WO2013094218A1 - 方向性電磁鋼板およびその製造方法 - Google Patents

方向性電磁鋼板およびその製造方法 Download PDF

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Publication number
WO2013094218A1
WO2013094218A1 PCT/JP2012/008202 JP2012008202W WO2013094218A1 WO 2013094218 A1 WO2013094218 A1 WO 2013094218A1 JP 2012008202 W JP2012008202 W JP 2012008202W WO 2013094218 A1 WO2013094218 A1 WO 2013094218A1
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Prior art keywords
steel sheet
magnetic domain
irradiation
grain
width
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PCT/JP2012/008202
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English (en)
French (fr)
Japanese (ja)
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WO2013094218A8 (ja
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重宏 ▲高▼城
岡部　誠司
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JFE Steel Corp
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JFE Steel Corp
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Priority to EP12860627.4A priority Critical patent/EP2796583B1/en
Priority to IN1092MUN2014 priority patent/IN2014MN01092A/en
Priority to US14/367,654 priority patent/US10020101B2/en
Priority to JP2013550134A priority patent/JP5761375B2/ja
Priority to RU2014130094/02A priority patent/RU2572636C1/ru
Priority to KR1020147016938A priority patent/KR101551782B1/ko
Priority to CN201280063637.4A priority patent/CN104011241B/zh
Publication of WO2013094218A1 publication Critical patent/WO2013094218A1/ja
Publication of WO2013094218A8 publication Critical patent/WO2013094218A8/ja
Anticipated expiration legal-status Critical
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/38—Heating by cathodic discharges
    • 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
    • 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
    • C21D8/1294—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a localized treatment
    • 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
    • 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
    • C21D2201/00—Treatment for obtaining particular effects
    • C21D2201/05—Grain orientation
    • 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
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest

Definitions

  • the present invention relates to a grain-oriented electrical steel sheet having a low hysteresis loss and a low coercive force suitable for applications such as transformer iron cores and a method for producing the same.
  • Patent Document 1 discloses a method for producing a grain-oriented electrical steel sheet having a magnetic flux density B 8 exceeding 1.97T. Yes.
  • Patent Document 1 discloses a method of producing a grain-oriented electrical steel sheet that is advantageous in iron loss by reducing the coercive force by adjusting the annealing separator.
  • Noise can be reduced by reducing a region having a magnetic moment that is perpendicular to the direction of the external magnetic field, called a return magnetic domain.
  • a method for reducing the reflux magnetic domain there is a method as described in Patent Document 3.
  • “aligning the ⁇ 100> direction of the crystal grains to the rolling direction” means that the magnetic flux density B 8 is improved and the hysteresis loss is reduced. Many reports have been made so far.
  • Patent Document 4 As a method for reducing eddy current loss, a magnetic domain refinement technique by improving the film tension or introducing thermal strain is used.
  • the method of improving the film tension as shown in Patent Document 4 has an effect of eliminating the reflux magnetic domain, and is advantageous for noise reduction, but there is a limit to the tension to be applied.
  • Patent Document 5 discloses a method of manufacturing an electrical steel sheet having an iron loss with W 17/50 less than 0.8 W / kg by electron beam irradiation. Electron beam irradiation is an extremely useful technique for reducing iron loss. It turns out that it is. Patent Document 6 discloses a method for reducing iron loss by laser irradiation.
  • Japanese Patent No. 4123679 Japanese Patent No. 3386727 Japanese Patent No. 4585101 Japanese Patent Publication No. 2-8027 Japanese Examined Patent Publication No. 7-65106 Japanese Patent Publication No. 3-13293 Japanese Patent No. 4091749 Japanese Patent No. 4344264
  • the hysteresis loss increases when strain is introduced, that is, the reduction of eddy current loss due to the increase of strain as shown in the schematic diagram of FIG.
  • the optimum stress strain that minimizes the iron loss, which is the sum of them, is added to the hysteresis loss, thus reducing the eddy current loss sufficiently and suppressing the increase in hysteresis loss as much as possible. Is ideal and that direction Realizing an electromagnetic steel sheet has been desired. "The at it.
  • Patent Document 8 reports that a hardened region generated in a steel plate by laser irradiation or the like hinders domain wall movement and increases hysteresis loss. Further, such a return magnetic domain is considered to increase magnetostriction, and therefore, when used as an iron core of a transformer, noise is increased during excitation.
  • Patent Document 8 by adjusting the laser output and the spot diameter ratio, the region cured by laser irradiation in the direction perpendicular to the laser scanning direction is reduced to 0.6 mm or less. A technique for further reducing iron loss by suppressing an increase in hysteresis loss is shown. However, there is still a problem that hysteresis loss and noise increase more than before irradiation when iron loss is minimized by irradiation with a laser or an electron beam.
  • the present invention has been developed in view of the above-described situation, and effectively suppresses an increase in hysteresis loss associated with laser irradiation and electron beam irradiation, which has been a concern in the past, and has a directionality with reduced hysteresis loss and coercive force.
  • the object is to propose an electrical steel sheet together with its advantageous manufacturing method.
  • the inventors have devised the magnetic domain subdivision processing using a laser or an electron beam to reduce the eddy current loss while reducing the hysteresis loss. It was also found that it can be reduced.
  • the above-mentioned magnetic domain subdivision treatment has a role of generating a reflux magnetic domain in the steel sheet, while eliminating a reflux magnetic domain called a lancet magnetic domain that existed before irradiation.
  • a lancet magnetic domain is a region having a magnetic moment in the plate thickness direction, which is generated to reduce magnetostatic energy generated when the crystal orientation ( ⁇ angle) is shifted by several degrees from the ideal ⁇ 100> direction. is there.
  • the newly generated reflux magnetic domain due to the magnetic domain subdivision stabilized the magnetostatic energy instead of the lancet magnetic domain, or was formed on the steel plate during the magnetic domain subdivision. It is thought that the lancet magnetic domain disappears because the internal stress destabilizes the lancet magnetic domain.
  • the inventors further reduced the hysteresis loss and coercivity from the values before irradiation by increasing the ratio of the disappearing return magnetic domain (lancet magnetic domain) to the return magnetic domain generated by laser or electron beam irradiation.
  • the present invention has been completed based on the new knowledge that can be achieved.
  • the gist configuration of the present invention is as follows. 1.
  • Directional electromagnetic wave having a return magnetic domain region X formed so as to divide a magnetic domain in a rolling direction, linearly or in a curved shape, from one width end to the other width end of a steel plate
  • the plate thickness is t (mm)
  • the width of the region X is measured by the bitter method from the front and back surfaces of the steel plate, the smaller value of which is w ( ⁇ m), and within one crystal grain
  • these w, s, and t are expressed by the following formula (1) -(500t-80) ⁇ s + 230 ⁇ w ⁇ ⁇ (500t-80) ⁇ s + 330
  • a grain-oriented electrical steel sheet characterized by satisfying the above relationship.
  • the grain-oriented electrical steel sheet of the present invention has not only low hysteresis loss but also low coercive force in 1.7T excitation, and therefore has the advantage of improving the energy use efficiency of the transformer. Furthermore, since the amount of the return magnetic domain, which is a cause of noise, is extremely small, noise suppression can also be achieved, which is extremely useful in the industry.
  • FIG. 4 is a diagram showing a formation procedure of a reflux magnetic domain region X. It is a graph which shows the influence which the width w of the recirculation
  • the present invention is applied to grain-oriented electrical steel sheets.
  • As the grain-oriented electrical steel sheet there may be no problem even if an insulating coating or the like is coated, the coating is partially peeled off, or the coating is not entirely present.
  • the magnetic steel sheet of the present invention is a reflux formed so as to divide the magnetic domain in the rolling direction, linearly or in a curved shape, from the width end of the steel sheet to the other width end, periodically in the rolling direction. It has a magnetic domain region X.
  • the crystal grain boundary is not included in the above-described reflux magnetic domain region formed so as to divide the magnetic domain in the rolling direction.
  • the width of the region X differs depending on whether it is observed from the front surface or the back surface of the steel plate, so it is defined by a smaller value and is set as w. However, when the region X was observed only on one side, the width on the one side was set to w. When w varies greatly in the width direction, an average value in the width direction is taken.
  • the bitter method is a method of observing a domain wall or the like with a magnetic colloid that is easily attracted to a portion with a large change in magnetization.
  • FIG. 2 shows the results of examining the influence of w and s caused by electron beam irradiation on magnetic domain fragmentation and hysteresis loss.
  • the condition that the magnetic domain is subdivided and the hysteresis loss is lower than that before irradiation is as follows: -(500t-80) ⁇ s + 230 ⁇ w ⁇ ⁇ (500t-80) ⁇ s + 330 (1) It became clear that it can be defined by.
  • the condition that the hysteresis loss is lower than that before irradiation is as follows: ⁇ 30 ⁇ s + 230 ⁇ w ⁇ ⁇ 30 ⁇ s + 330 (2) Can be specified.
  • w ⁇ 30 ⁇ s + 230 the reflux magnetic domain originally present in the steel sheet by irradiation is not reduced, and the effect of improving the hysteresis loss is insufficient.
  • Hysteresis loss cannot be improved due to too many reflux magnetic domains increasing.
  • the range of w in which the hysteresis loss is reduced becomes narrower as the plate thickness t increases.
  • the plate thickness t is small, the domain wall energy is low. Therefore, it is presumed that the magnetic domain fragmentation easily occurs when the laser or electron beam is irradiated, and the magnetostatic energy is reduced. It is considered that the lancet magnetic domain generated to reduce the temperature does not need to exist and disappears. Therefore, from the viewpoint of obtaining as large a hysteresis loss reduction effect as possible, the thickness t is preferably 0.27 mm or less.
  • the inventors have also found that the hysteresis loss tends to be excessively increased as s is increased. Although the detailed mechanism is unknown, the reflux magnetic domains originally present in the grains are almost disappeared when s is small, so even if s becomes larger, the effect of reducing the reflux magnetic domain is very poor. Thus, it is presumed that the hysteresis loss increases as the heat-affected region increases. On the other hand, if s is too small, the effect of improving hysteresis is insufficient. Accordingly, it is desirable that the number s of the regions X existing on average in one crystal grain is about 0.3 to 10. The width w of the reflux magnetic domain region X is preferably about 30 to 320 ⁇ m.
  • the inventors when irradiating a laser beam or an electron beam on the steel plate surface, the inventors have at least one of a periodic irradiation interval L, irradiation energy E, and beam diameter a in the rolling direction according to the average crystal grain size of the steel plate. It was found that a grain-oriented electrical steel sheet having a low hysteresis loss and a low coercive force as described above can be produced by adjusting the above and forming the region X.
  • the width w of the region X has a high correlation with the irradiation energy E and the beam diameter a. As E increases, w increases, and in the case of the same energy irradiation, w decreases as a decreases. If the relationship between w and E and a is derived experimentally, w can be controlled by adjusting E and a.
  • the amount of change recognized as the hysteresis loss is reduced by irradiation was set as (hysteresis loss before irradiation ⁇ hysteresis loss after irradiation) ⁇ 0.003 W / kg.
  • Introducing area X can be ruled with a ballpoint pen or knife, or heat, light, or particle beam irradiation, but when ruled with a ballpoint pen or knife, distortion is introduced more and hysteresis loss increases. Therefore, heat, light, and particle beam irradiation such as laser irradiation, electron beam irradiation, and plasma flame irradiation are desirable.
  • Example 1 The material used in this experiment has a measured thickness of 0.22 mm, a magnetic flux density B 8 in the rolling direction of 1.85 to 1.95 T, and a glassy coating mainly composed of Mg 2 SiO 4 on the surface of the ground iron. It is a grain-oriented electrical steel sheet having a two-layer coating film (phosphate coating) onto which an inorganic treatment liquid is baked.
  • the electron beam irradiation and laser irradiation were used as a method for introducing the reflux magnetic domain region X.
  • the electron beam irradiation part and the laser irradiation part were scanned linearly over the entire sheet width so as to cross the steel sheet in the direction perpendicular to the rolling direction of the steel sheet.
  • the irradiation time is repeated so as to repeat a long time (s 1 ) and a short time (s 2 ) along the scanning line, and this repeated distance period (dot pitch) is 0.05 to It was 0.6 mm.
  • s 2 is negligible short enough relative to s 1
  • the inverse of s 1 as an irradiation frequency was 10 ⁇ 250 kHz.
  • the scanning speed was 4 to 80 m / s, and the repetition interval in the rolling direction was 3 to 50 mm.
  • the shortest distance from the center of the focusing coil to the irradiated material was 700 mm, and the pressure in the processing chamber was 2 Pa or less.
  • the width of the region X was measured from the front and back surfaces by a bitter method using a magnet viewer (MV-95 manufactured by Sigma High Chemical Co.), and w was determined. Subsequently, the iron loss was measured. Then, the film was formed with an aqueous solution obtained by mixing 35% hydrochloric acid water: 5L with 20L water and 47% hydrogen fluoride water: 500mL, and 67.5% sulfuric acid water: 500mL diluted with 10L water. It peeled. The number of regions X in each crystal grain of the sample from which the film was peeled was observed using a magnet viewer, and s was measured.
  • Table 1 shows the width w of the reflux magnetic domain region X and the number s of the reflux magnetic domain regions X.
  • Table 1 also shows hysteresis loss Wh 17/50 before irradiation, improvement amount ⁇ Hh 17/50 of hysteresis loss after irradiation (value before irradiation ⁇ value after irradiation), and improvement amount of eddy current loss ⁇ We 17 /
  • the results of examining 50 are also shown.
  • Table 1 also shows the results of investigation on the coercivity Hc before irradiation and the coercivity improvement amount ⁇ Hc after irradiation (value before irradiation ⁇ value after irradiation).
  • the tension applied by the coating is indicated by symbols A, B, and C, where A is more than 10 MPa to 15 MPa, B is more than 5 MPa to 10 MPa, and C is 5 MPa or less.
  • Example 2 Electron beam irradiation was performed under the same conditions as in Example 1 except that grain-oriented electrical steel sheets having actual thickness values of 0.18 mm, 0.19 mm, and 0.24 mm were used, respectively. The results are shown in Table 2.
  • Example 3 Furthermore, using a steel plate with a width of 100 mm with magnetic domain subdivision, a model transformer with an outer diameter of 500 mm simulating a three-phase tripod-stacked iron core type transformer was fabricated and evaluated for noise.
  • This model transformer was manufactured by laminating steel sheets cut at an oblique angle so that the stacking thickness was about 15 mm and the iron core weight was about 20 kg.
  • the three phases were excited by shifting the phase by 120 °, and the noise was measured in the case of 1.7T, 50Hz excitation. Noise was measured with a microphone at a position 20 cm away from the iron core surface (2 locations), and expressed in dBA units with A scale correction (JIS C 1509). Table 3 shows the measurement results.

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PCT/JP2012/008202 2011-12-22 2012-12-21 方向性電磁鋼板およびその製造方法 Ceased WO2013094218A1 (ja)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP12860627.4A EP2796583B1 (en) 2011-12-22 2012-12-21 Grain-oriented electrical steel sheet and method for producing same
IN1092MUN2014 IN2014MN01092A (cg-RX-API-DMAC10.html) 2011-12-22 2012-12-21
US14/367,654 US10020101B2 (en) 2011-12-22 2012-12-21 Grain-oriented electrical steel sheet and method for producing same
JP2013550134A JP5761375B2 (ja) 2011-12-22 2012-12-21 方向性電磁鋼板およびその製造方法
RU2014130094/02A RU2572636C1 (ru) 2011-12-22 2012-12-21 Лист текстурированной электротехнической стали и способ его изготовления
KR1020147016938A KR101551782B1 (ko) 2011-12-22 2012-12-21 방향성 전자 강판 및 그의 제조 방법
CN201280063637.4A CN104011241B (zh) 2011-12-22 2012-12-21 取向性电磁钢板及其制造方法

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JP2011-282271 2011-12-22
JP2011282271 2011-12-22

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WO2013094218A8 WO2013094218A8 (ja) 2014-06-05

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KR (1) KR101551782B1 (cg-RX-API-DMAC10.html)
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IN (1) IN2014MN01092A (cg-RX-API-DMAC10.html)
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Cited By (5)

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JP2015052144A (ja) * 2013-09-06 2015-03-19 Ｊｆｅスチール株式会社 変圧器鉄心用方向性電磁鋼板およびその製造方法
JP2015063753A (ja) * 2013-08-30 2015-04-09 Ｊｆｅスチール株式会社 低騒音変圧器鉄心用方向性電磁鋼板およびその製造方法
JP2017106117A (ja) * 2017-01-04 2017-06-15 Ｊｆｅスチール株式会社 変圧器鉄心用方向性電磁鋼板およびその製造方法
US20190013126A1 (en) * 2016-01-25 2019-01-10 Jfe Steel Corporation Grain-oriented electrical steel sheet and method for manufacturing the same
JP2022515236A (ja) * 2018-12-19 2022-02-17 ポスコ 方向性電磁鋼板およびその製造方法

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JP6010907B2 (ja) * 2011-12-28 2016-10-19 Ｊｆｅスチール株式会社 方向性電磁鋼板およびその製造方法
JP5935880B2 (ja) 2012-04-27 2016-06-15 新日鐵住金株式会社 方向性電磁鋼板及びその製造方法
JP6060988B2 (ja) 2015-02-24 2017-01-18 Ｊｆｅスチール株式会社 方向性電磁鋼板及びその製造方法
RU2741403C1 (ru) 2018-01-31 2021-01-25 ДжФЕ СТИЛ КОРПОРЕЙШН Текстурированный лист из электротехнической стали, ленточный сердечник трансформатора из текстурированного листа из электротехнической стали и способ изготовления ленточного сердечника
CA3095320C (en) * 2018-03-30 2023-10-03 Jfe Steel Corporation Iron core for transformer
WO2019189859A1 (ja) * 2018-03-30 2019-10-03 Ｊｆｅスチール株式会社 変圧器用鉄心
JP7393698B2 (ja) * 2020-07-15 2023-12-07 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

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JP7260649B2 (ja) 2018-12-19 2023-04-18 ポスコ カンパニー リミテッド 方向性電磁鋼板およびその製造方法

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