WO2025142748A1 - 方向性電磁鋼板 - Google Patents

方向性電磁鋼板 Download PDF

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Publication number
WO2025142748A1
WO2025142748A1 PCT/JP2024/045059 JP2024045059W WO2025142748A1 WO 2025142748 A1 WO2025142748 A1 WO 2025142748A1 JP 2024045059 W JP2024045059 W JP 2024045059W WO 2025142748 A1 WO2025142748 A1 WO 2025142748A1
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Prior art keywords
steel sheet
grain
oriented electrical
electrical steel
content
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PCT/JP2024/045059
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English (en)
French (fr)
Japanese (ja)
Inventor
真理 ▲高▼橋
猛 今村
之啓 新垣
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JFE Steel Corp
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JFE Steel Corp
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Priority to JP2025524387A priority Critical patent/JPWO2025142748A1/ja
Publication of WO2025142748A1 publication Critical patent/WO2025142748A1/ja
Pending legal-status Critical Current
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    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties

Definitions

  • the present invention relates to grain-oriented electrical steel sheets, and in particular to grain-oriented electrical steel sheets suitable for use as transformer core materials.
  • Grain-oriented electrical steel sheet is a soft magnetic material used as the iron core material of transformers, and has a crystal structure in which the ⁇ 001> orientation, the axis of easy magnetization of iron, is highly aligned in the rolling direction of the steel sheet.
  • This texture is formed during the manufacturing process of grain-oriented electrical steel sheet, through a phenomenon called secondary recrystallization, which preferentially grows crystal grains with the ⁇ 110 ⁇ 001> orientation, known as the Goss orientation, during purification annealing.
  • the commonly used technique for this formation method is to use a precipitate called an inhibitor to cause secondary recrystallization of grains with Goss orientation during purification annealing.
  • a precipitate called an inhibitor to cause secondary recrystallization of grains with Goss orientation during purification annealing.
  • the method using AlN described in Patent Document 1 and the method using MnS and MnSe described in Patent Document 2 have been put into industrial use.
  • the method of using these inhibitors is useful for stably developing secondary recrystallized grains, but in order to finely disperse the inhibitors in the steel, it is necessary to heat the slab at high temperatures of over 1300°C and dissolve the inhibitor components once.
  • Patent Document 3 and other publications disclose a technique for developing Goss-oriented crystal grains by secondary recrystallization in materials that do not contain inhibitor components.
  • This technique makes the grain boundary misorientation angle dependency of the grain boundary energy that the grain boundaries have during primary recrystallization apparent by eliminating impurities such as inhibitor components as much as possible, and allows grains with Goss orientation to undergo secondary recrystallization without the use of inhibitors; this effect is called the texture inhibition effect.
  • this method there is no need to finely disperse inhibitors in the steel. As a result, this method has great advantages in terms of both cost and maintenance, such as not requiring high-temperature slab heating, which was essential in methods that use inhibitors.
  • Grain-oriented electrical steel sheets are primarily used as transformer cores, and are required to have excellent magnetic properties, especially low iron loss. To achieve this, it is important to highly align the secondary recrystallized grains in the steel sheet to the Goss orientation, and to reduce impurities in the finished sheet.
  • Patent Document 4 proposes a technology in which a final product sheet is irradiated with a laser to introduce a high dislocation density region into the surface layer of the steel sheet, thereby narrowing the magnetic domain width and thereby reducing the iron loss of the steel sheet.
  • Patent Document 5 also proposes a technology in which the magnetic domain width is controlled by irradiation with an electron beam. The hysteresis loss is reduced by aligning the orientation after secondary recrystallization to the Goss orientation and by reducing impurities, while the application of magnetic domain refinement technology primarily reduces eddy current loss.
  • grain-oriented electrical steel sheets are mainly used as the cores of transformers.
  • the iron loss value of a transformer core there is a discrepancy between the iron loss value of a transformer core and the iron loss value of the grain-oriented electrical steel sheets that are the material, with the transformer core having a larger iron loss.
  • the ratio of the iron losses between the two is called the building factor. In other words, even if the material has good core loss, if the building factor is high, the core loss of the transformer will increase, resulting in the problem of being unable to achieve sufficient performance.
  • the object of the present invention is therefore to provide a grain-oriented electrical steel sheet that can adequately suppress the building factor when used as a transformer core material.
  • a three-phase three-legged model transformer was made from the obtained samples, with an external shape simulating a transformer: 500 mm square, with each leg and yoke having a plate width of 100 mm.
  • the iron loss WT 17/50 transformer iron loss when excited to 1.7 T at 50 Hz
  • the number of sample layers in the model transformer was 50, and they were stacked in pairs.
  • the building factor F17 of the model transformer was calculated by dividing the model transformer iron loss WT17 /50 by the sample iron loss W17 /50 (WT17 /50 /W17 /50 ). The relationship between this F17 and the W content (unit: mass%) in the base steel sheet was then investigated. The results are shown in Figure 1.
  • the second point is when the Ti content in the undercoated steel sheet (grain-oriented electrical steel sheet) is less than 0.0050 mass% or more than 0.0200 mass%. It is speculated that the presence of a certain amount of Ti in the forsterite coating improves the coating properties. For example, if the coating tension of the undercoating is improved due to the presence of Ti, the magnetic domains in the base steel sheet become finer, which may result in a reduction in eddy current loss in transformers using grain-oriented electrical steel sheets. In that case, the eddy current loss ratio decreases, in contrast to the high R17 and R19 cases mentioned above, and it is believed that the building factor can be reduced.
  • the present invention by controlling the amount of W in the base steel sheet and the amount of Ti in the grain-oriented electrical steel sheet having a base coating on the surface of the base steel sheet within a predetermined range and satisfying a predetermined loss relationship, it is possible to provide a grain-oriented electrical steel sheet that can reduce the building factor.
  • Mn 0.02-1.00% Mn is an element necessary for improving hot workability, but if it is less than 0.02%, there is no effect. On the other hand, if the Mn content exceeds 1.00%, the magnetic flux density of the grain-oriented electrical steel sheet product decreases. Therefore, the Mn content in the base steel sheet is set to the range of 0.02 to 1.00%.
  • the Mn content is preferably 0.04% or more. On the other hand, the Mn content is preferably 0.20% or less.
  • One or more of the following elements may be added: 0.020%, Ga: 0.0001-0.0050%, V: 0.001-0.020%, As: 0.0010-0.0200%, Zn: 0.001-0.020%, Pb: 0.0001-0.0100%, Co: 0.002-0.050%, and Ge: 0.0001-0.0050%.
  • Ga acts as an inhibitor during secondary recrystallization, suppressing the normal grain growth of grains that deviate from the Goss orientation. However, Ga is not completely removed during purification, but remains finely dispersed in the steel. This finely residual Ga serves as the origin of rotating magnetic flux without impairing iron loss, and is presumed to have improved the building factor.
  • the Ga content is more preferably 0.0005% or more, and even more preferably 0.0010% or more. Also, the Ga content is more preferably 0.0040% or less, and even more preferably 0.0030% or less.
  • Ti 0.0030% or less
  • the Ti content in the base steel sheet is preferably 0.0030% or less, more preferably 0.0015% or less, and may be 0% (not contained). This is because if the Ti content in the base steel sheet exceeds 0.0030%, Ti precipitates are likely to form in the steel, which may significantly deteriorate the iron loss.
  • the Ti content in a grain-oriented electrical steel sheet having a base coating mainly composed of forsterite formed on the surface thereof is further limited to 0.0050-0.0200% for the reasons mentioned above.
  • the Ti content in the grain-oriented electrical steel sheet is preferably 0.0060% or more.
  • the Ti content in the grain-oriented electrical steel sheet is preferably 0.0100% or less.
  • the Ti content in grain-oriented electrical steel sheet is the ratio (mass %) of the total amount of Ti present in the base steel sheet and the base coating to the total mass (solid content equivalent) of the base steel sheet and the base coating.
  • the Ti content in grain-oriented electrical steel sheet can be measured in accordance with JIS G1223, regardless of whether the base coating is formed on only one side or both sides of the base steel sheet.
  • the Ti content in the forsterite coating is preferably 0.0020% or more, more preferably 0.0050% or more, and even more preferably 0.0060% or more.
  • the Ti content in the forsterite coating is preferably 0.0150% or less.
  • the Ti content in steel sheet when limiting the Ti content in steel sheet (grain-oriented electrical steel sheet) with a base coating to 0.0050-0.0200%, as mentioned above, it is preferable that the Ti content in the base steel sheet is 0.0030% or less.
  • the grain-oriented electrical steel sheet does not satisfy the above formula (1), it cannot achieve a low building factor.
  • These values can be measured by the method described in JIS C2550-1.
  • the hysteresis loss can be calculated by multiplying the energy loss of the iron core in one revolution of the hysteresis loop by 50, which is the excitation frequency, in order to match the iron loss at 50 Hz.
  • the value of R19/R17 is not particularly limited, and can be controlled, for example, by changing the conditions of each process in the production to change the magnetic flux density B8 .
  • a method for manufacturing a general electrical steel sheet can be used.
  • a slab may be manufactured from the molten steel adjusted to the above-mentioned predetermined component composition by a normal ingot-making method or a continuous casting method.
  • a thin cast piece having a thickness of 100 mm or less may be manufactured from the molten steel by a direct casting method.
  • the molten steel may be manufactured by a blast furnace method or an electric furnace method. Since it is difficult to add the above-mentioned optional components that are desirably added during the intermediate process, it is desirably added at the molten steel stage.
  • the slab can be heated and hot rolled in the usual way.
  • the slab may be cast and hot rolled immediately without heating.
  • heating for component systems with a small amount of inhibitor components, high temperature heating to dissolve the inhibitor is not required, so keeping the temperature low, below 1300°C, is effective for reducing costs.
  • the heating temperature of the slab is preferably below 1250°C.
  • Hot rolling conditions can be in accordance with the usual methods. In this way, a hot-rolled sheet can be obtained.
  • the hot-rolled sheet annealing temperature is preferably about 950 to 1150°C. If the hot-rolled sheet annealing temperature is less than 950°C, unrecrystallized parts are likely to remain in the steel. On the other hand, if the hot-rolled sheet annealing temperature exceeds 1150°C, the grain size in the steel after annealing may become too coarse, and the subsequent primary recrystallization texture may become inappropriate.
  • the hot-rolled sheet annealing temperature is preferably 950°C or higher, more preferably 1000°C or higher, preferably 1150°C or lower, and more preferably 1100°C or lower.
  • the hot-rolled sheet annealing temperature range is preferably 1000°C or higher and 1100°C or lower. In this manner, a hot-rolled annealed sheet can be obtained.
  • the hot-rolled sheet after hot rolling or the hot-rolled annealed sheet after hot-rolled sheet annealing can be made into a cold-rolled sheet having the final sheet thickness by one cold rolling or two or more cold rollings with intermediate annealing in between.
  • the annealing temperature of the intermediate annealing is preferably 900°C or higher, preferably 1200°C or lower, and more preferably in the range of 900 to 1200°C. If the intermediate annealing temperature is less than 900°C, the recrystallized grains after the intermediate annealing tend to be fine. Furthermore, the number of Goss nuclei in the primary recrystallized structure decreases, and the magnetic properties of the grain-oriented electrical steel sheet, which is the product sheet, may deteriorate.
  • the intermediate annealing temperature exceeds 1200°C, the crystal grains may become too coarse, as in the case of hot-rolled sheet annealing, making it difficult to obtain a uniform primary recrystallized structure. In this way, a cold-rolled sheet can be obtained.
  • the cold-rolled sheet having been reduced to the final thickness can then be subjected to primary recrystallization annealing, which also serves as decarburization annealing.
  • the annealing temperature in this primary recrystallization annealing is preferably 800°C or higher, and preferably 900°C or lower, more preferably in the range of 800 to 900°C, in order to allow the decarburization reaction to proceed quickly.
  • the atmosphere during the primary recrystallization annealing, which also serves as decarburization annealing is a humid atmosphere. In this way, a primary recrystallized sheet (decarburization annealed sheet) can be obtained.
  • an annealing separator mainly composed of MgO can be applied to one or both surfaces of the primary recrystallized sheet, followed by secondary recrystallization annealing.
  • the secondary recrystallization annealing may also serve as purification annealing for purifying the components.
  • a grain-oriented electrical steel sheet according to the present invention having a base coating mainly composed of forsterite formed on the surface of the base steel sheet can be suitably obtained.
  • "mainly composed of MgO" means that the annealing separator contains 75 mass % or more of MgO in terms of solid content.
  • Ti can be effectively present in the forsterite coating.
  • TiO2 and TiN are preferred as Ti compounds, and TiO2 is more preferred.
  • the content of the compound in the annealing separator is preferably 2 parts by mass or more and 15 parts by mass or less relative to MgO.
  • the above requirement regarding Ti may be met by other methods, such as adding Ti as a material component and changing the purification annealing conditions.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Soft Magnetic Materials (AREA)
PCT/JP2024/045059 2023-12-27 2024-12-19 方向性電磁鋼板 Pending WO2025142748A1 (ja)

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09291313A (ja) * 1996-04-25 1997-11-11 Kawasaki Steel Corp 磁気特性・被膜特性に優れる方向性けい素鋼板の製造方法
JP2017020059A (ja) * 2015-07-08 2017-01-26 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法
JP2021123766A (ja) * 2020-02-06 2021-08-30 日本製鉄株式会社 方向性電磁鋼板、および方向性電磁鋼板の製造方法、ならびに焼鈍分離剤
KR20230094748A (ko) * 2021-12-21 2023-06-28 주식회사 포스코 방향성 전기강판 및 이의 제조방법
WO2024053608A1 (ja) * 2022-09-09 2024-03-14 Ｊｆｅスチール株式会社 方向性電磁鋼板

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH09291313A (ja) * 1996-04-25 1997-11-11 Kawasaki Steel Corp 磁気特性・被膜特性に優れる方向性けい素鋼板の製造方法
JP2017020059A (ja) * 2015-07-08 2017-01-26 Ｊｆｅスチール株式会社 方向性電磁鋼板とその製造方法
JP2021123766A (ja) * 2020-02-06 2021-08-30 日本製鉄株式会社 方向性電磁鋼板、および方向性電磁鋼板の製造方法、ならびに焼鈍分離剤
KR20230094748A (ko) * 2021-12-21 2023-06-28 주식회사 포스코 방향성 전기강판 및 이의 제조방법
WO2024053608A1 (ja) * 2022-09-09 2024-03-14 Ｊｆｅスチール株式会社 方向性電磁鋼板

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