WO2023095637A1 - 無方向性電磁鋼板用熱延鋼板の製造方法および無方向性電磁鋼板の製造方法 - Google Patents

無方向性電磁鋼板用熱延鋼板の製造方法および無方向性電磁鋼板の製造方法 Download PDF

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WO2023095637A1
WO2023095637A1 PCT/JP2022/041981 JP2022041981W WO2023095637A1 WO 2023095637 A1 WO2023095637 A1 WO 2023095637A1 JP 2022041981 W JP2022041981 W JP 2022041981W WO 2023095637 A1 WO2023095637 A1 WO 2023095637A1
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steel sheet
hot
rolling
less
rolled
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PCT/JP2022/041981
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English (en)
French (fr)
Japanese (ja)
Inventor
龍一 末廣
智幸 大久保
雅康 植野
慎也 山口
茂宏 丸山
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JFE Steel Corp
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JFE Steel Corp
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Priority to MX2024006366A priority Critical patent/MX2024006366A/es
Priority to US18/698,972 priority patent/US20240410037A1/en
Priority to JP2023512807A priority patent/JP7338808B1/ja
Priority to CN202280074693.1A priority patent/CN118318053A/zh
Priority to KR1020247010909A priority patent/KR20240058900A/ko
Priority to EP22898421.7A priority patent/EP4407051A4/en
Publication of WO2023095637A1 publication Critical patent/WO2023095637A1/ja
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
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    • 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
    • C21D8/1244—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 characterised by the heat treatment
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    • C—CHEMISTRY; METALLURGY
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    • 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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    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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Definitions

  • the present invention relates to a method for manufacturing hot-rolled steel sheets for non-oriented electrical steel sheets and a method for manufacturing non-oriented electrical steel sheets.
  • a non-oriented electrical steel sheet is a material used for the iron cores of motors and generators.
  • CO2 reduction there is a strong demand for higher efficiency of electrical equipment, and further reduction in iron loss is required for non-oriented electrical steel sheets, which are iron core materials.
  • a method of manufacturing a non-oriented electrical steel sheet using a steel slab (thin slab) that is thinner than before has been proposed.
  • a thin slab is manufactured using a continuous casting machine called a thin slab caster, and then the thin slab is subjected to rolling.
  • the load in both hot rolling and cold rolling can be reduced.
  • energy costs can be greatly reduced because slab reheating is omitted by directly connecting a continuous casting machine (thin slab caster) and a hot rolling mill.
  • Patent Document 1 discloses a technique of hot-rolling a thin slab with a thickness of 20-100 mm to form a hot-rolled steel strip with a thickness of 1.0-4 mm.
  • Patent Document 2 discloses a technique of hot rolling a thin slab with a thickness of 30 to 140 mm to form a hot rolled steel strip with a thickness of 0.7 to 4.5 mm.
  • JP 2010-047785 A Japanese Patent Application Laid-Open No. 2002-206114
  • An object of the present invention is to solve the above problems.
  • the purpose is to suppress
  • the present invention has been completed based on the above findings, and the gist thereof is as follows.
  • a method for producing a hot-rolled steel sheet for a non-oriented electrical steel sheet comprising: A method for producing a hot-rolled steel sheet for non-oriented electrical steel sheet, wherein the hot-rolling step is performed under conditions satisfying (1) and (2) below.
  • the chemical composition of the steel slab is, in mass%, C: 0.005% or less, Cr: 3.0% or less, Ni: 2.0% or less, Cu: 2.0% or less, P: 0.2% or less, S: 0.0050% or less, N: 0.0050% or less, O: 0.0050% or less, Ti: 0.0040% or less, Sn: 0.20% or less, Sb: 0.20% or less, Mo: 0.10% or less, Ca: 0.01% or less, REM: 0.05% or less, 5.
  • the heat for non-oriented electrical steel sheet according to any one of 1 to 4 above, further containing at least one selected from the group consisting of Mg: 0.01% or less and Zn: 0.01% or less.
  • a method for manufacturing a rolled steel sheet is, in mass%, C: 0.005% or less, Cr: 3.0% or less, Ni: 2.0% or less, Cu: 2.0% or less, P: 0.2% or less, S: 0.0050% or less, N: 0.0050% or less, O
  • a thin non-oriented electrical steel sheet with a large alloy content can be produced at low cost without causing ridging.
  • 4 is a graph showing the correlation between the total content (% by mass) of Al and Mn in a steel slab and the arithmetic mean waviness Wa ( ⁇ m) in the width direction of a non-oriented electrical steel sheet.
  • 5 is a graph showing the correlation between the heat retention temperature (° C.) and heat retention time (seconds) in the heat retention step and the arithmetic mean waviness Wa ( ⁇ m) in the width direction of the non-oriented electrical steel sheet.
  • 4 is a graph showing the correlation between the total rolling reduction (%) in rough rolling, the total rolling reduction (%) in finish rolling, and the arithmetic mean waviness Wa ( ⁇ m).
  • Reheat rolling After removing the steel slab from the vacuum melting furnace, the entire steel slab was allowed to cool to room temperature in the atmosphere. Next, the steel slab was inserted into an electric furnace and reheated at 1100° C. for 30 minutes, after which the steel slab was removed from the electric furnace and inserted into a hot rolling mill.
  • the steel slab in the hot rolling, is roughly rolled to a plate thickness of 15 mm, then reheated to 1100 ° C. by an induction heating device, and then finish rolled to a plate thickness of 1.5 mm. Steel plate.
  • the obtained hot-rolled steel sheet was subjected to hot-rolled steel annealing at 1000°C for 40 seconds, and then cold-rolled to obtain a cold-rolled steel sheet having a thickness of 0.3 mm.
  • the cold-rolled steel sheet was subjected to finish annealing at 980° C. for 20 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa of the surface of the non-oriented electrical steel sheet was measured.
  • a stylus type surface roughness meter was used, and the arithmetic mean waviness Wa was calculated from the waviness curve obtained by measuring the steel sheet surface in the width direction with a measurement length of 16 mm.
  • Fig. 1 shows the relationship between the total content (% by mass) of Al and Mn in the steel slab used and the measured Wa ( ⁇ m).
  • [Al] is the Al content of the steel slab
  • [Mn] is the Mn content of the steel slab
  • [Al] + [Mn] is the total content of Al and Mn in the steel slab. write.
  • Example 2 The present inventors presumed that fine precipitates such as MnS and AlN precipitated in direct rolling, and that these fine precipitates prevented recrystallization during hot-rolled sheet annealing. Therefore, it was decided that the precipitating process should be performed before the hot rolling process to precipitate and grow the precipitates to reduce the fine precipitates.
  • the steel slab was taken out from the electric furnace, inserted into a hot rolling mill, and hot rolled.
  • the steel slab is roughly rolled to a thickness of 10 mm, then reheated to 1100° C. by an induction heating apparatus, and then finish rolled to a thickness of 1.2 mm to obtain a hot rolled steel sheet.
  • the obtained hot-rolled steel sheet was subjected to hot-rolled steel annealing at 1000°C for 40 seconds, and then cold-rolled to obtain a cold-rolled steel sheet having a thickness of 0.3 mm.
  • the cold-rolled steel sheet was subjected to finish annealing at 980° C. for 20 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa on the surface of the obtained non-oriented electrical steel sheet was measured by the same procedure as in Experiment 1 above.
  • Fig. 2 shows the relationship between the heat retention temperature and heat retention time in the heat retention process and the arithmetic mean waviness Wa.
  • the heat retention time was less than 60 seconds, ridging occurred at any heat retention temperature.
  • the heat retention time was 60 seconds or more, ridging was suppressed within the heat retention temperature range of 1100°C or higher and 1300°C or lower.
  • a steel slab with a thickness of 160 mm was melted in a vacuum melting furnace. While maintaining the surface temperature of the steel slab at 800° C. or higher, the steel slab was transported and inserted into an electric furnace, where it was heat-treated at 1150° C. for 300 seconds. After that, the steel slab was taken out from the electric furnace, inserted into a hot rolling mill, and hot rolled.
  • the steel slab was subjected to rough rolling, reheat treatment, and finish rolling in order to obtain a hot-rolled steel sheet with a thickness of 0.6 mm, 1.0 mm, or 1.8 mm.
  • the total rolling reduction in the rough rolling was 70.0 to 98.0%, and the total rolling reduction in the finish rolling was 43.8 to 98.8%.
  • the reheating treatment was performed using an induction heating apparatus, and the sheet bar (steel after rough rolling) was heated to 1100°C.
  • the obtained hot-rolled steel sheet was subjected to hot-rolled sheet annealing at 1000°C for 25 seconds, and then cold-rolled at a cold-rolling reduction of 80% to obtain a cold-rolled steel sheet.
  • the cold-rolled steel sheet was subjected to finish annealing at 980° C. for 20 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa on the surface of the obtained non-oriented electrical steel sheet was measured by the same procedure as in Experiment 1 above.
  • Fig. 3 shows the relationship between the total rolling reduction in rough rolling, the total rolling reduction in finish rolling, and the arithmetic mean waviness Wa.
  • the three lines in FIG. 3 respectively correspond to the results at the delivery side thickness in the finish rolling (final thickness in the hot rolling process): 0.6 mm, 1.0 mm and 1.8 mm. Also, the numerical value attached to each point is the total rolling reduction (%) in the finish rolling.
  • the heat retention temperature is 1100 ° C. or more and 1300 ° C. or less, and the heat retention time is It was found that the ridging can be suppressed by performing the heat-retaining treatment for 60 seconds or more and setting the total rolling reduction ratio in each of the rough rolling and the finish rolling to 80% or more.
  • the total rolling reduction in rough rolling the amount of dislocations in the sheet bar increases, the rolled structure of the sheet bar is refined, and the grain boundary density increases. These dislocations and grain boundaries serve as precipitation sites for MnS and AlN that were not precipitated by the heat treatment, and promote the precipitation. Furthermore, by increasing the total rolling reduction in the finish rolling, the hot-rolled structure becomes finer, and the grain boundary density that becomes the recrystallization site increases.
  • Si 2.0-5.0%
  • Si is an element that has the effect of increasing the specific resistance of the steel sheet and reducing iron loss.
  • the Si content is set to 2.0% or more.
  • the Si content is made 5.0% or less.
  • the Si content is preferably 2.5% or more, more preferably 2.8% or more.
  • the Si content is preferably 4.5% or less, more preferably 4.0% or less.
  • Al 3.0% or less
  • Al is an element that has the effect of increasing the specific resistance of the steel sheet and reducing iron loss. However, if the Al content exceeds 3.0%, rolling becomes difficult. Therefore, the Al content is set to 3.0% or less. From the viewpoint of improving castability, the Al content is preferably 1.5% or less.
  • the lower limit of the Al content is not limited, but from the viewpoint of the balance between iron loss and manufacturability, the Al content is preferably 0.2% or more, more preferably 0.3% or more. It is preferably 0.5% or more, and more preferably 0.5% or more.
  • Mn 3.0% or less
  • Mn is an element that has the effect of increasing the specific resistance of the steel sheet and further reducing iron loss.
  • the Mn content is set to 3.0% or less.
  • the lower limit of the Mn content is not limited, but from the viewpoint of further suppressing the precipitation of fine MnS, it is preferably 0.20% or more.
  • Total content of Al and Mn 0.40% or more
  • the total content of Al and Mn should be 0.40% or more, preferably 1.00% or more, and more preferably 1.50% or more.
  • the upper limit of the total content of Al and Mn is not particularly limited. However, since the Al content is 3.0% or less and the Mn content is 3.0% or less as described above, the maximum total content of Al and Mn is 6.00%.
  • the steel slab is Si: 2.0% or more and 5.0% or less, Al: 3.0% or less, Mn: 3.0% or less,
  • the balance consists of Fe and unavoidable impurities, It may have a component composition in which the total content of Al and Mn is 0.40% or more.
  • the chemical composition of the steel slab may further optionally contain at least one of the following elements.
  • C 0.005% or less C contained in a non-oriented electrical steel sheet is a harmful element that forms carbides, causes magnetic aging, and deteriorates iron loss characteristics. Therefore, when the steel slab contains C, the C content is made 0.005% or less, preferably 0.004% or less.
  • the lower limit of the C content is not particularly limited, but from the viewpoint of suppressing the decarburization cost in the refining process, the C content is preferably 0.0001% or more.
  • Cr 3.0% or less Cr is an element that has the effect of increasing the resistivity of the steel sheet and reducing iron loss. However, if the Cr content exceeds 3.0%, carbide precipitates and the iron loss rather increases. Therefore, when Cr is added, the Cr content is made 3.0% or less. From the viewpoint of magnetic properties, the Cr content is preferably 1.5% or less. On the other hand, the lower limit of the Cr content is not limited, but from the viewpoint of enhancing the effect of adding Cr, the Cr content is preferably 0.001% or more, more preferably 0.005% or more. , more preferably 0.01% or more.
  • Ni 2.0% or less
  • Ni is an element that has the effect of improving the magnetic flux density of the steel sheet.
  • Ni is an expensive element, and if the Ni content exceeds 2.0%, the cost becomes very high. Therefore, when Ni is added, the Ni content is set to 2.0% or less. From the viewpoint of the balance between magnetic properties and cost, the Ni content is preferably 0.5% or less.
  • the lower limit of the Ni content is not limited, but from the viewpoint of enhancing the effect of Ni addition, the Ni content is preferably 0.001% or more, more preferably 0.005% or more. , more preferably 0.01% or more.
  • Cu 2.0% or less
  • Cu is an element that has the effect of improving the magnetic flux density of the steel sheet.
  • the Cu content exceeds 2.0%, it causes hot shortness and causes surface defects. Therefore, when Cu is added, the Cu content is set to 2.0% or less. From the viewpoint of the balance between magnetic properties and cost, the Cu content is preferably 0.5% or less.
  • the lower limit of the Cu content is not limited, but from the viewpoint of enhancing the effect of adding Cu, the Cu content is preferably 0.005% or more, more preferably 0.01% or more. , more preferably 0.05% or more.
  • P 0.2% or less
  • P is an element used for strength adjustment of the steel sheet.
  • the P content should be 0.2% or less.
  • the P content is preferably 0.1% or less.
  • the lower limit of the P content is not limited, but from the viewpoint of increasing the effect of adding P, the P content is preferably 0.001% or more, more preferably 0.005% or more. , more preferably 0.01% or more.
  • S 0.0050% or less
  • S is an element that forms sulfide and increases iron loss. Therefore, when S is contained, the S content should be 0.0050% or less, preferably 0.0020% or less, more preferably 0.0010% or less.
  • the lower limit of the S content is not limited, and may be 0%.
  • S is an element inevitably mixed into steel as an impurity, and excessive reduction causes an increase in manufacturing costs. Therefore, from the viewpoint of cost, the S content is preferably 0.0001% or more, more preferably 0.0005% or more.
  • N 0.0050% or less
  • N is an element that forms nitrides and increases iron loss. Therefore, when N is contained, the N content is made 0.0050% or less, preferably 0.0030% or less, more preferably 0.0020% or less.
  • the lower limit of the N content is not limited, and may be 0%.
  • N is an element that is inevitably mixed into steel as an impurity, and excessive reduction causes an increase in manufacturing costs. Therefore, from the viewpoint of cost, the N content is preferably 0.0001% or more, more preferably 0.0005% or more.
  • O 0.0050% or less
  • O is an element that forms an oxide and increases iron loss. Therefore, when O is contained, the O content should be 0.0050% or less, preferably 0.0020% or less, and more preferably 0.0010% or less.
  • the lower limit of the O content is not limited, and may be 0%.
  • O is an element that is inevitably mixed into steel as an impurity, and excessive reduction causes an increase in manufacturing costs. Therefore, from the viewpoint of cost, the O content is preferably 0.0005% or more, more preferably 0.001% or more.
  • Ti is an element that forms carbonitrides and increases iron loss. Therefore, when Ti is contained, the Ti content should be 0.0040% or less, preferably 0.0020% or less, and more preferably 0.0010% or less. On the other hand, from the viewpoint of iron loss, the lower the Ti content, the better. Therefore, the lower limit of the Ti content is not limited, and may be 0%. However, Ti is an element that is inevitably mixed into steel as an impurity, and excessive reduction causes an increase in manufacturing costs. Therefore, from the viewpoint of cost, the Ti content is preferably 0.0001% or more, more preferably 0.0005% or more.
  • Sn 0.20% or less
  • Sn is an element that suppresses nitridation and oxidation of the surface layer and has the effect of reducing iron loss. However, the effect saturates even if it is added in excess of 0.20%, so when Sn is added, the Sn content is made 0.20% or less, preferably 0.10% or less. On the other hand, from the viewpoint of enhancing the above effect, the Sn content is preferably 0.005% or more.
  • Sb 0.20% or less
  • Sb is an element that has the effect of suppressing nitridation and oxidation of the surface layer and reducing iron loss. However, the effect saturates even if it is added in excess of 0.20%, so when Sb is added, the Sb content is made 0.20% or less, preferably 0.10% or less. On the other hand, from the viewpoint of enhancing the above effects, the Sb content is preferably 0.005 or more.
  • Mo 0.10% or less
  • Mo is an element that has the effect of suppressing nitridation and oxidation of the surface layer and reducing iron loss. However, adding more than 0.10% rather increases the core loss. Therefore, when Mo is added, the Mo content should be 0.10% or less, preferably 0.05% or less. On the other hand, from the viewpoint of enhancing the above effects, it is preferable to set the Mo content to 0.001% or more.
  • Ca 0.01% or less Ca is an element that suppresses the formation of fine oxides and sulfides and reduces iron loss. However, even if it is added in excess of 0.01%, the effect is saturated. Therefore, when Ca is added, the Ca content should be 0.01% or less, preferably 0.006% or less. On the other hand, from the viewpoint of enhancing the effect, the Ca content is preferably 0.001% or more.
  • REM 0.05% or less REM (rare earth metal) is an element that suppresses the formation of fine sulfides and reduces iron loss. However, even if it is added in excess of 0.05%, the effect is saturated. Therefore, when REM is added, the REM content should be 0.10% or less, preferably 0.03% or less. On the other hand, from the viewpoint of enhancing the above effects, the REM content is preferably 0.005% or more.
  • Mg 0.01% or less Mg is an element that suppresses the formation of fine sulfides and reduces iron loss. However, even if it is added in excess of 0.01%, the effect is saturated. Therefore, when Mg is added, the Mg content should be 0.10% or less, preferably 0.006% or less. On the other hand, from the viewpoint of enhancing the effect, the Mg content is preferably 0.001% or more.
  • Zn 0.01% or less
  • Zn is an element that suppresses the formation of fine oxides and sulfides and reduces iron loss. However, even if it is added in excess of 0.01%, the effect is saturated. Therefore, when Zn is added, the Zn content should be 0.01% or less, preferably 0.005% or less. On the other hand, from the viewpoint of enhancing the above effects, the Zn content is preferably 0.001 or more.
  • a method for producing a hot-rolled steel sheet for a non-oriented electrical steel sheet includes a continuous casting step of producing a steel slab by a continuous casting method, and a conveying step of conveying the steel slab to the furnace, a heat retaining step of retaining the steel slab in the furnace under conditions of a heat retention temperature of 1100 ° C. or more and 1300 ° C. or less and a heat retention time of 60 seconds or more, and rough rolling and reheating of the steel slab , and a hot rolling step in which finish rolling is sequentially performed to form a hot rolled steel sheet.
  • a continuous casting step of producing a steel slab by a continuous casting method
  • a conveying step of conveying the steel slab to the furnace
  • a heat retaining step of retaining the steel slab in the furnace under conditions of a heat retention temperature of 1100 ° C. or more and 1300 ° C. or less and a heat retention time of 60 seconds or more
  • rough rolling and reheating of the steel slab and a hot rolling step in which
  • a steel slab having the above-described composition is manufactured by a continuous casting method (continuous casting process).
  • a method for continuous casting is not particularly limited, and a conventional method can be used.
  • a method for adjusting the components of molten steel used for continuous casting is also not particularly limited, and any method can be used.
  • a converter, an electric furnace, a vacuum degassing device, and other devices and methods can be used to adjust the composition of the molten steel.
  • Steel slab thickness 50-200mm
  • a steel slab having a thickness of 50 mm or more and 200 mm or less is manufactured. If the thickness of the steel slab is less than 50 mm, a sufficient rolling reduction in rough rolling and finish rolling in the hot rolling process cannot be obtained, and recrystallization in hot-rolled sheet annealing is inhibited. Therefore, the thickness of the steel slab shall be 50 mm or more. From the viewpoint of suppressing a decrease in slab temperature between the continuous casting process and the heat retention process, it is preferable to set the thickness of the steel slab to 100 mm or more. Furthermore, from the viewpoint of ensuring a sufficient rolling reduction in rough rolling and finish rolling, it is more preferable to set the thickness of the steel slab to 140 mm or more. On the other hand, if the thickness of the steel slab exceeds 200 mm, the rolling load in the hot rolling process increases, leading to an increase in the length of the rolling equipment and the equipment cost. Therefore, the thickness of the steel slab shall be 200 mm or less.
  • the steel slab manufactured in the continuous casting process is conveyed to a furnace used for thermal insulation (conveyance process).
  • the transporting step it is important to transport while maintaining the surface temperature of the steel slab at 800° C. or higher.
  • the steel slab is conveyed so that the surface temperature of the steel slab does not drop below 800° C. from the time it is produced in the continuous casting process until it reaches the furnace.
  • the surface temperature of the steel slab is less than 800°C, the energy required for reheating the steel slab increases, and the effect of energy saving cannot be obtained.
  • the method for suppressing the surface temperature drop of the steel slab in the transport process is not particularly limited, but for example, the surface temperature drop can be suppressed by increasing the casting speed or increasing the slab thickness.
  • the steel slab may be cut and then transported to the furnace.
  • Heat Retention Step the steel slab is heated in the furnace at a heat retention temperature of 1100° C. or higher and 1300° C. or lower for a heat retention time of 60 seconds or longer (heat retention step).
  • heat retention step By promoting the precipitation and coarsening of MnS and AlN by heat-retaining treatment, recrystallization is promoted in the hot-rolled sheet annealing process when manufacturing a non-oriented electrical steel sheet.
  • Heat retention temperature 1100-1300°C If the heat retention temperature is lower than 1100° C., coarsening of precipitates is not promoted, and fine precipitates remain in the slab. As a result, recrystallization in hot-rolled sheet annealing is inhibited, and ridging is likely to occur. Therefore, the heat retention temperature is set to 1100° C. or higher, preferably 1150° C. or higher. On the other hand, if the heat retention temperature is higher than 1300° C., precipitation of precipitates does not progress, and fine precipitation of MnS and AlN occurs during hot rolling after heat retention. As a result, recrystallization in hot-rolled sheet annealing is inhibited, and ridging is likely to occur. Therefore, the heat retention temperature is set to 1300° C. or lower, preferably 1250° C. or lower.
  • Heat retention time 60 s or more If the heat retention time is less than 60 s, precipitation and coarsening of MnS and AlN do not proceed, and thus ridging is likely to occur. Therefore, the heat retention time is set to 60 s or longer, preferably 300 s or longer. On the other hand, the upper limit of the heat retention time is not particularly limited, but if it exceeds 3600 seconds, the effect is saturated and the construction cost of the facility increases. Therefore, the retention time is preferably 3600 s or less, more preferably 2400 s or less, and even more preferably 2000 s or less.
  • a heating method in the heat insulating treatment is not particularly limited, and any method such as induction heating, gas furnace, electric furnace, or the like can be used.
  • any method such as induction heating, gas furnace, electric furnace, or the like can be used.
  • gas furnace when a gas furnace is used, scale is generated on the surface of the steel sheet by the combustion gas. Therefore, from the viewpoint of suppressing scale formation and CO 2 emission, it is preferable to use induction heating or an electric furnace, which are heating methods using electric energy.
  • the electric furnace is suitable for continuously heating the steel slab for a long time, and the construction cost is low. Therefore, it is more preferable to use an electric furnace for the thermal insulation.
  • Hot rolling step the steel slab is subjected to rough rolling, reheat treatment, and finish rolling in order to form a hot rolled steel sheet (hot rolling step).
  • hot rolling step it is important to carry out the hot rolling step under conditions satisfying the following (1) and (2).
  • Total rolling reduction in rough rolling 80% or more If the total rolling reduction in rough rolling is less than 80%, the promotion of precipitation of MnS and AlN due to the introduction of dislocations is insufficient, and the subsequent reheating treatment causes precipitates to coarsen. do not have. Also, the grain boundary density after hot rolling is not sufficiently refined. As a result, recrystallization is not promoted in hot-rolled sheet annealing for producing non-oriented electrical steel sheets, and ridging tends to occur. Therefore, the total reduction in rough rolling is set to 80% or more, preferably 88% or more, and more preferably 91% or more.
  • the total rolling reduction of rough rolling is the rolling reduction calculated from the thickness before the start of rough rolling (thickness of steel slab) and the thickness after completion of rough rolling (thickness at delivery side).
  • the number of passes of the rough rolling is not particularly limited, and may be any number of passes of 1 or more.
  • Total rolling reduction in finish rolling 80% or more If the total rolling reduction in finish rolling is less than 80%, the grain boundary density after hot rolling will not be sufficiently refined, so recrystallization in hot rolled sheet annealing will occur. is not promoted, and ridging tends to occur. Therefore, the total reduction in finish rolling is set to 80% or more, preferably 88% or more, and more preferably 91% or more. In particular, when the total rolling reduction in finish rolling is 91% or more, the grain boundary density after hot rolling increases significantly, and the number of dislocations remaining in the steel sheet after hot rolling also increases significantly. . As a result, recrystallization is more likely to occur during hot-rolled sheet annealing, and ridging can be more effectively suppressed.
  • the total reduction ratio of finish rolling is a reduction ratio calculated from the thickness before the start of finish rolling and the thickness after completion of finish rolling (delivery side thickness).
  • the number of passes in the finish rolling is not particularly limited, and may be an arbitrary number of passes greater than or equal to one.
  • the total rolling reduction in rough rolling is preferably larger than the total rolling reduction in finish rolling.
  • the limitation of the rolling reduction in the present invention is for solving the problem of ridging peculiar to direct rolling, and is based on a novel idea that is completely different from the control of the rolling reduction in conventional reheat rolling. It was made.
  • Reheating is performed between the above rough rolling and finish rolling. It is necessary to carry out the reheating treatment in order to coarsen the precipitates finely precipitated in rough rolling and suppress ridging. Further, by performing the reheating treatment, the temperature of the material can be raised to lower the deformation resistance during finish rolling.
  • the heating temperature in the reheating treatment is not particularly limited, but is preferably 950°C or higher, more preferably 1050°C or higher.
  • the upper limit of the heating temperature is not particularly limited, but if the heating temperature is excessively high, the effect is saturated and the energy efficiency is lowered. Therefore, the heating temperature in the reheating treatment is preferably 1300° C. or lower, more preferably 1200° C. or lower.
  • the heating method in the reheating treatment is not particularly limited, and any method such as induction heating, gas furnace, electric furnace, etc. can be used.
  • the delivery side thickness (the thickness of the finally obtained hot-rolled steel sheet) in the finish rolling is not particularly limited, and may be any thickness. However, if the delivery-side plate thickness is less than 0.4 mm, the total length of the steel plate becomes excessively long, resulting in a decrease in productivity. Therefore, from the viewpoint of productivity, it is preferable to set the delivery side plate thickness in the finish rolling to 0.4 mm or more. On the other hand, if the delivery side plate thickness exceeds 2.0 mm, the cold rolling load increases. Therefore, from the viewpoint of reducing the load in cold rolling, it is preferable to set the delivery side plate thickness in finish rolling to 2.0 mm or less. From the viewpoint of reducing the cold rolling load even when the final thickness after cold rolling is thin, it is more preferable to set the delivery side thickness to 1.5 mm or less.
  • a method for manufacturing a non-oriented electrical steel sheet according to one embodiment of the present invention comprises a hot-rolled steel sheet manufacturing step of manufacturing a hot-rolled steel sheet by the manufacturing method described above, and a hot-rolled sheet annealing step of subjecting the hot-rolled steel sheet to hot-rolled sheet annealing. and a cold-rolling step of cold-rolling the hot-rolled steel sheet to form a cold-rolled steel sheet, and a finish annealing step of subjecting the cold-rolled steel sheet to finish annealing.
  • the steps of hot-rolled sheet annealing, cold rolling, and finish annealing are not particularly limited, and can be carried out according to conventional methods.
  • pickling after the hot-rolled sheet annealing and prior to the cold rolling. It is also preferable to form an insulating coating on the surface of the obtained non-oriented electrical steel sheet after the finish annealing.
  • the pickling and formation of the insulating coating are not particularly limited, either, and can be carried out according to conventional methods.
  • Example 1 C: 0.002%, Si: 3.2%, Al: 0.60%, Mn: 0.50%, S: 0.0010%, N: 0.0015%, O: 0.0010%, Cr : 0.02%, Ni: 0.01%, Cu: 0.02%, P: 0.01%, and Ti: 0.001%, and the balance is Fe and unavoidable impurities.
  • 60 mm thick steel slabs were produced by continuous casting. Without cutting the steel slab, the surface temperature of the slab was maintained at 800° C. or higher and conveyed to a tunnel electric furnace, where heat-retaining treatment was performed in the electric furnace. The heat retention temperature and heat retention time in the heat retention treatment were as shown in Table 1. For comparison, some examples were not subjected to thermal insulation.
  • the steel slab was subjected to hot rolling consisting of 3 passes of rough rolling, reheat treatment, and 4 passes of finish rolling under the conditions shown in Table 1 to obtain hot rolled steel sheets.
  • reheating treatment the slab immediately after rough rolling was heated by an induction heating method.
  • reheating treatment was omitted in some examples.
  • the hot-rolled steel sheet after finish rolling was continuously wound into a coil to form a hot-rolled coil, and the hot-rolled coil was subjected to hot-rolled sheet annealing at 1030°C for 40 seconds to obtain a hot-rolled annealed sheet.
  • the hot-rolled and annealed sheet was cold-rolled at a rolling reduction of 85% to obtain a cold-rolled steel sheet.
  • the cold-rolled steel sheet was subjected to finish annealing at 1000° C. for 15 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa of the surface of the non-oriented electrical steel sheet was measured.
  • a stylus type surface roughness meter was used, and the arithmetic mean waviness Wa was calculated from the waviness curve obtained by measuring the steel sheet surface in the width direction with a measurement length of 16 mm. The measurement results are also shown in Table 1.
  • Example 2 C: 0.002%, Si: 3.0%, Al: 1.3%, Mn: 0.40%, S: 0.0005%, N: 0.0015%, O: 0.0010%, Cr : 0.10%, Ni: 0.15%, Cu: 0.18%, P: 0.02%, and Ti: 0.0015%, and the balance is Fe and unavoidable impurities.
  • 160 mm thick steel slabs were produced by continuous casting. Without cutting the steel slab, the surface temperature of the slab was maintained at 800° C. or higher, and the steel slab was conveyed to a tunnel-type gas furnace, and heat-retaining treatment was performed in the gas furnace. The heat retention temperature and heat retention time in the heat retention treatment were as shown in Table 2. For comparison, some examples were not subjected to thermal insulation.
  • the steel slab was subjected to hot rolling consisting of 4 passes of rough rolling, reheat treatment, and 5 passes of finish rolling under the conditions shown in Table 2 to obtain hot rolled steel sheets.
  • reheating treatment the slab immediately after rough rolling was heated by an induction heating method.
  • reheating treatment was omitted in some examples.
  • the hot-rolled steel sheet after finish rolling was continuously wound into a coil to form a hot-rolled coil, and the hot-rolled coil was subjected to hot-rolled sheet annealing at 1020°C for 30 seconds to obtain a hot-rolled annealed sheet.
  • the hot-rolled and annealed sheet was cold-rolled at a rolling reduction of 85% to obtain a cold-rolled steel sheet.
  • the cold-rolled steel sheet was subjected to finish annealing at 1000° C. for 15 seconds to obtain a non-oriented electrical steel sheet.
  • Example 3 C: 0.002%, Si: 3.4%, Al: 0.3%, Mn: 0.60%, S: 0.0008%, N: 0.010%, O: 0.0010%, Cr : 0.015%, Ni: 0.015%, Cu: 0.03%, P: 0.015%, and Ti: 0.0015%, and the balance is Fe and unavoidable impurities.
  • a steel slab with a thickness of 190 mm was produced by continuous casting. Without cutting the steel slab, the surface temperature of the slab was maintained at 800° C. or higher, and the steel slab was conveyed to a tunnel-type gas furnace, and heat-retaining treatment was performed in the gas furnace. The heat retention temperature and heat retention time in the heat retention treatment were as shown in Table 3. For comparison, some examples were not subjected to thermal insulation.
  • the steel slab was subjected to hot rolling consisting of 4 passes of rough rolling, reheat treatment, and 5 passes of finish rolling under the conditions shown in Table 3 to obtain hot rolled steel sheets.
  • reheating treatment the slab immediately after rough rolling was heated by an induction heating method.
  • reheating treatment was omitted in some examples.
  • the hot-rolled steel sheet after finish rolling was continuously wound into a coil to form a hot-rolled coil, and the hot-rolled coil was subjected to hot-rolled sheet annealing at 1050°C for 20 seconds to obtain a hot-rolled annealed sheet.
  • the hot-rolled and annealed sheet was cold-rolled at a rolling reduction of 85% to obtain a cold-rolled steel sheet.
  • the cold-rolled steel sheet was subjected to finish annealing at 1000° C. for 15 seconds to obtain a non-oriented electrical steel sheet.
  • Example 4 A steel slab having a thickness of 150 mm and having the chemical composition shown in Tables 4 to 6 was produced by a continuous casting method. Without cutting the steel slab, the surface temperature of the slab was maintained at 800° C. or higher, and the steel slab was conveyed to a tunnel-type gas furnace, and heat-retaining treatment was performed in the gas furnace. The heat retention temperature in the heat retention treatment was set to 1150° C., and the heat retention time was set to 1500 seconds.
  • the steel slab was subjected to hot rolling consisting of 4 passes of rough rolling, reheat treatment, and 5 passes of finish rolling to obtain a hot rolled steel sheet.
  • the total rolling reduction in the rough rolling was 90%, and the total rolling reduction in the finish rolling was 93.3%.
  • the slab immediately after rough rolling was heated to 1100° C. by an induction heating method.
  • the hot-rolled steel sheet after finish rolling was continuously wound into a coil to form a hot-rolled coil, and the hot-rolled coil was subjected to hot-rolled sheet annealing at 1050°C for 20 seconds to obtain a hot-rolled annealed sheet.
  • the hot-rolled and annealed steel sheet was cold-rolled at a rolling reduction of 80% to obtain a cold-rolled steel sheet having a thickness of 0.20 mm.
  • the cold-rolled steel sheet was subjected to finish annealing at 1000° C. for 20 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa of the surface of the non-oriented electrical steel sheet was measured in the same manner as in Example 1 above. The measurement results are also shown in Tables 4-6.
  • Example 5 Steel slabs having a thickness of 150 mm and having chemical compositions shown in Tables 7-9 were produced by continuous casting. Without cutting the steel slab, the surface temperature of the slab was maintained at 800° C. or higher, and the steel slab was conveyed to a tunnel-type gas furnace, and heat-retaining treatment was performed in the gas furnace. The heat retention temperature in the heat retention treatment was 1150° C., and the heat retention time was 500 seconds.
  • the steel slab was subjected to hot rolling consisting of 4 passes of rough rolling, reheat treatment, and 5 passes of finish rolling to obtain a hot rolled steel sheet.
  • the total rolling reduction in the rough rolling was 92%, and the total rolling reduction in the finish rolling was 91.7%.
  • the slab immediately after rough rolling was heated to 1100° C. by an induction heating method.
  • the hot-rolled steel sheet after finish rolling was continuously wound into a coil to form a hot-rolled coil, and the hot-rolled coil was subjected to hot-rolled sheet annealing at 1050°C for 20 seconds to obtain a hot-rolled annealed sheet.
  • the hot-rolled and annealed steel sheet was cold-rolled at a rolling reduction of 80% to obtain a cold-rolled steel sheet having a thickness of 0.20 mm.
  • the cold-rolled steel sheet was subjected to finish annealing at 1000° C. for 20 seconds to obtain a non-oriented electrical steel sheet.
  • the arithmetic mean waviness Wa of the surface of the non-oriented electrical steel sheet was measured in the same manner as in Example 1 above. The measurement results are also shown in Tables 4-6.

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US20250101541A1 (en) * 2022-02-01 2025-03-27 Jfe Steel Corporation Method of producing hot-rolled steel sheet for non-oriented electrical steel sheet, method of producing non-oriented electrical steel sheet, and hot-rolled steel sheet for non-oriented electrical steel sheet
JPWO2025204271A1 (https=) * 2024-03-26 2025-10-02
KR20260037677A (ko) * 2024-09-09 2026-03-18 현대제철 주식회사 무방향성 전기강판 및 무방향성 전기강판 제조 방법

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58123825A (ja) * 1982-01-20 1983-07-23 Kawasaki Steel Corp 無方向性電磁鋼板の製造方法
JPH1161256A (ja) * 1997-08-08 1999-03-05 Nkk Corp 表面性状が優れ且つ鉄損の低い無方向性電磁鋼板の製造方法
JP2007516345A (ja) * 2003-05-14 2007-06-21 エイケイ・スティール・プロパティーズ・インコーポレイテッド 無方向性電磁鋼ストリップの改善された製造方法
KR20200065141A (ko) * 2018-11-29 2020-06-09 주식회사 포스코 낮은 철손 및 우수한 표면품질을 갖는 무방향성 전기강판 및 그 제조방법
JP2020186433A (ja) * 2019-05-14 2020-11-19 日本製鉄株式会社 スラブの製造方法

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002206114A (ja) 2000-12-28 2002-07-26 Nippon Steel Corp 無方向性電磁鋼板の製造方法
JP5388506B2 (ja) 2008-08-19 2014-01-15 新日鐵住金株式会社 磁束密度の高い無方向性電磁鋼板の製造方法
CA2956686C (en) * 2014-07-31 2019-01-08 Jfe Steel Corporation Non-oriented electrical steel sheet and method for producing the same, and motor core and method of producing the same
WO2019225529A1 (ja) * 2018-05-21 2019-11-28 Ｊｆｅスチール株式会社 無方向性電磁鋼板およびその製造方法
KR102241985B1 (ko) * 2018-12-19 2021-04-19 주식회사 포스코 무방향성 전기강판 및 그 제조방법
JP7196939B2 (ja) * 2019-02-08 2022-12-27 日本製鉄株式会社 方向性電磁鋼板、方向性電磁鋼板の絶縁被膜形成方法、及び方向性電磁鋼板の製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58123825A (ja) * 1982-01-20 1983-07-23 Kawasaki Steel Corp 無方向性電磁鋼板の製造方法
JPH1161256A (ja) * 1997-08-08 1999-03-05 Nkk Corp 表面性状が優れ且つ鉄損の低い無方向性電磁鋼板の製造方法
JP2007516345A (ja) * 2003-05-14 2007-06-21 エイケイ・スティール・プロパティーズ・インコーポレイテッド 無方向性電磁鋼ストリップの改善された製造方法
KR20200065141A (ko) * 2018-11-29 2020-06-09 주식회사 포스코 낮은 철손 및 우수한 표면품질을 갖는 무방향성 전기강판 및 그 제조방법
JP2020186433A (ja) * 2019-05-14 2020-11-19 日本製鉄株式会社 スラブの製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP4407051A4 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4596744A4 (en) * 2023-09-12 2026-04-08 Baoshan Iron & Steel NON-ORIENTED SILICON STEEL WITH EXCELLENT OVERALL PERFORMANCE AND ASSOCIATED MANUFACTURING PROCESS
CN118291877A (zh) * 2024-04-10 2024-07-05 东北大学 磁性能和耐蚀性能优异的高强度无取向硅钢及其制造方法

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