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WO2025047016A1 - Tôle recuite laminée à chaud pour tôle d'acier électromagnétique non orienté, son procédé de fabrication et procédé de fabrication de tôle d'acier électromagnétique non orienté - Google Patents

Tôle recuite laminée à chaud pour tôle d'acier électromagnétique non orienté, son procédé de fabrication et procédé de fabrication de tôle d'acier électromagnétique non orienté Download PDF

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Publication number
WO2025047016A1
WO2025047016A1 PCT/JP2024/019129 JP2024019129W WO2025047016A1 WO 2025047016 A1 WO2025047016 A1 WO 2025047016A1 JP 2024019129 W JP2024019129 W JP 2024019129W WO 2025047016 A1 WO2025047016 A1 WO 2025047016A1
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WIPO (PCT)
Prior art keywords
hot
sheet
rolled
less
group
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PCT/JP2024/019129
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English (en)
Japanese (ja)
Inventor
勇人 齋藤
智幸 大久保
茂宏 丸山
孝明 田中
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JFE Steel Corp
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JFE Steel Corp
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Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to JP2024552680A priority Critical patent/JPWO2025047016A1/ja
Publication of WO2025047016A1 publication Critical patent/WO2025047016A1/fr
Pending legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • 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

Definitions

  • the present invention relates to a hot-rolled annealed sheet for non-oriented electrical steel sheet that has excellent resistance to fracture during cold rolling, a manufacturing method thereof, and a manufacturing method of non-oriented electrical steel sheet using the above hot-rolled annealed sheet.
  • Patent Document 1 discloses a non-oriented electrical steel sheet containing, by mass%, 0.0010 to 0.0050% C, 2.5 to 4.0% Si, 0.2 to 2.0% Al, 0.05 to 2.0% Mn, 0.005 to 0.15% P, 0.0001 to 0.0030% S, 0.0005 to 0.0030% Ti, 0.0010 to 0.0030% N, with the balance being Fe and unavoidable impurities, with the base steel having a sheet thickness of 0.10 mm or more and 0.35 mm or less, and with the Al concentration in the depth direction from the surface of the base steel satisfying the relational expression shown in Formula (1) below.
  • Patent Document 1 The inventors' investigation revealed that the control of the hot-rolled sheet annealing conditions described in Patent Document 1 alone does not necessarily prevent breakage, and that it is difficult to achieve both breakage resistance during cold rolling and good magnetic properties after cold-rolled sheet annealing.
  • the hot-rolled annealed sheet for non-oriented electrical steel sheet further contains, in addition to the above-mentioned composition, one or more components selected from the following groups A to D, in mass %: Group A: one or more selected from Ca, Mg and REM, in total 0.0010 to 0.0080% Group B: 0.01 to 0.60% in total of one or more elements selected from Cr, Mo, Cu, and Ni Group C: one or more selected from Ti, Nb and V, in total 0.0005 to 0.0030% ⁇ Group D; B: 0.0001-0.0020% [3]
  • Group A one or more selected from Ca, Mg and REM, in total 0.0010 to 0.0080%
  • Group B 0.01 to 0.60% in total of one or more elements selected from Cr, Mo, Cu, and Ni
  • Group C one or more selected from Ti, Nb and V, in total 0.0005 to 0.0030%
  • Group D B: A manufacturing method of 0.0001 to 0.0020%.
  • the steel slab further contains, in addition to the above-mentioned component composition, one or more components selected from the following groups A to D, in mass %, in the method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet.
  • Group A one or more selected from Ca, Mg and REM, in total 0.0010 to 0.0080%
  • Group B 0.01 to 0.60% in total of one or more elements selected from Cr, Mo, Cu, and Ni
  • Group C one or more selected from Ti, Nb and V, in total 0.0005 to 0.0030%
  • Group D B: A manufacturing method of 0.0001 to 0.0020%.
  • C 0.0050% or less
  • C is an element that forms carbides and deteriorates the iron loss after finish annealing.
  • C increases the hardness of the hot-rolled annealed sheet and induces sheet breakage during cold rolling.
  • the C content is 0.0050% or less.
  • a preferred C content is 0.0030% or less.
  • Si 2.0-5.0% Since Si has the effect of increasing the resistivity of steel and reducing iron loss after final annealing, the content is set to 2.0% or more. Preferably, the content is set to 2.7% or more. On the other hand, if the Si content exceeds 5.0%, the hot-rolled annealed sheet becomes excessively hard and embrittled, and is easily broken during cold rolling, so the upper limit is set to 5.0%. Preferably, the content is set to 4.5% or less.
  • S 0.0050% or less S segregates at grain boundaries and embrittles hot-rolled annealed sheets, making the steel sheet more likely to break during cold rolling, and also forms fine sulfides, deteriorating iron loss after finish annealing. Therefore, the upper limit of the S content is 0.0050%.
  • the preferred S content is 0.0025% or less.
  • the upper limit of Al is set to 2.50%. It is preferably 2.30% or less.
  • N 0.0050% or less N forms nitrides which may become the starting points of sheet fracture during cold rolling, so the upper limit of the N content is set to 0.0050%. Note that fine nitrides inhibit grain growth and deteriorate iron loss after final annealing, so the preferred N content is 0.0035% or less.
  • O 0.0050% or less O forms oxides which may become the starting points of sheet fracture during cold rolling, so the upper limit is set to 0.0050%.
  • the formed oxides inhibit grain growth of the ferrite structure and deteriorate the iron loss after final annealing, so the preferred O content is 0.0025% or less.
  • Sn and Sb one or more, total amount 0.01 to 0.20%
  • Sn and Sb have the effect of improving the magnetic properties by improving the texture after cold rolling and finish annealing, and also have the effect of suppressing the generation of Fe-Al oxides by surface segregation, thereby improving the fracture resistance in cold rolling. Therefore, the total content of one or more of Sn and Sb is set to 0.01% or more. It is preferably 0.02% or more.
  • the upper limit of the total content of Sn and Sb is set to 0.20%.
  • the above are the basic components of the hot-rolled annealed sheet for non-oriented electrical steel sheet according to this embodiment, but in order to further improve various properties, it is preferable to contain at least one group of components selected from the following groups A to D.
  • Group A one or more selected from Ca, Mg and REM, in total 0.0010 to 0.0080% Ca, Mg and REM have the effect of fixing S as sulfides and improving iron loss. For this reason, it is preferable that one or more of Ca, Mg and REM are contained in a total amount of 0.0010% or more. More preferably, it is 0.0020% or more. On the other hand, if the total content of Ca, Mg and REM exceeds 0.0080%, inclusions are excessively generated and manufacturability is reduced, so the upper limit is set to 0.0080%. The preferred total content of Ca, Mg and REM is 0.0060% or less.
  • Group B 0.01 to 0.60% in total of one or more elements selected from Cr, Mo, Cu, and Ni Cr, Mo, Cu, and Ni have the effect of increasing the resistivity of steel and improving iron loss. Therefore, it is preferable to contain at least one of Cr, Mo, Cu, and Ni in a total amount of 0.01% or more. On the other hand, if added in excess, the hot-rolled annealed sheet is hardened and the sheet is easily broken during cold rolling, so the upper limit of the total content is preferably 0.40%.
  • G group one or more elements selected from Ga and Ge, in total 0.0001 to 0.0200% Ga and Ge have the effect of improving the texture of the finish annealed sheet and improving the magnetic properties. For this reason, it is preferable to contain at least one selected from Ga and Ge in a total amount of 0.0001% or more. On the other hand, even if the content exceeds 0.0200%, the above effect is saturated, so the upper limit is preferably set to 0.0200%.
  • Co 0.001-0.100%
  • Co has the effect of improving magnetic flux density. For this reason, it is preferable to include 0.001% or more of Co.
  • the upper limit is preferably set to 0.100%.
  • the chemical composition of the hot-rolled annealed sheet for the non-oriented electrical steel sheet according to this embodiment is such that the remainder other than the above elements is Fe and unavoidable impurities.
  • the steel structure of the hot-rolled annealed sheet for the non-oriented electrical steel sheet according to this embodiment will be described.
  • Average grain size in the rolling direction of the steel plate 40 to 250 ⁇ m If the structure of the hot-rolled annealed sheet is coarse, the hot-rolled annealed sheet becomes embrittled and is easily broken during cold rolling, so the average crystal grain size is set to 250 ⁇ m or less. From the viewpoint of preventing breakage, the average grain size is preferably 180 ⁇ m or less, and more preferably 120 ⁇ m or less.
  • the average crystal grain size is less than 40 ⁇ m, the hot-rolled annealed sheet will harden and the load during cold rolling will increase, making the sheet more likely to break, so the average crystal grain size must be 40 ⁇ m or more.
  • the preferred average crystal grain size is 60 ⁇ m or more.
  • Integral intensity of Fe-Al oxides on the steel sheet surface 200 cps-degrees or less Since Fe-Al oxides are hard and have poor wettability with lubricating oil, if they remain on the steel sheet surface, they will damage the rolling rolls during cold rolling, increasing the friction coefficient and rolling load, making rolling unstable and leading to sheet breakage. Therefore, it is necessary to sufficiently remove Fe-Al oxides in the pickling process, and as an indicator, the integrated intensity of Fe-Al oxides on the steel sheet surface measured by X-ray diffraction of a hot-rolled annealed sheet after pickling needs to be 200 cps-degrees or less.
  • the manufacturing method of the hot-rolled annealed sheet for the non-oriented electrical steel sheet according to the present embodiment includes a hot rolling process in which a steel slab having the above-mentioned composition is heated and hot-rolled to obtain a hot-rolled steel sheet, a hot-rolled sheet annealing process in which the hot-rolled steel sheet is annealed to obtain a hot-rolled annealed sheet, a shot blasting process in which the hot-rolled annealed sheet is shot blasted, and a pickling process in which the shot-blasted hot-rolled annealed sheet is pickled.
  • the composition of the steel slab used in the manufacture of the hot-rolled annealed sheet for the non-oriented electrical steel sheet of this embodiment is adjusted to the range described above.
  • the method of smelting the steel can be a known refining process such as a converter, an electric furnace, or a vacuum degassing device, and is not particularly limited.
  • continuous casting is preferable as the method of manufacturing the steel slab.
  • iron scrap or direct reduced iron may be used as the raw material.
  • it is preferable to use iron scrap since elements such as Cu and Ni that are useful for reducing iron loss can be obtained inexpensively from the iron scrap.
  • Finish rolling temperature 960°C or less If the finish rolling temperature of the hot rolling exceeds 960°C, the scale of the hot rolled sheet becomes thick and the pickling property is reduced, so the finish rolling temperature is set to 960°C or less.
  • a preferred finish rolling temperature is 920°C or less.
  • the lower limit is preferably 750°C. More preferably, it is 780°C or more.
  • Coiling temperature 700°C or less If the coiling temperature exceeds 700°C, scale increases, and in particular Fe-Al-based oxides become thicker, decreasing pickling properties, so the upper limit is set to 700°C.
  • the coiling temperature is preferably 620°C or less.
  • the lower limit is preferably 450°C. From the viewpoint of reducing iron loss by coarsening precipitates during coiling, the coiling temperature is preferably 480°C or more.
  • Hot-rolled sheet annealing temperature 800 to 1100°C
  • the hot-rolled sheet annealing is performed to homogenize the structure and control the ferrite grain size within a predetermined range, thereby improving the fracture resistance during cold rolling and improving the magnetic properties after cold rolling and finish annealing. If the hot-rolled sheet annealing temperature is higher than 1100° C., the structure becomes too coarse, the toughness decreases, and the sheet is likely to break during cold rolling, so it is necessary to set the temperature at 1100° C. or less.
  • the hot-rolled sheet annealing temperature is preferably 1030° C. or less.
  • the hot-rolled sheet annealing temperature is lower than 800° C., the grain size does not become large enough, and the magnetic properties after the final annealing are deteriorated, so it is necessary to set the temperature to 800° C. or higher.
  • the preferred hot-rolled sheet annealing temperature is 900° C. or higher.
  • the annealing time is not particularly determined, but it is preferably 10 s or more from the viewpoint of ensuring uniformity.
  • shot blasting density 10 to 40 kg/ m2
  • the shot blasting density required for this purpose is 10 kg/m2 or more , preferably 15 kg/m2 or more .
  • the projection density exceeds 40 kg/ m2 , not only will cracks be introduced into the scale, but the surface layer of the base steel will also be deformed, which will become the starting point for sheet breakage during cold rolling, so the projection density is set to 40 kg/m2 or less .
  • the preferred projection density is 35 kg/ m2 or less.
  • the average particle size of the shot blast particles is preferably 0.50 mm or less. From the viewpoint of promoting pickling properties, 0.30 mm or less is more preferable.
  • the average particle size of the shot blast particles is preferably 0.15 mm or more.
  • the average particle size of the shot blast particles can be measured, for example, by the particle size analysis - laser diffraction and scattering method described in JIS Z 8825:2013.
  • the shot blast particles are soft, the shot blast particles themselves will deform when colliding with the steel plate, and cracks cannot be efficiently introduced into the scale, so the Vickers hardness of the shot blast particles is preferably 400 HV or more.
  • brush grinding may be performed on the hot-rolled annealed steel sheet before pickling, which can also introduce cracks into the scale, facilitating the removal of the scale during pickling.
  • a brush roll for brush grinding.
  • the brush material and grinding conditions can be selected as appropriate, but from the viewpoint of grinding evenly by following the shape of the steel plate, it is preferable to use chemical fibers, which are softer than metal, for the brush bristles.
  • the brush contains abrasive grains such as alumina, silicon carbide, or diamond. It is preferable to spray cooling water during brush grinding to remove grinding powder and prevent the brush from overheating.
  • [Pickling process] Hydrochloric acid concentration 5% or more, pickling temperature 70°C or more, pickling time 10s or more, 120s or less
  • the pickling process is a process for removing scale from the hot-rolled annealed sheet subjected to the above-mentioned shot blasting and brush grinding, and by sufficiently removing not only iron oxide but also Fe-Al-based scale, sheet breakage during cold rolling can be suppressed.
  • the hydrochloric acid concentration is set to 5% or more. It is preferably set to 8% or more. Although there is no particular upper limit, it is preferable that the hydrochloric acid concentration is set to 20% or less because over-pickling may occur.
  • the temperature of the pickling solution (pickling temperature) is set to 70°C or more. It is preferably set to 75°C or more. If the pickling temperature is too high, over-pickling is likely to occur, and the amount of evaporation of the pickling solution increases, increasing the production cost, so it is preferably set to 96°C or less.
  • the pickling time is set to 10s or more. It is preferably set to 15s or more. If the pickling time exceeds 120 s, hydrogen generation increases and hydrogen embrittlement occurs, making the steel more susceptible to fracture during cold rolling, so the upper limit of the pickling time is set to 120 s. As described above, the pickling properties change depending on the Al content, the hot rolling finish temperature, and the coiling temperature, so that the pickling solution may be adjusted by appropriately adding a pickling accelerator or a pickling inhibitor as necessary.
  • iron oxide that is relatively easily soluble in acid is generated in the area where the base steel is exposed, and the iron oxide in this area dissolves during pickling, which then becomes the starting point for dissolution of the base steel, and the Fe-Al-based scale can be removed by dissolving the base steel.
  • the elongation rate is 10.0% or less. More preferably, it is 6.0% or less.
  • rolling and/or tensile bending with an elongation rate of 0.1 to 10.0% is performed before hot-rolled sheet annealing, it is preferable to perform the above processing so that the integrated strength of the hot-rolled annealed sheet after pickling is 150 cps degrees or less.
  • the slab was heated in a gas furnace under the conditions shown in Tables 2-1 and 2-2, and then hot-rolled by rough rolling and finish rolling to obtain a hot-rolled sheet having a thickness of 1.8 mm and a width of 1200 mm.
  • the hot-rolled sheet was then subjected to hot-rolled sheet annealing, and then pickled to obtain a hot-rolled annealed sheet.
  • one or both of light rolling before hot-rolling annealing using a skin pass rolling machine and brush grinding after pickling were applied to some of the hot-rolled sheets.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Electromagnetism (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)

Abstract

Selon la présente invention, une brame d'acier contenant une quantité prédéterminée de C, Si, Mn, P, S, Al, N, O, Sn et Sb est chauffée sous une condition prédéfinie, laminée à chaud, recuite à chaud, grenaillée et décapée, ou la brame d'acier est chauffée sous une condition prédéfinie, laminée à chaud, recuite à chaud, meulée à la brosse et décapée de telle sorte que la taille moyenne de grain dans une section transversale dans la direction de laminage d'une tôle d'acier après le décapage est de 40 à 250 µm et l'intensité intégrée des oxydes à base de Fe-Al dans la couche de surface de la tôle d'acier mesurée par diffraction aux rayons X est inférieure ou égale à 200 cps ∙ degré, ce qui permet d'obtenir une tôle recuite laminée à chaud pour une tôle d'acier électromagnétique non orienté, qui permet d'éviter une rupture de tôle pendant le laminage à froid et présente d'excellentes propriétés magnétiques après recuit de tôle laminée à froid. De plus, une tôle d'acier électromagnétique non orienté est fabriquée à l'aide de la tôle recuite laminée à chaud.
PCT/JP2024/019129 2023-08-30 2024-05-24 Tôle recuite laminée à chaud pour tôle d'acier électromagnétique non orienté, son procédé de fabrication et procédé de fabrication de tôle d'acier électromagnétique non orienté Pending WO2025047016A1 (fr)

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000054025A (ja) * 1998-07-30 2000-02-22 Kawasaki Steel Corp 電磁鋼板の製造方法
JP2006161094A (ja) * 2004-12-06 2006-06-22 Nippon Steel Corp 高級無方向性電磁鋼板の製造方法
JP2021038458A (ja) * 2019-08-30 2021-03-11 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
KR20230096879A (ko) * 2021-12-22 2023-06-30 주식회사 포스코 무방향성 전기강판 및 그를 포함하는 모터 코어
WO2023149249A1 (fr) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication
WO2023149269A1 (fr) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000054025A (ja) * 1998-07-30 2000-02-22 Kawasaki Steel Corp 電磁鋼板の製造方法
JP2006161094A (ja) * 2004-12-06 2006-06-22 Nippon Steel Corp 高級無方向性電磁鋼板の製造方法
JP2021038458A (ja) * 2019-08-30 2021-03-11 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
KR20230096879A (ko) * 2021-12-22 2023-06-30 주식회사 포스코 무방향성 전기강판 및 그를 포함하는 모터 코어
WO2023149249A1 (fr) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication
WO2023149269A1 (fr) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Tôle d'acier électromagnétique non orientée et son procédé de fabrication

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JPWO2025047016A1 (fr) 2025-03-06

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