WO2015111434A1 - 方向性電磁鋼板およびその製造方法 - Google Patents
方向性電磁鋼板およびその製造方法 Download PDFInfo
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- WO2015111434A1 WO2015111434A1 PCT/JP2015/050321 JP2015050321W WO2015111434A1 WO 2015111434 A1 WO2015111434 A1 WO 2015111434A1 JP 2015050321 W JP2015050321 W JP 2015050321W WO 2015111434 A1 WO2015111434 A1 WO 2015111434A1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
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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
- B23K15/00—Electron-beam welding or cutting
- B23K15/0006—Electron-beam welding or cutting specially adapted for particular articles
-
- 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
- B23K26/0006—Working by laser beam, e.g. welding, cutting or boring taking account of the properties of the material involved
-
- 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
- B23K26/352—Working by laser beam, e.g. welding, cutting or boring for surface treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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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- 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
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/18—Sheet panels
-
- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel alloys
-
- 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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/50—Inorganic material, e.g. metals, not provided for in B23K2103/02 – B23K2103/26
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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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—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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- 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
- C22C38/60—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 and a method for producing the grain-oriented electrical steel sheet.
- Oriented electrical steel sheets are mainly used as iron core materials for transformers and motor cores, and therefore are strongly required to have excellent magnetic properties, particularly excellent iron loss properties (low iron loss).
- iron loss properties low iron loss
- Patent Document 1 proposes a technique for narrowing the magnetic domain width and reducing iron loss by irradiating a final product plate with laser and introducing a high dislocation density region into the steel sheet surface layer.
- Patent Document 2 proposes a technique for controlling the magnetic domain width by electron beam irradiation.
- the beam convergence or irradiation speed That is, there are cases where it is difficult to irradiate the full width of the steel sheet with one beam irradiation device due to restrictions such as the beam scanning speed on the steel sheet surface (hereinafter simply referred to as “scanning speed”).
- the irradiation areas of the respective beam irradiation apparatuses are set appropriately, and at the same time, adjacent beam irradiation apparatuses are It is necessary to control in synchronization.
- the beam irradiation region may be displaced in the longitudinal direction and / or the plate width direction, and the beam irradiation region may be discontinuous.
- Patent Document 3 discloses a beam irradiation method that detects the meandering amount of a steel strip and changes the scanning range of the beam irradiation. Further, a method of sensing the beam irradiation area by some method and performing feedback control of the beam irradiation area is also conceivable.
- the present invention has been made in view of the above-mentioned problems of the prior art, and its purpose is to provide a grain-oriented electrical steel sheet having excellent iron loss characteristics and a method for manufacturing the steel sheet with high productivity. There is to do.
- the inventors diligently investigated the influence of the properties of the discontinuous joints in the beam irradiation region on the iron loss characteristics in order to solve the above problems. As a result, by controlling the properties at the joints of adjacent beam irradiation areas to a specific range, it is possible to suppress an increase in iron loss even if there is a deviation, and to perform magnetic domain fragmentation with high productivity. As a result, the present invention has been developed.
- the present invention provides a plurality of beam irradiation regions in the plate width direction on the surface of the steel plate, in which linear or dot-sequence continuous strain is introduced at an angle within 30 degrees with the plate width direction by laser irradiation or electron beam irradiation.
- the present invention is also a method for producing the grain-oriented electrical steel sheet, wherein the steel sheet surface is divided into a plurality of regions in the plate width direction, a laser irradiation device or an electron beam irradiation device is installed in each region, and the beam is irradiated. Then, in forming the beam irradiation region and performing the magnetic domain subdivision processing, the beam is irradiated with the TD interval ⁇ at the joint of the beam irradiation region set to a range of -3 to 0 mm. It is a manufacturing method of a steel plate.
- the discontinuity (displacement) in the rolling direction and the sheet width direction at the joint between adjacent beam irradiation regions can be controlled within an appropriate range, and an increase in iron loss can be suppressed. It is possible to manufacture a grain-oriented electrical steel sheet excellent in productivity with high productivity.
- the inventors set the beam line interval a to 5 mm (constant), and the properties of the joint portion are different.
- Various steel plates were prepared and the iron loss was measured. Specifically, as shown in FIG. 1, due to electron beam irradiation, the amount of displacement in the longitudinal direction and the amount of displacement in the plate width direction at the joint of a 100 mm wide steel plate having a joint between two beam irradiation regions at the center of the plate width. Samples with various changes were prepared, and the iron loss W 17/50 was measured with a single plate magnetometer.
- the electron beam irradiation conditions at this time were acceleration voltage: 60 kV, beam current: 9.5 mA, and scanning speed: 30 m / s.
- FIG. 2 shows the amount of shift in the longitudinal direction (RD direction) at the joint between adjacent beam irradiation regions (hereinafter this amount is referred to as “RD interval ⁇ ”. Note that there are two RD intervals in the same joint, In the present invention, it is the narrower one) and the iron loss W 17/50 . Also, FIG. 3 shows the amount of deviation in the plate width direction (TD direction) at the joint between adjacent beam irradiation regions (hereinafter, this amount of deviation is referred to as “TD interval ⁇ ”. This is a relationship between the iron loss W 17/50 and “positive (+)”.
- the iron loss increases.
- the degree of discontinuity (deviation amount) is within a predetermined range, the iron loss does not increase. Therefore, it can be seen that if the deviation amount can be suppressed within the predetermined range, a low iron loss directional electrical steel sheet can be produced with high productivity even if the discontinuity cannot be completely eliminated.
- the inventors separated the iron loss measured in the above experiment into hysteresis loss and eddy current loss in order to investigate the cause of deterioration of the iron loss characteristic due to discontinuity of the joint of the beam irradiation region. The following was found.
- the iron loss at the time of direct current excitation was defined as hysteresis loss
- the difference between the iron loss at the time of alternating current excitation and the iron loss at the time of direct current excitation was defined as eddy current loss.
- Beam irradiation region refers to a region irradiated with a laser or an electron beam.
- the coating formed on the surface of the steel sheet by the beam irradiation is damaged and an irradiation mark is generated, so that the beam irradiation region can be easily identified visually or using a microscope.
- the magnetic domain structure parallel to the rolling direction may be interrupted or discontinuous in the region irradiated with the beam. Visualize it using a magnetic domain observation method such as the bitter method. Thus, the beam irradiation area can be identified.
- RD interval (mm) at the joint of the beam irradiation area The amount of deviation in the rolling direction of the beam irradiation region at the joint is called the RD interval, and the smaller one of the two RD intervals at the same joint is adopted as the “RD interval ⁇ ” in the present invention (see FIG. 5). Further, when the beam line interval fluctuates in the longitudinal direction and the RD interval at the joint of the beam irradiation region is not constant, the RD interval is measured at five locations in the rolling direction of 500 mm, and the average value is obtained. Moreover, when there are a plurality of joints in the plate width direction of the steel plate, the average value thereof is used.
- TD interval ⁇ TD interval of the beam irradiation region at the joint (mm)
- the deviation in the plate width direction of the beam irradiation area at the joint is referred to as “TD interval ⁇ ” as described above, “negative ( ⁇ )” when the beam irradiation areas overlap, and “positive (+)” when the beam irradiation areas overlap. (See FIG. 5).
- the width of the beam irradiation region varies and the TD interval is not constant, five TD intervals are measured in the longitudinal direction of 500 mm, and the average value is taken as the TD interval ⁇ .
- Beam line interval It is defined by the interval in the longitudinal direction of the beam irradiation line in the beam irradiation region (see FIG. 5).
- the beam line interval is not constant within the same beam irradiation region, five points are measured in the longitudinal direction of 500 mm, and the average value is obtained.
- Magnetic domain discontinuity average width ( ⁇ m)
- the magnetic domain discontinuity is a portion where the magnetic domain structure is locally disturbed by the introduction of thermal strain due to beam irradiation, and as shown in FIG. 4, the magnetic domain structure parallel to the rolling direction is interrupted or becomes discontinuous. It refers to the part that is. It can be measured by magnetic domain observation by the bitter method. Since this width is not necessarily constant in the beam irradiation portion, five or more locations are measured in the 100 mm direction of the beam line, and the average value is defined as the width of the magnetic domain discontinuity in the line row. The measurement is made at 5 lines or more in the direction of 500 mm, and the average value is defined as the magnetic domain discontinuity average width.
- the TD interval ⁇ at the joint between adjacent beam irradiation regions is set to 0 mm (constant), the RD interval ⁇ and the beam line interval a are changed variously, and the iron loss W 17/50 at each beam line interval a is changed.
- interval (alpha) in which the increase amount of A does not exceed 0.01 W / kg is shown.
- the electron beam irradiation conditions at this time were acceleration voltage: 60 kV, beam current: 9.5 mA, and scanning speed: 30 m / s. From this figure, as the beam line interval a becomes narrower, the allowable RD interval ⁇ becomes smaller.
- FIG. 7 shows an increase in iron loss W 17/50 at each beam line interval a by changing the RD interval ⁇ of the joint of the beam irradiation region to 0 mm (constant) and changing the TD interval ⁇ and the beam line interval a in various ways .
- interval (beta) whose quantity does not exceed 0.01 W / kg is shown.
- the electron beam irradiation conditions were set to acceleration voltage: 60 kV, beam current: 9.5 mA, and scanning speed: 30 m / s, as in FIG.
- the magnetic domain discontinuity average width w is an index representing the amount of thermal strain introduced in the beam irradiation region.
- FIG. 8 shows an increase in iron loss W 17/50 at each w by changing the beam line interval a to 5 mm, the RD interval ⁇ to 0 mm (constant), and variously changing the TD interval ⁇ and the magnetic domain discontinuity average width w.
- required (beta) which quantity does not exceed 0.01 W / kg is shown.
- the electron beam irradiation conditions were set to acceleration voltage: 60 kV, beam current: 9.5 mA, and scanning speed: 30 m / s, as in FIG.
- FIG. 9 shows a case where the beam line interval a is 5 mm, the TD interval ⁇ and the RD interval ⁇ are variously changed, and the increase amount of the iron loss W 17/50 at each ⁇ does not exceed 0.01 W / kg. This shows the result of obtaining.
- the electron beam irradiation conditions were set to acceleration voltage: 60 kV, beam current: 9.5 mA, and scanning speed: 30 m / s, as in FIG.
- the overall intercept is estimated to be -6.5 on the side where the beam irradiation areas overlap in the plate width direction at the joint ( ⁇ ⁇ 0), and 5. on the open side ( ⁇ > 0). 4 was estimated. From the above results, it may be necessary to control the TD interval ⁇ to satisfy the above formula (2) so that the increase in the iron loss W 17/50 does not exceed 0.01 W / kg due to the properties at the joint. Recognize.
- the allowable range of the deviation amount (TD interval ⁇ ) in the TD direction so that the increase amount of the iron loss W 17/50 does not exceed 0.01 W / kg is on the side where the beam irradiation regions overlap ( ⁇ ⁇ 0). Because it is wide, if the beam irradiation area is controlled so that it overlaps in the range of 0 to 3 mm in the plate width direction, that is, the TD interval ⁇ -3 to 0 mm, there will be some meandering of the steel plate in the passing plate. Even if it occurs, the increase amount of the iron loss W 17/50 can be suppressed to 0.01 W / kg or less.
- laser irradiation or electron beam irradiation capable of irradiating large energy with a reduced beam diameter is preferable.
- magnetic domain subdivision processing conditions by laser irradiation will be described.
- solid lasers such as YAG lasers and fiber lasers, gas lasers such as CO 2 lasers, and the like can be suitably used.
- the laser oscillation mode may be either continuous oscillation or pulse oscillation such as a Q switch type.
- the amount of energy input per unit length of scanning the beam is not particularly limited, but in order to sufficiently obtain the magnetic domain fragmentation effect, the amount of energy input per unit length of scanning the beam.
- (P / V) is preferably larger than 10 W ⁇ s / m.
- the laser irradiation to the steel plate may be performed continuously in a linear manner or in a point sequence.
- the point interval irradiated in the form of a point sequence is too wide, the effect of subdividing the magnetic domain becomes small, so it is preferable to set it to 1.00 mm or less.
- the acceleration voltage E, beam current I, and beam scanning speed V when irradiating the electron beam are not particularly limited. However, since it is necessary to sufficiently obtain the magnetic domain fragmentation effect, it is preferable that the amount of heat input per unit length (E ⁇ I / V) for scanning the beam is larger than 6 W ⁇ s / m. Further, the pressure in the processing chamber for irradiating the steel sheet with the electron beam is desirably 2 Pa or less.
- the pressure is higher than this, the electron beam will be diffusely reflected by the residual gas in the path from the electron gun to the steel sheet, causing the beam to blur, or the energy at the center of the beam will be attenuated and the energy given to the steel sheet will be reduced.
- the subdivision effect is reduced.
- the electron beam may be irradiated to the steel sheet in a linear manner or a point sequence.
- the method of irradiating in a dot array is realized by repeating the process of stopping scanning at a predetermined time interval while scanning the beam quickly, irradiating the beam at that point for a predetermined time, and starting scanning again. Can do.
- the deflection voltage of the electron beam may be changed using an amplifier having a large capacity.
- the effect of subdividing the magnetic domain is reduced if the point interval when irradiating in a dot sequence is too wide, it is preferably 0.80 mm or less.
- the beam line spacing a in the rolling direction when performing magnetic domain subdivision processing by laser irradiation or electron beam irradiation is not limited as long as the above-mentioned formulas (1) and (2) are satisfied. In order to increase, it is preferable to set in the range of 3 to 15 mm.
- the angle formed between the beam line and the sheet width direction (a direction perpendicular to the rolling direction) needs to be within 30 °. This is because when the angle exceeds 30 °, the magnetic domain refinement effect is reduced and the iron loss cannot be sufficiently reduced.
- purification process process is demonstrated.
- the steel raw material used for manufacture of the grain-oriented electrical steel sheet of the present invention has a predetermined component composition.
- an inhibitor is used to cause secondary recrystallization, for example, when using an AlN-based inhibitor, Al and N are used, and when using an MnS / MnSe-based inhibitor. It is preferable to use those containing appropriate amounts of Mn and S and / or Se. Of course, both inhibitors may be included.
- preferable contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, and S: 0.005 to 0.03 mass%, respectively. And Se: a range of 0.005 to 0.03 mass%.
- the content of Al, N, S and Se forming the inhibitor is preferably as small as possible.
- the content is preferably reduced to Al: 0.0100 mass% or less, N: 0.0050 mass% or less, S: 0.0050 mass% or less, and Se: 0.0050 mass% or less.
- C As basic components contained in the steel material used in the present invention, there are C, Si and Mn other than the above-mentioned components forming the inhibitor, and the following composition ranges are preferable.
- C 0.08 mass% or less
- C exceeds 0.08 mass%, it is difficult to reduce to 0.0050 mass% or less where magnetic aging does not occur due to decarburization annealing during the manufacturing process. The following is preferable. Even when C is not included, secondary recrystallization is possible, so there is no need to provide a lower limit.
- Si 2.0 to 8.0 mass%
- Si is an element effective for increasing the electrical resistance of steel and reducing iron loss, but if it is less than 2.0 mass%, a sufficient effect of reducing iron loss cannot be obtained. On the other hand, if it exceeds 8.0 mass%, the workability is remarkably lowered, and it becomes difficult to roll and manufacture, and the magnetic flux density is also lowered. Therefore, Si is preferably in the range of 2.0 to 8.0 mass%.
- Mn 0.005 to 1.0 mass%
- Mn is an element necessary for improving the hot workability of steel, but if it is less than 0.005 mass%, the above improvement effect is poor. On the other hand, if it exceeds 1.0 mass%, the magnetic flux density decreases. Therefore, Mn is preferably in the range of 0.005 to 1.0 mass%.
- Ni 0.03-1.50 mass%, Sn: 0.01-1.50 mass%, Sb: 0.005-1.50 mass for the purpose of improving magnetic properties.
- % Cu: 0.03-3.0 mass%, P: 0.03-0.50 mass%, Cr: 0.03-1.50 mass%, and Mo: 0.005-0.10 mass% 1 type (s) or 2 or more types can be contained.
- Ni is an element useful for improving the steel structure of hot-rolled sheets and improving magnetic properties. However, if it is less than 0.03 mass%, the effect of improving the magnetic properties is small. On the other hand, if it exceeds 1.5 mass%, the secondary recrystallization becomes unstable and the magnetic properties deteriorate. Therefore, when adding Ni, it is preferable to be in the range of 0.03 to 1.5 mass%.
- Sn, Sb, Cu, P, Cr, and Mo are elements that are useful for improving the magnetic properties, respectively, but if any of them does not satisfy the lower limit value of each component, the effect of improving the magnetic properties is small.
- the upper limit value of each component described above is exceeded, the development of secondary recrystallized grains is hindered and the magnetic properties are deteriorated. Therefore, it is preferable to contain in the said range, respectively.
- the balance other than the above components is Fe and inevitable impurities mixed in in the manufacturing process.
- the steel material may be a slab having a normal thickness of 100 mm or more obtained by melting a steel having the above component composition by a normal refining process and then continuously casting or ingot-bundling rolling.
- a thin slab having a thickness of 100 mm or less by a slab casting method may be used.
- the slab having the normal thickness is generally heated and subjected to hot rolling, but may be immediately subjected to hot rolling without being heated after continuous casting. In the case of a thin slab, hot rolling may be performed, or hot rolling may be omitted and the subsequent process may be performed as it is.
- the hot-rolled steel sheet or the slab from which hot-rolling is omitted is then subjected to hot-rolled sheet annealing as necessary, and then the final plate thickness is obtained by one or more cold rollings sandwiching intermediate annealing.
- the primary recrystallization annealing or decarburization annealing after applying the annealing separator to the steel sheet surface, the secondary recrystallization and the final annealing to be purified, and further, the insulation coating
- a grain-oriented electrical steel sheet is obtained by performing flattening annealing that doubles as both baking and shape correction.
- the thickness of the grain-oriented electrical steel sheet, that is, the final thickness of the cold rolling is not particularly specified, but is 0.15 to 0.35 mm from the viewpoint of reducing iron loss and ensuring good punchability. A range is preferable.
- the surface of the steel plate obtained as described above is irradiated with a beam from a laser irradiation device or an electron beam irradiation device, and subjected to a magnetic domain fragmentation treatment.
- the said beam irradiation apparatus installs multiple units
- the beam irradiation width which one beam irradiation apparatus takes it is preferable to set it as the range of 150 mm or more and 1000 mm or less.
- an annealing separator mainly composed of MgO is added. Apply to the surface of the steel sheet, finish annealing including secondary recrystallization annealing and purification annealing to make a directional electrical steel sheet with a forsterite film, and then apply an insulation coat consisting of 60 mass% colloidal silica and aluminum phosphate Then, it was baked by performing flattening annealing at a temperature of 800 ° C.
- a continuous laser is irradiated linearly with a fiber laser installed in the plate width direction in a direction perpendicular to the rolling direction of the steel plate, or electrons are emitted by an electron beam irradiation device installed in the plate width direction.
- the magnetic domain was subdivided by irradiating the beam in the form of dots at intervals of 0.20 mm.
- the beam irradiation conditions were changed as shown in Table 1-1 to Table 1-4.
- the setting (target) of the displacement amount (RD interval ⁇ ) in the longitudinal direction (RD direction ⁇ ) and the displacement amount (TD interval ⁇ ) in the plate width direction (target) at the joint of the beam irradiation region is intentionally varied in various ways to change the properties of the joint.
- the grain- oriented electrical steel sheet in which the properties of the joints of the beam irradiation regions satisfy the conditions of the present invention has a small deterioration amount of the iron loss W 17/50 compared with the case where there is no joint displacement, and is 0.01 W / kg or less. It can be seen that
- the directional magnetic steel sheet with a final plate thickness of 0.23 mm and a plate width of 1250 mm and having a coil length of 5000 m is irradiated with an electron beam with six electron beam irradiation devices installed in the plate width direction.
- the electron beam was irradiated while changing the target ⁇ value so that the TD interval ⁇ at the joint of the beam irradiation region was ⁇ 5 mm, ⁇ 3 mm, 0 mm and 3 mm. Thereafter, a total of 51 test pieces were sampled every 100 m from the product coil, and the TD interval ⁇ of the joint of the beam irradiation region was measured.
- Table 2 shows the maximum and minimum values of the TD interval ⁇ of the 51 samples measured. It was. From this result, by setting the target value of the TD interval ⁇ to -3 to 0 mm and irradiating the beam, the range of the actual TD interval ⁇ is biased to the minus side (overlapping side) where the deterioration of the iron loss characteristic is small. As a result, it can be seen that the beam irradiation can be performed under the condition that the iron loss is good even if the irradiation condition varies slightly.
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Abstract
Description
0≦α≦0.3×a ・・・(1)
-1.2×a+0.02×w-0.5×α-6.5≦β≦-0.13×a-200×(1/w)+5.4 ・・・(2)
ここで、α:ビーム照射領域のつなぎ目におけるRD間隔(mm)
β:ビーム照射領域のつなぎ目におけるTD間隔(mm)
a:ビーム線間隔(mm)
w:磁区不連続部平均幅(μm)
を満たすことを特徴とする方向性電磁鋼板である。
(1)隣り合うビーム照射領域が長手方向でずれが生じた場合(α>0)には、ビーム照射領域が連続している場合と比べ、鉄損が増加する。
(2)隣り合うビーム照射領域がつなぎ目で板幅方向に重なる場合(β<0)、開いている場合(β>0)のいずれの場合にも、ビーム照射領域が連続している場合(β=0)と比べて鉄損は増加する。しかし、開いている場合の方が、鉄損の増加量は大きい。
(3)しかし、ビーム照射領域の不連続が、幅方向および長手方向ともに、ある範囲内であれば、鉄損の増加量は小さく、つなぎ目の不連続により悪影響を受けない。
(1)隣り合うビーム照射領域が長手方向にずれる場合(α>0)には、ビーム照射領域が連続的に続く場合(α=0)と比べてヒステリシス損が増加した。これは、ずれによって歪みが不均一に導入されるため、局所的に磁化過程が複雑となる結果、ヒステリシス損が大きくなったものと考えられる。
(2)隣り合うビーム照射領域が幅方向に重なる場合(β<0)には、ビーム照射領域が連続的に続く場合(β=0)と比べてヒステリシス損が増加した。これは、ビーム照射領域が重なる場合には、その部分に歪みが過剰に導入されるため、その部分の透磁率が小さくなり、鋼板全体として透磁率が不均一になるとともに透磁率も小さくなってヒステリシス損が増大したものと考えられる。
(3)一方、ビーム照射領域が幅方向に開く場合(β>0)には、ビーム照射領域が連続的に続く場合(β=0)と比べて渦電流損が増加した。これは、ビーム照射領域が開く場合には、その部分が磁区細分化されないために磁区幅の減少が起こらず、渦電流損が増加したものと考えられる。
記
0≦α≦0.3×a ・・・(1)
-1.2×a+0.02×w-0.5×α-6.5≦β≦-0.13×a-200(μm・mm)×(1/w)+5.4 ・・・(2)
ただし、α:ビーム照射領域のつなぎ目におけるRD間隔(mm)
β:ビーム照射領域のつなぎ目におけるTD間隔(mm)
a:ビーム線間隔(mm)
w:磁区不連続部平均幅(μm)
ビーム照射領域
本発明におけるビーム照射領域とは、レーザを照射あるいは電子ビームを照射した領域をいう。ビーム出力が大きい場合は、ビーム照射によって鋼板表面に被成された被膜が損傷し、照射痕が生ずるため、ビーム照射領域を目視あるいは顕微鏡を用いて簡単に識別することができる。また、照射痕が生じない場合には、ビームを照射した領域では、圧延方向に平行な磁区構造が途切れたり、不連続になったりするので、ビッター法などの磁区観察手法を用いて可視化することで、ビーム照射領域を識別することができる。
つなぎ目におけるビーム照射領域の圧延方向のずれ量をRD間隔といい、同一つなぎ目にある2つのRD間隔のうち狭い方を本発明では「RD間隔α」として採用する(図5参照)。また、ビーム線間隔が長手方向で変動し、ビーム照射領域のつなぎ目のRD間隔が一定でない場合には、圧延方向500mm間で5箇所についてRD間隔を測定し、その平均値とする。また、鋼板の板幅方向に複数のつなぎ目がある場合には、それらの平均値とする。
つなぎ目におけるビーム照射領域の板幅方向のずれ量を、先述したように「TD間隔β」といい、ビーム照射領域が重なる場合を「負(-)」、開いている場合を「正(+)」とする(図5参照)。ビーム照射領域の幅が変動し、TD間隔が一定でない場合には、長手方向500mmの間で5箇所のTD間隔を測定し、その平均値をTD間隔βとする。また、鋼板幅方向に複数のつなぎ目がある場合には、平均せず、それぞれのつなぎ目におけるβ値によって上記(2)式を満たすか否かを判断する。これは、+側に外れたものと-側に外れたものを単純平均したり、絶対値を平均したりすると、+側と-側の効果が異なるので、鉄損値が適正な範囲となるTD間隔βを正しく評価できないという問題があるからである。
ビーム照射領域におけるビーム照射線の長手方向の間隔で定義する(図5参照)。同じビーム照射領域内で、ビーム線間隔が一定でない場合には、長手方向500mmで5箇所を測定し、その平均値とする。
磁区不連続部は、ビーム照射による熱歪み導入によって、局所的に磁区構造が乱れた箇所であり、図4に示したように、圧延方向に平行な磁区構造が途切れたり、不連続になっている部分を指す。ビッター法による磁区観察で測定することができる。この幅は、ビーム照射部で必ずしも一定ではないので、ビーム線の線列方向100mm間において5箇所以上を測定し、その平均値をその線列における磁区不連続部幅とし、これを、さらに長手方向500mmにおいて5線列以上で測定し、その平均値を磁区不連続部平均幅とする。
0≦α≦0.3×a ・・・(1)
隣り合うビーム照射領域が長手方向にずれている場合、つなぎ目には歪みが不均一に導入されるため、規則的な磁区構造が局所的に乱れ、ヒステリシス損が大きくなる。この場合、ビーム線間隔aが狭くなる程、単位面積当たりのビーム照射による熱歪み量は大きくなるので、上記歪の不均一導入によるヒステリシス損増加は大きくなることが予想される。
まず、ビーム線間隔aの効果について説明する。
図7は、ビーム照射領域のつなぎ目のRD間隔αを0mm(一定)とし、TD間隔βとビーム線間隔aを種々に変化させて、それぞれのビーム線間隔aにおける鉄損W17/50の増加量が0.01W/kgを超えないTD間隔βを求めた結果を示したものである。なお、電子ビーム照射条件は、図6と同様、加速電圧:60kV、ビーム電流:9.5mA、走査速度:30m/sとした。
磁区不連続部平均幅wは、ビーム照射領域における熱歪み導入量を表す指標である。wが大きい場合、熱歪み導入量は多く、ヒステリシス損は大きくなる。図8は、ビーム線間隔aを5mm、RD間隔αを0mm(一定)とし、TD間隔βおよび磁区不連続部平均幅wを種々に変えて、それぞれのwにおける鉄損W17/50の増加量が0.01W/kgを超えないβを求めた結果を示したものである。なお、電子ビーム照射条件は、図6と同様、加速電圧:60kV、ビーム電流:9.5mA、走査速度:30m/sとした。
図9は、ビーム線間隔aを5mmとし、TD間隔βおよびRD間隔αを種々に変えて、それぞれのαにおける鉄損W17/50の増加量が0.01W/kgを超えないTD間隔βを求めた結果を示したものである。なお、電子ビーム照射条件は、図6と同様、加速電圧:60kV、ビーム電流:9.5mA、走査速度:30m/sとした。
ビーム照射領域のつなぎ目におけるずれ量を小さくする方法としては、レーザ反射ミラーや電子銃の設置位置を機械的に変更することで、ビーム照射の走査範囲を調整する方法、ビームの照射領域事態を光学的、磁気的な何らかの方法で感知し、走査範囲を電気的にフィードバック制御する方法も考えられる。また、検知した鋼板の蛇行量に合わせてビームの照射領域を変更したり、鋼板の蛇行量自体を、ライン制御で最小としたりする方法もある。その際、ずれ量の変動を先述した範囲に制御することが重要である。
先ず、レーザ照射による磁区細分化処理条件について説明する。
レーザ照射に使用できるレーザの種類としては、YAGレーザやファイバーレーザなどの固体レーザ、CO2レーザなどの気体レーザ等を好適に用いることができる。また、レーザの発振形態は、連続発振、Qスイッチ型のようなパルス発振のいずれでもよい。
照射するレーザの平均出力Pやビームの走査速度V、ビーム径d等は、特に制限はないが、磁区細分化効果を十分に得るためには、ビームを走査する単位長さ当たりのエネルギー入熱量(P/V)は10W・s/mより大きいことが好ましい。
また、鋼板へのレーザ照射は、線状に連続して照射しても、点列状に照射してもよい。また、点列状に照射する点間隔は、広すぎると磁区細分化効果が小さくなるので、1.00mm以下とするのが好ましい。
電子ビームを照射する際の加速電圧E、ビーム電流I、ビームの走査速度Vは、特に制限はない。ただし、磁区細分化効果を十分に得ることが必要となるので、ビームを走査する単位長さ当たりのエネルギー入熱量(E×I/V)は、6W・s/mより大きいことが好ましい。
また、電子ビームを鋼板に照射する加工室における圧力は、2Pa以下であることが望ましい。これより圧力が高いと、電子銃から鋼板までの行路中に残存ガスによって電子ビームが乱反射してビームがぼやけたり、ビーム中心部のエネルギーが減衰して鋼板に与えるエネルギーが小さくなったりし、磁区細分化効果が小さくなる。
先ず、本発明の方向性電磁鋼板の製造に用いる鋼素材は、所定の成分組成を有するものであることが好ましい。具体的には、二次再結晶を起こさせるのにインヒビターを利用する場合には、例えば、AlN系インヒビターを利用する場合にはAlおよびNを、また、MnS・MnSe系インヒビターを利用する場合にはMnとSおよび/またはSeを適量含有したものを用いるのが好ましい。勿論、両方のインヒビターを含有してもよい。この場合におけるAl,N,SおよびSeの好ましい含有量は、それぞれ、Al:0.01~0.065mass%、N:0.005~0.012mass%、S:0.005~0.03mass%およびSe:0.005~0.03mass%の範囲である。
C:0.08mass%以下
Cは、0.08mass%を超えると、製造工程中の脱炭焼鈍で磁気時効の起こらない0.0050mass%以下まで低減することが困難になるため、0.08mass%以下とするのが好ましい。なお、Cを含まない場合でも、二次再結晶は可能であるので、下限は特に設ける必要はない。
Siは、鋼の電気抵抗を高め、鉄損を低減するのに有効な元素であるが、2.0mass%未満では、十分な鉄損低減効果が得られない。一方、8.0mass%を超えると、加工性が著しく低下し、圧延して製造することが難しくなる他、磁束密度も低下してしまう。よって、Siは2.0~8.0mass%の範囲とするのが好ましい。
Mnは、鋼の熱間加工性を改善にするのに必要な元素であるが、0.005mass%未満では上記改善効果に乏しい。一方、1.0mass%を超えると、磁束密度が低下する。よって、Mnは0.005~1.0mass%の範囲とするのが好ましい。
なお、上記成分以外の残部は、Feおよび製造工程において混入してくる不可避的不純物である。
次いで、上記鋼板板の圧延方向と直角方向に、板幅方向に4台設置したファイバーレーザにて線状に連続レーザを照射し、または、板幅方向に8台設置した電子ビーム照射装置で電子ビームを0.20mmの間隔で点列状に照射して磁区細分化処理を施した。その際、ビーム照射条件は、表1-1~表1-4に示したように変化させた。さらに、ビーム照射領域のつなぎ目における長手方向(RD方向)のずれ量(RD間隔α)および板幅方向のずれ量(TD間隔β)の設定(目標)を故意に種々に振ってつなぎ目の性状を変化させた。
その後、上記つなぎ目部分を幅中央部に含む幅100mm×長さ400mmの試料を剪断して採取し、単板磁気測定装置にて鉄損W17/50を測定した。
また、上記鉄損測定に用いた試料について、前述した方法で、ビーム照射領域のつなぎ目におけるRD間隔αおよびTD間隔β、ビーム線間隔aならびに磁区不連続部平均幅wを測定した。
その後、製品コイルから100mおきに合計51の試験片を採取し、ビーム照射領域のつなぎ目のTD間隔βを測定し、測定した51の試料のTD間隔βの最大値および最小値を表2に示した。この結果から、TD間隔βの目標値を-3~0mmに設定してビーム照射することによって、実績のTD間隔βの範囲は、鉄損特性の劣化が小さいマイナス側(重なる側)に偏らせることができ、ひいては、照射条件に多少の変動があっても、鉄損が良好となる条件でビーム照射を行うことができることがわかる。
Claims (2)
- レーザ照射または電子ビーム照射により、板幅方向と30度以内の角度で線状または点列状の連続した歪みを導入したビーム照射領域を、鋼板表面に板幅方向に複数に分けて形成されてなる方向性電磁鋼板であって、
上記ビーム照射領域のつなぎ目の性状が、下記(1)および(2)式を満たすことを特徴とする方向性電磁鋼板。
記
0≦α≦0.3×a ・・・(1)
-1.2×a+0.02×w-0.5×α-6.5≦β≦-0.13×a-200×(1/w)+5.4 ・・・(2)
ここで、α:ビーム照射領域のつなぎ目におけるRD間隔(mm)
β:ビーム照射領域のつなぎ目におけるTD間隔(mm)
a:ビーム線間隔(mm)
w:磁区不連続部平均幅(μm) - 請求項1に記載の方向性電磁鋼板の製造方法であって、
鋼板表面を板幅方向に複数の領域に分け、それぞれの領域にレーザ照射装置または電子ビーム照射装置を設置し、ビームを照射してビーム照射領域を形成し、磁区細分化処理を施すにあたり、
上記ビーム照射領域のつなぎ目におけるTD間隔βを-3~0mmの範囲に設定してビームを照射することを特徴とする方向性電磁鋼板の製造方法。
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JP6299987B2 (ja) | 2018-03-28 |
JPWO2015111434A1 (ja) | 2017-03-23 |
EP3098328A4 (en) | 2017-01-18 |
EP3098328B1 (en) | 2019-08-14 |
US10704113B2 (en) | 2020-07-07 |
EP3098328A1 (en) | 2016-11-30 |
MX2016009420A (es) | 2016-09-16 |
US20160333435A1 (en) | 2016-11-17 |
CN106414779B (zh) | 2018-12-14 |
CN106414779A (zh) | 2017-02-15 |
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