WO2012017655A1 - 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 PDFInfo
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- WO2012017655A1 WO2012017655A1 PCT/JP2011/004410 JP2011004410W WO2012017655A1 WO 2012017655 A1 WO2012017655 A1 WO 2012017655A1 JP 2011004410 W JP2011004410 W JP 2011004410W WO 2012017655 A1 WO2012017655 A1 WO 2012017655A1
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- H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
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- 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
- H01F1/18—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 with insulating coating
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- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
Definitions
- the present invention relates to a grain-oriented electrical steel sheet suitable as an iron core material such as a transformer and a method for manufacturing the same.
- the grain-oriented electrical steel sheet is mainly used as an iron core of a transformer and is required to have excellent magnetization characteristics, particularly low iron loss.
- it is important to highly align secondary recrystallized grains in the steel sheet in the (110) [001] orientation (so-called Goth orientation) and to reduce impurities in the product steel sheet.
- Goth orientation secondary recrystallized grains in the steel sheet in the (110) [001] orientation
- impurities in the product steel sheet Furthermore, there is a limit in controlling the crystal orientation and reducing impurities in terms of the manufacturing cost. Therefore, a technique for reducing the iron loss by introducing non-uniformity to the surface of the steel sheet by a physical method and subdividing the width of the magnetic domain, that is, a magnetic domain subdivision technique has been developed.
- Patent Document 1 proposes a technique for reducing the iron loss of a steel sheet by irradiating the final product plate with a laser, introducing a high dislocation density region into the steel sheet surface layer, and narrowing the magnetic domain width.
- Patent Document 2 proposes a technique for controlling the magnetic domain width by electron beam irradiation.
- the present invention has been developed in view of the above-mentioned present situation.
- a grain-oriented electrical steel sheet capable of obtaining excellent low noise characteristics and low iron loss characteristics, together with its advantageous manufacturing method.
- the purpose is to provide.
- the increase in transformer noise is caused by a decrease in the thickness of the forsterite film (coating mainly composed of Mg 2 SiO 4 ) in the strain-introduced portion when thermal strain is introduced to subdivide the magnetic domains.
- noise deterioration can be prevented if the ratio of the film thickness Wa of the forsterite film on the strain introduction side of the steel sheet to the film thickness Wb of the forsterite film on the non-introduction side is properly adjusted. It turned out to be.
- the strain introduction side refers to the side irradiated with the electron beam
- the strain non-introduction side refers to the side not subjected to the electron beam irradiation.
- the gist configuration of the present invention is as follows. 1.
- a directional electrical steel sheet having a forsterite film on the surface and introduced with strain by an electron beam and having a magnetic flux density B 8 of 1.92 T or more, and the film thickness Wa and strain of the forsterite film on the strain-introducing side of the steel sheet The non-introduced forsterite film thickness Wb ratio (Wa / Wb) is 0.5 or more, the average width of the magnetic domain discontinuities on the strain-introduced steel plate surface is 150 to 300 ⁇ m, and the non-introduced steel plate surface
- the grain-oriented electrical steel sheet having an average width of magnetic domain discontinuities of 250 to 500 ⁇ m.
- decarburization annealing is performed, and then the steel sheet surface is coated with an annealing separator mainly composed of MgO, and then the final finish annealing is performed.
- a magnetic domain fragmentation treatment is performed by electron beam irradiation.
- the degree of vacuum during electron beam irradiation is 0.1-5 Pa.
- a method for producing a grain-oriented electrical steel sheet in which the tension applied to the steel sheet during flattening annealing is controlled to 5 to 15 MPa.
- the slab for grain-oriented electrical steel sheet is hot-rolled and then subjected to hot-rolled sheet annealing as necessary, and then subjected to one or more cold rollings or two or more cold rollings sandwiching intermediate annealing, and finally 3.
- the point for suppressing the increase in the noise of the actual transformer using the grain-oriented electrical steel sheet that has been subjected to strain application and subjected to the magnetic domain subdivision treatment is to satisfy all of the following three points.
- the first point is the control of the thickness of the forsterite film where strain is introduced, and the reason why the control of the thickness of the forsterite film is important is as follows.
- the forsterite film on the surface of the steel sheet imparts tension to the steel sheet.
- the tension distribution of the steel sheet becomes non-uniform.
- the distortion of the magnetostrictive vibration waveform of the steel sheet, which causes noise occurs, resulting in an increase in noise due to superposition of harmonic components. Therefore, in order to suppress this increase in noise, it is important to suppress a reduction in the thickness of the forsterite film that occurs when thermal strain is introduced.
- the ratio (Wa / Wb) of the film thickness Wa of the forsterite film on the strain introduction side to the film thickness Wb of the forsterite film on the non-strain introduction side needs to be 0.5 or more. Preferably, it is 0.7 or more. Normally, the thickness of the forsterite coating on both sides of the steel plate before strain introduction is about the same. Therefore, the maximum value of Wa / Wb is about 1.
- FIG. 1 is a schematic view of a cross section of a steel plate having a forsterite film.
- the thickness of the forsterite film is not uniform and has large irregularities when viewed in a short period, but the thickness can be determined from the average value by taking a sufficient measurement distance. Specifically, a sample of a cross section of a steel plate is cut out, the area of the forsterite coating is obtained for a predetermined measurement distance (preferably 1 mm) (SEM observation and image analysis are preferably used), and the average thickness of the coating on the surface is calculated. It can be obtained by calculating.
- a good forsterite film means a forsterite film having a high density with few voids due to cracks or the like in the film.
- the most important factor that causes damage to the forsterite film, such as cracking is the tension applied to the steel sheet during flattening annealing. If this tension is strong, the forsterite film is damaged and cracked. Etc. will occur. Therefore, it is necessary to control the tension to 15 MPa (1.5 kgf / mm 2 ) or less in an annealing furnace in which the steel plate temperature is high and the tension sensitivity is high.
- the above-described tension needs to be 5 MPa (0.5 kgf / mm 2 ) or more. This is because the shape correction of the steel sheet becomes insufficient when the pressure is less than 5 MPa.
- the inventors have found that it is effective to appropriately leave oxygen during electron beam irradiation in order to suppress the reduction of the forsterite film. The reason for this is not clear, but it is thought that oxidation of the steel sheet by residual oxygen at the time of introduction of thermal strain has some influence on the maintenance of the film thickness of the forsterite film.
- the degree of vacuum needs to be in the range of 0.1 to 5 Pa. If the degree of vacuum is increased from 0.1 Pa, the decrease in forsterite film cannot be suppressed. On the other hand, if the degree of vacuum is lower than 5 Pa, thermal strain is not effectively applied to the steel sheet. More preferably, it is in the range of 0.5 to 3 Pa.
- the second point is the control of the magnetic domain discontinuity on the steel sheet surface on the strain introduction side and the steel sheet surface on the non-strain introduction side.
- the average width of the magnetic domain discontinuity on the strain-introduced steel sheet surface is 150 to 300 ⁇ m
- the magnetic The average width of the continuous part is 250 to 500 ⁇ m. That is, the present invention satisfies the above (i) by defining the average width of the magnetic domain discontinuities on the steel sheet surface on the non-introduced side, and sets the upper limit of each average width (ii) above. Meet. Furthermore, the reason why the lower limit value of each average width is set is that if the width is narrower than this, the magnetic domain refinement effect cannot be obtained.
- the average width of the magnetic domain discontinuity is the average irradiation width.
- the heat spreads in all directions, such as the thickness direction and the width direction, so that the magnetic domain discontinuity affected by such a thermal effect usually tends to be wider than the irradiation width. Because there is. For the same reason, the width of the magnetic domain discontinuity portion on the strain non-introduction side is larger than that of the magnetic domain discontinuity portion on the strain introduction side.
- the width of the magnetic domain discontinuity is visualized by a bitter method using a magnetic colloid or the like so that the discontinuity formed by electron beam irradiation can be identified (see FIG. 2), and is further predetermined.
- the measurement distance (preferably 20 mm) can be obtained by measuring the width of the magnetic domain discontinuity and calculating the average.
- FIG. 2 is a schematic diagram showing the magnetic domain structure of the grain-oriented electrical steel sheet after the magnetic domain subdivision treatment, and there is a main magnetic domain in the left-right direction, and an electron beam is irradiated in the vertical direction in the center of the paper almost perpendicularly to it. It shows a state.
- the magnetic domain discontinuity is a region where the structure of the main magnetic domain is disturbed by the electron beam irradiation, and substantially corresponds to a region affected by the electron beam irradiation.
- the third point is that the degree of integration of the material crystal grains on the easy axis of magnetization is high.
- transformer noise that is, magnetostrictive vibration
- the magnetic flux density B 8 is less than 1.92 T, the rotational motion of the magnetic domain to be parallel to the excitation magnetic field in the magnetization process generates a large magnetostriction, which increases the noise of the transformer.
- the magnetic flux density B 8 needs to be 1.92 T or more from the viewpoint of reducing iron loss.
- the strain introduction processing in the present invention is limited to a method using an electron beam that can reduce film damage at the strain introduction portion.
- the irradiation direction is a direction crossing the rolling direction, preferably 60 ° to 90 ° in the rolling direction, and the electron beam irradiation interval is about 3 to 15 mm.
- the electron beam irradiation conditions are as follows: an acceleration voltage of 10 to 200 kV, a current of 0.1 to 100 mA, and a beam diameter (diameter) of 0.01 to 0.5 mm.
- a preferable beam diameter is 0.01 to 0.3 mm.
- the component composition of the slab for grain-oriented electrical steel sheet may be a component composition that causes secondary recrystallization.
- an inhibitor for example, when using an AlN-based inhibitor, Al and N, and when using an MnS / MnSe-based inhibitor, an appropriate amount of Mn and Se and / or S should be contained. Good. Of course, both inhibitors may be used in combination.
- the preferred contents of Al, N, S and Se are Al: 0.01 to 0.065 mass%, N: 0.005 to 0.012 mass%, S: 0.005 to 0.03 mass%, and Se: 0.005 to 0.03 mass%, respectively. .
- the present invention can also be applied to grain-oriented electrical steel sheets in which the contents of Al, N, S, and Se are limited and no inhibitor is used.
- the amounts of Al, N, S and Se are preferably suppressed to Al: 100 mass ppm or less, N: 50 mass ppm or less, S: 50 mass ppm or less, and Se: 50 mass ppm or less, respectively.
- C 0.08 mass% or less
- the burden of reducing C to 50 massppm or less where no magnetic aging occurs during the manufacturing process increases. Therefore, the content is preferably 0.08% by mass or less.
- the lower limit since a secondary recrystallization is possible even for a material not containing C, it is not particularly necessary to provide it.
- Si 2.0-8.0% by mass Si is an element effective for increasing the electrical resistance of steel and improving iron loss, and its content of 2.0% by mass or more is particularly effective for reducing iron loss. On the other hand, when it is 8.0% by mass or less, particularly excellent workability and magnetic flux density can be obtained. Accordingly, the Si content is preferably in the range of 2.0 to 8.0% by mass.
- Mn 0.005 to 1.0 mass%
- Mn is an element advantageous for improving the hot workability, but if the content is less than 0.005% by mass, the effect of addition is poor. On the other hand, if it is 1.0 mass% or less, the magnetic flux density of a product board will become especially favorable. Therefore, the Mn content is preferably in the range of 0.005 to 1.0% by mass.
- Ni 0.03-1.50 mass%
- Sn 0.01-1.50 mass%
- Sb 0.005-1.50 mass%
- Cu 0.03-3.0 mass%
- P 0.03-0.50 mass%
- Mo 0.005-0.10 mass%
- Cr At least one Ni selected from 0.03 to 1.50 mass% is an element useful for further improving the hot rolled sheet structure and further improving the magnetic properties.
- the content is less than 0.03% by mass, the effect of improving the magnetic properties is small.
- the content is 1.5% by mass or less, the stability of secondary recrystallization is increased, and the magnetic properties are further improved. Therefore, the Ni content is preferably in the range of 0.03 to 1.5% by mass.
- Sn, Sb, Cu, P, Mo and Cr are elements useful for improving the magnetic properties, respectively, but if any of them is less than the lower limit of each component described above, the effect of improving the magnetic properties is small, When the amount is not more than the upper limit amount of each component described above, the development of secondary recrystallized grains is the best. For this reason, it is preferable to make it contain in said range, respectively.
- the balance other than the above components is inevitable impurities and Fe mixed in the manufacturing process.
- the slab having the above-described component composition is heated and subjected to hot rolling according to a conventional method, but may be immediately hot rolled after casting without being heated.
- hot rolling may be performed, or the hot rolling may be omitted and the process may proceed as it is.
- hot-rolled sheet annealing is performed as necessary.
- the main purpose of hot-rolled sheet annealing is to eliminate the band structure generated by hot rolling and to make the primary recrystallized structure sized, thereby further developing the goth structure and improving the magnetic properties in the secondary recrystallization annealing. That is.
- the hot rolled sheet annealing temperature is preferably in the range of 800 to 1100 ° C.
- the hot-rolled sheet annealing temperature is less than 800 ° C, the band structure in hot rolling remains, making it difficult to achieve a sized primary recrystallized structure and obtaining the desired secondary recrystallization improvement. I can't.
- the hot-rolled sheet annealing temperature exceeds 1100 ° C., the grain size after the hot-rolled sheet annealing becomes too coarse, and it becomes difficult to realize a sized primary recrystallized structure.
- the hot-rolled sheet annealing After the hot-rolled sheet annealing, it is preferable to finish the final sheet thickness after performing at least one cold rolling or two or more cold rolling sandwiching the intermediate annealing.
- decarburization annealing also used for recrystallization annealing
- an annealing separator is applied. After applying the annealing separator, a final finish annealing is performed for the purpose of secondary recrystallization and forsterite film formation.
- the annealing separator is preferably composed mainly of MgO in order to form forsterite.
- MgO as a main component means that it may contain a known annealing separator component or property improving component other than MgO as long as it does not inhibit the formation of the forsterite film that is the object of the present invention. To do.
- an insulating coating is applied to the steel sheet surface before or after planarization annealing.
- this insulating coating means a coating (hereinafter referred to as tension coating) capable of imparting tension to a steel sheet in order to reduce iron loss.
- the tension coating include silica-containing inorganic coating, physical vapor deposition, and ceramic coating by chemical vapor deposition.
- the magnetic domain refinement treatment is performed by irradiating the surface of the steel sheet with an electron beam at any one of the above points, on the grain-oriented electrical steel sheet after the final finish annealing or after the tension coating described above.
- a method of manufacturing a grain-oriented electrical steel sheet that is subjected to a magnetic domain fragmentation process using a conventionally known electron beam can be applied except for the steps and manufacturing conditions described above.
Abstract
Description
そのためには、鋼板中の二次再結晶粒を(110)[001]方位(いわゆる、ゴス方位)に高度に揃えることや製品鋼板中の不純物を低減することが重要である。さらに、結晶方位の制御や、不純物を低減することは、製造コストとの兼ね合い等で限界がある。そこで、鋼板の表面に対して物理的な手法で不均一性を導入し、磁区の幅を細分化して鉄損を低減する技術、すなわち磁区細分化技術が開発されている。
また、磁区細分化処理による鉄損低減効果が最大限得られる条件を調査した結果、歪導入側の鋼板面における磁区不連続部の平均幅、および歪非導入側の鋼板面における磁区不連続部の平均幅をそれぞれ適正範囲に調整する必要があることが判明した。ここで歪導入側とは電子ビームを照射した側を指し、歪非導入側は電子ビームの照射を施さなかった側を指す。
本発明は、上記した知見に基づき開発されたものである。
1.表面にフォルステライト被膜をそなえ、電子ビームにより歪導入を施した、磁束密度B8が1.92T以上の方向性電磁鋼板であって、該鋼板の歪導入側のフォルステライト被膜の膜厚Waと歪非導入側のフォルステライト被膜の膜厚Wbの比(Wa/Wb)が0.5以上で、かつ歪導入側の鋼板面における磁区不連続部の平均幅が150~300μm、歪非導入側の鋼板面における磁区不連続部の平均幅が250~500μmである方向性電磁鋼板。
(1) 電子ビーム照射時の真空度を0.1~5Paとする、
(2) 平坦化焼鈍時における鋼板への付与張力を5~15MPaに制御する
方向性電磁鋼板の製造方法。
本発明において、歪み付与を施し、磁区細分化処理済みの方向性電磁鋼板を用いた実機トランスの騒音の増加を抑制するためのポイントは、以下の3つのポイントを全て満足することである。
第1のポイントは、歪を導入した部分のフォルステライト被膜の厚みの制御であり、フォルステライト被膜の厚みの制御が重要な理由は次のとおりである。
鋼板表面のフォルステライト被膜は、鋼板に張力を付与している。このフォルステライト被膜の厚みが変動すると、鋼板の張力分布が不均一になる。張力分布の不均一が生じると、騒音の原因となる鋼板の磁歪振動波形の歪みが発生し、結果的に高調波成分が重畳して騒音の増加を招くこととなる。従って、この騒音増加を抑制するには、熱歪み導入時に発生するフォルステライト被膜の厚みの減少を抑えることが重要である。すなわち、歪導入側のフォルステライト被膜の膜厚Waと歪非導入側のフォルステライト被膜の膜厚Wbの比(Wa/Wb)を0.5以上とする必要がある。好ましくは、0.7以上である。
なお、通常、歪導入前の鋼板両面のフォルステライト被膜の厚みは同程度となる。従ってWa/Wbの最大値は約1である。
まず大事なことは、良好なフォルステライト被膜を形成することである。ここに、良好なフォルステライト被膜とは、被膜中に、割れなどに起因した空隙が少なくて、緻密度の高いフォルステライト被膜のことをいう。また、フォルステライト被膜に割れなどのダメージを与える因子で最も影響が大きいのは、平坦化焼鈍中の鋼板に付与される張力であり、この張力が強いとフォルステライト被膜がダメージを受けて、割れなどが生じてしまう。従って、鋼板温度が高く、張力感受性が高くなる焼鈍炉内では、張力を15MPa(1.5kgf/mm2)以下に制御する必要がある。
第2のポイントは、歪導入側の鋼板面および歪非導入側の鋼板面における磁区不連続部の制御である。
前記のフォルステライト被膜の厚みの制御により、騒音増加はある程度抑制できるが、実機トランスはさらに低騒音かつ低鉄損であることが要求される。
すなわち、トランス鉄損を低くするためには、素材の鉄損低減も大切である。すなわち、素材における磁区細分化効果を十分得るためには、
(i)歪導入側の鋼板面および歪非導入側の鋼板面にも磁区不連続部が生じるまで歪みを導入すること、
(ii)歪み導入は、履歴損の劣化を招くので、磁区不連続部の幅はできる限り狭くすること
が重要である。
なお、前記した第1のポイントである平坦化焼鈍時の最大張力および電子ビーム照射時の真空度を満足していない場合には、フォルステライト被膜の厚みを減少させずに、上記の熱影響幅を満足させるのは極めて困難である。
第3のポイントは、素材結晶粒の磁化容易軸への集積度が高いことである。
変圧器騒音すなわち磁歪振動については、素材結晶粒の磁化容易軸への集積度が高いほど振動振幅が小さくなる。そのため、騒音抑制には、磁化容易軸への集積度の指標ともなる磁束密度B8が1.92T以上であることが必要である。ここに、磁束密度B8が1.92T未満の場合は、磁化過程における励磁磁界と平行になるための磁区の回転運動が大きな磁歪を発生させるので、変圧器の騒音を増大させることとなる。また、集積度が高い方が磁区細分化効果も高くなるので、鉄損低減の観点からも磁束密度B8は1.92T以上である必要がある。
本発明において、方向性電磁鋼板用スラブの成分組成は、二次再結晶が生じる成分組成であればよい。
また、インヒビターを利用する場合、例えばAlN系インヒビターを利用する場合であればAlおよびNを、またMnS・MnSe系インヒビターを利用する場合であればMnとSeおよび/またはSを適量含有させればよい。勿論、両インヒビターを併用してもよい。この場合におけるAl、N、SおよびSeの好適含有量はそれぞれ、Al:0.01~0.065質量%、N:0.005~0.012質量%、S:0.005~0.03質量%、Se:0.005~0.03質量%である。
この場合には、Al、N、SおよびSe量はそれぞれ、Al:100質量ppm以下、N:50質量ppm以下、S:50質量ppm以下、Se:50質量ppm以下に抑制することが好ましい。
C:0.08質量%以下
Cは、熱延板組織の改善のために添加をするが、0.08質量%を超えると製造工程中に磁気時効の起こらない50質量ppm以下までCを低減する負担が増大するため、0.08質量%以下とすることが好ましい。なお、下限に関しては、Cを含まない素材でも二次再結晶が可能であるので特に設ける必要はない。
Siは、鋼の電気抵抗を高め、鉄損を改善するのに有効な元素であり、含有量が2.0質量%以上でとくに鉄損低減効果が良好である。一方、8.0質量%以下の場合、とくに優れた加工性や磁束密度を得ることができる。従って、Si量は2.0~8.0質量%の範囲とすることが好ましい。
Mnは、熱間加工性を良好にする上で有利な元素であるが、含有量が0.005質量%未満ではその添加効果に乏しい。一方1.0質量%以下とすると製品板の磁束密度がとくに良好となる。このため、Mn量は0.005~1.0質量%の範囲とすることが好ましい。
Ni:0.03~1.50質量%、Sn:0.01~1.50質量%、Sb:0.005~1.50質量%、Cu:0.03~3.0質量%、P:0.03~0.50質量%、Mo:0.005~0.10質量%およびCr:0.03~1.50質量%のうちから選んだ少なくとも1種
Niは、熱延板組織をさらに改善して磁気特性を一層向上させるために有用な元素である。しかしながら、含有量が0.03質量%未満では磁気特性の向上効果が小さく、一方1.5質量%以下ではとくに二次再結晶の安定性が増し、磁気特性がさらに改善される。そのため、Ni量は0.03~1.5質量%の範囲とするのが好ましい。
なお、上記成分以外の残部は、製造工程において混入する不可避不純物およびFeである。
その後、圧延方向と直角方向に照射幅:0.15mm、照射間隔:5.0mmにて電子ビームを照射する磁区細分化処理を片面に施し、製品として磁気特性を評価した。一次再結晶焼鈍温度を変更して磁束密度B8値で1.90~1.95Tの材料を得た。また電子ビーム照射についても、ビーム電流値およびビーム走査速度を変更して種々の条件で照射を行った。次いで、各製品を斜角せん断し、500kVAの三相トランスを組み立て、50Hz、1.7Tで励磁した状態での鉄損および騒音を測定した。本トランスにおける鉄損および騒音の設計値は55dB,0.83W/kgである。
上記した鉄損および騒音の測定結果を表1に示す。
これに対し、磁束密度が本発明の範囲を外れたNo.11および12の比較例は、どちらも低騒音性および低鉄損性が共に得られていない。また、(Wa/Wb)が0.5に満たないNo.1~3および10の比較例はいずれも低騒音性が得られていない。さらに、歪導入側または歪非導入側の鋼板面における磁区不連続部の平均幅が本発明の範囲を外れたNo.6,8,9の比較例はいずれも鉄損性が劣っている。
Claims (3)
- 表面にフォルステライト被膜をそなえ、電子ビームにより歪導入を施した、磁束密度B8が1.92T以上の方向性電磁鋼板であって、該鋼板の歪導入側のフォルステライト被膜の膜厚Waと歪非導入側のフォルステライト被膜の膜厚Wbの比(Wa/Wb)が0.5以上で、かつ歪導入側の鋼板面における磁区不連続部の平均幅が150~300μm、歪非導入側の鋼板面における磁区不連続部の平均幅が250~500μmである方向性電磁鋼板。
- 方向性電磁鋼板用スラブを圧延して最終板厚に仕上げたのち、脱炭焼鈍を施し、ついで鋼板表面にMgOを主成分とする焼鈍分離剤を塗布してから、最終仕上げ焼鈍を行った後、張力コーティングを施し、該仕上げ焼鈍後または該張力コーティング後に、電子ビーム照射による磁区細分化処理を行う方向性電磁鋼板の製造方法において、
(1) 電子ビーム照射時の真空度を0.1~5Paとする、
(2) 平坦化焼鈍時における鋼板への付与張力を5~15MPaに制御する
方向性電磁鋼板の製造方法。 - 方向性電磁鋼板用スラブを、熱間圧延し、ついで必要に応じて熱延板焼鈍を施したのち、1回の冷間圧延または中間焼鈍を挟む2回以上の冷間圧延を施して、最終板厚に仕上げる請求項2に記載の方向性電磁鋼板の製造方法。
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- 2011-08-03 MX MX2013000028A patent/MX335959B/es unknown
- 2011-08-03 US US13/814,357 patent/US9330839B2/en active Active
- 2011-08-03 BR BR112013001358-3A patent/BR112013001358B1/pt active IP Right Grant
- 2011-08-03 WO PCT/JP2011/004410 patent/WO2012017655A1/ja active Application Filing
- 2011-08-03 CN CN201180036001.6A patent/CN103025903B/zh active Active
- 2011-08-05 JP JP2011172254A patent/JP5927804B2/ja active Active
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JP2014070975A (ja) * | 2012-09-28 | 2014-04-21 | Jfe Steel Corp | 磁区不連続部検出装置および磁区不連続部検出方法 |
US20160133368A1 (en) * | 2013-06-19 | 2016-05-12 | Jfe Steel Corporation | Grain-oriented electrical steel sheet and transformer iron core using same |
US10559410B2 (en) * | 2013-06-19 | 2020-02-11 | Jfe Steel Corporation | Grain-oriented electrical steel sheet and transformer iron core using same |
US20180066346A1 (en) * | 2015-03-05 | 2018-03-08 | Jfe Steel Corporation | Grain-oriented electrical steel sheet and method for manufacturing same |
US10889880B2 (en) * | 2015-03-05 | 2021-01-12 | Jfe Steel Corporation | Grain-oriented electrical steel sheet and method for manufacturing same |
Also Published As
Publication number | Publication date |
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KR101421388B1 (ko) | 2014-07-18 |
BR112013001358A2 (pt) | 2016-05-17 |
CN103025903A (zh) | 2013-04-03 |
BR112013001358B1 (pt) | 2019-07-02 |
MX2013000028A (es) | 2013-02-01 |
EP2602340A1 (en) | 2013-06-12 |
US20130130043A1 (en) | 2013-05-23 |
EP2602340A4 (en) | 2017-08-02 |
US20160102378A1 (en) | 2016-04-14 |
JP5927804B2 (ja) | 2016-06-01 |
MX335959B (es) | 2016-01-05 |
EP2602340B1 (en) | 2019-06-12 |
KR20130037216A (ko) | 2013-04-15 |
CN103025903B (zh) | 2015-05-06 |
US9330839B2 (en) | 2016-05-03 |
JP2012052230A (ja) | 2012-03-15 |
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