[go: up one dir, main page]

WO2025047016A1 - Hot-rolled annealed sheet for non-oriented electromagnetic steel sheet, method for manufacturing same, and method for manufacturing non-oriented electromagnetic steel sheet - Google Patents

Hot-rolled annealed sheet for non-oriented electromagnetic steel sheet, method for manufacturing same, and method for manufacturing non-oriented electromagnetic steel sheet Download PDF

Info

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
Authority
WO
WIPO (PCT)
Prior art keywords
hot
sheet
rolled
less
group
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
PCT/JP2024/019129
Other languages
French (fr)
Japanese (ja)
Inventor
勇人 齋藤
智幸 大久保
茂宏 丸山
孝明 田中
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
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/en
Pending legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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.

Landscapes

  • 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

According to the present invention, a steel slab containing a predetermined amount of C, Si, Mn, P, S, Al, N, O, Sn, and Sb is heated under a predetermined condition, hot rolled, hot annealed, shot blasted and pickled, or the steel slab is heated under a predetermined condition, hot rolled, hot annealed, brush ground and pickled such that the average grain size in a cross section in the rolling direction of a steel sheet after the pickling is 40-250 μm and the integrated intensity of Fe-Al-based oxides in the surface layer of the steel sheet measured by X-ray diffraction is 200 cps∙degree or less, thereby obtaining a hot-rolled annealed sheet for a non-oriented electromagnetic steel sheet, which enables the prevention of sheet breakage during cold rolling and exhibits excellent magnetic properties after cold-rolled sheet annealing. In addition, a non-oriented electromagnetic steel sheet is manufactured using the hot-rolled annealed sheet.

Description

無方向性電磁鋼板用の熱延焼鈍板とその製造方法ならびに無方向性電磁鋼板の製造方法Hot-rolled annealed sheet for non-oriented electrical steel sheet, its manufacturing method, and manufacturing method for non-oriented electrical steel sheet

　本発明は、冷間圧延での耐破断性に優れた無方向性電磁鋼板用の熱延焼鈍板とその製造方法ならびに上記熱延焼鈍版を用いた無方向性電磁鋼板の製造方法に関するものである。 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.

　近年、環境問題への意識の高まりから排出ＣＯ２の削減や省エネルギーに対するニーズが強くなっており、電動車を含めた電気機器においても高効率化が強く求められている。そのため、電気機器に用いられるモーターの鉄心材料として広く使用されている無方向性電磁鋼板にも、鉄損特性の向上が強く求められている。そのため、これまでにＳｉやＡｌ等の固有抵抗を高める元素を多量に添加したり、板厚を低減したりすることなどで鉄損の改善がなされてきた。
　一方、ＳｉやＡｌ等の多量添加や最終板厚の低減は、冷間圧延での製造負荷が大きくなることにつながるため、磁気特性の向上に加えて、冷間圧延で鋼板が破断するなどのトラブルが発生しないことが重要となってきている。 In recent years, with the growing awareness of environmental issues, there is a strong need to reduce CO2 emissions and conserve energy, and there is a strong demand for high efficiency in electrical equipment, including electric vehicles. Therefore, there is a strong demand for improved iron loss properties in non-oriented electrical steel sheets, which are widely used as iron core materials for motors used in electrical equipment. For this reason, improvements in iron loss have been made so far by adding large amounts of elements such as Si and Al that increase the specific resistance, or by reducing the sheet thickness.
On the other hand, the addition of large amounts of Si, Al, etc., and the reduction of the final sheet thickness lead to an increased production load in cold rolling, so in addition to improving the magnetic properties, it is becoming important to prevent problems such as breakage of the steel sheet during cold rolling.

　そこで、この問題を解決するため、熱延板焼鈍温度を制御し、靭性を改善することで冷間圧延での板破断を抑制するなどの技術が提案されている。 To solve this problem, technologies have been proposed that control the annealing temperature of hot-rolled sheets and improve toughness to prevent sheet breakage during cold rolling.

　例えば、特許文献１には、質量％で、Ｃ：０．００１０～０．００５０％、Ｓｉ：２．５～４．０％、Ａｌ：０．２～２．０％、Ｍｎ：０．０５～２．０％、Ｐ：０．００５～０．１５％、Ｓ：０．０００１～０．００３０％、Ｔｉ：０．０００５～０．００３０％、Ｎ：０．００１０～０．００３０％を含有し、残部がＦｅ及び不可避的不純物からなり、地鉄の板厚が０．１０ｍｍ以上０．３５ｍｍ以下であり、地鉄表面からの深さ方向でのＡｌ濃度について、以下の式（１）に示す関係式を満足する、無方向性電磁鋼板が開示されている。これによれば、熱延板焼鈍の均熱温度が１１００℃を超える場合、又は、均熱時間が３００秒を超える場合には、後段の冷間圧延において地鉄が破断してしまう可能性が生じるとの説明がある。
　０．１≦Ａｌ（ｘ≦２μｍ）／Ａｌ（ｘ＝１０μｍ）＜１．０　・・・（１）
　ここで、上記式（１）において、ｘ：地鉄表面からの深さ［μｍ］、Ａｌ（ｘ≦２μｍ）：地鉄表面から深さ２μｍまでのＡｌ濃度の平均値、Ａｌ（ｘ＝１０μｍ）：深さ１０μｍの位置でのＡｌ濃度である。 For example, 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. According to this, it is explained that if the soaking temperature in the hot-rolled sheet annealing exceeds 1100°C or the soaking time exceeds 300 seconds, there is a possibility that the base steel may break in the subsequent cold rolling.
0.1≦Al(x≦2μm)/Al(x=10μm)<1.0 (1)
Here, in the above formula (1), x is the depth [μm] from the surface of the steel substrate, Al(x≦2 μm): the average Al concentration from the surface of the steel substrate to a depth of 2 μm, and Al(x=10 μm): the Al concentration at a depth of 10 μm.

特開２０１８－０２１２４１号公報JP 2018-021241 A

　しかしながら、上記特許文献に開示された従来技術には、以下のような問題がある。 However, the conventional technology disclosed in the above patent document has the following problems:

　発明者らの調査した結果によると、上記の特許文献１に記載された熱延板焼鈍条件の制御のみでは、必ずしも破断発生を抑制できないこと、また、冷間圧延での耐破断性と冷延板焼鈍後の良好な磁気特性との両立が困難であることがわかった。 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.

　本発明は、かかる問題点に鑑みてなされたものであり、熱延板焼鈍後の冷間圧延での破断防止と冷延板焼鈍後の磁気特性に優れた無方向性電磁鋼板用の熱延焼鈍板を提供するとともに、その製造方法ならびに上記熱延焼鈍板を用いた無方向性電磁鋼板の製造方法を提案することを目的とする。 The present invention was made in consideration of these problems, and aims to provide a hot-rolled annealed sheet for non-oriented electrical steel sheet that prevents breakage during cold rolling after hot-rolled sheet annealing and has excellent magnetic properties after cold-rolled sheet annealing, as well as to propose a manufacturing method thereof and a manufacturing method for non-oriented electrical steel sheet using the above-mentioned hot-rolled annealed sheet.

　上記課題を有利に解決する本発明に係る無方向性電磁鋼板用の熱延焼鈍板は、以下のように構成される。
［１］質量％で、Ｃ：０．００５０％以下、Ｓｉ：２．０～５．０％、Ｍｎ：０．２～２．０％、Ｐ：０．０３０％以下、Ｓ：０．００５０％以下、Ａｌ：０．２５～２．５０％、Ｎ：０．００５０％以下、Ｏ：０．００５０％以下、ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有し、鋼板の圧延方向断面の平均結晶粒径が４０～２５０μｍであり、Ｘ線回折にて測定した鋼板表層のＦｅ－Ａｌ系酸化物の積分強度が２００ｃｐｓ・度以下である無方向性電磁鋼板用の熱延焼鈍板である。
［２］上記の［１］において、上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有する無方向性電磁鋼板用の熱延焼鈍板である。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％
［３］上記の［１］または［２］において、上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする無方向性電磁鋼板用の熱延焼鈍板である。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％ The hot-rolled annealed sheet for non-oriented electrical steel sheet according to the present invention, which advantageously solves the above problems, is configured as follows.
[1] A hot-rolled annealed sheet for non-oriented electrical steel sheet, which contains, by mass%, C: 0.0050% or less, Si: 2.0 to 5.0%, Mn: 0.2 to 2.0%, P: 0.030% or less, S: 0.0050% or less, Al: 0.25 to 2.50%, N: 0.0050% or less, O: 0.0050% or less, Sn and/or Sb: one or more types in total of 0.01 to 0.20%, with the balance being Fe and unavoidable impurities, has an average crystal grain size of 40 to 250 μm in a cross section in the rolling direction of the steel sheet, and has an integrated intensity of Fe-Al-based oxides in the steel sheet surface layer measured by X-ray diffraction of 200 cps-degree or less.
[2] In the above [1], 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] The hot-rolled annealed sheet for non-oriented electrical steel sheet according to the above [1] or [2], further comprising, in addition to the above-mentioned chemical composition, one or more components selected from the following groups E to J, in mass %:
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total, 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020%

　上記課題を有利に解決する本発明に係る無方向性電磁鋼板用の熱延焼鈍板の製造方法は、以下のように構成される。
［４］質量％で、Ｃ：０．００５０％以下、Ｓｉ：２．０～５．０％、Ｍｎ：０．２～２．０％、Ｐ：０．０３０％以下、Ｓ：０．００５０％以下、Ａｌ：０．２５～２．５０％、Ｎ：０．００５０％以下、Ｏ：０．００５０％以下、ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有する鋼スラブを加熱し、熱間圧延して熱延鋼板とする熱間圧延工程と、上記熱延鋼板を焼鈍して熱延焼鈍板とする熱延板焼鈍工程と、上記熱延焼鈍板にショットブラストを施すショットブラスト工程と、上記ショットブラストされた熱延焼鈍板を酸洗する酸洗工程とを含み、上記熱間圧延工程では、上記鋼スラブの加熱温度を１１５０℃以下、仕上げ圧延温度を９６０℃以下、巻取温度を７００℃以下とし、上記熱延板焼鈍工程では、焼鈍温度を８００℃以上１１００℃以下とし、上記ショットブラスト工程では、投射密度１０～４０ｋｇ／ｍ２のショットブラストを上記熱延焼鈍板に施し、上記酸洗工程では、塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０ｓ以上、１２０ｓ以下で、ショットブラストされた鋼板を酸洗する無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
［５］上記の［４］において、上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有することを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％の製造方法である。
［６］上記の［４］又は［５］において、上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％
［７］上記の［４］から［６］のいずれか一において、上記熱延鋼板を焼鈍する前に、上記熱延鋼板に伸長率が０．１～１０．０％の圧延及び／又は引張り曲げ加工を施すことを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
［８］上記の［４］から［７］のいずれか一において、上記酸洗工程後に、酸洗された鋼板の表裏面に対してブラシ研削を行うことを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。 The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to the present invention, which advantageously solves the above problems, is configured as follows.
[4] A hot rolling process in which a steel slab having a composition containing, by mass%, C: 0.0050% or less, Si: 2.0 to 5.0%, Mn: 0.2 to 2.0%, P: 0.030% or less, S: 0.0050% or less, Al: 0.25 to 2.50%, N: 0.0050% or less, O: 0.0050% or less, Sn and Sb: one or more kinds in total 0.01 to 0.20%, and the balance consisting of Fe and unavoidable impurities is heated and hot rolled to obtain a hot-rolled steel sheet, and the hot-rolled steel sheet is annealed. The method includes a hot-rolled sheet annealing step of annealing the hot-rolled annealed sheet by shot blasting the hot-rolled annealed sheet, and a pickling step of pickling the shot-blasted hot-rolled annealed sheet. In the hot-rolling step, the heating temperature of the steel slab is 1150°C or less, the finish rolling temperature is 960°C or less, and the coiling temperature is 700°C or less. In the hot-rolled sheet annealing step, the annealing temperature is 800°C or more and 1100°C or less. In the shot blasting step, the hot-rolled annealed sheet is subjected to shot blasting with a projection density of 10 to 40 kg/ m2. In the pickling step, the shot-blasted steel sheet is pickled with a hydrochloric acid concentration of 5% or more, a pickling temperature of 70°C or more, and a pickling time of 10 s to 120 s. This is a manufacturing method of a hot-rolled annealed sheet for non-oriented electrical steel sheet.
[5] In the above [4], the steel slab 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: A manufacturing method of 0.0001 to 0.0020%.
[6] In the above [4] or [5], the steel slab further contains, in addition to the above-mentioned chemical composition, one or more components selected from the following groups E to J, in mass %.
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020%
[7] In any one of the above [4] to [6], the method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet is characterized in that, before annealing the hot-rolled steel sheet, the hot-rolled steel sheet is subjected to rolling and/or tensile bending with an elongation rate of 0.1 to 10.0%.
[8] The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to any one of the above [4] to [7], characterized in that, after the above pickling step, brush grinding is performed on both sides of the pickled steel sheet.

　上記課題を有利に解決する本発明に係る無方向性電磁鋼板の製造方法は、以下のように構成される。
［９］上記の［４］から［８］のいずれか一において得た熱延焼鈍板を、１回の冷間圧延または中間焼鈍を含む２回以上の冷間圧延をして最終板厚の冷延板とし、上記冷延板を、均熱温度７００～１１００℃で冷延板焼鈍して冷延焼鈍板とする無方向性電磁鋼板の製造方法である。 The method for producing a non-oriented electrical steel sheet according to the present invention, which advantageously solves the above problems, is configured as follows.
[9] A method for producing a non-oriented electrical steel sheet, comprising the steps of: subjecting a hot-rolled annealed sheet obtained in any one of the above [4] to [8] to one cold rolling or two or more cold rolling including intermediate annealing to obtain a cold-rolled sheet having a final thickness; and annealing the cold-rolled sheet at a soaking temperature of 700 to 1100°C to obtain a cold-rolled annealed sheet.

　上記課題を有利に解決する本発明に係る無方向性電磁鋼板用の熱延焼鈍板の他の製造方法は、以下のように構成される。
［１０］質量％で、Ｃ：０．００５０％以下、Ｓｉ：２．０～５．０％、Ｍｎ：０．２～２．０％、Ｐ：０．０３０％以下、Ｓ：０．００５０％以下、Ａｌ：０．２５～２．５０％、Ｎ：０．００５０％以下、Ｏ：０．００５０％以下、ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有する鋼スラブを加熱し、熱間圧延して熱延鋼板とする熱間圧延工程と、上記熱延鋼板を焼鈍して熱延焼鈍板とする熱延板焼鈍工程と、上記熱延焼鈍板にブラシ研削を施すブラシ研削工程と、上記ブラシ研削された熱延焼鈍板を酸洗する酸洗工程とを含み、上記熱間圧延工程では、上記鋼スラブの加熱温度を１１５０℃以下、仕上げ圧延温度を９６０℃以下、巻取温度を７００℃以下とし、上記熱延板焼鈍工程では、焼鈍温度を８００℃以上１１００℃以下とし、上記酸洗工程では、塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０ｓ以上、１２０ｓ以下で、ブラシ研削された鋼板を酸洗する無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
［１１］上記の［１０］において、上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有する無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％の製造方法である。
［１２］上記の［１０］または［１１］において、上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％
［１３］上記の［１０］から［１２］のいずれか一において、上記熱延鋼板を焼鈍する前に、上記熱延鋼板に伸長率が０．１～１０．０％の圧延及び／又は引張り曲げ加工を施すことを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。
［１４］上記の［１０］から［１３］のいずれか一において、上記酸洗工程後に、酸洗された鋼板の表裏面に対してブラシ研削を行うことを特徴とする無方向性電磁鋼板用の熱延焼鈍板の製造方法である。 Another method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to the present invention, which advantageously solves the above problems, is configured as follows.
[10] A hot rolling process in which a steel slab having a composition containing, by mass%, C: 0.0050% or less, Si: 2.0 to 5.0%, Mn: 0.2 to 2.0%, P: 0.030% or less, S: 0.0050% or less, Al: 0.25 to 2.50%, N: 0.0050% or less, O: 0.0050% or less, Sn and Sb: one or more in total of 0.01 to 0.20%, and the balance consisting of Fe and unavoidable impurities, 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; and This is a manufacturing method of a hot-rolled annealed sheet for non-oriented electrical steel sheet, which includes a brush grinding step of brush-grinding a annealed sheet, and a pickling step of pickling the brush-ground hot-rolled annealed sheet, wherein in the hot rolling step, the heating temperature of the steel slab is 1150°C or less, the finish rolling temperature is 960°C or less, and the coiling temperature is 700°C or less, in the hot-rolled sheet annealing step, the annealing temperature is 800°C or more and 1100°C or less, and in the pickling step, the brush-ground steel sheet is pickled with a hydrochloric acid concentration of 5% or more, a pickling temperature of 70°C or more, and a pickling time of 10 s or more and 120 s or less.
[11] In the above [10], 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%.
[12] The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to the above [10] or [11], wherein the steel slab further contains, in addition to the above-mentioned chemical composition, one or more components selected from the following groups E to J, in mass %:
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total, 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020%
[13] In any one of the above [10] to [12], the method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet is characterized in that, before annealing the hot-rolled steel sheet, the hot-rolled steel sheet is subjected to rolling and/or tensile bending with an elongation rate of 0.1 to 10.0%.
[14] The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to any one of the above [10] to [13], characterized in that, after the above pickling step, brush grinding is performed on both sides of the pickled steel sheet.

　上記課題を有利に解決する本発明に係る無方向性電磁鋼板の他の製造方法は、以下のように構成される。
［１５］上記の［１０］から［１４］のいずれか一において得た熱延焼鈍板を、１回の冷間圧延または中間焼鈍を含む２回以上の冷間圧延をして最終板厚の冷延板とし、上記冷延板を、均熱温度７００～１１００℃で冷延板焼鈍して冷延焼鈍板とする無方向性電磁鋼板の製造方法である。 Another method for producing a non-oriented electrical steel sheet according to the present invention, which advantageously solves the above problems, is configured as follows.
[15] A method for producing a non-oriented electrical steel sheet, comprising the steps of: subjecting a hot-rolled annealed sheet obtained in any one of the above [10] to [14] to one cold rolling or two or more cold rolling including intermediate annealing to obtain a cold-rolled sheet having a final thickness; and annealing the cold-rolled sheet at a soaking temperature of 700 to 1100°C to obtain a cold-rolled annealed sheet.

　本発明によれば、冷間圧延における鋼板の破断を抑制しつつ、磁気特性に優れた無方向性電磁鋼板を効率的に製造することが可能となる。 The present invention makes it possible to efficiently manufacture non-oriented electrical steel sheets with excellent magnetic properties while suppressing breakage of the steel sheets during cold rolling.

　発明者らは、冷間圧延での板破断の原因について鋭意検討を行った。その結果、本発明のようにＳｉおよびＡｌが多量に添加されている鋼板では、熱間圧延時または熱延板焼鈍時に鋼板表面に鉄酸化物のみならずＳｉやＡｌの酸化物が生成する。特に地鉄と酸化物層の界面近傍にはＦｅ－Ａｌ系スケールが緻密に生成する。このＦｅ－Ａｌ系スケールは、酸に難溶性であるため、酸洗工程で完全に除去しきれない場合には、冷間圧延の圧延ロールの摩耗を促進し、鋼板が破断しやすくなるという知見を得た。これを解決するため、スケール除去に関わる機械的および化学的条件を検討し、Ｆｅ－Ａｌ系スケールを含むスケールを安定的に除去できる適切な条件を見出し、本発明を開発するに至った。 The inventors conducted extensive research into the causes of sheet breakage during cold rolling. As a result, in steel sheets containing large amounts of Si and Al as in the present invention, not only iron oxides but also oxides of Si and Al are formed on the surface of the steel sheet during hot rolling or hot-rolled sheet annealing. In particular, Fe-Al scale is densely formed near the interface between the base steel and the oxide layer. This Fe-Al scale is poorly soluble in acid, and it was discovered that if it cannot be completely removed in the pickling process, it will promote wear of the rolling rolls in cold rolling, making the steel sheet more likely to break. To solve this problem, the inventors investigated the mechanical and chemical conditions related to scale removal and found appropriate conditions for stably removing scale, including Fe-Al scale, which led to the development of the present invention.

　以下、本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板について説明する。
　まず、本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の成分組成とその限定理由について説明する。以下の説明において、特に断らない限り、「％」の表記は「質量％」を意味する。
＜無方向性電磁鋼板用の熱延焼鈍板＞
　本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板は、質量％で、Ｃ：０．００５０％以下、Ｓｉ：２．０～５．０％、Ｍｎ：０．２～２．０％以下、Ｐ：０．０３０％以下、Ｓ：０．００５０％以下、Ａｌ：０．２５～２．５０％以下、Ｎ：０．００５０％以下、Ｏ：０．００５０％以下、ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を含有する。 Hereinafter, the hot-rolled annealed sheet for the non-oriented electrical steel sheet according to this embodiment will be described.
First, the chemical composition of the hot-rolled annealed sheet for the non-oriented electrical steel sheet according to the present embodiment and the reasons for limiting the composition will be described. In the following description, unless otherwise specified, the notation "%" means "mass %".
<Hot-rolled annealed sheet for non-oriented electrical steel sheet>
The hot-rolled annealed sheet for non-oriented electrical steel sheet according to this embodiment contains, by mass%, C: 0.0050% or less, Si: 2.0 to 5.0%, Mn: 0.2 to 2.0% or less, P: 0.030% or less, S: 0.0050% or less, Al: 0.25 to 2.50% or less, N: 0.0050% or less, O: 0.0050% or less, Sn and/or Sb: 0.01 to 0.20% in total of one or more types, and the balance being Fe and unavoidable impurities.

Ｃ：０．００５０％以下
　Ｃは、炭化物を形成して、仕上げ焼鈍後の鉄損を劣化させる元素である。また、Ｃは、熱延焼鈍板の硬さを上昇させて冷間圧延での板破断を誘発する。このため、Ｃ含有量は、０．００５０％以下とする。好ましいＣ含有量は、０．００３０％以下である。Ｃ含有量の下限は特に定めないが、熱延焼鈍板の靭性を向上し、冷間圧延での板破断を防止する観点から０．００１０％以上とすることが好ましい。 C: 0.0050% or less C is an element that forms carbides and deteriorates the iron loss after finish annealing. In addition, C increases the hardness of the hot-rolled annealed sheet and induces sheet breakage during cold rolling. For this reason, the C content is 0.0050% or less. A preferred C content is 0.0030% or less. There is no particular lower limit for the C content, but it is preferably 0.0010% or more from the viewpoint of improving the toughness of the hot-rolled annealed sheet and preventing sheet breakage during cold rolling.

Ｓｉ：２．０～５．０％
　Ｓｉは、鋼の比抵抗を高めて、仕上げ焼鈍後の鉄損を低減する効果があるため、２．０％以上とする。好ましくは２．７％以上である。一方、Ｓｉ含有量が５．０％を超えると熱延焼鈍板が過剰に硬化および脆化して、冷間圧延で破断しやすくなるため、上限を５．０％とする。好ましくは４．５％以下である。 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.

Ｍｎ：０．２～２．０％
　Ｍｎは、Ｓｉ同様、鉄損の低減に有用な元素であり、また、地鉄の靭性を向上させ、冷間圧延での板破断を抑制する効果があるため、Ｍｎ含有量は０．２％以上とする。好ましくは０．３５％以上である。一方、Ｍｎ含有量が２．０％を超えると、熱延焼鈍板が過度に硬化して冷間圧延で破断しやすくなるため、２．０％以下とする。 Mn: 0.2-2.0%
Like Si, Mn is an element useful for reducing iron loss, and also has the effect of improving the toughness of the base steel and suppressing sheet breakage during cold rolling, so the Mn content is set to 0.2% or more, and preferably 0.35% or more. On the other hand, if the Mn content exceeds 2.0%, the hot-rolled annealed sheet becomes excessively hard and easily breaks during cold rolling, so the Mn content is set to 2.0% or less.

Ｐ：０．０３０％以下
　Ｐは、鋼の強度を上げる効果があり、強度調整に用いることができる。一方で、Ｐ含有量が０．０３０％を超えると、鋼が脆化し、製造性の低下を招く。そのため、Ｐ含有量は０．０３０％以下とする。脆化防止の観点から好ましいＰ含有量は０．０１５％以下である。なお、Ｐ含有量の下限は特に規定しないが、脱Ｐ負荷を軽減する観点からは、０．００４％程度とするのが好ましい。 P: 0.030% or less P has the effect of increasing the strength of steel and can be used for strength adjustment. On the other hand, if the P content exceeds 0.030%, the steel becomes embrittled, leading to a decrease in manufacturability. Therefore, the P content is set to 0.030% or less. From the viewpoint of preventing embrittlement, the preferred P content is 0.015% or less. There is no particular lower limit for the P content, but from the viewpoint of reducing the de-P load, it is preferably set to about 0.004%.

Ｓ：０．００５０％以下
　Ｓは、結晶粒界に偏析して、熱延焼鈍板を脆化させるため、冷間圧延で鋼板が破断しやすくなり、また微細な硫化物を形成して、仕上げ焼鈍後の鉄損を劣化させる。よって、Ｓ含有量の上限は０．００５０％とする。好ましいＳ含有量は０．００２５％以下である。なお、Ｓ含有量の下限は特に規定しないが、脱Ｓ負荷を軽減する観点からは、０．００１％程度とするのが好ましい。 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. There is no particular lower limit for the S content, but from the viewpoint of reducing the desulfurization load, it is preferably about 0.001%.

Ａｌ：０．２５～２．５０％
　Ａｌは、Ｓｉ同様に、鋼板の比抵抗を高めて、仕上げ焼鈍後の鉄損を低減する効果があるため、Ａｌ含有量は０．２５％以上とする。また、ＡｌはＡｌＮを形成して、ピン止め効果により熱延焼鈍板の平均結晶粒径を小さくし、冷間圧延での耐破断性を向上する効果がある。このため、Ａｌは０．５０％以上含有することが好ましい。さらに好ましくは０．７０％以上である。一方、Ａｌ含有量が２．５０％を超えると、熱間圧延および熱延板焼鈍で生成するスケール中のＦｅ－Ａｌ系酸化物が多量になり、酸洗工程にて除去しきれず、冷間圧延での板破断の要因となる。このためＡｌの上限は２．５０％とする。好ましくは２．３０％以下である。 Al: 0.25-2.50%
Like Si, Al has the effect of increasing the resistivity of the steel sheet and reducing the iron loss after finish annealing, so the Al content is set to 0.25% or more. In addition, Al forms AlN, and has the effect of reducing the average crystal grain size of the hot-rolled annealed sheet by the pinning effect, thereby improving the fracture resistance in cold rolling. For this reason, it is preferable that Al is contained at 0.50% or more. More preferably, it is 0.70% or more. On the other hand, if the Al content exceeds 2.50%, the amount of Fe-Al-based oxides in the scale generated by hot rolling and hot-rolled sheet annealing becomes large, and it cannot be completely removed in the pickling process, which causes the sheet to break in cold rolling. For this reason, the upper limit of Al is set to 2.50%. It is preferably 2.30% or less.

Ｎ：０．００５０％以下
　Ｎは、窒化物を形成して、冷間圧延時の板破断の起点となる場合があるため、Ｎ含有量の上限は０．００５０％とする。なお、微細な窒化物は、粒成長を阻害し、仕上げ焼鈍後の鉄損を劣化させるため、好ましいＮ含有量は０．００３５％以下である。 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％以下
　Ｏは、酸化物を形成して冷間圧延時の板破断の起点となる場合があるので上限は０．００５０％とする。また、形成された酸化物は、フェライト組織の粒成長を阻害し、仕上げ焼鈍後の鉄損を劣化させるため、好ましいＯ含有量は、０．００２５％以下である。 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%. In addition, 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およびＳｂ：一種以上を合計で０．０１～０．２０％
　ＳｎおよびＳｂは、冷間圧延および仕上げ焼鈍後の集合組織の改善により磁気特性を改善する効果があることに加え、表面偏析によりＦｅ－Ａｌ系酸化物の生成を抑制して、冷間圧延での耐破断性を向上する効果がある。このため、ＳｎおよびＳｂの含有量は、一種以上を合計で０．０１％以上とする。好ましくは０．０２％以上である。一方、過剰に添加しても効果が飽和するのみならず、熱延焼鈍板の靭性を劣化させ、冷間圧延で板破断しやすくなるため、ＳｎおよびＳｂの合計含有量の上限は０．２０％とする。 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. On the other hand, even if added excessively, not only the effect is saturated, but also the toughness of the hot-rolled annealed sheet is deteriorated, and the sheet is easily fractured in cold rolling, so the upper limit of the total content of Sn and Sb is set to 0.20%.

　以上が本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の基本成分であるが、さらに、種々の特性向上のため、下記Ａ～Ｄ群のうちから選ばれる少なくとも一群の成分を含有することが好ましい。 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.

Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
　Ｃａ、ＭｇおよびＲＥＭは、Ｓを硫化物として固定し、鉄損を改善する効果がある。このため、Ｃａ、ＭｇおよびＲＥＭは、一種以上を合計で０．００１０％以上含有することが好ましい。より好ましくは０．００２０％以上である。一方、Ｃａ、ＭｇおよびＲＥＭの含有量の合計が０．００８０％を超えると、介在物が過剰に生成して、製造性が低下するため、上限は０．００８０％とする。好ましいＣａ、ＭｇおよびＲＥＭの合計含有量は０．００６０％以下である。 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.

Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
　Ｃｒ、Ｍｏ、ＣｕおよびＮｉは、鋼の比抵抗を高めて、鉄損を改善する効果がある。このため、Ｃｒ、Ｍｏ、ＣｕおよびＮｉは、一種以上を合計で０．０１％以上含有することが好ましい。一方、過剰に添加した場合、熱延焼鈍板を硬化させて、冷間圧延で板破断しやすくなるため、合計含有量の上限は０．４０％とすることが好ましい。 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%.

Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
　Ｔｉ、ＮｂおよびＶは、熱延焼鈍板の組織を微細化し、靭性を向上させて冷間圧延での板破断を抑制する効果がある。このため、Ｔｉ、ＮｂおよびＶの含有量は、合計で０．０００５％以上とすることが好ましい。一方、過剰に添加すると、微細析出物を多量に生成して粒成長を著しく阻害するため、Ｔｉ、ＮｂおよびＶの合計含有量の上限は０．００３０％とすることが好ましい。 Group C: one or more selected from Ti, Nb and V, in total 0.0005 to 0.0030%
Ti, Nb and V have the effect of refining the structure of the hot-rolled annealed sheet, improving toughness and suppressing sheet breakage during cold rolling. Therefore, the total content of Ti, Nb and V is preferably 0.0005% or more. On the other hand, if added in excess, a large amount of fine precipitates are generated, significantly inhibiting grain growth, so the upper limit of the total content of Ti, Nb and V is preferably 0.0030%.

Ｄ群；Ｂ：０．０００１～０．００２０％
　Ｂは、粒界に偏析して靭性を向上し、冷間圧延での板破断を抑制する効果がある。このため、Ｂ含有量は、０．０００１％以上とすることが好ましい。より好ましくは０．０００３％以上である。一方、Ｂ含有量が０．００２０％を超えると、鉄硼化物を形成して、靭性向上効果が無くなるため、上限は０．００２０％とすることが好ましい。 Group D; B: 0.0001-0.0020%
B has the effect of improving toughness by segregating at grain boundaries and suppressing sheet breakage during cold rolling. Therefore, the B content is preferably 0.0001% or more, and more preferably 0.0003% or more. On the other hand, if the B content exceeds 0.0020%, iron borides are formed and the toughness improving effect is lost, so the upper limit is preferably 0.0020%.

　さらに、種々の特性向上のため、下記Ｅ～Ｊ群のうちから選ばれる少なくとも一群の成分を含有することが好ましい。 Furthermore, in order to improve various properties, it is preferable to contain at least one group of components selected from the following groups E to J.

Ｅ群；Ｚｎ：０．００１～０．０１０％
　Ｚｎは、介在物を粗大化させ、仕上げ焼鈍時の粒成長を促進することで仕上げ焼鈍板の鉄損を改善する効果がある。このため、Ｚｎの含有量は０．００１％以上とすることが好ましい。一方、Ｚｎの含有量が０．０１０％を超えても、上記効果が飽和するため、上限は０．０１０％とすることが好ましい。 Group E; Zn: 0.001-0.010%
Zn has the effect of improving the iron loss of the finish-annealed sheet by coarsening inclusions and promoting grain growth during finish annealing. Therefore, the Zn content is preferably 0.001% or more. On the other hand, even if the Zn content exceeds 0.010%, the above effect is saturated, so the upper limit is preferably 0.010%.

Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
　Ｚｒ、Ｔａ、ＷおよびＳｅは、析出物を形成して、熱延焼鈍板の粒径を小さくすることで冷間圧延性の向上に寄与する効果がある。このため、Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１％以上含有することが好ましい。一方、合計の含有量が０．０１０％を超えると、仕上げ焼鈍板の鉄損が劣化することがあるので、上限は０．０１０％とすることが好ましい。 Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Zr, Ta, W and Se have the effect of forming precipitates and reducing the grain size of the hot-rolled annealed sheet, thereby contributing to improving the cold rolling property. For this reason, it is preferable to contain at least one selected from Zr, Ta, W and Se in a total amount of 0.001% or more. On the other hand, if the total content exceeds 0.010%, the iron loss of the finish annealed sheet may deteriorate, so the upper limit is preferably 0.010%.

Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
　ＧａおよびＧｅは、仕上げ焼鈍板の集合組織を改善して磁気特性を向上する効果がある。このため、ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１％以上含有することが好ましい。一方、０．０２００％を超えて含有しても上記効果が飽和するため、上限は０．０２００％とすることが好ましい。 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%.

Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
　ＰｂおよびＢｉは、熱延焼鈍板の粒径を小さくすることで冷間圧延性の向上に効果がある。このため、ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５％以上含有することが好ましい。一方、０．００２０％を超えて含有すると、仕上げ焼鈍板の鉄損が劣化するため、上限は０．００２０％とすることが好ましい。 Group H: 0.00005 to 0.0020% in total of one or more selected from Pb and Bi
Pb and Bi are effective in improving cold rolling properties by reducing the grain size of the hot-rolled annealed sheet. Therefore, it is preferable to contain at least one selected from Pb and Bi in total at 0.00005% or more. On the other hand, if it is contained in excess of 0.0020%, the iron loss of the finish annealed sheet is deteriorated, so the upper limit is preferably set to 0.0020%.

Ｉ群；Ｃｏ：０．００１～０．１００％
　Ｃｏは、磁束密度を向上する効果がある。このため、０．００１％以上含有することが好ましい。一方、０．１００％を超えて含有すると、析出物を形成して、仕上げ焼鈍板の鉄損が劣化するため、上限は０．１００％とすることが好ましい。 Group I; 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. On the other hand, if it is included in excess of 0.100%, precipitates are formed and the iron loss of the finish annealed steel sheet is deteriorated, so the upper limit is preferably set to 0.100%.

Ｊ群；Ａｓ：０．０００５～０．０２０％
　Ａｓは、粒界に偏析して、熱延焼鈍板の粒径を小さくすることで冷間圧延性の向上に効果がある。このため、０．０００５％以上含有することが好ましい。一方、０．０２０％を超えて含有した場合、粒界破壊を促進して冷間圧延性が却って低下するため、上限は０．０２０％とすることが好ましい。 Group J; As: 0.0005-0.020%
As is effective in improving cold rolling properties by segregating at grain boundaries and reducing the grain size of the hot-rolled annealed sheet. Therefore, it is preferable to contain 0.0005% or more. On the other hand, if it is contained in excess of 0.020%, it promotes grain boundary fracture and the cold rolling properties are rather deteriorated, so the upper limit is preferably set to 0.020%.

　本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の化学組成は、上記の元素以外の残部は、Ｆｅ及び不可避的不純物である。 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.

＜無方向性電磁鋼板用の熱延焼鈍板の鋼組織＞
　次に、本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の鋼組織について説明する。
鋼板の圧延方向断面の平均結晶粒径：４０～２５０μｍ
　熱延焼鈍板の組織が粗大であると、熱延焼鈍板が脆化し、冷間圧延で板破断しやすくなるため、平均結晶粒径を２５０μｍ以下とする。破断抑制の観点から好ましくは１８０μｍ以下であり、より好ましくは１２０μｍ以下である。
　一方、平均結晶粒径が４０μｍ未満では、熱延焼鈍板が硬化して冷間圧延での荷重が増加し、板破断しやすくなるため４０μｍ以上とする必要がある。好ましい平均結晶粒径は、６０μｍ以上である。 <Steel structure of hot-rolled annealed sheet for non-oriented electrical steel sheet>
Next, 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 μm
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 μm or less. From the viewpoint of preventing breakage, the average grain size is preferably 180 μm or less, and more preferably 120 μm or less.
On the other hand, if the average crystal grain size is less than 40 μm, 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 μm or more.The preferred average crystal grain size is 60 μm or more.

鋼板表層のＦｅ－Ａｌ系酸化物の積分強度：２００ｃｐｓ・度以下
　Ｆｅ－Ａｌ系酸化物は、硬質かつ潤滑油との濡れ性が悪いため、鋼板表面に残存していると、冷間圧延時に圧延ロールにダメージを与え、摩擦係数および圧延荷重が増加して圧延が不安定になり、板破断に至ってしまう。そのため、Ｆｅ－Ａｌ系酸化物は酸洗工程で十分に除去する必要あり、指標として、酸洗後の熱延焼鈍板をＸ線回折で測定した鋼板表層のＦｅ－Ａｌ系酸化物の積分強度を２００ｃｐｓ・度以下とする必要がある。 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.

＜無方向性電磁鋼板用の熱延焼鈍板の製造方法＞
　次に、本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の製造方法を説明する。 <Manufacturing method of hot-rolled annealed sheet for non-oriented electrical steel sheet>
Next, a method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to this embodiment will be described.

　本実施形態に係る無方向性電磁鋼板用の熱延焼鈍板の製造方法は、上記の成分組成を有する鋼スラブを加熱し熱間圧延して熱延鋼板とする熱間圧延工程と、上記熱延鋼板を焼鈍して熱延焼鈍板とする熱延板焼鈍工程と、上記熱延焼鈍板にショットブラストを施すショットブラスト工程と、ショットブラストされた上記熱延焼鈍板を酸洗する酸洗工程とを含む。熱間圧延工程では、鋼スラブの加熱温度は１１５０℃以下、仕上げ圧延温度は、９６０℃以下、巻取温度は７００℃以下とする。熱延板焼鈍工程では、焼鈍温度を８００℃以上１１００℃以下とし、ショットブラスト工程では、投射密度１０～４０ｋｇ／ｍ２のショットブラストを熱延焼鈍板に施す。次いで、酸洗工程では、塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０ｓ以上、１２０ｓ以下で、ショットブラストされた鋼板を酸洗する。
　以下に具体的に説明する。 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. In the hot-rolling process, the heating temperature of the steel slab is 1150°C or less, the finish rolling temperature is 960°C or less, and the coiling temperature is 700°C or less. In the hot-rolled sheet annealing process, the annealing temperature is 800°C or more and 1100°C or less, and in the shot blasting process, the hot-rolled annealed sheet is subjected to shot blasting with a projection density of 10 to 40 kg/ m2 . Next, in the pickling step, the shot blasted steel sheet is pickled with a hydrochloric acid concentration of 5% or more, a pickling temperature of 70° C. or more, and a pickling time of 10 seconds or more and 120 seconds or less.
The details are explained below.

［熱間圧延工程］
鋼スラブ
　本実施形態の無方向性電磁鋼板用の熱延焼鈍板の製造に用いる鋼スラブの成分組成は、上記に記載した範囲に調整する。その鋼の溶製方法は、転炉、電気炉、真空脱ガス装置等の公知の精錬プロセスを用いることができ、特に限定しない。また、鋼スラブの製造方法は連続鋳造が好ましい。また、原料として、鉄スクラップや直接還元鉄を使用しても良い。特に鉄スクラップからは、ＣｕやＮｉといった鉄損低減に有用な元素を廉価に取り込むことができるため、使用することが好ましい。 [Hot rolling process]
Steel Slab 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. In addition, continuous casting is preferable as the method of manufacturing the steel slab. In addition, iron scrap or direct reduced iron may be used as the raw material. In particular, 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.

加熱温度：１１５０℃以下
　熱間圧延は、上記の成分を有する鋼スラブを製造した後、直ちに熱間圧延し、もしくは、冷却してから所定の温度に加熱した後、熱間圧延し、所定の板厚の熱延板を得る工程である。スラブの加熱温度が高すぎる場合、ＡｌＮやＭｎＳが再溶解し、熱間圧延以降の工程で微細に析出し、粒成長性や鉄損を劣化させるため、上限を１１５０℃とする。鋼スラブ中のＡｌＮやＭｎＳを粗大化させて、粒成長性や鉄損を改善するためには、加熱温度は１０００℃以上とするのが好ましい。また、熱延荷重の低減による安定製造の観点からは、１０５０℃以上がより好ましい。 Heating temperature: 1150°C or less Hot rolling is a process in which a steel slab having the above-mentioned components is produced, and then immediately hot-rolled, or cooled and heated to a predetermined temperature, and then hot-rolled to obtain a hot-rolled sheet of a predetermined thickness. If the heating temperature of the slab is too high, AlN and MnS are remelted and finely precipitated in the process after hot rolling, deteriorating grain growth and iron loss, so the upper limit is set to 1150°C. In order to coarsen AlN and MnS in the steel slab and improve grain growth and iron loss, the heating temperature is preferably 1000°C or more. In addition, from the viewpoint of stable production by reducing the hot rolling load, 1050°C or more is more preferable.

仕上げ圧延温度：９６０℃以下
　熱間圧延の仕上げ圧延温度が９６０℃を超えると熱延板のスケールが厚くなり、酸洗性が低下するため、仕上げ圧延温度は９６０℃以下とする。好ましい仕上げ圧延温度は９２０℃以下である。一方、仕上げ圧延温度が低すぎると、圧延負荷が増大して圧延荷重が大きくなるため、下限は７５０℃とすることが好ましい。より好ましくは７８０℃以上である。 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. On the other hand, if the finish rolling temperature is too low, the rolling load increases, so the lower limit is preferably 750°C. More preferably, it is 780°C or more.

巻取り温度：７００℃以下
　巻取り温度が７００℃を超えると、スケールが増加し、特にＦｅ－Ａｌ系酸化物が厚くなって酸洗性が低下するため上限は７００℃とする。好ましくは６２０℃以下である。一方、巻取り温度が低すぎると、熱間圧延完了から巻取りまでの間の急冷により温度のバラツキが大きくなるため、下限は４５０℃とすることが好ましい。巻取り中に析出物を粗大化させて鉄損を低減する観点からの好ましい巻取り温度は４８０℃以上である。 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. On the other hand, if the coiling temperature is too low, the temperature varies greatly due to rapid cooling from the end of hot rolling to coiling, so 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.

［熱延板焼鈍工程］
熱延板焼鈍温度：８００～１１００℃
　熱延板焼鈍は、組織を均一化し、フェライト粒径を所定の範囲に制御することで、冷間圧延での耐破断性を向上しつつ、冷間圧延及び仕上げ焼鈍後の磁気特性を向上するために行う。
　熱延板焼鈍温度が１１００℃より高い場合は、組織が粗大化しすぎて靭性が低下し、冷間圧延にて板破断を起こしやすくなるため、１１００℃以下とする必要がある。好ましい熱延板焼鈍温度は１０３０℃以下である。さらに、熱延板焼鈍時のスケールの成長を抑制する観点からは９６０℃以下とすることが好ましい。
　一方、熱延板焼鈍温度が８００℃より低いと、粒径が十分に大きくならず、仕上げ焼鈍後の磁気特性が低下するため、８００℃以上とする必要がある。好ましい熱延板焼鈍温度は、９００℃以上である。焼鈍時間は特に定めないが、均一性を確保する観点からは１０ｓ以上とすることが好ましい。 [Hot-rolled sheet annealing process]
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. Furthermore, from the viewpoint of suppressing the growth of scale during hot-rolled sheet annealing, it is preferably 960° C. or less.
On the other hand, if 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.

［ショットブラスト工程］
ショットブラストの投射密度：１０～４０ｋｇ／ｍ２
　酸洗前に熱延焼鈍板に対してショットブラストを行ない、スケールに亀裂を導入することで、酸洗中のスケールの除去が促進される。特にＦｅ－Ａｌ系スケールは、酸に難溶性であるため、亀裂を導入して露出した地鉄部に酸を浸透させ、地鉄界面の地鉄側から溶解して除去する必要がある。そのために必要なショットブラストの投射密度は、１０ｋｇ／ｍ２以上である。好ましくは１５ｋｇ／ｍ２以上である。
　一方、４０ｋｇ／ｍ２を超えると、スケールへの亀裂導入だけでは無く、地鉄の表層近傍も変形を受けてしまい、冷間圧延での板破断の起点となるため、投射密度は、４０ｋｇ／ｍ２以下とする。好ましい投射密度は、３５ｋｇ/ｍ２以下である。 [Shot blasting process]
Shot blasting density: 10 to 40 kg/ m2
By shot blasting the hot-rolled annealed sheet before pickling and introducing cracks into the scale, the removal of the scale during pickling is promoted. In particular, since Fe-Al-based scale is poorly soluble in acid, it is necessary to introduce cracks to allow the acid to penetrate into the exposed base steel portion and dissolve and remove the scale from the base steel side at the base steel interface. The shot blasting density required for this purpose is 10 kg/m2 or more , preferably 15 kg/m2 or more .
On the other hand, if 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.

　ショットブラスト粒子の粒径が大きいと、同じ投射密度でも単位面積当たりの衝突個数が減少する、即ち、スケールに導入される亀裂の数が減少して、酸洗性が低下するため、ショットブラスト粒子の平均粒径は０．５０ｍｍ以下が好ましい。酸洗性を促進する観点からは０．３０ｍｍ以下がより好ましい。逆に、粒径が小さすぎると、亀裂導入効果が弱まるためショットブラスト粒子の平均粒径は０．１５ｍｍ以上が好ましい。ショットブラスト粒子の平均粒径は、例えば、ＪＩＳ　Ｚ　８８２５：２０１３に記載の粒子径解析－レーザー回折・散乱法で測定することができる。また、ショットブラスト粒子が柔らかい場合、鋼板と衝突した際に、ショットブラスト粒自身が変形してしまい、効率的にスケールに亀裂を導入することができないため、ショットブラスト粒子のビッカース硬さは、４００ＨＶ以上が好ましい。 If the particle size of the shot blast particles is large, the number of collisions per unit area decreases even with the same projection density, i.e., the number of cracks introduced into the scale decreases and the pickling properties deteriorate, so 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. On the other hand, if the particle size is too small, the effect of introducing cracks is weakened, so 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. In addition, if 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.

[ブラシ研削工程(酸洗前)]
　ショットブラストに替えて、ブラシ研削を酸洗前の熱延焼鈍板に対して行うことでも、スケールに亀裂を導入することができ、酸洗中のスケールの除去が促進される。
　鋼板表面をムラ無く研削するため、ブラシ研削にはブラシロールを用いることが好ましい。ブラシの素材や研削条件は適宜選定すれば良いが、鋼板の形状に追従してムラなく研削する観点から、ブラシの毛材は金属より軟質な化学繊維を用いることが好ましい。また、効率的にスケールにクラックを導入する観点からは、ブラシにアルミナ系、炭化ケイ素系やダイヤモンドなどの砥粒が含まれることが好ましい。ブラシ研削時は冷却水を噴射して、研削粉を除去するとともに、ブラシの過加熱を防止することが好ましい。 [Brush grinding process (before pickling)]
Instead of shot blasting, 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.
In order to grind the steel plate surface evenly, it is preferable to use 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. Also, from the viewpoint of efficiently introducing cracks into the scale, it is preferable that 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.

［酸洗工程］
酸洗：塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０s以上、１２０s以下
　酸洗工程は、上記のショットブラストやブラシ研削を施した熱延焼鈍板のスケールを除去する工程であり、鉄酸化物のみならずＦｅ－Ａｌ系スケールを十分に除去することで冷間圧延での板破断を抑制することができる。このため、塩酸濃度は、５％以上とする。好ましくは８％以上である。上限は特に定めないが、過酸洗となる場合があるため塩酸濃度は、２０％以下とすることが好ましい。酸洗を促進するため、酸洗液の温度（酸洗温度）は、７０℃以上とする。好ましくは７５℃以上である。酸洗温度が高すぎると、過酸洗が起こりやすくなり、また酸洗液の蒸発量が多くなって製造コストが増大するため、９６℃以下とすることが好ましい。十分に酸洗するため、酸洗時間は１０ｓ以上とする。好ましくは１５ｓ以上である。１２０ｓを超えると発生する水素が増加し水素脆化により、冷間圧延時に破断し易くなるため酸洗時間の上限を１２０ｓとする。前述したように、Ａｌ含有量や熱延仕上げ温度、巻取り温度により酸洗性が変化するため、酸洗液には、必要に応じて酸洗促進剤や酸洗抑制剤を適宜添加して調整しても良い。 [Pickling process]
Pickling: 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. For this reason, 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. In order to promote pickling, 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. In order to perform sufficient pickling, 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.

　また、本発明では、Ｆｅ－Ａｌ系スケールを完全に除去する観点から、上記に説明した脱スケール工程に、以下の工程を加えて実施することが好ましい。
熱延板焼鈍工程前の伸長率０．１～１０．０％の圧延及び／又は引張り曲げ加工工程
　熱延板時点でのスケール、特に、Ｆｅ－Ａｌ系スケールに亀裂を導入し、地鉄を露出させることで、熱延板焼鈍時の酸化挙動が変化する。即ち、地鉄が露出した部分では相対的に酸に易溶性な鉄酸化物が生成するため、酸洗時にこの部分の鉄酸化物が溶解し、続いて地鉄の溶解の起点となり、地鉄の溶解により、Ｆｅ－Ａｌ系スケールを除去することができる。
　このため、熱延板を、軽圧延及び／又は引張り曲げ加工により、伸長することが好ましい。スキンパス圧延機やテンションレベラーで伸長率０．１％以上の加工を、熱延焼鈍前の熱延板に施すことが好ましい。好ましくは伸長率０．３％以上である。１０．０％を超えると、上記の効果が飽和するだけでは無く、歪み誘起粒成長により熱延焼鈍板の平均結晶粒径が大きくなりすぎるため、伸長率を１０．０％以下とすることが好ましい。より好ましくは６．０％以下である。なお、熱延板焼鈍前に伸長率０．１～１０．０％の圧延及び／又は引張り曲げ加工を行う場合、酸洗後の熱延焼鈍板の積分強度が１５０ｃｐｓ・度以下となるよう上記加工を施すことが好ましい。 In the present invention, from the viewpoint of completely removing Fe-Al-based scale, it is preferable to add the following steps to the descaling step described above.
Rolling and/or tensile bending process with an elongation rate of 0.1 to 10.0% before the hot-rolled sheet annealing process By introducing cracks into the scale at the time of hot-rolling, particularly the Fe-Al-based scale, and exposing the base steel, the oxidation behavior during the annealing of the hot-rolled sheet changes. That is, 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.
For this reason, it is preferable to elongate the hot-rolled sheet by light rolling and/or tensile bending. It is preferable to subject the hot-rolled sheet before hot-rolling annealing to processing at an elongation rate of 0.1% or more using a skin pass rolling machine or a tension leveler. The elongation rate is preferably 0.3% or more. If it exceeds 10.0%, not only the above effects are saturated, but also the average crystal grain size of the hot-rolled annealed sheet becomes too large due to strain-induced grain growth, so it is preferable to set the elongation rate to 10.0% or less. More preferably, it is 6.0% or less. In addition, when 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.

［ブラシ研削工程（酸洗後）］
　酸洗後の鋼板の表裏面をブラシ研削して、酸洗時に一部残存したＦｅ－Ａｌ系スケールを機械的に除去することが好ましい。ブラシ研削のみで、Ｆｅ系スケールおよびＦｅ－Ａｌ系スケール等のスケールを全て除去するためには、装置を大型化する必要があり、導入コストや維持コストが大きくなってしまう。
　そのため、酸洗にて大部分のスケールを除去し、ブラシ研削では一部残存したＦｅ－Ａｌ系スケールのみを除去することで装置コストを低減することが出来る。
　鋼板表面をムラ無く研削するため、ブラシ研削にはブラシロールを用いることが好ましい。ブラシの素材や研削条件は適宜選定すれば良いが、鋼板の板形状に追従してムラなく研削する観点から、ブラシの毛材は金属より軟質な化学繊維を用いることが好ましく、効率的にＦｅ－Ａｌ系スケールを除去する観点からはブラシにアルミナ系、炭化ケイ素系やダイヤモンドなどの砥粒が含まれることが好ましい。ブラシ研削時は冷却水を噴射して、研削粉を除去するとともに、ブラシの過加熱を防止することが好ましい。
　なお、酸洗後に鋼板の表裏面に対してブラシ研削を行う場合、ブラシ研削後の熱延焼鈍板の積分強度が６０ｃｐｓ・度以下となるようブラシ研削するのが好ましい。 [Brush grinding process (after pickling)]
It is preferable to mechanically remove the Fe-Al-based scale that remains partially during pickling by brush grinding the front and back surfaces of the steel sheet after pickling. In order to remove all scale, such as Fe-based scale and Fe-Al-based scale, by brush grinding alone, it is necessary to enlarge the equipment, which increases the introduction cost and maintenance cost.
Therefore, most of the scale is removed by pickling, and only the remaining Fe-Al-based scale is removed by brush grinding, thereby making it possible to reduce equipment costs.
In order to grind the steel plate surface evenly, it is preferable to use a brush roll for brush grinding. The brush material and grinding conditions can be selected appropriately, but from the viewpoint of grinding evenly by following the plate shape of the steel plate, it is preferable to use chemical fibers that are softer than metal for the brush bristles, and from the viewpoint of efficiently removing Fe-Al-based scale, it is preferable that the brush contains abrasive grains such as alumina, silicon carbide, diamond, etc. During brush grinding, it is preferable to spray cooling water to remove grinding powder and prevent the brush from overheating.
When brush grinding is performed on the front and back surfaces of the steel sheet after pickling, the brush grinding is preferably performed so that the integrated strength of the hot-rolled annealed sheet after brush grinding is 60 cps·degrees or less.

　次に、上記した本発明の製造方法で得た熱延焼鈍板から無方向性電鋼板を製造する方法について説明する。
［冷間圧延工程］
　上記の酸洗した熱延焼鈍板は、１回もしくは中間焼鈍を含む２回以上の冷間圧延をして最終板厚の冷延板とすることが好ましい。生産効率の観点からは、タンデム圧延機を用いることが好ましいが、リバース圧延機を用いてもよく、常法にて圧延すればよい。 Next, a method for producing a non-oriented electrical steel sheet from the hot-rolled and annealed steel sheet obtained by the above-mentioned production method of the present invention will be described.
[Cold rolling process]
The pickled hot-rolled annealed sheet is preferably cold-rolled once or twice or more including intermediate annealing to obtain a cold-rolled sheet having a final thickness. From the viewpoint of production efficiency, it is preferable to use a tandem rolling mill, but a reverse rolling mill may also be used, and rolling may be performed in a conventional manner.

［仕上げ焼鈍工程］
仕上げ焼鈍温度：７００～１１００℃
　上記冷間圧延後の仕上げ焼鈍工程は、上記の冷延板を再結晶および粒成長させて良好な磁気特性を得る工程である。上記仕上げ焼鈍における均熱温度は７００℃以上とすることが好ましい。さらに好ましくは８００℃以上である。一方、仕上げ焼鈍における均熱温度が高すぎると、焼鈍中に窒化が起こったり、結晶粒が粗大になりすぎて鉄損が劣化したりするため、１１００℃以下とすることが好ましい。より好ましくは１０５０℃以下である。 [Finish annealing process]
Finish annealing temperature: 700 to 1100°C
The finish annealing process after the cold rolling is a process for recrystallizing and growing the grains of the cold-rolled sheet to obtain good magnetic properties. The soaking temperature in the finish annealing is preferably 700°C or higher, more preferably 800°C or higher. On the other hand, if the soaking temperature in the finish annealing is too high, nitridation occurs during annealing or the crystal grains become too coarse, resulting in deterioration of iron loss, so the soaking temperature is preferably 1100°C or lower, more preferably 1050°C or lower.

　本発明の実施形態を実施例によりさらに説明する。なお、本発明は、以下の実施例で示す製造条件及び製品性能に限定されるものではない。実施形態が本発明の範囲内では、所望の性能を達成し得るものである。 The embodiments of the present invention will be further explained using examples. Note that the present invention is not limited to the manufacturing conditions and product performance shown in the following examples. As long as the embodiments are within the scope of the present invention, they can achieve the desired performance.

（実施例１）
　表１に示す種々の成分を含有し、残部がＦｅおよび不可避不純物からなる成分組成の鋼を常法の精錬プロセスで溶製した後、連続鋳造法でスラブとした。次いで、上記スラブを表２－１および表２－２に示す条件にて、ガス炉で加熱した後、粗圧延と仕上圧延からなる熱間圧延をして板厚１．８ｍｍ、板幅１２００ｍｍの熱延板とした。その後、上記熱延板に熱延板焼鈍を施した後、酸洗して、熱延焼鈍板を得た。この際、一部の熱延板には、スキンパス圧延機を用いた熱延焼鈍前の軽圧延、または、酸洗後のブラシ研削の一方もしくは両方を適用した。ブラシ研削は、ナイロンを毛材とし、炭化ケイ素系を砥粒とした炭化ケイ素系のブラシロールを用いた。熱延焼鈍前の軽圧延の伸長率（％）、酸洗後のブラシロールでの研削時のトルク（Ｎ・ｍ）と回転数（ｒｐｍ）を表２－１および表２－２に併記した。 Example 1
Steel containing various components shown in Table 1, with the balance being Fe and inevitable impurities, was melted by a conventional refining process, and then made into a slab by a continuous casting method. Next, 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. At this time, 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. For brush grinding, a silicon carbide-based brush roll with nylon bristles and silicon carbide-based abrasive grains was used. The elongation rate (%) of the light rolling before the hot rolling annealing, and the torque (N·m) and the rotation speed (rpm) during grinding with a brush roll after pickling are also shown in Tables 2-1 and 2-2.

鋼板組織
　得られた熱延焼鈍板から圧延方向の板厚断面を観察できるようにサンプルを切り出し、埋込み、研磨し、エッチングして組織を現出させた後、鋼板組織を観察した。撮影した組織写真から画像解析にて平均結晶粒径を算出した。ここで平均粒径は、円相当径とした。 Steel sheet structure Samples were cut out from the obtained hot-rolled annealed sheets so that the sheet thickness cross section in the rolling direction could be observed, and then the samples were embedded, polished, and etched to reveal the structure, and the steel sheet structure was observed. The average crystal grain size was calculated from the photographed structure by image analysis. Here, the average grain size was defined as the circle equivalent diameter.

酸化物の積分強度
　得られた熱延焼鈍板から板厚×２５×３０ｍｍのサンプルを切り出し、鋼板表面に対して、Ｘ線回折にてスケールの残存量を測定した。Ｘ線の入射角を１度として測定し、２θ＝約３６．４度に現れるＦｅ－Ａｌ系酸化物（ハーシナイト、ＦｅＡｌ２Ｏ４）の（３１１）面ピークの積分強度を算出した。 A sample measuring 25 mm × sheet thickness × 30 mm was cut from the hot-rolled annealed sheet, and the amount of remaining scale on the steel sheet surface was measured by X-ray diffraction. The X-ray incident angle was set to 1 degree, and the integrated intensity of the (311) plane peak of Fe-Al oxide (hercynite, FeAl 2 O 4 ) appearing at 2θ = approximately 36.4 degrees was calculated.

冷間圧延での耐破断性
　得られた熱延焼鈍板を、タンデム冷間圧延機にて、仕上げ厚を０．２５ｍｍとし、最終スタンド出側での通板速度を溶接部近傍の非定常部を除いて６００ｍ／ｍｉｎとして計８０００ｍ圧延し、１回以上破断したものを×、破断しなかったものを〇、破断しない、かつ、初段スタンドの荷重変動が小さいものを◎とした。
　ここで、上記荷重変動が小さいとは、タンデム圧延機で６００ｍ／ｍｉｎで圧延しているときの＃１ｓｔｄの圧延荷重の平均値をＬａｖｅ、上記圧延過重の最大値と最小値の差をΔＬとしたとき、上記圧延荷重の平均値Ｌａｖｅと最大値と最小値の差ΔＬとの比ΔＬ／Ｌａｖｅ×１００が１０％以下であることをいう。 The obtained hot-rolled annealed sheet was rolled in a tandem cold rolling mill to a finishing thickness of 0.25 mm, and the sheet passing speed at the delivery side of the final stand was 600 m/min excluding the unsteady portion near the welded portion, for a total of 8,000 m. Sheets that broke once or more were marked with ×, sheets that did not break were marked with ◯, and sheets that did not break and had small load fluctuations in the first stand were marked with ◎.
Here, the load fluctuation is small means that, when the average value of the rolling load of #1std when rolling at 600 m/min with a tandem rolling mill is Lave and the difference between the maximum and minimum values of the rolling excess load is ΔL, the ratio ΔL/L ave × 100 of the average rolling load Lave to the difference ΔL between the maximum and minimum values is 10% or less.

仕上げ焼鈍板の鉄損Ｗ１０／４００
　上記の冷間圧延板を表２－１および表２－２に示した条件で仕上げ焼鈍を行った。均熱時間は１０ｓとした。得られた仕上げ焼鈍板から幅３０ｍｍ×長さ２８０ｍｍの試験片をＬ方向（圧延方向）およびＣ方向（圧延方向と直角方向）から採取し、ＪＩＳ　Ｃ２５５０－１に準拠して鉄損Ｗ１０／４００を測定した。 Iron loss of finish annealed sheet W 10/400
The above cold-rolled sheet was subjected to finish annealing under the conditions shown in Tables 2-1 and 2-2. The soaking time was 10 s. Test pieces with a width of 30 mm and a length of 280 mm were taken from the obtained finish-annealed sheet in the L direction (rolling direction) and the C direction (direction perpendicular to the rolling direction), and the iron loss W 10/400 was measured in accordance with JIS C2550-1.

　上記測定結果を表２－１および表２－２に併記した。この結果から、鋼板の製造条件を本発明の範囲に制御することにより、熱延板焼鈍後の冷間圧延での破断防止と、冷延板焼鈍後の優れた磁気特性とが両立した無方向性電磁鋼板用熱延焼鈍板が得られることがわかる。 The above measurement results are shown in Tables 2-1 and 2-2. These results show that by controlling the manufacturing conditions of the steel sheet within the range of the present invention, it is possible to obtain a hot-rolled annealed sheet for non-oriented electrical steel sheet that is both able to prevent breakage during cold rolling after hot-rolled sheet annealing and has excellent magnetic properties after cold-rolled sheet annealing.

Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001

Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002

Figure JPOXMLDOC01-appb-T000003
Figure JPOXMLDOC01-appb-T000003

（実施例２）
　実施例１で製造した、表１に示す種々の成分を含有し、残部がＦｅおよび不可避不純物からなる成分組成を有するスラブを、表３－１および表３－２に示す条件にて、ガス炉で加熱した後、粗圧延と仕上圧延からなる熱間圧延をして板厚１．８ｍｍ、板幅１２００ｍｍの熱延板とした。その後、上記熱延板に熱延板焼鈍を施した後、ブラシ研削を施し、酸洗して、熱延焼鈍板を得た。この際、一部の熱延板には、スキンパス圧延機を用いた熱延焼鈍前の軽圧延、または、酸洗後のブラシ研削の、一方もしくは両方を適用した。ブラシ研削は、ナイロンを毛材とし、炭化ケイ素系を砥粒とした炭化ケイ素系のブラシロールを用いた。熱延焼鈍前の軽圧延の伸長率（％）、酸洗前のブラシロールでの研削時のトルク（Ｎ・ｍ）と回転数（ｒｐｍ）、酸洗後のブラシロールでの研削時のトルク（Ｎ・ｍ）と回転数（ｒｐｍ）を表３－１および表３－２に併記した。 Example 2
The slab produced in Example 1, containing various components shown in Table 1, with the balance being Fe and inevitable impurities, was heated in a gas furnace under the conditions shown in Tables 3-1 and 3-2, 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, brush grinding, and pickling to obtain a hot-rolled annealed sheet. At this time, 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. For brush grinding, a silicon carbide brush roll with nylon bristles and silicon carbide abrasive grains was used. The elongation rate (%) of light rolling before hot rolling annealing, the torque (N m) and rotation speed (rpm) during grinding with a brush roll before pickling, and the torque (N m) and rotation speed (rpm) during grinding with a brush roll after pickling are also shown in Tables 3-1 and 3-2.

鋼板組織
　得られた熱延焼鈍板から圧延方向の板厚断面を観察できるようにサンプルを切り出し、埋込み、研磨し、エッチングして組織を現出させた後、鋼板組織を観察した。撮影した組織写真から画像解析にて平均結晶粒径を算出した。ここで平均粒径は、円相当径とした。 Steel sheet structure Samples were cut out from the obtained hot-rolled annealed sheets so that the sheet thickness cross section in the rolling direction could be observed, and then the samples were embedded, polished, and etched to reveal the structure, and the steel sheet structure was observed. The average crystal grain size was calculated from the photographed structure by image analysis. Here, the average grain size was defined as the circle equivalent diameter.

酸化物の積分強度
　得られた熱延焼鈍板から板厚×２５×３０ｍｍのサンプルを切り出し、鋼板表面に対して、Ｘ線回折にてスケールの残存量を測定した。Ｘ線の入射角を１度として測定し、２θ＝約３６．４度に現れるＦｅ－Ａｌ系酸化物（ハーシナイト、ＦｅＡｌ２Ｏ４）の（３１１）面ピークの積分強度を算出した。 A sample measuring 25 mm × sheet thickness × 30 mm was cut from the hot-rolled annealed sheet, and the amount of remaining scale on the steel sheet surface was measured by X-ray diffraction. The X-ray incident angle was set to 1 degree, and the integrated intensity of the (311) plane peak of Fe-Al oxide (hercynite, FeAl 2 O 4 ) appearing at 2θ = approximately 36.4 degrees was calculated.

冷間圧延での耐破断性
　得られた熱延焼鈍板を、タンデム冷間圧延機にて、仕上げ厚を０．２５ｍｍとし、最終スタンド出側での通板速度を溶接部近傍の非定常部を除いて６００ｍ／ｍｉｎとして計８０００ｍ圧延し、１回以上破断したものを×、破断しなかったものを〇、破断しない、かつ、初段スタンドの荷重変動が小さいものを◎とした。
　ここで、上記荷重変動が小さいとは、タンデム圧延機で６００ｍ／ｍｉｎで圧延しているときの＃１ｓｔｄの圧延荷重の平均値をＬａｖｅ、上記圧延過重の最大値と最小値の差をΔＬとしたとき、上記圧延荷重の平均値Ｌａｖｅと最大値と最小値の差ΔＬとの比ΔＬ／Ｌａｖｅ×１００が１０％以下であることをいう。 The obtained hot-rolled annealed sheet was rolled in a tandem cold rolling mill to a finishing thickness of 0.25 mm, and the sheet passing speed at the delivery side of the final stand was 600 m/min excluding the unsteady portion near the welded portion, for a total of 8,000 m. Sheets that broke once or more were marked with ×, sheets that did not break were marked with ◯, and sheets that did not break and had small load fluctuations in the first stand were marked with ◎.
Here, the load fluctuation is small means that, when the average value of the rolling load of #1std when rolling at 600 m/min with a tandem rolling mill is Lave and the difference between the maximum and minimum values of the rolling excess load is ΔL, the ratio ΔL/L ave × 100 of the average rolling load Lave to the difference ΔL between the maximum and minimum values is 10% or less.

仕上げ焼鈍板の鉄損Ｗ１０／４００
　上記の冷間圧延板を表３－１および表３－２に示した条件で仕上げ焼鈍を行った。均熱時間は１０ｓとした。得られた仕上げ焼鈍板から幅３０ｍｍ×長さ２８０ｍｍの試験片をＬ方向（圧延方向）およびＣ方向（圧延方向と直角方向）から採取し、ＪＩＳ　Ｃ２５５０－１に準拠して鉄損Ｗ１０／４００を測定した。 Iron loss of finish annealed sheet W 10/400
The above cold-rolled sheet was subjected to finish annealing under the conditions shown in Tables 3-1 and 3-2. The soaking time was 10 s. Test pieces with a width of 30 mm and a length of 280 mm were taken from the obtained finish-annealed sheet in the L direction (rolling direction) and the C direction (direction perpendicular to the rolling direction), and the iron loss W 10/400 was measured in accordance with JIS C2550-1.

　上記測定結果を表３－１および表３－２に併記した。この結果から、鋼板の製造条件を本発明の範囲に制御することにより、熱延板焼鈍後の冷間圧延での破断防止と冷延板焼鈍後の優れた磁気特性とが両立した無方向性電磁鋼板用熱延焼鈍板が得られることがわかる。 The above measurement results are shown in Tables 3-1 and 3-2. These results show that by controlling the manufacturing conditions of the steel sheet within the range of the present invention, it is possible to obtain a hot-rolled annealed sheet for non-oriented electrical steel sheet that is both able to prevent breakage during cold rolling after hot-rolled sheet annealing and has excellent magnetic properties after cold-rolled sheet annealing.

Figure JPOXMLDOC01-appb-T000004
Figure JPOXMLDOC01-appb-T000004

Figure JPOXMLDOC01-appb-T000005

 
Figure JPOXMLDOC01-appb-T000005
 

Claims (15)

質量％で、
Ｃ：０．００５０％以下、
Ｓｉ：２．０～５．０％、
Ｍｎ：０．２～２．０％、
Ｐ：０．０３０％以下、
Ｓ：０．００５０％以下、
Ａｌ：０．２５～２．５０％、
Ｎ：０．００５０％以下、
Ｏ：０．００５０％以下、
ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有し、
鋼板の圧延方向断面の平均結晶粒径が４０～２５０μｍであり、
Ｘ線回折にて測定した鋼板表層のＦｅ－Ａｌ系酸化物の積分強度が２００ｃｐｓ・度以下である無方向性電磁鋼板用の熱延焼鈍板。 In mass percent,
C: 0.0050% or less,
Si: 2.0 to 5.0%,
Mn: 0.2 to 2.0%,
P: 0.030% or less,
S: 0.0050% or less,
Al: 0.25-2.50%,
N: 0.0050% or less,
O: 0.0050% or less,
Sn and Sb: one or more of 0.01 to 0.20% in total, with the balance being Fe and unavoidable impurities;
The average grain size in the rolling direction cross section of the steel sheet is 40 to 250 μm,
A hot-rolled annealed sheet for use as a non-oriented electrical steel sheet, in which the integrated intensity of Fe-Al oxides in the surface layer of the steel sheet as measured by X-ray diffraction is 200 cps·degree or less. 上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有することを特徴とする請求項１に記載の無方向性電磁鋼板用の熱延焼鈍板。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％ The hot-rolled annealed sheet for non-oriented electrical steel sheet according to claim 1, characterized in that in addition to the above-mentioned composition, it further contains, in mass%, one or more 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%
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% 上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする請求項１または２に記載の無方向性電磁鋼板用の熱延焼鈍板。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％ The hot-rolled annealed sheet for non-oriented electrical steel sheet according to claim 1 or 2, characterized in that in addition to the above-mentioned composition, it further contains, in mass%, one or more components selected from the following groups E to J.
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total, 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020% 質量％で、
Ｃ：０．００５０％以下、
Ｓｉ：２．０～５．０％、
Ｍｎ：０．２～２．０％、
Ｐ：０．０３０％以下、
Ｓ：０．００５０％以下、
Ａｌ：０．２５～２．５０％、
Ｎ：０．００５０％以下、
Ｏ：０．００５０％以下、
ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有する鋼スラブを加熱し、熱間圧延して熱延鋼板とする熱間圧延工程と、
上記熱延鋼板を焼鈍して熱延焼鈍板とする熱延板焼鈍工程と、
上記熱延焼鈍板にショットブラストを施すショットブラスト工程と、
上記ショットブラストされた熱延焼鈍板を酸洗する酸洗工程とを含み、
上記熱間圧延工程では、上記鋼スラブの加熱温度を１１５０℃以下、仕上げ圧延温度を９６０℃以下、巻取温度を７００℃以下とし、
上記熱延板焼鈍工程では、焼鈍温度を８００℃以上１１００℃以下とし、
上記ショットブラスト工程では、投射密度１０～４０ｋｇ／ｍ２のショットブラストを上記熱延焼鈍板に施し、
上記酸洗工程では、塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０ｓ以上、１２０ｓ以下で、ショットブラストされた鋼板を酸洗する無方向性電磁鋼板用の熱延焼鈍板の製造方法。 In mass percent,
C: 0.0050% or less,
Si: 2.0 to 5.0%,
Mn: 0.2-2.0%,
P: 0.030% or less,
S: 0.0050% or less,
Al: 0.25-2.50%,
N: 0.0050% or less,
O: 0.0050% or less,
A hot rolling process in which a steel slab having a composition containing at least one of Sn and Sb in total at 0.01 to 0.20%, with the balance being Fe and unavoidable impurities, 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 step of subjecting the hot-rolled annealed sheet to shot blasting;
and a pickling step of pickling the shot blasted hot rolled annealed sheet,
In the hot rolling process, the heating temperature of the steel slab is 1150° C. or less, the finish rolling temperature is 960° C. or less, and the coiling temperature is 700° C. or less,
In the hot-rolled sheet annealing process, the annealing temperature is set to 800° C. or more and 1100° C. or less,
In the shot blasting process, the hot-rolled annealed sheet is subjected to shot blasting at a shot density of 10 to 40 kg/ m2 ,
In the pickling step, the shot-blasted steel sheet is pickled with a hydrochloric acid concentration of 5% or more, a pickling temperature of 70° C. or more, and a pickling time of 10 s or more and 120 s or less. 上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有することを特徴とする請求項４に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％ The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to claim 4, characterized in that the steel slab further contains, in mass%, one or more components selected from the following groups A to D in addition to the above-mentioned composition.
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% 上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする請求項４または５に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％ The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to claim 4 or 5, characterized in that the steel slab further contains, in addition to the above-mentioned composition, one or more components selected from the following groups E to J, in mass %:
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total, 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020% 上記熱延鋼板を焼鈍する前に、上記熱延鋼板に伸長率が０．１～１０．０％の圧延及び／又は引張り曲げ加工を施すことを特徴とする請求項４から６のいずれか一項に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。 A method for manufacturing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to any one of claims 4 to 6, characterized in that the hot-rolled steel sheet is subjected to rolling and/or tensile bending with an elongation rate of 0.1 to 10.0% before annealing the hot-rolled steel sheet. 上記酸洗工程後に、酸洗された鋼板の表裏面に対してブラシ研削することを特徴とする請求項４から７のいずれか一項に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。 A method for manufacturing a hot-rolled annealed sheet for non-oriented electrical steel sheet according to any one of claims 4 to 7, characterized in that after the pickling process, the front and back surfaces of the pickled steel sheet are brush-ground. 上記請求項４から８のいずれか一項に記載の製造方法で得た熱延焼鈍板を、１回の冷間圧延または中間焼鈍を含む２回以上の冷間圧延をして最終板厚の冷延板とし、上記冷延板を、均熱温度７００～１１００℃で焼鈍して冷延焼鈍板とする無方向性電磁鋼板の製造方法。 A method for producing a non-oriented electrical steel sheet, in which a hot-rolled annealed sheet obtained by the method according to any one of claims 4 to 8 is subjected to one cold rolling or two or more cold rolling steps including intermediate annealing to produce a cold-rolled sheet of final thickness, and the cold-rolled sheet is annealed at a soaking temperature of 700 to 1100°C to produce a cold-rolled annealed sheet. 質量％で、
Ｃ：０．００５０％以下、
Ｓｉ：２．０～５．０％、
Ｍｎ：０．２～２．０％、
Ｐ：０．０３０％以下、
Ｓ：０．００５０％以下、
Ａｌ：０．２５～２．５０％、
Ｎ：０．００５０％以下、
Ｏ：０．００５０％以下、
ＳｎおよびＳｂ：一種以上を合計で０．０１～０．２０％を含有し、残部がＦｅ及び不可避的不純物からなる成分組成を有する鋼スラブを加熱し、熱間圧延して熱延鋼板とする熱間圧延工程と、
上記熱延鋼板を焼鈍して熱延焼鈍板とする熱延板焼鈍工程と、
上記熱延焼鈍板にブラシ研削を施すブラシ研削工程と、
上記ブラシ研削された熱延焼鈍板を酸洗する酸洗工程とを含み、
上記熱間圧延工程では、上記鋼スラブの加熱温度を１１５０℃以下、仕上げ圧延温度を９６０℃以下、巻取温度を７００℃以下とし、
上記熱延板焼鈍工程では、焼鈍温度を８００℃以上１１００℃以下とし、
上記酸洗工程では、塩酸濃度５％以上、酸洗温度７０℃以上、酸洗時間１０ｓ以上、１２０ｓ以下で、ブラシ研削された鋼板を酸洗する無方向性電磁鋼板用の熱延焼鈍板の製造方法。 In mass percent,
C: 0.0050% or less,
Si: 2.0 to 5.0%,
Mn: 0.2-2.0%,
P: 0.030% or less,
S: 0.0050% or less,
Al: 0.25-2.50%,
N: 0.0050% or less,
O: 0.0050% or less,
A hot rolling process in which a steel slab having a composition containing at least one of Sn and Sb in total at 0.01 to 0.20%, with the balance being Fe and unavoidable impurities, 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 brush grinding step of brush grinding the hot-rolled annealed sheet;
and a pickling step of pickling the brush-ground hot-rolled annealed sheet,
In the hot rolling process, the heating temperature of the steel slab is 1150° C. or less, the finish rolling temperature is 960° C. or less, and the coiling temperature is 700° C. or less,
In the hot-rolled sheet annealing process, the annealing temperature is set to 800° C. or more and 1100° C. or less,
In the pickling step, the brush-ground steel sheet is pickled with a hydrochloric acid concentration of 5% or more, a pickling temperature of 70° C. or more, and a pickling time of 10 s or more and 120 s or less. 上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ａ～Ｄ群から選ばれる一群以上の成分を含有することを特徴とする請求項１０に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。
・Ａ群；Ｃａ、ＭｇおよびＲＥＭから選ばれる一種以上を合計で０．００１０～０．００８０％
・Ｂ群；Ｃｒ、Ｍｏ、ＣｕおよびＮｉから選ばれる一種以上を合計で０．０１～０．６０％
・Ｃ群；Ｔｉ、ＮｂおよびＶから選ばれる一種以上を合計で０．０００５～０．００３０％
・Ｄ群；Ｂ：０．０００１～０．００２０％ The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to claim 10, characterized in that the steel slab further contains, in mass%, one or more components selected from the following groups A to D in addition to the above-mentioned composition.
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% 上記鋼スラブは、上記成分組成に加えてさらに、質量％で、下記Ｅ～Ｊ群から選ばれる一群以上の成分を含有することを特徴とする請求項1０または１１に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。
・Ｅ群；Ｚｎ：０．００１～０．０１０％
・Ｆ群；Ｚｒ、Ｔａ、ＷおよびＳｅから選ばれる一種以上を合計で０．００１～０．０１０％
・Ｇ群；ＧａおよびＧｅから選ばれる１種以上を合計で０．０００１～０．０２００％
・Ｈ群；ＰｂおよびＢｉから選ばれる1種以上を合計で０．００００５～０．００２０％
・Ｉ群；Ｃｏ：０．００１～０．１００％
・Ｊ群；Ａｓ：０．０００５～０．０２０％ The method for producing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to claim 10 or 11, characterized in that the steel slab further contains, in addition to the above-mentioned chemical composition, one or more components selected from the following groups E to J, in mass %:
・Group E; Zn: 0.001-0.010%
Group F: 0.001 to 0.010% in total of one or more elements selected from Zr, Ta, W, and Se
Group G: one or more elements selected from Ga and Ge, in total 0.0001 to 0.0200%
H group: Pb and/or Bi, total content of 0.00005 to 0.0020%
・Group I; Co: 0.001-0.100%
・G group; As: 0.0005-0.020% 上記熱延鋼板を焼鈍する前に、上記熱延鋼板に伸長率が０．１～１０．０％の圧延及び／又は引張り曲げ加工を施すことを特徴とする請求項１０から１２のいずれか一項に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。 A method for manufacturing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to any one of claims 10 to 12, characterized in that the hot-rolled steel sheet is subjected to rolling and/or tensile bending with an elongation rate of 0.1 to 10.0% before annealing the hot-rolled steel sheet. 上記酸洗工程後に、酸洗された鋼板の表裏面に対してブラシ研削することを特徴とする請求項１０から１３のいずれか一項に記載の無方向性電磁鋼板用の熱延焼鈍板の製造方法。 A method for manufacturing a hot-rolled annealed sheet for a non-oriented electrical steel sheet according to any one of claims 10 to 13, characterized in that after the pickling process, the front and back surfaces of the pickled steel sheet are brush-ground. 上記請求項１０から１４のいずれか一項に記載の製造方法で得た熱延焼鈍板を、1回の冷間圧延または中間焼鈍を含む２回以上の冷間圧延をして最終板厚の冷延板とし、上記冷延板を、均熱温度を７００～１１００℃で焼鈍して冷延焼鈍板とする無方向性電磁鋼板の製造方法。

  A method for producing a non-oriented electrical steel sheet, comprising the steps of: subjecting a hot-rolled annealed sheet obtained by the production method according to any one of claims 10 to 14 to one cold rolling or two or more cold rolling steps including intermediate annealing to obtain a cold-rolled sheet having a final thickness; and annealing the cold-rolled sheet at a soaking temperature of 700 to 1100°C to obtain a cold-rolled annealed sheet.
PCT/JP2024/019129 2023-08-30 2024-05-24 Hot-rolled annealed sheet for non-oriented electromagnetic steel sheet, method for manufacturing same, and method for manufacturing non-oriented electromagnetic steel sheet Pending WO2025047016A1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2024552680A JPWO2025047016A1 (en) 2023-08-30 2024-05-24

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2023139498 2023-08-30
JP2023-139498 2023-08-30

Publications (1)

Publication Number Publication Date
WO2025047016A1 true WO2025047016A1 (en) 2025-03-06

Family

ID=94818669

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2024/019129 Pending WO2025047016A1 (en) 2023-08-30 2024-05-24 Hot-rolled annealed sheet for non-oriented electromagnetic steel sheet, method for manufacturing same, and method for manufacturing non-oriented electromagnetic steel sheet

Country Status (2)

Country Link
JP (1) JPWO2025047016A1 (en)
WO (1) WO2025047016A1 (en)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000054025A (en) * 1998-07-30 2000-02-22 Kawasaki Steel Corp Manufacturing method of electrical steel sheet
JP2006161094A (en) * 2004-12-06 2006-06-22 Nippon Steel Corp Manufacturing method of high grade non-oriented electrical steel sheet
JP2021038458A (en) * 2019-08-30 2021-03-11 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for producing the same
KR20230096879A (en) * 2021-12-22 2023-06-30 주식회사 포스코 Non-oriented electrical steel sheet and motor core comprising the same
WO2023149249A1 (en) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for manufacturing same
WO2023149269A1 (en) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for manufacturing same

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000054025A (en) * 1998-07-30 2000-02-22 Kawasaki Steel Corp Manufacturing method of electrical steel sheet
JP2006161094A (en) * 2004-12-06 2006-06-22 Nippon Steel Corp Manufacturing method of high grade non-oriented electrical steel sheet
JP2021038458A (en) * 2019-08-30 2021-03-11 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for producing the same
KR20230096879A (en) * 2021-12-22 2023-06-30 주식회사 포스코 Non-oriented electrical steel sheet and motor core comprising the same
WO2023149249A1 (en) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for manufacturing same
WO2023149269A1 (en) * 2022-02-02 2023-08-10 Ｊｆｅスチール株式会社 Non-oriented electromagnetic steel sheet and method for manufacturing same

Also Published As

Publication number Publication date
TW202511504A (en) 2025-03-16
JPWO2025047016A1 (en) 2025-03-06

Similar Documents

Publication Publication Date Title
JP6855895B2 (en) Non-oriented electrical steel sheet and its manufacturing method
EP2799578B1 (en) High-strength hot-rolled steel sheet and manufacturing method therefor
KR100651302B1 (en) High carbon steel wire rod superior in wire-drawability and method for producing the same
EP3159423B1 (en) Cold-rolled ferritic stainless steel sheet
EP2796584B1 (en) High-strength steel sheet and process for producing same
WO2008156195A1 (en) Ferritic stainless steel sheet having excellent corrosion resistance against sulfuric acid, and method for production thereof
JP5924459B1 (en) Stainless steel for cold rolled steel
TWI639714B (en) Steel plate
EP3290539A1 (en) Non-oriented magnetic steel sheet
CN110325656A (en) Steel plate
CN115298341B (en) High-strength hot-rolled steel plate and manufacturing method thereof
TWI815504B (en) Cold-rolled steel plate, steel parts, manufacturing method of cold-rolled steel plate, and manufacturing method of steel parts
EP4467669A1 (en) Method for manufacturing hot-rolled steel sheet for non-oriented electrical steel sheet, method for manufacturing non-oriented electrical steel sheet, and hot-rolled steel sheet for non-oriented electrical steel sheet
KR101850231B1 (en) Ferritic stainless steel and method for producing same
WO2017002148A1 (en) Cold-rolled stainless steel sheet material, manufacturing method therefor, and cold-rolled steel sheet
CN117043374B (en) Cold-rolled steel sheet and method for producing cold-rolled steel sheet
CN120858192A (en) Hot rolled steel sheet and method for manufacturing the same
JP2005305454A (en) Manufacturing method of fine grain hot rolled steel sheet
WO2025047016A1 (en) Hot-rolled annealed sheet for non-oriented electromagnetic steel sheet, method for manufacturing same, and method for manufacturing non-oriented electromagnetic steel sheet
TWI901151B (en) Hot rolled annealed sheet for non-oriented electromagnetic steel sheet and method for manufacturing the same, and method for manufacturing non-oriented electromagnetic steel sheet
JP2001207244A (en) Ferritic stainless cold-rolled steel sheet excellent in ductility, workability and ridging resistance and method for producing the same
CN119137299A (en) Hot rolled steel plate
JP2002241843A (en) Method for producing ferritic stainless steel sheet with excellent surface gloss and workability
JPH11264049A (en) High carbon steel strip and method of manufacturing the same
JP7744616B1 (en) Steel plate and its manufacturing method

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2024552680

Country of ref document: JP

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 2024552680

Country of ref document: JP

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 24859065

Country of ref document: EP

Kind code of ref document: A1