WO2021020026A1 - 方向性電磁鋼板 - Google Patents
方向性電磁鋼板 Download PDFInfo
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- WO2021020026A1 WO2021020026A1 PCT/JP2020/026181 JP2020026181W WO2021020026A1 WO 2021020026 A1 WO2021020026 A1 WO 2021020026A1 JP 2020026181 W JP2020026181 W JP 2020026181W WO 2021020026 A1 WO2021020026 A1 WO 2021020026A1
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C21D8/1294—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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- 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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- 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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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1277—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular surface treatment
- C21D8/1288—Application of a tension-inducing coating
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- 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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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- 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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- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
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- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
- C25F3/00—Electrolytic etching or polishing
- C25F3/02—Etching
- C25F3/06—Etching of iron or steel
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- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25F—PROCESSES FOR THE ELECTROLYTIC REMOVAL OF MATERIALS FROM OBJECTS; APPARATUS THEREFOR
- C25F3/00—Electrolytic etching or polishing
- C25F3/02—Etching
- C25F3/14—Etching locally
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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
- H01F1/147—Alloys characterised by their composition
- H01F1/14766—Fe-Si based alloys
- H01F1/14775—Fe-Si based alloys in the form of sheets
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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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- 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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
Definitions
- the present invention relates to grain-oriented electrical steel sheets, and particularly to grain-oriented electrical steel sheets suitable as iron core materials for transformers and the like.
- the iron loss of the grain-oriented electrical steel sheet is separated into the hysteresis loss and the eddy current loss.
- a method for improving the hysteresis loss a method called a GOSS direction (110) [001] direction is highly oriented in the rolling direction, a method for reducing impurities contained in the steel sheet, and the like have been developed.
- a method for improving the eddy current loss a method for increasing the electric resistance by adding Si, a method for applying a coating tension in the rolling direction, and the like have been developed.
- these methods have manufacturing limitations.
- magnetic domain subdivision technology that introduces magnetic flux non-uniformity by physical methods such as groove formation and introduction of local strain in the steel sheet after finish annealing and insulation coating baking.
- This technique is a method of subdividing the width of a 180 ° magnetic domain (main magnetic domain) formed along the rolling direction to reduce iron loss, particularly eddy current loss.
- a method in which the effect is not lost even if the product plate is strain-removed and annealed is particularly called a heat-resistant magnetic domain subdivision method.
- This method is generally applied to materials for wound iron cores, which require strain relief annealing in the manufacturing process.
- Patent Document 1 by introducing a linear groove having a width of 300 ⁇ m or less and a depth of 100 ⁇ m or less on the surface of a steel sheet, the iron loss that was originally 0.80 W / kg or more at W 17/50 is reduced to the linear groove.
- a technique for improving to 0.70 W / kg or less after the formation of the above has been proposed.
- Patent Document 2 As a method of forming a groove in a directional electromagnetic steel sheet, for example, an electrolytic etching method (Patent Document 2) in which a groove is formed on the surface of the steel sheet by electrolytic etching, and a laser method in which the steel sheet is locally melted and evaporated by a high-power laser.
- Patent Document 3 a gear pressing method (Patent Document 4) has been proposed in which an indentation is given by pressing a gear-shaped roll against a steel plate.
- the increase in the groove volume not only deteriorates the magnetic properties of the steel sheet such as a decrease in magnetic permeability, but also increases manufacturing disadvantages such as breakage during the production line passing. .. Therefore, in the conventional magnetic domain subdivided material using grooves, the effect of improving iron loss is improved by optimizing the groove formation pattern.
- a plurality of linear groove groups are formed on the surface of a steel sheet, and linear grooves adjacent to each other in the forming direction of the linear grooves are projected by separating both ends thereof or orthogonal to the rolling direction.
- a method of arranging them so as to overlap on the surface has been proposed.
- the present invention has been made in view of the above circumstances, and provides a grain-oriented electrical steel sheet in which linear grooves are formed, which can achieve both an excellent iron loss reduction effect and a high magnetic flux density.
- the purpose is to do.
- the present inventors have made extensive studies to solve the above problems.
- the shape of the groove formed on the surface of the steel sheet was examined. As described above, when a groove is formed in a steel sheet, the magnetic permeability deteriorates. Since the magnitude of the deterioration of the magnetic permeability correlates with the volume of the groove, it is preferable that the volume of the groove to be formed is as small as possible. Therefore, it is considered most preferable that the shape of the groove formed on the steel sheet is continuously formed in the plate width direction, that is, the groove is formed without interruption in the plate width direction.
- the effect of reducing iron loss by the grooves formed in this way is that small-scale groove groups that are not continuously formed in the plate width direction are formed on a projection plane in which the ends of adjacent grooves are orthogonal to the rolling direction. It is smaller than the one formed so as to overlap with. This is because the magnetic domain subdivision effect is higher as the surface area of the discontinuous portion of magnetization, that is, the groove is larger.
- the present inventors have diligently studied a method for further improving the iron loss by devising the shape of the groove even in the groove formed in a straight line (continuously).
- the grained grain-oriented electrical steel sheet is finally annealed by applying an annealing separator after the grooves are formed.
- the purpose of this final annealing is to recrystallize the steel sheet and form a forsterite film.
- a forsterite film is also formed at the bottom of the groove. It is known that when this forsterite film is densely formed, iron loss is improved by increasing the film tension. That is, it is considered possible to further improve the iron loss by forming a dense forsterite film on the bottom of the groove.
- the iron loss is We found a significant improvement.
- the discontinuous portion 2 of the center line passes through the center of the center line P (the center of the groove width a of the linear groove 1) and is in the length direction of the linear groove 1 (the forming direction of the linear groove 1).
- a line parallel to) is a region that is parallel but not on the same straight line (a region where the center lines exist in parallel).
- the present invention has been made based on the above findings. That is, the gist structure of the present invention is as follows.
- a grain-oriented electrical steel sheet in which linear grooves are periodically formed in the rolling direction in a direction intersecting the rolling direction of the grain-oriented electrical steel sheet.
- the linear groove has a discontinuous portion of the center line in which the position of the center line of the groove width of the linear groove is deviated in the groove width direction of the linear groove.
- the groove width of the linear groove is a and the distance in the groove width direction between the center lines in the discontinuous portion of the center line is b.
- the present invention it is possible to provide a grain-oriented electrical steel sheet in which linear grooves are formed, which can achieve both an excellent iron loss reduction effect and a high magnetic flux density.
- a heat-resistant magnetic domain subdivision directional electromagnetic steel sheet having a linear groove formed it is possible to obtain a high iron loss reduction effect while suppressing deterioration of magnetic flux density as compared with the conventional case.
- FIG. 1A is a diagram for explaining the shape of the linear groove formed in the direction intersecting the rolling direction
- FIG. 1B is a diagram for explaining the shape of the linear groove having a discontinuity portion of the center line. It is a figure.
- FIG. 2 is a graph showing the relationship between b / a at the discontinuous portion of the center line and iron loss.
- FIG. 3 is a graph showing the relationship between the lap length c at the discontinuous portion of the center line and the iron loss.
- FIG. 4 is a diagram showing an example of the resist pattern formed in the examples.
- a linear groove extending in a direction intersecting the rolling direction of the grain-oriented electrical steel sheet and having a discontinuity in the center line was formed in the grain-oriented electrical steel sheet (cold-rolled steel strip).
- the distance b in the groove width direction between the center lines is variously changed with respect to the groove width a (see FIG. 1 (b)), and the grooved sample is decarburized and annealed.
- An annealing separator was applied and wound into a coil, and final annealing was performed.
- flattening and annealing were performed to form a tension film on the surface of the steel sheet to prepare a final product plate, and its magnetic properties were investigated.
- the groove width a, the length of the discontinuous portion of the center line in the linear groove length direction (wrap length c), and the groove depth (the formation depth of the groove in the plate thickness direction) were kept constant.
- the iron loss W 17/50 and the magnetic flux density B 8 were used.
- W 17/50 means the iron loss value when the alternating magnetization of 1.7 T and 50 Hz is applied in the rolling direction of the steel sheet, and B 8 is magnetized in the rolling direction with a magnetization force of 800 A / m. It means the magnetic flux density of time.
- the magnetic flux density (B 8 ) tends to deteriorate when b / a exceeds 0.95. It is considered that this is because the volume of the groove is increased due to the increase of the distance b in the groove width direction between the center lines, and the magnetic permeability of the steel sheet is lowered. From the above results, the appropriate range of b / a was set to 0.05 or more and 0.95 or less. b / a is more preferably 0.10 or more. Further, b / a is more preferably 0.90 or less.
- the final product plate is subjected to the same process as above for a sample in which a groove is formed by variously changing the lap length c while keeping the groove width a, the distance b in the groove width direction between the center lines, and the groove depth constant.
- the magnetic properties of the product were investigated. The results are shown in FIG.
- the lap length c is 50 mm or less, a large iron loss improving effect has been confirmed. It is considered that this is because a dense forsterite film was formed due to the retention of the atmospheric gas in the discontinuous portion of the center line as described above.
- the lap length c was made longer than 50 mm, deterioration in the amount of iron loss improvement was observed. It is considered that this is because the longer lap length improves the flowability of the atmospheric gas flowing in the groove and makes it difficult to form a dense forsterite film.
- the lap length c when the lap length c was longer than 50 mm, deterioration of B 8 was also confirmed. It is considered that this is because the volume of the groove increased due to the increase in the lap length c. Further, since it is a linear groove, the lap length c of the discontinuous portion of the center line needs to be 0 mm or more. From the above, the preferable range of the lap length c is set to 0 mm or more and 50 mm or less. More preferably, the lap length c is 0.1 mm or more. Further, more preferably, the lap length c is 40 mm or less.
- (Basic ingredient) C 0.08% by mass or less C is added to improve the structure of the hot-rolled plate, but if the C content exceeds 0.08% by mass, magnetic aging does not occur up to 50% by mass or less during the manufacturing process. It is desirable that the C content is 0.08% by mass or less because it becomes difficult to decarburize. Further, since the steel material containing no C is recrystallized secondarily, the lower limit of the C content is not particularly set.
- Si 2.0 to 8.0% by mass Si is an element effective in increasing the electrical resistance of steel and improving iron loss. However, if the Si content is less than 2.0% by mass, the improvement effect is not sufficiently exhibited, while if it exceeds 8.0% by mass, the workability and plate-passability are significantly deteriorated, and the magnetic flux density is also increased. descend. Therefore, it is desirable that the Si content is in the range of 2.0 to 8.0% by mass.
- Mn 0.005 to 1.0% by mass
- Mn is an element necessary for improving hot workability. However, if the Mn content is less than 0.005% by mass, the effect cannot be sufficiently obtained, while if it exceeds 1.0% by mass, the magnetic flux density deteriorates. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
- the component composition of the slab of the grain-oriented electrical steel sheet may be any component composition that causes secondary recrystallization.
- an inhibitor used to generate secondary recrystallization
- Al and N are used when an AlN-based inhibitor is used, and Mn and Se and / / when a MnS / MnSe-based inhibitor is used.
- an appropriate amount of S may be contained.
- both inhibitors may be used in combination.
- the preferable contents of Al, N, S and Se are, respectively.
- the present invention can also be applied to grain-oriented electrical steel sheets that do not use inhibitors and have limited contents of Al, N, S, and Se.
- the contents of Al, N, S, and Se are, respectively.
- Ni 0.03 to 1.50% by mass
- Sn 0.01 to 1.50% by mass
- Sb 0.005 to 1.50% by mass
- Cu 0.03 to 3.0% by mass
- P 0.03 to 0.50% by mass
- Mo 0.005 to 0.10% by mass
- Cr One or more selected from 0.03 to 1.50% by mass
- Ni is an effective element for improving the hot-rolled plate structure and improving the magnetic properties.
- the Ni content is less than 0.03% by mass, the contribution to the magnetic characteristics is small, while if it exceeds 1.50% by mass, the secondary recrystallization becomes unstable and the magnetic characteristics deteriorate. Therefore, it is desirable that the Ni content is in the range of 0.03 to 1.50% by mass.
- Sn, Sb, Cu, P, Mo, and Cr are also elements that improve the magnetic properties, but if the content is less than the above lower limit, the effect is not sufficient, and if the content exceeds the upper limit, the effect is not sufficient. Since the growth of the next recrystallized grains is suppressed, the magnetic properties deteriorate. Therefore, it is preferable to set the content in the above range.
- the product board consists of Fe and unavoidable impurities.
- the amount of the basic component other than C and the optional additive component contained in the steel material (slab) is also contained in the product board as it is.
- C is reduced by decarburization annealing
- the inhibitor component is purified by the final annealing described later, and the content of the product board is reduced to about unavoidable impurities.
- the steel material (slab) of the grain-oriented electrical steel sheet composed of the above component system is hot-rolled and then hot-rolled and annealed. Then, cold rolling is performed once or twice or more with intermediate annealing in between to finish the steel strip with the final plate thickness. Then, the steel strip is decarburized and annealed, an annealing separator containing MgO as a main component is applied, and then the steel strip is wound into a coil to be finally annealed for the purpose of secondary recrystallization and formation of a forsterite film. To give. After flattening and annealing the steel strip after final annealing, for example, a magnesium phosphate-based tension film is formed to form a steel strip of a product plate.
- a linear groove is formed on the surface of the grain-oriented electrical steel sheet (steel strip) in an arbitrary step after cold rolling and before applying the annealing separator.
- the method for forming a groove in the present invention includes a method in which a resist pattern is printed by a gravure printing method or an inkjet printing method so that a discontinuous portion of the center line is formed, and a non-printed portion is formed by an electrolytic etching method. After applying resist ink to the entire surface of the steel plate to form a resist, patterning (resist removal) is performed so that a discontinuous portion of the center line is formed by laser irradiation, and then the exposed portion from which the resist has been removed is subjected to an electrolytic etching method.
- a method of forming a groove and the like can be mentioned, but the method is not particularly limited.
- the groove dimensions suitable for the present invention are shown below.
- the groove dimensions are not only the groove width and the groove depth, but also the distance between the grooves periodically formed in the rolling direction of the grain-oriented electrical steel sheet (steel strip), and the extending direction and the plate width direction of the linear groove. It means the angle formed.
- Groove width 10-300 ⁇ m
- the groove width is preferably 300 ⁇ m or less.
- the lower limit of the groove width it is preferable to set the lower limit of the groove width to 10 ⁇ m.
- Groove depth 4 to 25% of plate thickness
- the effect of improving iron loss due to groove formation is higher as the surface area of the groove side wall portion, that is, the groove formation depth is larger (deeper). Therefore, it is preferable to form a groove having a depth of 4% or more with respect to the plate thickness.
- the depth of the groove is increased, the volume of the groove naturally increases, and the magnetic permeability tends to deteriorate. Further, there is a risk of breakage starting from the groove when passing the plate. Based on the above, it is preferable that the upper limit of the groove depth is 25% with respect to the plate thickness.
- Rolling direction formation interval of linear grooves 1.5 to 10 mm
- the iron loss improving effect is improved as the surface area of the groove side wall portion is larger. Therefore, the narrower the groove formation interval in the rolling direction, the better the result can be obtained.
- the groove formation interval in the rolling direction is 1.5 mm to 10 mm.
- Angle formed by the linear groove and the plate width direction within ⁇ 30 °
- the angle formed by the linear groove in the plate width direction is preferably within ⁇ 30 °.
- the groove width a, the distance b in the groove width direction between the center lines, and the lap length c at the discontinuous portion of the center line of the present invention correspond to the surface of the directional electromagnetic steel plate after forming the tension film by observing with an optical microscope. Obtain by measuring the length of the part. To measure the groove depth, the surface of the steel sheet is observed using a laser microscope, and the depth profile of the groove portion is acquired along the stretching direction. The average value of the deepest part in the depth profile of each obtained point is defined as the groove depth.
- the steel material (slab) of the grain-oriented electrical steel sheet containing the composition shown in Table 1 and the balance consisting of Fe and unavoidable impurities was hot-rolled and annealed by hot rolling. After that, cold rolling was performed twice with intermediate annealing in between to obtain a cold-rolled steel strip having a plate thickness of 0.23 mm.
- a groove was formed by an electrolytic etching method. At this time, as shown in FIG. 4, the resist pattern formed by the resist portion and the non-resist portion has a groove width of 200 ⁇ m, a groove forming interval of 4 mm in the rolling direction, and an angle formed by the groove stretching direction and the plate width direction.
- the steel strip was decarburized and annealed after removing the resist on the surface in an alkaline solution, coated with an annealing separator containing MgO as a main component, and wound into a coil. After that, the final annealing was applied. The steel strip after the final annealing was subjected to flattening annealing, and then a magnesium phosphate-based tension film was formed to obtain a final product steel strip.
- the steel strip thus produced was cut out to RD: 280 mm ⁇ TD: 100 mm so as to include one discontinuity of the center line for each linear groove, and W 17/50 by the SST (single plate magnetic test) method. , B 8 was measured.
- RD means the rolling direction of the steel sheet
- TD means the sheet width direction.
- the surface of the sample after the magnetic measurement was observed with an optical microscope, and the groove width a, the distance b in the groove width direction between the center lines at the discontinuity of the center lines, and the lap length c were measured.
- a groove pattern is formed in which small-scale grooves that are not continuously formed in the plate width direction are formed so that adjacent grooves in the plate width direction overlap each other on a projection plane orthogonal to the rolling direction.
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Abstract
Description
まず、鋼板表面に形成する溝の形状について検討を行った。前述の通り、鋼板に溝を形成した時、透磁率が劣化する。この透磁率の劣化の大きさは、溝の体積に相関するものであるため、形成する溝の体積は極力小さい方が好ましい。したがって、鋼板に形成する溝の形状は、板幅方向に連続的に形成させたもの、すなわち板幅方向に途切れなく溝を形成させたものが最も好ましいと考えられる。一方、このように形成させた溝による鉄損低減効果は、板幅方向に連続的に形成されていない小規模の溝群を、隣り合う溝の端部同士を圧延方向と直交する投影面上で重なるように形成したものに比べて小さい。これは、磁区細分化効果は、磁化の不連続部分、すなわち溝の表面積が大きいほど高い効果が得られるためである。
0.05≦b/a≦0.95 ・・・(1)
なお、前記中心線の不連続部2は、より詳細には、中心線P(線状溝1の溝幅aの中心を通り、線状溝1の長さ方向(線状溝1の形成方向)に平行な線)が、平行ではあるが、同一直線上にはない領域(中心線が並行して存在する領域)である。
前記線状溝は、前記線状溝の溝幅の中心線の位置が、前記線状溝の溝幅方向にずれた中心線の不連続部を有し、
前記線状溝の溝幅をa、前記中心線の不連続部における中心線間の溝幅方向の距離をbとしたとき、
前記a及びbが下記式(1)の関係を満たす、方向性電磁鋼板。
0.05≦b/a≦0.95 ・・・(1)
[2]前記中心線の不連続部の線状溝長さ方向の長さが、0mm以上50mm以下である、[1]に記載の方向性電磁鋼板。
本発明によれば、線状溝を形成した耐熱型磁区細分化方向性電磁鋼板において、従来よりも磁束密度の劣化を抑制しつつ、高い鉄損低減効果を得ることができる。
本発明の方向性電磁鋼板用の鋼素材(スラブ)の基本成分、インヒビター成分および任意添加成分について具体的に述べる。
C:0.08質量%以下
Cは、熱延板組織の改善のために添加するが、Cの含有量が0.08質量%を超えると磁気時効の起こらない50質量ppm以下まで製造工程中に脱炭することが困難となるため、C含有量は0.08質量%以下とすることが望ましい。また、Cを含まない鋼素材でも二次再結晶することから、C含有量の下限については特に設けない。
Siは、鋼の電気抵抗を増大させ、鉄損を改善するのに有効な元素である。しかしながら、Siの含有量が2.0質量%未満ではその改善効果が十分に発揮されず、一方8.0質量%を超えると加工性、通板性が著しく劣化することに加え、磁束密度も低下する。そのため、Si含有量は2.0~8.0質量%の範囲とすることが望ましい。
Mnは、熱間加工性を向上させるうえで必要な元素である。しかしながら、Mnの含有量が0.005質量%未満ではその効果を十分に得ることが出来ず、一方1.0質量%を超えると磁束密度が劣化する。そのため、Mn含有量は0.005~1.0質量%の範囲とすることが好ましい。
本発明において、方向性電磁鋼板のスラブの成分組成は、二次再結晶が生じる成分組成であればよい。二次再結晶を生じさせるためにインヒビターを利用する場合、例えばAlN系インヒビターを利用する場合であればAlおよびNを、またMnS・MnSe系インヒビターを利用する場合であれば、MnとSe及び/またはSを適量含有させればよい。もちろん両インヒビターを併用してもよい。この場合における、Al、N、S及びSeの好適含有量はそれぞれ、
Al:0.010~0.065質量%
N:0.0050~0.0120質量%
S:0.005~0.030質量%
Se:0.005~0.030質量%
である。
Al:0.010質量%以下
N:0.0050質量%以下
S:0.0050質量%以下
Se:0.0050質量%以下
に抑制することが好ましい。
Ni:0.03~1.50質量%、
Sn:0.01~1.50質量%、
Sb:0.005~1.50質量%、
Cu:0.03~3.0質量%、
P:0.03~0.50質量%、
Mo:0.005~0.10質量%、
Cr:0.03~1.50質量%のうちから選ばれる1種以上
本発明における溝の形成方法には、グラビア印刷法やインクジェット印刷法によって、中心線の不連続部が形成されるようにレジストパターンを印刷し、非印刷部を電解エッチング法により溝形成する方法、鋼板全面にレジストインクを塗布しレジストを形成した後、レーザー照射によって中心線の不連続部が形成されるようにパターニング(レジスト除去)を行った後、レジストが除去された露出部を電解エッチング法により溝形成する方法等が挙げられるが、特に限定するものではない。
下記に、本発明において好適な溝寸法を示す。ここで溝寸法とは、溝幅、溝深さに加え、方向性電磁鋼板(鋼帯)の圧延方向に周期的に形成する溝同士の間隔及び、線状溝の延伸方向と板幅方向の成す角を意味する。
溝幅が広いほど、同程度の溝深さとしたときの透磁率の劣化が大きいため、狭いほど好適である。したがって、溝幅は300μm以下とするのが好ましい。しかし、溝幅が過剰に狭くなった時、溝両端における磁極カップリングにより、鉄損改善効果が低下してしまうため、溝幅の下限を10μmとするのが好適である。
溝形成による鉄損改善効果は、溝側壁部の表面積、すなわち溝の形成深さが大きい(深い)ほど高い効果が得られる。したがって、板厚に対して4%以上の深さの溝を形成させることが好適である。一方、溝の深さを増していくと、当然溝の体積も増加し、透磁率が劣化する傾向となる。さらに、通板時に溝部を起点に破断のリスクがある。以上を踏まえ、溝深さの上限を板厚に対して25%とするのが好適である。
先述の通り、鉄損改善効果は溝側壁部の表面積が大きいほど向上するため、圧延方向における溝の形成間隔は狭いほど良好な結果を得られる。しかしながら、溝の形成間隔が狭まるにつれ、鋼板に対する溝の体積分率も増加し透磁率の劣化に加えて、操業時の破断のリスクも高まる。したがって、圧延方向における溝の形成間隔を1.5mm~10mmとするのが好適である。
溝の延伸方向が板幅方向から傾くほど、溝の体積が増加するため、透磁率が劣化する傾向となる。したがって、線状溝と板幅方向の成す角は±30°以内とすることが好ましい。
本発明の中心線の不連続部における溝幅a、中心線間の溝幅方向の距離b、ラップ長cは、張力被膜形成後の方向性電磁鋼板の表面を、光学顕微鏡で観察し、該当箇所の長さを計測して求める。溝深さの測定は、レーザー顕微鏡を用いて前記鋼板の表面を観察し、延伸方向に沿って溝部の深度プロファイルを取得する。得られた各点の深度プロファイルにおける、最深部の平均値を溝深さとする。
2 中心線の不連続部
Claims (2)
- 方向性電磁鋼板の圧延方向と交差する方向に、線状溝が、前記圧延方向に周期的に形成された方向性電磁鋼板であって、
前記線状溝は、前記線状溝の溝幅の中心線の位置が、前記線状溝の溝幅方向にずれた中心線の不連続部を有し、
前記線状溝の溝幅をa、前記中心線の不連続部における中心線間の溝幅方向の距離をbとしたとき、
前記a及びbが下記式(1)の関係を満たす、方向性電磁鋼板。
0.05≦b/a≦0.95 ・・・(1) - 前記中心線の不連続部の線状溝長さ方向の長さが、0mm以上50mm以下である、請求項1に記載の方向性電磁鋼板。
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