガス流量の最小値A1と最大値A2が等しく、且つアシストガス流量を時間的に変動させない例、すなわち、アシストガスの流量を一定に制御する例を示している。
得られた方向性電磁鋼板の平均溝幅、平均溝深さ、平均突起高さ、突起連続性指標、磁束密度、及び、鉄損の測定結果を表1に示す。
なお、方向性電磁鋼板の鉄損は、単板(W100mm×L500mm)を採取して、800℃で2時間の歪取焼鈍を施した後に、単板測定法により評価した。また、W17/50は、1.7T/50Hzのときの鉄損値である。
さらに、磁束密度B8は、磁化力Hが800A/mにおいて発生する磁束密度[T]で定義される。特に、方向性電磁鋼板の場合、B8は、鋼板が圧延方向に磁化したときの磁束密度である。B8が高いほど鋼板の結晶方位性が高く(結晶配向性が大きく)、一般に鉄損も低い。
突起連続性指標については、レーザ顕微鏡等、被測定鋼板面の三次元形状を測定できる装置を用いて、溝部を含む鋼板面画像を測定して、溝周辺部で基準面BLより高い位置の突起部分を同定した後、この突起部分の内、連続する部分のピーク位置での高さ値の50%以上の値を示す等高線位置の溝部に延伸する長さから突起連続性指標を測定した。
これらの巻鉄心に一次巻線(励磁巻線)と二次巻線(サーチコイル)を巻き、それぞれのコア鉄損を電力計で測定した。測定結果を表2に示す。
ただし、表1に示すように、電磁鋼板単体でみたときに、実施例と比較例とで、磁束密度及び鉄損に大差がないことがわかる。つまり、平均突起高さと突起連続性指標は、電磁鋼板単体の磁束密度及び鉄損に大きく影響しない。
2 レーザ装置
3 光ファイバ(伝送ファイバ)
4 レーザ照射装置
5 コリメータ
6 ポリゴンミラー(回転ポリゴンミラー)
7 fθレンズ
10 溝(線状)
11 溝(断続線状)
12 表面突起
13 表面突起
100 周辺部
110 周辺部
Claims (1)
- 溝が設けられた鋼板表面を有する方向性電磁鋼板であって、
前記溝の溝幅方向端部から溝幅方向外側に向かって広がる領域において、前記鋼板表面から隆起する表面突起が前記溝の溝長手方向に沿って延在し、
前記表面突起の平均突起高さが5μm超10μm以下であり、
前記溝長手方向及び前記鋼板表面の法線方向を含む断面で前記表面突起をみた場合に、前記表面突起の輪郭線に現れるピーク点の高さの50%以上の高さを有する部分の前記溝長手方向の合計長さが、前記表面突起の前記溝長手方向の全長に対して30%以上の長さである
ことを特徴とする方向性電磁鋼板。
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CN201980011736.XA CN111684087B (zh) | 2018-02-08 | 2019-02-08 | 方向性电磁钢板 |
US16/961,286 US11551838B2 (en) | 2018-02-08 | 2019-02-08 | Grain-oriented electrical steel sheet |
RU2020129234A RU2749826C1 (ru) | 2018-02-08 | 2019-02-08 | Лист электротехнической анизотропной стали |
JP2019571169A JP7010311B2 (ja) | 2018-02-08 | 2019-02-08 | 方向性電磁鋼板 |
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EP19751084.5A EP3751014B1 (en) | 2018-02-08 | 2019-02-08 | Grain-oriented electrical steel sheet |
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CN117415448A (zh) * | 2022-07-11 | 2024-01-19 | 宝山钢铁股份有限公司 | 一种用于低铁损取向硅钢板的激光刻痕方法及取向硅钢板 |
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