WO2022250157A1 - 方向性電磁鋼板の製造方法 - Google Patents

方向性電磁鋼板の製造方法 Download PDF

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WO2022250157A1
WO2022250157A1 PCT/JP2022/021830 JP2022021830W WO2022250157A1 WO 2022250157 A1 WO2022250157 A1 WO 2022250157A1 JP 2022021830 W JP2022021830 W JP 2022021830W WO 2022250157 A1 WO2022250157 A1 WO 2022250157A1
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less
annealing
sheet
hot
cold
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French (fr)
Japanese (ja)
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猛 今村
雅紀 竹中
広 山口
広朗 戸田
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JFE Steel Corp
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JFE Steel Corp
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • 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
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the present disclosure relates to a method for manufacturing a grain-oriented electrical steel sheet.
  • Electrical steel sheet is a material widely used as iron cores for transformers and motors. Electrical steel sheets are broadly classified into grain-oriented electrical steel sheets and non-oriented electrical steel sheets.
  • the ⁇ 001> orientation which is the axis of easy magnetization of iron, has a texture that is highly aligned in the rolling direction of the steel sheet. It is characteristic that Such a texture is formed by causing secondary recrystallization in the final annealing.
  • the secondary recrystallization refers to a phenomenon in which crystal grains of ⁇ 110 ⁇ 001> orientation, so-called Goss orientation, preferentially grow into large grains by utilizing grain boundary energy.
  • inhibitors As a representative technique for causing the above secondary recrystallization, there is a technique that utilizes precipitates called inhibitors. For example, a method using AlN and MnS described in Patent Document 1, a method using MnS and MnSe described in Patent Document 2, and the like are known and have been industrially put into practical use. Methods using these inhibitors are useful for stably developing secondary recrystallized grains. In these methods, in order to finely disperse the inhibitor in the steel, it is necessary to heat the slab at a high temperature of 1300° C. or higher to dissolve the inhibitor component once.
  • Patent Document 3 and the like disclose a technique for developing Goss-oriented crystal grains by secondary recrystallization in a material that does not contain an inhibitor component. By eliminating impurities such as inhibitor components as much as possible, the dependence of the grain boundary energy on the grain boundary during the primary recrystallization on the grain boundary misorientation angle is revealed, and the Goss orientation can be obtained without using an inhibitor. It is a technique for secondary recrystallization of grains with grains, and its effect is called texture inhibition effect. Since this method does not require fine dispersion of the inhibitor in the steel, it does not require high-temperature slab heating, which was essential, and thus has advantages over the method using the inhibitor in terms of production.
  • One of the uses of magnetic steel sheets is to roll them into a cylindrical shape as shown in Fig. 1, gradually changing the rolling diameter and laminating them in the radial direction to form an iron core.
  • the direction of excitation is one of the upper and lower directions in FIG. can be expected.
  • the present disclosure has been made in view of such circumstances, and an object thereof is to provide a grain-oriented electrical steel sheet with good processing accuracy in rounding while maintaining core loss characteristics.
  • a steel slab having a chemical composition consisting of Fe and unavoidable impurities is slab-heated to 1300 ° C.
  • the hot-rolled sheet is cold-rolled twice with intermediate annealing to obtain a cold-rolled sheet, Then, the cold-rolled sheet is subjected to decarburization annealing to obtain a decarburization-annealed sheet, Next, in the method for producing a grain-oriented electrical steel sheet, an annealing separator is applied to the surface of the decarburized annealed sheet, and then finish annealing is performed to obtain a grain-oriented electrical steel sheet,
  • the total rolling reduction R1 (%) of the first cold rolling and the total rolling reduction R2 (%) of the second cold rolling satisfy the following formula (1), Furthermore, in the final annealing, the average temperature increase rate H1 (° C./hr) from 50° C.
  • the steel slab is subjected to one pass or more of rough rolling at 1100° C. or higher and 1300° C. or lower, followed by two or more passes of finish rolling at 800° C. or higher and 1100° C. or lower. and the winding temperature is 400° C. or higher and 750° C. or lower
  • the hot-rolled sheet annealing the hot-rolled sheet is held at 800° C. or higher and 1250° C. or lower for 5 seconds or longer, and then cooled from 800° C. to 350° C. at an average cooling rate of 5° C./s or higher and 100° C./s or lower.
  • the cold-rolled sheet after the first cold rolling is held at 800 ° C. or higher and 1250 ° C. or lower for 5 seconds or longer, and then the average cooling rate from 800 ° C. to 350 ° C. is 5 ° C./s or more and 100 Cooling as below ° C / s
  • the decarburization annealing the cold-rolled sheet is heated to 750° C. or more and 950° C. in an atmosphere containing H 2 and N 2 and in a wet atmosphere having a dew point of 20° C. or more and 80° C. or less in at least a part of the decarburization annealing.
  • the annealing separator containing MgO is applied to the surface of the decarburized annealed sheet in an amount of 2.5 g/m 2 or more per side,
  • the decarburization-annealed sheet is held at 1050° C. or higher and 1300° C. or lower for 3 hours or more under conditions in which the atmosphere in at least a part of the temperature range of 1050° C. or higher contains H 2 .
  • the method for producing a grain-oriented electrical steel sheet according to 1.
  • the component composition is further mass % or mass ppm, Ni: 0% or more and 1.50% or less, Cr: 0% or more and 0.50% or less Cu: 0% or more and 0.50% or less, P: 0% or more and 0.50% or less, Sb: 0% or more and 0.50% or less, Sn: 0% or more and 0.50% or less, Bi: 0% or more and 0.50% or less, Mo: 0% or more and 0.50% or less, B: 0 ppm or more and 25 ppm or less, Nb: 0% or more and 0.020% or less, V: 0% or more and 0.010% or less and Zr: 0% or more and 0.10% or less containing one or more selected from the group consisting of [1] or [2].
  • a method for manufacturing an electromagnetic steel sheet is further mass % or mass ppm, Ni: 0% or more and 1.50% or less, Cr: 0% or more and 0.50% or less Cu: 0% or more and 0.50% or less, P:
  • the component composition is further mass %, Co: 0% or more and 0.050% or less and Pb: 0% or more and 0.0100% or less containing one or two selected from the group consisting of [1] to [3].
  • the above component composition is further mass %, As: 0% or more and 0.0200% or less, Zn: 0% or more and 0.020% or less, W: 0% or more and 0.0100% or less Ge: 0% or more and 0.0050% or less Ga: 0% or more and 0.0050% or less ] to [4], the method for producing a grain-oriented electrical steel sheet.
  • FIG. 10 is a diagram showing an ideal shape after rounding; It is a figure which shows the shape when processing precision is bad after a rounding process. It is a figure showing the parameter which shows the processing accuracy by rounding processing.
  • FIG. 2 is a diagram showing the relationship between the total rolling reduction of cold rolling and working accuracy. This is a diagram showing the relationship between the heating rate of finish annealing and the processing accuracy.
  • the present invention has made intensive studies on conditions for secondary recrystallization, and as a result, has succeeded in improving the processing accuracy of rounding by making secondary recrystallized grains finer.
  • the experiments that have led to the success of the present invention are described below.
  • the cold-rolled sheet was further subjected to decarburization annealing at 850° C. for 120 seconds, 60% H 2 +40% N 2 , dew point 60° C. to obtain a decarburization-annealed sheet.
  • decarburization annealing is performed at 1200 ° C. for 5 hours in an H 2 atmosphere to obtain a grain-oriented electrical steel sheet.
  • the heating rate was 25°C/hr from room temperature to 900°C, the heating rate was 18°C/hr from 900°C to 1150°C, and the heating rate was 1150°C to 1200°C. 10° C./hr.
  • a 60 mm square sample was cut out from the obtained grain-oriented electrical steel sheet. Then, the sample was rounded using a twin roll processing machine composed of an iron roll with a diameter of 20 mm and a urethane roll with a diameter of 300 mm. The direction of rounding was the direction perpendicular to the rolling of the sample (the width direction of the steel sheet).
  • H is the distance between the butted sample angles a and b
  • ⁇ is the angle between the two butted sides A and B.
  • H 2.0 mm and ⁇ : 0°. The greater the deviation from this value, the poorer the machining accuracy. If each parameter is within the ranges of H: 1.8 to 3.0 mm and ⁇ : 0 to 2.5°, the sample is judged as acceptable.
  • FIG. 4 shows the relationship between the total rolling reduction of the first and second cold rollings and the working accuracy. As shown in FIG. 4, when the total rolling reduction of the first and second cold rolling is both 50% or more and the total rolling reduction of the first cold rolling is larger than that of the second cold rolling, rounding It became clear that the processing accuracy in processing is good.
  • the sheet was first cold-rolled to a thickness of 0.68 mm.
  • the cold-rolled sheet was subjected to intermediate annealing at 1025° C.
  • the cold-rolled sheet is further subjected to decarburization annealing at 840° C. ⁇ 80 seconds, 50% H 2 +50% N 2 , dew point 60° C.
  • An annealing separator containing 90% by mass or more of MgO in terms of solid content on the surface of the steel sheet. was applied, and then finish annealing was performed at 1200°C for 10 hours in an H2 atmosphere to obtain a grain-oriented electrical steel sheet.
  • the temperature rising rate from room temperature to 900°C and the temperature rising rate from 900°C to 1150°C were variously changed.
  • the rate of temperature increase from 1150°C to 1200°C was 5°C/hr.
  • a 50 mm square sample was cut from the obtained grain-oriented electrical steel sheet, and the sample was rounded using a twin roll processing machine composed of an iron roll with a diameter of 20 mm and a urethane roll with a diameter of 300 mm.
  • the direction of rounding was the direction perpendicular to the rolling of the sample (the width direction of the steel sheet).
  • the processing accuracy of the obtained samples after rounding was evaluated in the same manner as in Experiment 1 for the processing accuracy in rounding.
  • FIG. 5 shows the relationship between the evaluation results of working accuracy and the reduction ratio of cold rolling.
  • the temperature increase rate H1 from room temperature to 900° C. is greater than 1.1 times the temperature increase rate H2 from 900° C. to 1150° C.
  • H1 is 5° C./hr or more and 40° C./s. It was found that the rounding shape was good in the following cases.
  • the size of the secondary recrystallized grains is clearly smaller in the grain-oriented electrical steel sheet in which the processing accuracy in rounding is good, compared to the grain-oriented electrical steel sheet in which the processing accuracy is inferior. It became clear. That is, it means that there are many grain boundaries of the secondary recrystallized grains under the condition that the processing accuracy in the rounding processing is good.
  • Rounding is a kind of plastic working and is considered to have crystal orientation dependence. That is, when rounding is performed in one direction, there is a slight misalignment in the orientation of each crystal grain, so the degree of processing of each crystal grain may differ slightly. It is thought that the grain boundaries that allow some accumulation of strain absorb the difference in the working degree of the crystal grains.
  • the grain boundaries are few, the grain boundaries cannot absorb the difference in the working degree of each crystal grain, and the steel sheet is distorted, resulting in poor working accuracy.
  • the difference can be absorbed, so it is considered that the processing accuracy is improved.
  • the present inventors have found that there are roughly two techniques for reducing the size of secondary crystal grains and increasing grain boundaries. First, it is possible to increase the number of crystal grains that are the source of secondary recrystallization, that is, the crystal grains having a Goss orientation, before finish annealing. Second, in the final annealing. The point is to control the conditions so that secondary recrystallization occurs simultaneously and from all locations. In this experiment, controlling the total rolling reduction of the two cold rollings within a certain range corresponds to the former, and defining the temperature rise rate in the final annealing corresponds to the latter.
  • C 0.01% or more and 0.10% or less, If the C content exceeds 0.10%, magnetic aging may occur after decarburization annealing. On the other hand, if the amount of C is less than 0.01%, secondary recrystallized grains become coarse, causing an increase in core loss and deterioration in bending workability. Therefore, C is limited to 0.01% or more and 0.10% or less. The amount of C is preferably 0.03% or more. Moreover, the amount of C is preferably 0.06% or less.
  • Si 2.0% or more and 4.0% or less Si is an element necessary for increasing the resistivity of steel and improving iron loss. %, the secondary recrystallization becomes unstable and the magnetic properties deteriorate, so the Si content is limited to 2.0% or more and 4.0% or less.
  • the amount of Si is preferably 3.0% or more.
  • the amount of Si is preferably 3.6% or less.
  • Mn 0.01% or more and 0.20% or less
  • Mn is an element necessary for using MnS or MnSe as an inhibitor. If it exceeds 0.20%, the secondary recrystallization becomes unstable and the magnetic properties deteriorate. Therefore, the Mn content is set to 0.01% or more and 0.20% or less.
  • the amount of Mn is preferably 0.03% or more.
  • the Mn amount is preferably 0.15% or less.
  • Ti and Al form nitrides, impairing the inhibitory effects of MnS and MnSe and degrading the magnetic properties. Therefore, Ti: 0.010% or less, Al: 0.010% or less, and N: 0.0050% or less.
  • Ti, Al and N are each 0.0020% or less.
  • Ti and Al are each preferably 0.001% or more, and N is 0.0005% or more.
  • the total content of S and Se should be in the range of 0.005% or more and 0.10% or less. It is preferably 0.010% or more and 0.040% or less.
  • Ni 0% to 1.50%
  • Cr 0% to 0.50%
  • Cu 0% to 0.50%
  • P 0% to 0.50%
  • Sb 0% or more and 0.50% or less
  • Sn 0% or more and 0.50% or less
  • Bi 0% or more and 0.50% or less
  • Mo 0% or more and 0.50% or less
  • B 0 ppm or more At least one selected from the group consisting of 25 ppm or less, Nb: 0% or more and 0.020% or less, V: 0% or more and 0.010% or less
  • Zr 0% or more and 0.10% or less
  • Ni 0.01% or more
  • Sb 0.005% or more
  • Sn 0.005% or more
  • Cu 0.01% or more
  • Cr 0.01%
  • P 0.005% or more
  • Mo 0.005% or more
  • Nb 0.001% or more
  • V 0.001% or more
  • B 0.0002% or more
  • Bi 0.005% or more
  • Zr It is preferable to add 0.001% or more.
  • Co 0% or more and 0.050% or less and Pb: 0% or more and 0.0100% or less for the purpose of further reducing the angle formed by the two butted sides A and B in terms of rounding workability.
  • Pb 0% or more and 0.0100% or less
  • the contents of these elements are equal to or less than the above upper limits, the magnetic properties are more favorable.
  • Co 0.002% or more and Pb: 0.0001% or more.
  • Magnetic properties are more favorable if each is equal to or less than the above upper limit.
  • a steel slab is manufactured using molten steel having the chemical composition described above.
  • the method of manufacturing the steel slab is not particularly limited, and the steel slab may be manufactured by a normal ingot casting method and continuous casting method, or a steel slab with a thickness of 100 mm or less may be manufactured by a direct casting method. These steel slabs are subjected to hot rolling after slab heating in the usual manner. Hot rolling may be performed immediately after casting without heating.
  • the steel slab is slab-heated to 1300°C or higher before hot rolling.
  • the inhibitor component can be sufficiently solid-dissolved.
  • the slab heating temperature is based on the surface temperature of the steel slab.
  • the hot rolling conditions are not particularly limited. From the viewpoint of controlling the structure of the hot-rolled sheet, the rough rolling is preferably performed at 1100° C. or higher, more preferably at 1300° C. or lower for one or more passes. Subsequently, from the viewpoint of controlling the structure of the hot-rolled sheet, it is preferable to carry out two or more passes of finish rolling at a temperature of 800° C. or higher and 1100° C. or lower. Further, it is preferable to set the winding temperature to 400° C. or higher and 750° C. or lower from the viewpoint of both control of carbide structure and prevention of defects such as cracks. The winding temperature is more preferably 500°C or higher and 700°C or lower. The temperature in hot rolling and the coiling temperature are based on the steel sheet surface temperature immediately before coiling.
  • the hot-rolled sheet is optionally subjected to hot-rolled sheet annealing.
  • the conditions for hot-rolled sheet annealing are not particularly limited, and conventional methods can be used.
  • the structure can be homogenized, and variations in magnetic properties can be reduced.
  • the annealing conditions for the hot-rolled sheet annealing are preferably set to 800° C. or more and 1250° C. or less and holding for 5 seconds or more. More preferably, the temperature is maintained at 900° C. or higher and 1150° C. or lower for 10 seconds or longer and 180 seconds or shorter.
  • Cooling after holding is a cooling rate of 5°C/s or more and 100°C/s or less in the temperature range from 800°C to 350°C, so that the morphology of the second phase and precipitates is appropriately controlled. It is preferable because it improves the magnetic properties.
  • the cooling rate after holding is more preferably 15° C./s or more and 45° C./s or less.
  • the annealing temperature in the hot-rolled sheet annealing is based on the surface of the hot-rolled sheet.
  • a method for removing scale is not particularly limited, and known methods such as a method using heated acid (pickling) and a method for mechanically removing scale may be used.
  • the hot-rolled sheet is subjected to two cold rollings with intermediate annealing to obtain a cold-rolled sheet having a final thickness.
  • the total rolling reduction R1 of the first cold rolling is higher than the total rolling reduction R2 of the second cold rolling, and the total rolling reductions R1 and R2 of the first cold rolling are of 50% or more is essential as described above. That is, the total rolling reduction R1 (%) of the first cold rolling and the total rolling reduction R2 (%) of the second cold rolling satisfy the following formula (1).
  • Both R1 and R2 refer to the total rolling reduction, and the number of passes of the first cold rolling and the second cold rolling and the rolling reduction in each pass are not particularly limited. R1 ⁇ R2 ⁇ 50 (1)
  • the total rolling reduction R1 of the first cold rolling is higher than the total rolling reduction R2 of the second cold rolling, and the total rolling reductions R1 and R2 of the first and second cold rolling are both 50%. By doing so, it is possible to obtain a grain-oriented electrical steel sheet having excellent processing accuracy in rounding while maintaining magnetic properties.
  • the total rolling reduction of the first cold rolling is preferably 60% or more, more preferably 65% or more.
  • the total rolling reduction of the second cold rolling is preferably 58% or more, more preferably 60% or more. From the viewpoint of structure control, it is preferable to set the total rolling reduction of both the first and second cold rolling to 92% or less. More preferably, the total rolling reduction of the first and second cold rollings is 85% or less. In cold rolling, it is preferable to use a lubricant such as rolling oil in order to reduce the rolling load and improve the rolling shape.
  • intermediate annealing is applied.
  • the conditions for the intermediate annealing are not particularly limited, it is preferable to hold the temperature in the temperature range of 800° C. or higher and 1250° C. or lower for 5 seconds or longer.
  • the temperature of the intermediate annealing By setting the temperature of the intermediate annealing to 800° C. or higher, it is possible to prevent the recrystallized grains from becoming excessively fine, and to favorably grow the nuclei of the Goss orientation crystal grains in the primary recrystallized structure, thereby further improving the magnetic properties.
  • the temperature of the intermediate annealing By setting the temperature of the intermediate annealing to 1250° C. or lower, the rapid growth and decomposition of the inhibitor can be prevented, and the magnetic properties can be further improved.
  • the average cooling rate from 800 ° C. to 350 ° C. is 5 ° C./s or more and 100 ° C./s or less, from the viewpoint of controlling the morphology of the second phase and precipitates.
  • the average cooling rate from 900°C to 350°C is 15°C/s or more and 45°C/s or less.
  • the temperature in the intermediate annealing is based on the surface of the steel sheet.
  • a method for removing scale is not particularly limited, and known methods such as a method using heated acid (pickling) and mechanical scale removal may be used.
  • the cold-rolled sheet is subjected to decarburization annealing to obtain a decarburization-annealed sheet. It is preferable to clean the surface of the cold-rolled sheet by degreasing and pickling before the decarburization annealing.
  • Conditions for decarburization annealing are not particularly limited, and conventional methods can be used.
  • the decarburization annealing is preferably performed in a temperature range of 750°C or higher and 950°C or lower.
  • the holding time in the above temperature range is preferably 10 seconds or longer.
  • the atmosphere in the above temperature range for decarburization annealing preferably contains H 2 and N 2 .
  • the decarburization annealing is performed in a moist atmosphere with a dew point of 20° C. or more and 80° C. or less. More preferably, in the decarburization annealing, the dew point is set to 40° C. or higher and 70° C. or lower in the temperature range of 800° C. or higher and 900° C. or lower. In addition, the temperature in decarburization annealing is based on the steel plate surface.
  • annealing separator mainly composed of MgO to the surface of the decarburized annealed sheet in an amount of 2.5 g/m 2 or more per side.
  • mainly composed of MgO means that the content of MgO in the annealing separator is 60% or more in terms of solid content.
  • the content of MgO in the annealing separator is preferably 80% or more in terms of solid content.
  • the method of applying the annealing separator to the surface of the decarburized annealed sheet is not particularly limited, and any known method may be used.
  • the annealing separator may be applied in the form of a slurry to the surface of the decarburized annealed plate, or dry applied by electrostatic coating.
  • the slurry-like annealing separator is preferably kept at a constant temperature of 5° C. or higher and 30° C. or lower in order to suppress an increase in viscosity.
  • the decarburized annealed sheet is subjected to finish annealing.
  • finish annealing can be carried out by a conventional method.
  • the decarburization-annealed sheet is coiled into a steel sheet coil, and then subjected to finish annealing. Since finish annealing generally takes a long time, the steel sheet coil is preferably annealed in an up-end state (the central axis of the steel sheet coil is perpendicular to the ground). It is preferable to wind a band or the like around the steel sheet coil before the final annealing. This is because the outer winding of the up-end steel sheet coil can be prevented from unwinding during the finish annealing.
  • the steel is heated from room temperature to the maximum temperature, held in a specific temperature range for a certain period of time, and then cooled.
  • the average heating rate H1 (° C./hr) from 50° C. to 900° C. and the average heating rate H2 (° C./hr) from 900° C. (maximum attainment temperature ⁇ 50° C.) are calculated according to the following formula. It is essential to control so as to satisfy (2) and (3). By controlling H1 and H2 in the final annealing so as to satisfy both the following expressions (2) and (3), it is possible to improve the processing accuracy in rounding while maintaining the magnetic properties.
  • the temperature and average heating rate in the final annealing are the midpoint between the inner and outer turns of the steel plate coil (the radial thickness of the steel plate coil) on the surface where the up-end steel plate coil contacts the floor of the annealing furnace. 1/2 position).
  • room temperature means around 25 degreeC here. H1 ⁇ 1.1 ⁇ H2 (2) 5 ⁇ H1 ⁇ 40 (3)
  • the steel in order to obtain good iron loss properties by purifying inhibitor components and the like from the steel, it is preferable to hold the steel at 1100° C. or more and 1300° C. or less for 3 hours or more in the final annealing. Moreover, in the final annealing, it is preferable that at least part of the atmosphere within the temperature range of 1100°C or higher contains H2 .
  • an insulating coating may be applied to the surface of the grain-oriented electrical steel sheet in order to ensure insulation.
  • the insulating coating is preferably a coating capable of applying tension to the grain-oriented electrical steel sheet to reduce iron loss.
  • the insulating coating liquid may be applied before flattening annealing, and baking may be performed by flattening annealing.
  • a tension coating application method using a binder, a physical vapor deposition method, or a chemical vapor deposition method may be used to vapor-deposit an inorganic material on the steel sheet surface layer for coating. Coating by these methods is preferable because the coating adhesion is excellent and the effect of significantly reducing iron loss is obtained.
  • the manufacturing conditions other than the conditions described above can be according to the usual method.
  • Example 1 % by mass, C: 0.055%, Si: 3.02%, Mn: 0.06%, Se: 0.014%, Ti: 0.002%, Al: 0.003%, N: 0.05%.
  • a steel slab having a chemical composition containing 0015% and the balance being Fe and unavoidable impurities is slab-heated to 1400 ° C., rough rolling is performed from 1240 ° C. in 3 passes, and finish rolling is performed from 1000 ° C. in 5 to 7 passes.
  • Hot-rolled sheets with various thicknesses from 0.92 to 3.65 mm were produced by hot rolling performed at .
  • the first cold-rolling was performed to obtain various sheet thicknesses from 0.40 to 1.53 mm.
  • An intermediate anneal was then applied at 975° C. for 150 seconds.
  • the average cooling rate from 800°C to 350°C in the intermediate annealing was 25°C/s.
  • cold rolling was performed for the second time to finish a cold-rolled sheet with a sheet thickness of 0.23 mm.
  • Table 1 shows the total rolling reduction of the first and second cold rollings R1 and R2. Further, the cold-rolled sheet was subjected to decarburization annealing under conditions of 850° C. ⁇ 120 seconds, 60% H 2 +40% N 2 , dew point 60° C.
  • the iron loss properties of the obtained grain-oriented electrical steel sheets were evaluated according to JIS 2550, and are also shown in Table 1. If the iron loss was 0.980 W/kg or less, it was judged that the iron loss characteristics were excellent.
  • a 60 mm square sample was cut from the obtained grain-oriented electrical steel sheet and was rounded using a twin roll processing machine composed of an iron roll with a diameter of 20 mm and a urethane roll with a diameter of 300 mm.
  • the direction of rounding was the direction perpendicular to the rolling of the sample (the width direction of the steel sheet). That is, the sample was rounded so that the direction perpendicular to the rolling of the sample drew an arc.
  • the machining accuracy of the obtained sample after rounding was evaluated by the two parameters H and ⁇ described with reference to FIG. The details of the parameters H and ⁇ are as described above. Under these conditions, when an ideal shape is obtained, the respective parameters are H: 2.0 mm and ⁇ : 0°.
  • Example 2 A steel slab having the chemical composition shown in Table 2 is heated to a temperature of 1425°C, subjected to four passes of rough rolling from 1270°C, and five passes of finish rolling from 1050°C. It was finished as a hot-rolled sheet with a thickness of Next, after removing scales on the surface of the hot-rolled sheet by pickling, the sheet was first cold-rolled to a thickness of 0.68 mm, and then subjected to intermediate annealing at 1100° C. for 30 seconds. The average cooling rate in the intermediate annealing temperature range from 800°C to 350°C was 35°C/s. After that, cold rolling was performed for the second time to finish a cold-rolled sheet with a sheet thickness of 0.27 mm.
  • the cold-rolled sheet was decarburized and annealed at 830° C. for 120 seconds in 50% H 2 +50% N 2 with a dew point of 60° C. to obtain a decarburized annealed sheet.
  • finish annealing is performed at 1220 ° C. for 5 hours.
  • a grain oriented electrical steel sheet was obtained.
  • the average temperature rising rate from room temperature to 900°C was 23°C/s, and the atmosphere in this temperature range was N2 atmosphere.
  • the rate of temperature increase from 900° C. to 1170° C. was 15° C./s, and the atmosphere in this temperature range was 25% N 2 +75% H 2 atmosphere.
  • the rate of temperature increase from 1170° C. to 1220° C. was 10° C./hr, and the atmosphere in this temperature range was H 2 atmosphere.
  • cooling was performed in an Ar atmosphere.

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0776733A (ja) * 1993-06-30 1995-03-20 Kenichi Arai 磁束密度の高い方向性珪素鋼板の製造方法
JP2005163122A (ja) * 2003-12-03 2005-06-23 Jfe Steel Kk 高磁束密度方向性電磁鋼板の製造方法
JP2006274405A (ja) * 2005-03-30 2006-10-12 Jfe Steel Kk 高磁束密度方向性電磁鋼板の製造方法
WO2015199211A1 (ja) * 2014-06-26 2015-12-30 新日鐵住金株式会社 電磁鋼板
WO2020145319A1 (ja) * 2019-01-08 2020-07-16 日本製鉄株式会社 方向性電磁鋼板の製造方法および方向性電磁鋼板

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0776733A (ja) * 1993-06-30 1995-03-20 Kenichi Arai 磁束密度の高い方向性珪素鋼板の製造方法
JP2005163122A (ja) * 2003-12-03 2005-06-23 Jfe Steel Kk 高磁束密度方向性電磁鋼板の製造方法
JP2006274405A (ja) * 2005-03-30 2006-10-12 Jfe Steel Kk 高磁束密度方向性電磁鋼板の製造方法
WO2015199211A1 (ja) * 2014-06-26 2015-12-30 新日鐵住金株式会社 電磁鋼板
WO2020145319A1 (ja) * 2019-01-08 2020-07-16 日本製鉄株式会社 方向性電磁鋼板の製造方法および方向性電磁鋼板

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