WO2025005025A1 - 方向性電磁鋼板の製造方法および誘導加熱装置 - Google Patents

方向性電磁鋼板の製造方法および誘導加熱装置 Download PDF

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WO2025005025A1
WO2025005025A1 PCT/JP2024/022732 JP2024022732W WO2025005025A1 WO 2025005025 A1 WO2025005025 A1 WO 2025005025A1 JP 2024022732 W JP2024022732 W JP 2024022732W WO 2025005025 A1 WO2025005025 A1 WO 2025005025A1
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mass
sheet
steel sheet
rolling
annealing
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PCT/JP2024/022732
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English (en)
French (fr)
Japanese (ja)
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祐介 下山
之啓 新垣
敬 寺島
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JFE Steel Corp
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JFE Steel Corp
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Priority to CN202480041649.XA priority Critical patent/CN121399280A/zh
Priority to EP24831886.7A priority patent/EP4729640A1/en
Priority to KR1020267001603A priority patent/KR20260023067A/ko
Priority to JP2024556643A priority patent/JP7722600B2/ja
Publication of WO2025005025A1 publication Critical patent/WO2025005025A1/ja
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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
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    • 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
    • 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
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
    • B23K35/0222—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in soldering or brazing
    • B23K35/0244—Powders, particles or spheres; Preforms made therefrom
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    • C21D2201/05—Grain orientation

Definitions

  • the present invention relates to a method for manufacturing grain-oriented electrical steel sheets and an induction heating device used in the decarburization annealing step of the manufacturing method.
  • Grain-oriented electrical steel sheet is a soft magnetic material that is mainly used as the iron core material for transformers and generators. It has a crystal structure in which the ⁇ 110 ⁇ 001> orientation (Goss orientation), which is the axis of easy magnetization of iron, is highly aligned in the rolling direction of the steel sheet, so it has excellent magnetic properties, with low core loss and high magnetic flux density.
  • Goss orientation which is the axis of easy magnetization of iron
  • One way to further reduce the iron loss of grain-oriented electrical steel sheets is to highly concentrate the crystal grains in the Goss orientation after secondary recrystallization annealing.
  • To increase the concentration of secondary recrystallized grains in the Goss orientation it is important to form a large number of Goss-oriented grains in the steel sheet structure after primary recrystallization, and to create a difference in grain boundary mobility so that only sharp Goss-oriented grains grow preferentially during secondary recrystallization; in other words, it is important to optimize the texture of the steel sheet after primary recrystallization.
  • the primary recrystallization structure in which only sharp Goss orientation grains can grow preferentially includes ⁇ 111 ⁇ 112> orientation grains and ⁇ 411 ⁇ 148> orientation grains. By having these grains present in a balanced and frequent manner in the primary recrystallization structure, it is possible to highly accumulate Goss orientation grains in the rolling direction during secondary recrystallization annealing.
  • Patent Document 1 discloses a method in which a cold-rolled sheet is heat-treated at a low temperature during cold rolling and then aged.
  • Patent Document 2 discloses a method in which the cooling rate during hot-rolled sheet annealing or intermediate annealing before cold rolling to the final sheet thickness (final cold rolling) is 30°C/s or more, and interpass aging is performed two or more times during final cold rolling, in which the steel sheet is held at a temperature of 150 to 300°C for 2 minutes or more.
  • Patent Document 3 discloses a technology in which the steel sheet temperature during cold rolling is increased and then warm rolling is performed.
  • Patent Documents 1 to 3 all aim to improve the rolling texture by increasing the temperature of the steel sheet to an appropriate temperature before, during, or between passes of cold rolling, promoting the diffusion of solute elements carbon (C) and nitrogen (N) to fix dislocations introduced during cold rolling, inhibiting the movement of dislocations during subsequent rolling, and promoting shear deformation.
  • C solute elements carbon
  • N nitrogen
  • Patent Document 4 discloses a method of rapid heating during the heating process of decarburization annealing. This technology aims to suppress the development of gamma fiber structure ( ⁇ 111 ⁇ //ND), which is preferentially formed at normal heating rates, by heating from room temperature to near the recrystallization temperature in a short period of time using electrical heating or induction heating, and promote the formation of Goss-oriented grains, which serve as the nuclei of secondary recrystallized grains.
  • Patent Document 5 also discloses a method in which the decarburization annealing heating process involves rapid heating between 550 and 700°C at an average heating rate of 50°C/s or more, and maintaining the heating rate at 10°C/s or less for 1 to 10 seconds in any temperature range between 250 and 550°C.
  • This technology aims to promote the recovery of the ⁇ 111 ⁇ processed structure and suppress recrystallization by maintaining the temperature in the recovery temperature range of 250 to 550°C for a short period of time, thereby relatively increasing the proportion of Goss orientation grains.
  • Japanese Unexamined Patent Publication No. 50-016610 Japanese Patent Application Publication No. 08-253816 Japanese Patent Application Publication No. 01-215925 Japanese Patent Application Publication No. 04-160114 JP 2014-152393 A
  • the primary recrystallization texture is often not uniform across the width of the steel sheet. This can be caused by factors such as edge drop formed during hot rolling, which can result in the cold rolling reduction not being uniform across the width of the sheet, or the inability to heat the sheet evenly across the width by hot-rolled sheet annealing, which can result in non-uniform grain sizes across the width of the steel sheet before cold rolling.
  • edge drop formed during hot rolling which can result in the cold rolling reduction not being uniform across the width of the sheet, or the inability to heat the sheet evenly across the width by hot-rolled sheet annealing, which can result in non-uniform grain sizes across the width of the steel sheet before cold rolling.
  • the temperature drop at the ends of the steel sheet due to heat dissipation is large, and differences in the diffusion distances of carbon and nitrogen across the width of the sheet are also thought to be factors that cause the texture to change.
  • the secondary recrystallization behavior will also differ across the width of the sheet, causing the magnetic properties of the final product to vary across the width of the sheet.
  • One way to prevent this is to trim and remove the edges of the steel sheet after hot rolling or cold rolling, but this inevitably reduces the yield.
  • the present invention was made in consideration of the above problems with the conventional technology, and its purpose is to propose a method for manufacturing grain-oriented electrical steel sheet that has uniform and excellent magnetic properties in the sheet width direction, and to provide an induction heating device for decarburization annealing to be used in the method.
  • the inventors conducted extensive research into methods for homogenizing the primary recrystallization texture in the sheet width direction. As a result, they discovered that in the final cold rolling of the cold rolling process, the steel sheet is rolled at a temperature of 150°C or higher for at least one pass, and in the decarburization annealing that also serves as primary recrystallization annealing, when the temperature is rapidly increased from 500°C to 700°C during the temperature increase process, the heating rate is temporarily reduced during the process, and the time for this reduction is changed in the sheet width direction, thereby making it possible to homogenize the primary recrystallization texture after decarburization annealing in the sheet width direction, which led to the development of the present invention.
  • the present invention based on the above findings provides a method for producing a grain-oriented electrical steel sheet, which comprises hot rolling a steel material to obtain a hot-rolled sheet, cold rolling the hot-rolled sheet once or cold rolling two or more times with intermediate annealing in between to obtain a cold-rolled sheet of a final sheet thickness, subjecting the cold-rolled sheet to decarburization annealing that also serves as primary recrystallization annealing, and then subjecting the cold-rolled sheet to finish annealing for secondary recrystallization.
  • the steel sheet is rolled for at least one pass in a temperature range of 150° C. or more and 350° C.
  • the average heating rate T (° C./s) between 500° C. and 700° C. in the heating process is set to 250° C./s or more, and the heating rate at each position in the sheet width direction of the steel sheet in any of the temperature ranges between 500° C. and 700° C.
  • x/w is calculated according to the value of x/w at each position, as expressed by the following formula (1): 200/T ⁇ 0.2(1-x/w) ⁇ t ⁇ 200/T ⁇ 0.8(1-x/w)...(1)
  • x is the distance from the center of the plate width (mm)
  • w is 1/2 of the plate width (mm)
  • 0 ⁇ x ⁇ 0.9w The present invention proposes a method for producing a grain-oriented electrical steel sheet, characterized in that the temperature is reduced to 150° C./s or less for a time t (s) that satisfies the above condition.
  • the manufacturing method of the grain-oriented electrical steel sheet of the present invention is characterized in that the final cold rolling includes rolling at least one pass in a temperature range of 30°C to 130°C, and then rolling at least one pass in a temperature range of 150°C to 350°C.
  • the steel material used in the manufacturing method of the grain-oriented electrical steel sheet of the present invention is characterized by having a composition containing C: 0.01-0.10 mass%, Si: 2.0-4.5 mass%, Mn: 0.01-0.50 mass%, Al: 0.0100-0.0400 mass%, and N: 0.0050-0.0120 mass%, and further containing at least one of S and Se: 0.01-0.05 mass% in total, with the balance being Fe and unavoidable impurities.
  • the steel material used in the manufacturing method of the grain-oriented electrical steel sheet of the present invention is characterized by having a composition containing C: 0.01-0.10 mass%, Si: 2.0-4.5 mass%, Mn: 0.01-0.50 mass%, Al: less than 0.0100 mass%, N: 0.0050 mass% or less, S: less than 0.0100 mass%, and Se: less than 0.0100 mass%, with the balance being Fe and unavoidable impurities.
  • the steel material used in the manufacturing method of the grain-oriented electrical steel sheet of the present invention is characterized in that, in addition to the above-mentioned composition, it further contains at least one component selected from Sb: 0.005-0.500 mass%, Cu: 0.01-1.50 mass%, P: 0.005-0.500 mass%, Cr: 0.01-1.50 mass%, Ni: 0.005-1.500 mass%, Sn: 0.01-0.50 mass%, Nb: 0.0005-0.0100 mass%, Mo: 0.01-0.50 mass%, B: 0.0010-0.0070 mass%, and Bi: 0.0005-0.0500 mass%.
  • the method for producing the grain-oriented electrical steel sheet of the present invention is also characterized in that the rapid heating in the decarburization annealing is carried out using a transverse type induction heating device.
  • the present invention also relates to a transverse type induction heating device used for rapid heating in the decarburization annealing process in the above-mentioned method for producing grain-oriented electrical steel sheet.
  • the present invention makes it possible to stably manufacture grain-oriented electrical steel sheets that have uniform and excellent magnetic properties in the width direction of the steel sheet, which contributes greatly to improving the quality and yield of finished sheets.
  • FIG. 2 is a diagram for explaining a range of time for decreasing the temperature rise rate in the sheet width direction that is suitable for the present invention.
  • FIG. 11 is another diagram for explaining the range of the temperature rise rate reduction time in the sheet width direction that is suitable for the present invention.
  • FIG. 2 is a schematic diagram illustrating a transverse type induction heating device.
  • Example 1 A steel slab containing 0.033 mass% C, 3.4 mass% Si, 0.07 mass% Mn, 0.0081 mass% sol.Al, 0.0052 mass% N, 0.0030 mass% S and 0.0030 mass% Se, with the balance being Fe and unavoidable impurities, was heated to 1220 ° C. and then hot rolled to obtain a hot-rolled sheet having a thickness of 2.0 mm. Next, the hot-rolled sheet was subjected to hot-rolled sheet annealing at 1000 ° C. x 60 s, and then cold-rolled once to obtain a cold-rolled sheet having a final thickness of 0.20 mm.
  • the cold rolling was performed by warm rolling, in which the steel sheet temperature at the position just before the roll bite was increased to 200 ° C. by induction heating.
  • each of the above samples was subjected to decarburization annealing, which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100s.
  • the average heating rate during the heating process of decarburization annealing from 500°C to 700°C was 300°C/s, and further, under some conditions, the heating rate was reduced to 120°C/s for the time shown in Table 1 when 600°C was reached.
  • an annealing separator mainly composed of MgO was applied to the sample surface after the above decarburization annealing, and then finish annealing was performed to cause secondary recrystallization.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3:1:2 was applied to the sample surface after the above finish annealing, and the sample was baked by performing a heat treatment simulating flattening annealing at 800°C x 30s to obtain a product plate sample.
  • the average heating rate of 300°C/s between 500°C and 700°C is the average heating rate excluding the time during which the heating rate is reduced.
  • the cold rolling reduction rate is lower at the width ends than at the width center due to edge drop during hot rolling. This means that the amount of deformation during cold rolling is smaller at the width ends.
  • the temperature of the steel sheet during cold rolling is more likely to be lower at the width ends than at the width center due to heat dissipation. Due to these factors, the diffusion distance of carbon and nitrogen in the steel at the width ends is smaller, making it difficult for dislocations formed during rolling to be fixed, so the cold rolled structure at the width ends has less shear bands, which are the formation sites of Goss-oriented grains in primary recrystallization, than at the width center.
  • an annealing separator mainly composed of MgO was applied to the sample surface after the decarburization annealing, and the sample was subjected to finish annealing to cause secondary recrystallization.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3: 1: 2 was applied to the sample surface after the finish annealing, and the sample was baked by performing a heat treatment simulating flattening annealing at 800 ° C. x 30 s to obtain a product sheet sample.
  • the iron loss W 17/50 was measured in accordance with JIS Z 2550, and the difference between the maximum and minimum iron loss values in the sheet width direction is shown in Table 2.
  • x is the distance from the center of the plate width (mm)
  • w is 1/2 of the plate width (mm)
  • the steel material used in the present invention can be any conventionally known material used in the manufacture of grain-oriented electrical steel sheets, but from the perspective of obtaining excellent magnetic properties, it is preferable that the steel material has the following composition.
  • C 0.01 ⁇ 0.10mass% C is an element that contributes to improving the primary recrystallization texture by precipitating as fine carbides. However, if the C content is less than 0.01 mass%, the amount of precipitation of fine carbides is insufficient. On the other hand, if the content exceeds 0.10 mass%, it may be difficult to reduce the content to 0.0050 mass% or less, at which magnetic aging does not occur during decarburization annealing. Therefore, the C content is preferably in the range of 0.01 to 0.10 mass%, and more preferably in the range of 0.015 to 0.08 mass%.
  • Si 2.0 to 4.5 mass% Silicon is an element effective in increasing the resistivity of steel and improving iron loss. However, if the Si content is less than 2.0 mass%, the above-mentioned iron loss reduction effect cannot be sufficiently obtained. If the Si content exceeds 4.5 mass%, the workability is significantly reduced, and it becomes difficult to manufacture by rolling. Therefore, the Si content is preferably in the range of 2.0 to 4.5 mass%. is in the range of 2.5 to 4.0 mass%.
  • Mn 0.01 to 0.50 mass%
  • Mn is an element necessary for improving hot workability. If the Mn content is less than 0.01 mass%, it becomes difficult to obtain the above-mentioned effect of improving hot workability. On the other hand, if the Mn content is less than 0.50 mass%, If the Mn content exceeds 0.01 to 0.50 mass%, the primary recrystallized texture may deteriorate, and it may become difficult to obtain secondary recrystallized grains in which the Goss orientation is highly accumulated.
  • the range of 0.03 to 0.45 mass% is preferable, and the range of 0.03 to 0.45 mass% is more preferable.
  • the components other than the above C, Si and Mn differ depending on whether or not an inhibitor is used in the secondary recrystallization. Specifically, when an inhibitor is used for secondary recrystallization and AlN is used as the inhibitor, it is preferable to contain Al and N in the ranges of Al: 0.0100 to 0.0400 mass% and N: 0.0050 to 0.0120 mass% in addition to the above-mentioned C, Si, and Mn. If the Al content and N content are below the above-mentioned lower limit, it becomes difficult to obtain a desired inhibitor effect. On the other hand, if they exceed the above-mentioned upper limit, the dispersion state of the precipitates becomes non-uniform, and it also becomes difficult to obtain a desired inhibitor effect.
  • sulfides MnS, Cu 2 S, etc.
  • selenides MnSe, Cu 2 Se, etc.
  • the above sulfides and selenides may be precipitated in combination.
  • the steel material used to manufacture the grain-oriented electrical steel sheet of the present invention consists essentially of Fe and unavoidable impurities other than the above basic components.
  • Sb, Cu, P, Cr, Ni, Sn, Nb, Mo, B and Bi are elements that are useful for improving magnetic properties, and within the above ranges, the effect of improving magnetic properties can be obtained without inhibiting the development of secondary recrystallized grains.
  • the steel material (slab) used in the production of the grain-oriented electrical steel sheet of the present invention is preferably produced by melting steel having the above-described composition in a commonly known refining process in which molten steel obtained in a converter, electric furnace or the like is subjected to secondary refining such as vacuum degassing, and then converting the steel material into a steel material by a commonly known continuous casting method, ingot casting-slabbing rolling method or the like.
  • the steel material (slab) is heated to a predetermined temperature and then hot-rolled to obtain a hot-rolled sheet.
  • the heating temperature of the slab is preferably about 1050°C or higher from the viewpoint of ensuring hot rolling properties. There is no particular upper limit to the heating temperature, but if it exceeds 1450°C, it approaches the melting point of the steel and it becomes difficult to maintain the shape of the slab, so it is preferably 1450°C or lower.
  • the hot rolling following the slab heating can be carried out under generally known conditions, and is not particularly limited.
  • the steel sheet (hot-rolled sheet) after the above-mentioned hot rolling may be subjected to hot-rolled sheet annealing as necessary.
  • hot-rolled sheet annealing is performed, generally known conditions can be applied, and there are no particular limitations.
  • the reduction ratio of the final cold rolling is preferably in the range of 60% to 95%.
  • the above final cold rolling refers to the cold rolling that is performed last among one or more cold rollings. For example, when cold rolling is performed only once, that one rolling is the final cold rolling, and when cold rolling is performed two or more times, the final rolling is the final cold rolling.
  • At least one pass of rolling is performed at a rolling temperature in the low temperature range of 30°C to 130°C, and then at least one pass of rolling is performed at a rolling temperature in the high temperature range of 150°C to 350°C, thereby further enhancing the effect of increasing the Goss orientation grains in the primary recrystallization.
  • the ⁇ 111 ⁇ 112> orientation is a stable rolling orientation whose orientation does not change due to rolling, first rolling in the low temperature range to develop the ⁇ 111 ⁇ 112> structure, and then further rolling in the high temperature range, the shear bands formed in the ⁇ 111 ⁇ 112> processed structure, which serves as the nucleation site of the Goss orientation grains in the primary recrystallization, can be efficiently increased. If the rolling temperature in the low temperature range is less than 30°C, there is a risk that the sheet will crack and productivity will decrease significantly. On the other hand, if it exceeds 130°C, the ⁇ 111 ⁇ 112> structure will decrease conversely.
  • the preferred rolling temperature in the low temperature range is 40°C or higher and 100°C or lower.
  • decarburization annealing which also serves as primary recrystallization annealing.
  • the decarburization conditions (conditions during soaking) in this decarburization annealing can be any known condition and are not particularly limited, but for example, conditions of 720 to 870°C x 60 to 150s in a wet hydrogen atmosphere are preferable.
  • This decarburization annealing reduces the C content in the steel sheet to 0.0050 mass% or less, at which point magnetic aging does not occur.
  • the sheet width range that satisfies the above formula (1) is set to (0 ⁇ x ⁇ 0.9w) is that when transverse induction heating is used for rapid heating, the induced current flows concentratedly at the sheet width end, and there is a risk that the formula (1) cannot be satisfied over the entire width. Of course, it is preferable to satisfy the above formula (1) over the entire width.
  • the rate of heating that is temporarily reduced must be 150°C/s or less. At a rate of heating higher than this, the effect of suppressing the recrystallization of Goss-oriented grains becomes insufficient. There is no particular lower limit to the rate of heating that is reduced, but it is preferably 10°C/s or more.
  • the time period during which the rate of heating is temporarily reduced can be obtained by measuring the temperature of the steel sheet during the heating process with a thermocouple or the like and differentiating the temperature of the steel sheet at each time with respect to time.
  • the time for which the heating rate decreases can be adjusted by changing the output or line speed of the induction heating device.
  • the transverse type induction heating device can be preferably used in the present invention.
  • the coil diameter in the plate passing direction may be made larger in the center of the plate width and gradually become smaller toward the plate width ends.
  • the shape of the heating coil in the transverse type induction heating device may be any shape such as round, square, or elliptical, but as described above, it is preferable to change the coil diameter in the plate passing direction in the plate width direction.
  • the cold-rolled sheet that has been subjected to the above-mentioned decarburization annealing is subjected to finish annealing for secondary recrystallization after applying an annealing separator to the surface of the steel sheet.
  • an annealing separator a known one can be used, and there is no particular limitation thereto.
  • one containing MgO as the main component and adding an auxiliary such as TiO2 as necessary, one containing SiO2 or Al2O3 as the main component, etc. can be mentioned.
  • the steel sheet that has been subjected to the above-mentioned finish annealing is preferably subjected to the removal of unreacted annealing separator remaining on the steel sheet surface, followed by coating the surface with an insulating coating liquid and baking it in a flattening annealing process that also corrects the shape of the steel sheet that has been deteriorated by the finish annealing, to produce a finished sheet.
  • the coating of the insulating coating may be performed in a separate line.
  • magnetic domain refinement may be performed by a known method, such as forming grooves on the steel sheet surface in any of the processes after the cold rolling, forming mechanically distorted regions on the steel sheet surface after finish annealing, or forming thermally distorted regions by irradiating the steel sheet with a laser beam or electron beam.
  • the hot-rolled sheet was then subjected to hot-rolled sheet annealing at 1000°C for 60 seconds, and then cold-rolled once to obtain a cold-rolled sheet with a final thickness of 0.20 mm.
  • the cold rolling was performed by warm rolling, in which the steel sheet was heated to 250°C by induction heating.
  • the cold-rolled steel sheets were subjected to decarburization annealing, which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100 s.
  • x is the distance from the center of the plate width (mm)
  • w is 1/2 of the plate width (mm) where 0 ⁇ x ⁇ 0.9w
  • the heating rate at each position in the sheet width direction was reduced by a time t represented by the formula (1) so as to achieve the "reduced heating rate" shown in Table 3.
  • an annealing separator mainly composed of MgO was applied to the surface of the steel sheet after the above-mentioned decarburization annealing, and the steel sheet was subjected to finish annealing to cause secondary recrystallization.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3:1:2 was applied to the surface of the steel sheet after the above-mentioned finish annealing, and the steel sheet was baked by planarization annealing at 800°C for 30 s to obtain a product sheet.
  • a steel slab containing inhibitor-forming components which contains 0.06 mass% C, 3.4 mass% Si, 0.06 mass% Mn, 0.0250 mass% sol.Al, 0.0090 mass% N, 0.01 mass% S, and 0.01 mass% Se, with the balance being Fe and unavoidable impurities, was heated to 1400 ° C. and then hot-rolled to a hot-rolled sheet having a thickness of 2.0 mm. The hot-rolled sheet was then subjected to a first cold rolling to obtain an intermediate thickness of 1.2 mm.
  • intermediate annealing was performed at 1100°C for 80s in an atmosphere of 75 vol% N2 + 25 vol% H2 with a dew point of 46°C, and then a second cold rolling (final cold rolling) was performed using a tandem rolling mill to obtain a cold-rolled sheet with a final thickness of 0.20 mm.
  • final cold rolling was performed using a tandem rolling mill to obtain a cold-rolled sheet with a final thickness of 0.20 mm.
  • the flow rate of coolant sprayed onto the steel sheet was adjusted so that the steel sheet temperature during final cold rolling was 160°C to 250°C.
  • the cold-rolled sheet was subjected to decarburization annealing, which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100s.
  • decarburization annealing which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100s.
  • a transverse-type induction heating device was used to rapidly heat the steel sheet from 500°C to 700°C at an average heating rate of 300°C/s.
  • the output of the induction heating device and the line speed were adjusted so that the time in the sheet width direction at which the heating rate T becomes 100°C/s when the steel sheet temperature reaches 650°C during the induction heating was the 6th condition shown in Figure 2.
  • an annealing separator mainly composed of MgO was applied to the surface of the steel sheet after the decarburization annealing, and the steel sheet was subjected to finish annealing to cause secondary recrystallization.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3:1:2 was applied to the surface of the steel sheet after the finish annealing, and the steel sheet was subjected to flattening annealing at 800°C x 30s and baked to form a product sheet.
  • Steel slab A had a composition containing 0.035 mass% C, 3.3 mass% Si, 0.05 mass% Mn, 0.0084 mass% sol. Al, 0.0051 mass% N, 0.0031 mass% S, 0.0031 mass% Se, and the balance being Fe and unavoidable impurities, and contained no inhibitor-forming components;
  • Steel slab B having a composition containing inhibitor-forming components, including Al: 0.0250 mass%, N: 0.0095 mass%, S: 0.01 mass%, and Se: 0.01 mass%, with the balance being Fe and unavoidable impurities, was heated to a temperature of 1300°C, and then hot-rolled to a hot-rolled sheet having a thickness of 2.0 mm.
  • the hot-rolled sheet produced from the above steel slab A was subjected to hot-rolled sheet annealing at 1000°C x 60s, and then cold-rolled once to a final thickness of 0.20 mm.
  • the hot-rolled sheet produced from the steel slab B was subjected to hot-rolled sheet annealing at 1000°C x 60s, then the first cold rolling to an intermediate sheet thickness of 1.2 mm, and intermediate annealing at 1100°C x 80s in an atmosphere of N2 : 75 vol% + H2 : 25 vol%, dew point 46°C, and then the second cold rolling to a cold-rolled sheet with a final sheet thickness of 0.20 mm.
  • the cold rolling to the final sheet thickness (final cold rolling) among the above cold rolling was performed in four passes, and cold rolling was performed at the steel sheet temperatures listed in Table 5.
  • the cold-rolled sheet was subjected to decarburization annealing, which also served as primary recrystallization annealing, with a soaking temperature of 850° C. and a soaking time of 100 s.
  • decarburization annealing which also served as primary recrystallization annealing, with a soaking temperature of 850° C. and a soaking time of 100 s.
  • the average temperature rise rate from 500° C. to 700° C.
  • an annealing separator mainly composed of MgO was applied to the surface of the steel sheet after the decarburization annealing, and secondary recrystallization was performed by performing finish annealing.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3:1:2 was applied to the surface of the steel sheet after the finish annealing, and the surface was baked by performing flattening annealing at 800°C for 30 seconds to obtain a product sheet.
  • the average value of the iron loss value in the sheet width direction and the difference between the maximum value and the minimum value were obtained, and the results are shown in Table 5. From Table 5, it can be seen that the steel sheets that were rolled at least once or more at a steel sheet temperature of 150 ° C. or more and 350 ° C.
  • the hot-rolled sheet was annealed at 1000°C for 60 seconds, and then cold-rolled once (final cold rolling) using a tandem rolling mill to produce a cold-rolled sheet with a final thickness of 0.20 mm.
  • final cold rolling the flow rate of the coolant sprayed onto the steel sheet was adjusted so that the steel sheet temperature during rolling was 250°C to 300°C.
  • the cold-rolled sheet was subjected to decarburization annealing, which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100s.
  • decarburization annealing which also served as primary recrystallization annealing, with a soaking temperature of 850°C and a soaking time of 100s.
  • a transverse-type induction heating device was used as in Example 2, and rapid heating was performed with an average heating rate of 300°C/s from 500°C to 700°C, and the time in the sheet width direction for lowering the heating rate to 110°C/s when the steel sheet temperature reached 650°C was set to be the same as the condition No. 1 in Figure 2.
  • an annealing separator mainly composed of MgO was applied to the surface of the steel sheet after the decarburization annealing, and then the steel sheet was subjected to finish annealing to cause secondary recrystallization.
  • an insulating coating liquid containing phosphate-chromate-colloidal silica in a mass ratio of 3:1:2 was applied to the surface of the steel sheet after the finish annealing, and the surface was subjected to flattening annealing at 800°C for 30s and baked to form a product sheet.
  • the average iron loss value in the plate width direction of the product plate and the difference between the maximum and minimum values were calculated, and the results are shown in Table 6.
  • the product sheets manufactured under conditions conforming to the method of the present invention using a slab containing at least one element selected from Sb, Cu, P, Cr, Ni, Sn, Nb, Mo, B and Bi as the steel material and using a transverse type induction heating device during the temperature increase process of decarburization annealing all have an average iron loss value in the sheet width direction of 0.80 W/kg or less, and the difference between the maximum and minimum iron loss values in the sheet width direction is 0.04 W/kg or less, and have uniform and excellent magnetic properties in the sheet width direction.

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JP2014047411A (ja) * 2012-09-03 2014-03-17 Jfe Steel Corp 連続焼鈍設備の急速加熱装置
JP2014152393A (ja) 2013-02-14 2014-08-25 Jfe Steel Corp 方向性電磁鋼板の製造方法
JP2019167568A (ja) * 2018-03-22 2019-10-03 日本製鉄株式会社 方向性電磁鋼板の製造方法
JP2019178378A (ja) * 2018-03-30 2019-10-17 日本製鉄株式会社 方向性電磁鋼板の製造方法
JP2020084303A (ja) * 2018-11-30 2020-06-04 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法
WO2024053627A1 (ja) * 2022-09-06 2024-03-14 Ｊｆｅスチール株式会社 方向性電磁鋼板の製造方法および誘導加熱装置

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