WO2012001965A1 - 方向性電磁鋼板の鉄損改善装置および鉄損改善方法 - Google Patents
方向性電磁鋼板の鉄損改善装置および鉄損改善方法 Download PDFInfo
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- WO2012001965A1 WO2012001965A1 PCT/JP2011/003714 JP2011003714W WO2012001965A1 WO 2012001965 A1 WO2012001965 A1 WO 2012001965A1 JP 2011003714 W JP2011003714 W JP 2011003714W WO 2012001965 A1 WO2012001965 A1 WO 2012001965A1
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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
- B23K26/08—Devices involving relative movement between laser beam and workpiece
- B23K26/083—Devices involving movement of the workpiece in at least one axial direction
- B23K26/0838—Devices involving movement of the workpiece in at least one axial direction by using an endless conveyor belt
- B23K26/0846—Devices involving movement of the workpiece in at least one axial direction by using an endless conveyor belt for moving elongated workpieces longitudinally, e.g. wire or strip material
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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
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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
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
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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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
- C21D8/1272—Final recrystallisation annealing
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- C—CHEMISTRY; METALLURGY
- 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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- 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
- C22C38/002—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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- 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
- C22C38/02—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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
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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
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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
- B23K2101/16—Bands or sheets of indefinite length
-
- 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
-
- 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 an iron loss improvement apparatus and an iron loss improvement method for improving iron loss by performing magnetic domain subdivision on grain-oriented electrical steel sheets.
- the grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetization characteristics, particularly low iron loss.
- it is important to highly align the secondary recrystallized grains in the steel sheet in the (110) [001] orientation (so-called Goth orientation) and to reduce impurities in the product steel sheet.
- Goth orientation the crystal orientation and reducing impurities are limited in view of the manufacturing cost.
- a technique for reducing the iron loss by introducing non-uniformity (strain) to the surface of the steel sheet by a physical method and subdividing the width of the magnetic domain has been developed.
- Patent Document 1 proposes a technique for reducing the iron loss of a steel sheet by irradiating the final product plate with a laser, introducing a linear high dislocation density region into the steel sheet surface layer, and narrowing the magnetic domain width. ing. Magnetic domain fragmentation technology using laser irradiation has been improved thereafter (see Patent Document 2, Patent Document 3, and Patent Document 4), and grain oriented electrical steel sheets having good iron loss characteristics have been obtained.
- Patent Document 5 in order to prevent contamination of the optical control device of the irradiation apparatus, the exit of the laser beam is protected by a cover glass, and at the same time, a gas injection device is provided on one side of the laser irradiation apparatus and suction is performed on the other side.
- a technique has been proposed in which a device is provided and the dust is guided to the suction device and removed by suction.
- the present invention eliminates the problem of dust, which is insufficient with dust recovery using the gas flow described above, prevents the laser irradiation ability from being reduced due to contamination, and reliably reduces the iron loss of grain-oriented electrical steel sheets. It is an object to propose an apparatus and method that can be performed.
- the dust generated when the laser beam is irradiated onto the surface of the directionally annealed grain-oriented electrical steel sheet is caused by the evaporation of the steel sheet surface including the coating. . Therefore, the contamination is most severe when the irradiation device (laser radiation point) is directly above the laser irradiation point on the steel plate, and the contamination is more likely as the distance between the steel plate and the irradiation device is shorter.
- the irradiation device is retracted from directly above the laser irradiation point on the steel plate, contamination of the irradiation device cannot be completely prevented.
- the gist configuration of the present invention is as follows.
- An iron loss improvement device that reduces the iron loss of a magnetic steel sheet by irradiating the surface of a directionally annealed grain-oriented electrical steel sheet with a laser, the laser radiation point in the laser irradiation device and the laser irradiation on the steel plate
- L is 50 or more
- a directional electromagnetic steel sheet (hereinafter simply referred to as a steel sheet) S that has been subjected to finish annealing is unwound from a payoff reel 1, and a tension reel 2 via a pinch roll 3 and a support roll 4.
- a steel sheet S that has been subjected to finish annealing is unwound from a payoff reel 1, and a tension reel 2 via a pinch roll 3 and a support roll 4.
- L is 50 or more. Is important. That is, dust generated on the surface of the steel sheet S by laser irradiation is scattered at a high initial velocity, and therefore, if the distance from the dust generation source is less than 50 mm, contamination of the irradiation device 5 is completely suppressed even if the irradiation direction is changed. It becomes difficult.
- the angle ⁇ is important to regulate the angle ⁇ as follows in relation to the distance L. That is, When L ⁇ 100, 60-0.3L ⁇ ⁇ ⁇ 60 When 100 ⁇ L ⁇ 400, 40-0.1L ⁇ ⁇ ⁇ 60 If 400 ⁇ L, ⁇ ⁇ 60 Thus, the irradiation device 5 is prevented from being contaminated by arranging the irradiation device at a position where the inclination ⁇ from the vertical at the laser irradiation point 6 becomes larger as the distance L is shorter.
- the angle ⁇ is smaller than each lower limit angle, dust tends to adhere to the laser radiation point 7 of the irradiation device 5 (generally, a cover glass that protects the irradiation device), and frequent cleaning is required. Become.
- the upper limit of L is not limited as long as the laser can be focused, and the longer the distance, the more advantageous against contamination.
- the distance exceeds 400 mm dust (irradiation device) is present even in the vertical direction of the irradiation point. (Excluding the case where the dust is directly below the irradiation point and the dust falls to the irradiation point).
- the laser beam is irradiated in a state where the steel plate is horizontal, but the plate passing direction may have an inclination with respect to the horizontal direction.
- dust scatters most in the vertical direction regardless of the state of the steel sheet.
- the laser radiation point of the irradiation device and the irradiation point on the steel sheet If the angle formed by the connecting straight line and the vertical direction of the irradiation point on the steel sheet is within the range of the present invention, contamination is reliably prevented.
- the apparatus of the present invention is configured so that the irradiation apparatus 5 can be arranged at an arbitrary position within a range of L from 50 mm to the mechanical upper limit, and ⁇ that has the above-mentioned relationship with L can be set.
- the setting range of L may be made narrower, including the case where L is a fixed value. That is, as an example of such an apparatus, there is an apparatus that irradiates the surface of a steel sheet with ⁇ satisfying the above relationship, and thus with L being a value less than 400 mm (and thus ⁇ > 0 °).
- a device for controlling gas flow such as gas blowing or suction or an air curtain may be used in combination.
- the grain-oriented electrical steel sheet to be used for iron loss improvement in the present invention may be any conventional grain-oriented electrical steel sheet, but needs to be after finish annealing and formation of a tension coating.
- Heat treatment at a high temperature is required for finish annealing for growing goss-oriented secondary recrystallization, which is a characteristic of grain-oriented electrical steel sheets, and for formation of a tensile insulating film and manifestation of a tension effect.
- high temperature treatment removes or reduces strain introduced into the steel sheet, it must be performed before the magnetic domain refinement treatment of the present invention.
- the iron loss of the grain-oriented electrical steel sheet subjected to the magnetic domain refinement treatment is smaller when the orientation accumulation of secondary recrystallization is higher.
- B 8 magnetic flux density when magnetized at 800 A / m
- the grain-oriented electrical steel sheet used in the present invention has a B 8 of 1.88 T or more, more preferably 1.92 T or more. Those are preferred.
- the tension insulating coating formed on the surface of the electromagnetic steel plate or the forsterite coating formed on the surface of the steel plate by finish annealing may be a conventionally known tension insulating coating, but aluminum phosphate or magnesium phosphate and silica. It is preferable that it is a vitreous tension insulating coating mainly composed of.
- thermal strain As a means for introducing thermal strain, a known method such as pulse oscillation of a YAG laser, CO 2 laser, fiber laser, or continuous oscillation, or the like can be used.
- the present invention is particularly useful in the case where dust is generated due to instantaneous evaporation of the coating film due to high peak output such as a Q-switched pulse laser.
- the thermal strain is introduced linearly in a direction forming 90 ° to 60 ° with respect to the rolling direction, particularly in a direction perpendicular to the rolling direction, but may be continuous or dotted. This linear strain introduction region is formed repeatedly at intervals of 2 mm or more and 20 mm or less in the rolling direction.
- the depth of plastic strain applied to the steel sheet is preferably about 5 to 40 ⁇ m.
- An example of suitable irradiation conditions of the present invention is that the output of a Q-switched pulse YAG laser is 1 to 6 mJ per pulse, the focal point is 0.1 to 0.5 mm, and the dotted line is perpendicular to the rolling direction. Lines irradiated at intervals of 2 to 0.6 mm are repeated at intervals of 2 to 10 mm in the rolling direction.
- the method of the present invention is characterized by the strain introduction treatment applied to the grain-oriented electrical steel sheet on which the tension insulating coating is formed after the secondary recrystallization annealing. Therefore, the material may generally follow the grain-oriented electrical steel sheet. .
- an electromagnetic steel material containing Si: 2.0 to 8.0% by mass may be used.
- Si: 2.0-8.0% by mass Si is an element effective for increasing the electrical resistance of steel and improving iron loss, and its content of 2.0% by mass or more is particularly effective for reducing iron loss.
- the Si content is preferably in the range of 2.0 to 8.0% by mass.
- C 0.08 mass% or less C is added to improve the hot-rolled sheet structure, but if it exceeds 0.08 mass%, the burden of reducing C to 50 massppm or less where no magnetic aging occurs during the manufacturing process increases. Therefore, the content is preferably 0.08% by mass or less.
- the lower limit since a secondary recrystallization is possible even for a material not containing C, it is not particularly necessary to provide it.
- Mn 0.005 to 1.0 mass%
- Mn is an element advantageous for improving the hot workability, but if the content is less than 0.005% by mass, the effect of addition is poor. On the other hand, if it is 1.0 mass% or less, the magnetic flux density of a product board will become especially favorable. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
- Al and N are used when an AlN-based inhibitor is used, and Mn is used when an MnS ⁇ MnSe-based inhibitor is used.
- An appropriate amount of Se and / or S may be contained.
- the preferred contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, S: 0.005 to 0.03 mass%, and Se: 0.005 to 0.03 mass%, respectively.
- the present invention can also be applied to grain-oriented electrical steel sheets in which the contents of Al, N, S, and Se are limited and no inhibitor is used.
- the amounts of Al, N, S and Se are preferably suppressed to Al: 100 mass ppm or less, N: 50 mass ppm or less, S: 50 mass ppm or less, and Se: 50 mass ppm or less.
- Ni 0.03-1.50 mass%
- Sn 0.01-1.50 mass%
- Sb 0.005-1.50 mass%
- Cu 0.03-3.0 mass%
- P 0.03-0.50 mass%
- Mo 0.005-0.10 mass%
- Cr At least one Ni selected from 0.03 to 1.50 mass% is an element useful for further improving the magnetic properties by further improving the hot rolled sheet structure.
- the content is less than 0.03% by mass, the effect of improving magnetic properties is small.
- the content is 1.5% by mass or less, the stability of secondary recrystallization increases, and the magnetic properties are improved. Therefore, the Ni content is preferably in the range of 0.03 to 1.5% by mass.
- Sn, Sb, Cu, P, Cr, and Mo are elements that are useful for further improving the magnetic properties, but if any of them is less than the lower limit of each component, the effect of improving the magnetic properties is small.
- the amount is not more than the upper limit amount of each component described above, the secondary recrystallized grains develop best. For this reason, it is preferable to make it contain in said range, respectively.
- the balance other than the above components is preferably inevitable impurities and Fe mixed in the manufacturing process.
- the grain-oriented electrical steel sheet contains 3.4% by mass of Si, the magnetic flux density (B 8 ) at 800 A / m is 1.93 T and 1.7 T, and the iron loss (W 17/50 ) at 50 Hz is 0.90 W / kg is a general high-oriented grain-oriented electrical steel sheet, and the tensile insulation coating was baked at 840 ° C with a chemical solution consisting of colloidal silica, magnesium phosphate and chromic acid formed on the forsterite coating. It is a general tension insulating coating.
- the laser transmitter is a Q-switched pulse YAG laser, the output is 4 mJ per pulse, the beam diameter is 0.3 mm, the pulse repetition frequency is 25 kHz, and a dotted line with a spot spacing of 0.4 mm over a width of 120 mm in a direction perpendicular to the rolling direction by a galvano scanner.
- the film at the irradiation point was evaporated and peeled off.
- the laser beam transmittance was determined to be 90% or more as good and less than 90% as bad. As shown in FIG. 2, the contamination can be satisfactorily suppressed under the distance L and the angle ⁇ according to the present invention.
- the average value of the iron loss W 17/50 after the treatment was within the range of the present invention, 0.75 W / kg at the start of the continuous treatment, and 0.75 W / kg after the continuous four-day irradiation.
- it was 0.75 W / kg at the start of the continuous treatment, but deteriorated to 0.80 W / kg or more after continuous 4-day irradiation.
- Investigation of the material after processing revealed that the cause of the iron loss deterioration was a decrease in the laser irradiation energy. By the way, when the cover glass of the irradiation device was cleaned and the irradiation test was performed again, the iron loss after the treatment recovered to 0.75 W / kg.
- the iron loss reduction treatment by laser irradiation can be performed stably over a long period of time. For this reason, a high quality grain-oriented electrical steel sheet product can be provided stably, and an increase in manufacturing cost and a decrease in manufacturing efficiency can be avoided.
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Abstract
Description
そのためには、鋼板中の二次再結晶粒を、(110)[001]方位(いわゆる、ゴス方位)に高度に揃えることや、製品鋼板中の不純物を低減することが重要である。しかしながら、結晶方位を制御することや、不純物を低減することは、製造コストとの兼ね合い等で限界がある。そこで、鋼板の表面に対して物理的な手法で不均一性(歪)を導入し、磁区の幅を細分化して鉄損を低減する技術、すなわち磁区細分化技術が開発されている。
そこで、方向性電磁鋼板へのレーザー照射時に発生する粉塵の拡散状況を鋭意検討したところ、レーザー照射による鉄損改善効果を損ねることなく、拡散した粉塵の影響を受けない位置について、レーザーの放射点から鋼板上の照射点までの距離と、レーザーの照射角度との相関から導き出せることを知見し、本発明を完成するに到った。
(1)仕上げ焼鈍済みの方向性電磁鋼板の表面にレーザーを照射して電磁鋼板の鉄損を減少させる鉄損改善装置であり、前記レーザーの照射装置におけるレーザー放射点と前記鋼板上におけるレーザー照射点との距離をL(mm)、前記レーザー放射点と前記レーザー照射点とを結ぶ直線が鉛直方向となす角度をθ(°)とするとき、Lを50以上とし、かつ
L≦100の場合は、60-0.3L≦θ≦60
100<L≦400の場合は、40-0.1L≦θ≦60
400<Lの場合は、θ≦60
となる位置に、前記レーザー放射点を配することを特徴とする方向性電磁鋼板の鉄損改善装置。
(2)仕上げ焼鈍済みの方向性電磁鋼板の表面にレーザーを照射して電磁鋼板の鉄損を減少させるに当り、前記レーザーの照射装置におけるレーザー放射点と前記鋼板上におけるレーザー照射点との距離をL(mm)、前記レーザー放射点と前記レーザー照射点とを結ぶ直線が鉛直方向となす角度をθ(°)とするとき、Lを50以上とし、かつ
L≦100の場合は、60-0.3L≦θ≦60
100<L≦400の場合は、40-0.1L≦θ≦60
400<Lの場合は、θ≦60
となる位置に、前記レーザー放射点を配することを特徴とする方向性電磁鋼板の鉄損改善方法。
すなわち、レーザー照射によって鋼板S表面で発生する粉塵は、大きな初速度で飛散するため、粉塵発生源との距離が50mm未満では、照射方向を変えたとしても照射装置5の汚染を完全に抑制することが困難になる。
すなわち、
L≦100の場合は、60-0.3L≦θ≦60
100<L≦400の場合は、40-0.1L≦θ≦60
400<Lの場合は、θ≦60
となるように、照射装置を距離Lが近いほどレーザー照射点6における垂直からの傾きθが大きく傾く位置に配することにより、照射装置5の汚染を防止する。
各々の下限角度よりも角度θが小さい場合は、粉塵が照射装置5のレーザー放射点7(一般的には照射装置を保護するカバーガラスとなる)に付着しやすくなり、頻繁な清掃が必要になる。一方、いずれの場合も、角度θが60°を超えると照射点6のビーム形状は楕円状に引き伸ばされ、レーザー照射による歪導入領域が過大になって鉄損が劣化しやすくなるため、θは60°以下とする。
本発明の装置としては、Lを50mmから機械的上限までの範囲の、任意の位置に照射装置5を配置できるように構成し、Lと上記の関係にあるθを設定可能としたものが適合する。他方、Lを固定値とする場合を含み、Lの設定範囲をより狭くしてもよい。すなわち、このような装置の例としては、Lを400mm未満の値とし、上記関係を満たすθ(従ってθ>0°)にて鋼板表面をレーザー照射する装置がある。また、他の例としては、発振器の種類をファイバーレーザー等の高集光性のものとしてLを400mm以上の値とし、上記関係を満たすθ(θ=0°を含む)にて鋼板表面をレーザー照射する装置でもよい。
また、磁区細分化処理を施した方向性電磁鋼板の鉄損は、二次再結晶の方位集積が高い方がより小さいことが知られている。この方位集積の目安として、B8(800A/mで磁化した際の磁束密度)がよく用いられるが、本発明に用いる方向性電磁鋼板はB8が1.88T以上、より好ましくは1.92T以上のものが好適である。
本発明の好適な照射条件の例は、Qスイッチパルス型YAGレーザーの出力を1パルス当たり1~6mJとし、焦点径0.1~0.5mmに集光し、圧延方向に直交する方向に点線状に0.2~0.6mm間隔で照射したラインを圧延方向に2~10mm間隔で繰り返すものである。
Si:2.0~8.0質量%
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であり、含有量が2.0質量%以上でとくに鉄損低減効果が良好である。一方、8.0質量%以下の場合、とくに優れた加工性や磁束密度を得ることができる。したがって、Si量は2.0~8.0質量%の範囲とすることが好ましい。
C:0.08質量%以下
Cは、熱延板組織の改善のために添加をするが、0.08質量%を超えると製造工程中に磁気時効の起こらない50質量ppm以下までCを低減する負担が増大するため、0.08質量%以下とすることが好ましい。なお、下限に関しては、Cを含まない素材でも二次再結晶が可能であるので特に設ける必要はない。
Mnは、熱間加工性を良好にする上で有利な元素であるが、含有量が0.005質量%未満ではその添加効果に乏しい。一方1.0質量%以下とすると製品板の磁束密度がとくに良好となる。このため、Mn量は0.005~1.0質量%の範囲とすることが好ましい。
さらに、本発明は、Al、N、S、Seの含有量を制限した、インヒビターを使用しない方向性電磁鋼板にも適用することができる。この場合には、Al、N、SおよびSe量はそれぞれ、Al:100 質量ppm以下、N:50 質量ppm以下、S:50 質量ppm以下、Se:50 質量ppm以下に抑制することが好ましい。
Ni:0.03~1.50質量%、Sn:0.01~1.50質量%、Sb:0.005~1.50質量%、Cu:0.03~3.0質量%、P:0.03~0.50質量%、Mo:0.005~0.10質量%およびCr:0.03~1.50質量%のうちから選んだ少なくとも1種
Niは、熱延板組織をさらに改善して磁気特性をさらに向上させるために有用な元素である。しかしながら、含有量が0.03質量%未満では磁気特性の向上効果が小さい。一方1.5質量%以下ではとくに二次再結晶の安定性が増し、磁気特性が改善される。そのため、Ni量は0.03~1.5質量%の範囲とするのが好ましい。
なお、上記成分以外の残部は、製造工程において混入する不可避的不純物およびFeとすることが好ましい。
1 ペイオフリール
2 テンションリール
3 ピンチロール
4 支持ロール
5 照射装置
6 レーザー照射点
7 レーザー放射点
Claims (2)
- 仕上げ焼鈍済みの方向性電磁鋼板の表面にレーザーを照射して電磁鋼板の鉄損を減少させる鉄損改善装置であり、前記レーザーの照射装置におけるレーザー放射点と前記鋼板上におけるレーザー照射点との距離をL(mm)、前記レーザー放射点と前記レーザー照射点とを結ぶ直線が鉛直方向となす角度をθ(°)とするとき、Lを50以上とし、かつ
L≦100の場合は、60-0.3L≦θ≦60
100<L≦400の場合は、40-0.1L≦θ≦60
400<Lの場合は、θ≦60
となる位置に、前記レーザー放射点を配する方向性電磁鋼板の鉄損改善装置。 - 仕上げ焼鈍済みの方向性電磁鋼板の表面にレーザーを照射して電磁鋼板の鉄損を減少させるに当り、前記レーザーの照射装置におけるレーザー放射点と前記鋼板上におけるレーザー照射点との距離をL(mm)、前記レーザー放射点と前記レーザー照射点とを結ぶ直線が鉛直方向となす角度をθ(°)とするとき、Lを50以上とし、かつ
L≦100の場合は、60-0.3L≦θ≦60
100<L≦400の場合は、40-0.1L≦θ≦60
400<Lの場合は、θ≦60
となる位置に、前記レーザー放射点を配する方向性電磁鋼板の鉄損改善方法。
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CN102787276B (zh) * | 2012-08-30 | 2014-04-30 | 宝山钢铁股份有限公司 | 一种高磁感取向硅钢及其制造方法 |
EP2918689B1 (en) * | 2012-11-08 | 2020-01-01 | Nippon Steel Corporation | Laser processing apparatus and laser irradiation method |
JP6070403B2 (ja) | 2013-05-13 | 2017-02-01 | トヨタ自動車株式会社 | レーザ表面処理方法及びレーザ表面処理装置 |
JP2015202594A (ja) * | 2014-04-11 | 2015-11-16 | セイコーエプソン株式会社 | 造形装置、造形方法 |
KR101881708B1 (ko) * | 2014-07-03 | 2018-07-24 | 신닛테츠스미킨 카부시키카이샤 | 레이저 가공 장치 |
JP6455593B2 (ja) * | 2015-04-20 | 2019-01-23 | 新日鐵住金株式会社 | 方向性電磁鋼板 |
KR102148383B1 (ko) * | 2016-01-22 | 2020-08-26 | 주식회사 포스코 | 방향성 전기강판의 자구미세화 방법과 그 장치 |
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