JPH1112700A - Non-oriented electrical sheet having low iron loss - Google Patents
Non-oriented electrical sheet having low iron lossInfo
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- JPH1112700A JPH1112700A JP9186054A JP18605497A JPH1112700A JP H1112700 A JPH1112700 A JP H1112700A JP 9186054 A JP9186054 A JP 9186054A JP 18605497 A JP18605497 A JP 18605497A JP H1112700 A JPH1112700 A JP H1112700A
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- iron loss
- sheet
- oriented electrical
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、電気材料として用
いられるのに好適な、鉄損の低い無方向性電磁鋼板に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a non-oriented electrical steel sheet having a low iron loss and suitable for use as an electrical material.
【０００２】[0002]
【従来の技術】近年、電気機器の省エネルギーの観点よ
り、より鉄損の低い電磁鋼板が求められるようになって
いる。この鉄損を低減するためには結晶粒の粗大化が効
果的であり、低鉄損が特に要求されるSi+Al量が1〜3％
程度の中・高級グレードの無方向性電磁鋼板において
は、仕上焼鈍温度を1000℃程度まで高めたり、焼鈍時の
ラインスピードを下げ、焼鈍時間を長くすることにより
結晶粒の粗大化を図っている。2. Description of the Related Art In recent years, electromagnetic steel sheets having lower iron loss have been demanded from the viewpoint of energy saving of electric equipment. In order to reduce this iron loss, it is effective to make the crystal grains coarse, and the amount of Si + Al, which particularly requires low iron loss, is 1 to 3%.
For medium- and high-grade non-oriented electrical steel sheets of moderate grade, the grain size is increased by increasing the finish annealing temperature to about 1000 ° C, reducing the line speed during annealing, and lengthening the annealing time. .
【０００３】この仕上焼鈍時の粒成長性を良好にするた
めには、鋼板中の介在物、析出物量を低減することが効
果的である。このため、これまで介在物、析出物を無害
化することが試みられており、特に高級材ではMnＳの析
出防止の観点からＳ量を低減させる試みがなされてき
た。In order to improve the grain growth during the finish annealing, it is effective to reduce the amount of inclusions and precipitates in the steel sheet. For this reason, attempts have been made to render the inclusions and precipitates harmless, and particularly in high-grade materials, attempts have been made to reduce the S content from the viewpoint of preventing precipitation of MnS.
【０００４】例えば、特公昭５６−２２９３１号公報に
は、Si：2.5〜3.5％、Al：0.3〜1.0％の鋼においてＳ：
50ppm以下、Ｏ：25ppm以下とすることにより鉄損を低下
させる技術が開示されている。[0004] For example, Japanese Patent Publication No. 56-22931 discloses that in steel containing 2.5% to 3.5% of Si and 0.3% to 1.0% of Al, S:
There is disclosed a technique for reducing iron loss by reducing the content of iron to 50 ppm or less and O: 25 ppm or less.
【０００５】また、特公平２−５０１９０号公報には、
Si：2.5〜3.5％、Al：0.25〜1.0％の鋼においてＳ：15p
pm以下、Ｏ：20ppm以下、Ｎ：25ppm以下とすることによ
り鉄損を低下させる技術が開示されている。In Japanese Patent Publication No. 2-50190,
Si: 2.5-3.5%, Al: 0.25-1.0% steel: S: 15p
There is disclosed a technique for reducing iron loss by setting the pm or less, O: 20 ppm or less, and N: 25 ppm or less.
【０００６】さらに特開平５−１４０６７４号公報に
は、Si：2.0〜4.0％、Al：0.10〜2.0％の鋼において
Ｓ：30ppm以下、Ti、Zr、Nb、Ｖをそれぞれ50ppm以下と
することにより鉄損を低下させる技術が開示されてい
る。Further, Japanese Patent Application Laid-Open No. H5-140674 discloses that, in a steel containing 2.0% to 4.0% of Si and 0.10% to 2.0% of Al, S: 30 ppm or less and Ti, Zr, Nb, and V each being 50 ppm or less. Techniques for reducing iron loss have been disclosed.
【０００７】[0007]
【発明が解決しようとする課題】しかし、これらいずれ
の技術においても、Si、Al量がトータルで3〜3.5％程
度、Ｓ量を10ppm以下とした高級グレードの鋼板の鉄損
値は、Ｗ15/50＝2.4（Ｗ／kg）程度（板厚0.5mm）であ
り、これ以上の低鉄損は達成されていないのが現状であ
る。However, in any of these techniques, the iron loss value of a high-grade steel sheet in which the total amount of Si and Al is about 3 to 3.5% and the amount of S is 10 ppm or less is W 15 / 50 = a 2.4 (W / kg) approximately (thickness 0.5 mm), more low iron loss is has not yet been achieved.
【０００８】本発明はこのような問題点を解決するため
になされたものであり、仕上焼鈍後の鉄損のより低い無
方向性電磁鋼板を提供することを目的とする。The present invention has been made to solve such a problem, and an object of the present invention is to provide a non-oriented electrical steel sheet having lower iron loss after finish annealing.
【０００９】[0009]
【課題を解決するための手段】本発明の骨子は、Ｓ＝10
ppm以下の極低Ｓ材において、Ｐを0.03〜0.15％の範囲
で含有させることにより、無方向性電磁鋼板の鉄損を大
幅に低下させることにある。The gist of the present invention is that S = 10
The present invention is to significantly reduce iron loss of a non-oriented electrical steel sheet by containing P in an extremely low S material of not more than ppm in a range of 0.03 to 0.15%.
【００１０】すなわち、前記課題は、重量％で、Ｃ：0.
005％以下、Si：1.5〜3.5％、Mn：0.05〜1.0％、Ｐ：0.
03〜0.15％、Ｎ：0.005％以下(０を含む)、Al：0.1〜1.
0％、Ｓ：0.001％以下（０を含む）を含有し、残部が実
質的にFeであることを特徴とする鉄損の低い無方向性電
磁鋼板により解決される。[0010] That is, the above-mentioned problem is expressed by:
005% or less, Si: 1.5-3.5%, Mn: 0.05-1.0%, P: 0.
03-0.15%, N: 0.005% or less (including 0), Al: 0.1-1.
The problem is solved by a non-oriented electrical steel sheet having a low iron loss, containing 0% and S: 0.001% or less (including 0), and the balance being substantially Fe.
【００１１】ここに、「残部が実質的にFeである」と
は、不可避不純物の他、本発明の作用効果を妨げない範
囲で他の微量元素を添加したものも、本発明の範囲に含
まれる趣旨である。Here, "the balance is substantially Fe" means that in addition to unavoidable impurities, those to which other trace elements are added within a range not to impair the effects of the present invention are also included in the scope of the present invention. This is the purpose.
【００１２】なお、以下の説明において、鋼の成分を示
す％は全て重量％であり、ppmも重量ppmである。In the following description, all the percentages indicating the components of steel are% by weight, and ppm is also ppm by weight.
【００１３】（発明に至る経緯）本発明者らは、Ｓ＝10
ppm以下の極低Ｓ材において鉄損低減を阻害している要
因を詳細に調査した。その結果、Ｓ量の低減に伴い、鋼
板表層部に顕著な窒化層が認められ、この窒化層が鉄損
低減を阻害していることが明らかとなった。(Circumstances leading to the invention) The present inventors assume that S = 10
Factors that hinder reduction of iron loss in extremely low S materials of less than ppm were investigated in detail. As a result, a remarkable nitrided layer was observed in the surface layer of the steel sheet as the S content was reduced, and it became clear that the nitrided layer hindered the reduction of iron loss.
【００１４】そこで、本発明者らが、窒化を抑制し、鉄
損をさらに低減させる手法に関し鋭意検討した結果、P
を0.03〜0.15％の範囲で添加することにより、極低Ｓ材
の鉄損が大幅に低下することを見いだした。The present inventors have conducted intensive studies on a technique for suppressing nitriding and further reducing iron loss.
It has been found that the iron loss of the extremely low S material is significantly reduced by adding 0.03 to 0.15% in the range.
【００１５】（Ｓ、Ｎの限定理由）本発明を実験結果に
基づいて詳細に説明する。(Reasons for Limiting S and N) The present invention will be described in detail based on experimental results.
【００１６】最初に、鉄損に及ぼすＳの影響を調査する
ため、Ｃ：0.0025％、Si：1.85％、Mn：0.20％、Ｐ：0.
005％、Al：0.31％、Ｎ：0.0018％とし、Ｓ量をtr.〜15
ppmの範囲で変化させた鋼をラボ溶解し、熱延後、酸洗
を行った。引き続きこの熱延板に75％Ｈ2-25％Ｎ2雰囲
気で800℃×３hrの熱延板焼鈍を施し、その後、板厚0.5
mmまで冷間圧延し、10％Ｈ2-90％Ｎ2雰囲気で930℃×２
min間の仕上焼鈍を行った。図１に、このようにして得
られたサンプルのＳ量と鉄損Ｗ15/50の関係を示す（図
中×印）。First, in order to investigate the effect of S on iron loss, C: 0.0025%, Si: 1.85%, Mn: 0.20%, P: 0.
005%, Al: 0.31%, N: 0.0018%, and the S amount is tr.
The steel changed in the ppm range was melted in a laboratory, hot rolled, and then pickled. Subsequently, the hot-rolled sheet was annealed at 800 ° C. for 3 hours in a 75% H 2 -25% N 2 atmosphere, and then the sheet thickness was 0.5
Cold rolled to 930 ° C × 2 in a 10% H 2 -90% N 2 atmosphere
Finish annealing for min was performed. FIG. 1 shows the relationship between the S content of the sample thus obtained and the iron loss W 15/50 (marked by x in the figure).
【００１７】図１より、Ｓを10ppm以下とした場合に大
幅な鉄損低減が達成されＷ15/50＝2.8Ｗ／kgが達成され
ることがわかる。これは、Ｓ低減により粒成長性が向上
したためである。FIG. 1 shows that when S is set to 10 ppm or less, a large reduction in iron loss is achieved and W 15/50 = 2.8 W / kg is achieved. This is because grain growth was improved by reducing S.
【００１８】以上のことより本発明に於いては、Ｓ量の
範囲を10ppm以下、望ましくは5ppm以下に限定する。From the above, in the present invention, the range of S content is limited to 10 ppm or less, preferably 5 ppm or less.
【００１９】しかし、Ｓ量が10ppm以下となると鉄損の
低下は緩やかとなり、Ｓ量をさらに低減したとしても鉄
損は2.7Ｗ／kg程度にしかならない。However, when the S content is less than 10 ppm, the iron loss decreases gradually, and even if the S content is further reduced, the iron loss is only about 2.7 W / kg.
【００２０】本発明者らは、Ｓ≦10ppmの極低Ｓ材にお
いて鉄損の低減が阻害されるのは、MnＳ以外の未知の要
因によるものではないかと考え、光学顕微鏡にて組織観
察を行った。その結果、Ｓ≦10ppmの領域で鋼板表層に
顕著な窒化層が認められた。これに対し、Ｓ＞10ppmの
領域では窒化層は軽微となっていた。この窒化層は窒化
雰囲気で行った熱延板焼鈍時および仕上焼鈍時に生じた
ものと考えられる。The present inventors considered that the reduction of iron loss in the extremely low S material of S ≦ 10 ppm may be caused by unknown factors other than MnS, and observed the structure with an optical microscope. Was. As a result, a remarkable nitride layer was recognized on the surface layer of the steel sheet in the region of S ≦ 10 ppm. In contrast, in the region where S> 10 ppm, the nitrided layer was slight. It is considered that this nitrided layer was formed during hot rolled sheet annealing and finish annealing performed in a nitriding atmosphere.
【００２１】このＳ低減に伴う窒化反応促進の原因に関
しては次のように考えられる。すなわち、Ｓは表面およ
び粒界に濃化しやすい元素であることから、Ｓ＞10ppm
の領域では、Ｓが鋼板表面へ濃化し、熱延板焼鈍時およ
び仕上焼鈍時の窒素の吸着を抑制しており、一方、Ｓ≦
10ppmの領域ではＳによる窒素吸着の抑制効果が低下し
たためと考えられる。The cause of the acceleration of the nitridation reaction accompanying the reduction of S is considered as follows. That is, since S is an element which is easily concentrated on the surface and the grain boundaries, S> 10 ppm
In the region of S, S is concentrated on the surface of the steel sheet to suppress the adsorption of nitrogen during hot-rolled sheet annealing and finish annealing, while S ≦
It is considered that in the 10 ppm region, the effect of suppressing nitrogen adsorption by S was reduced.
【００２２】本発明者らは、この極低Ｓ材において顕著
に生じる窒化層が鋼板表層部の結晶粒の成長を妨げ、鉄
損の低下を抑制するのではないかと考えた。このような
考えの下に、本発明者らは窒素吸着の抑制が可能でかつ
極低Ｓ材の優れた粒成長性を妨げることのない元素を含
有させることができれば、極低Ｓ材の鉄損はさらに低下
するのではないかという着想を抱き、種々の検討を加え
た結果、Ｐの含有が有効であることを発見した。The present inventors have thought that the nitride layer which is remarkably generated in the extremely low S material may hinder the growth of crystal grains in the surface layer portion of the steel sheet and suppress the decrease in iron loss. Under such a concept, the present inventors have proposed that if the element capable of suppressing nitrogen adsorption and containing an element which does not hinder the excellent grain growth of the ultra-low S material can be contained, With the idea that the loss may be further reduced, as a result of various studies, it was found that the content of P was effective.
【００２３】図１に、前記×印で示したサンプルの成分
にＰを添加して0.04％としたサンプルについて同一の条
件で試験をした結果を○印で示す。Ｐの鉄損低減効果に
着目すると、Ｓ＞10ppmの領域では、Ｐ添加により鉄損
は0.02〜0.04Ｗ／kg程度しか低下しないが、Ｓ≦10ppm
の領域では、Ｐ添加により鉄損は0.20Ｗ／kg程度低下し
ており、Ｓ量が少ない場合にＰの鉄損低減効果は顕著に
認められる。また、このサンプルではＳ量によらず窒化
層は認められなかった。これはＰが鋼板表層部に濃化し
窒素の吸着を抑制したためと考えられる。FIG. 1 shows the results of a test conducted under the same conditions for a sample containing 0.04% of P by adding P to the components of the sample shown by the symbol x. Focusing on the iron loss reduction effect of P, in the region of S> 10 ppm, the iron loss is reduced only by about 0.02 to 0.04 W / kg by adding P, but S ≦ 10 ppm
In the region (2), the iron loss is reduced by about 0.20 W / kg by the addition of P, and when the amount of S is small, the iron loss reducing effect of P is remarkably recognized. In this sample, no nitrided layer was observed regardless of the S content. This is presumably because P became concentrated in the surface layer of the steel sheet and suppressed the adsorption of nitrogen.
【００２４】次にＰの最適添加量を調査するため、Ｃ：
0.0020％、Si：1.87％、Mn：0.20％、Al：0.30％、Ｓ：
0.0003％、Ｎ：0.0017％とし、Ｐ量をtr.〜0.20％の範
囲で変化させた鋼をラボ溶解し、熱延後、酸洗を行っ
た。引き続きこの熱延板に75％Ｈ2-25％Ｎ2雰囲気で800
℃×３hrの熱延板焼鈍を施し、その後、板厚0.5mmまで
冷間圧延し、10％Ｈ2-90％Ｎ2雰囲気で930℃×２min間
の仕上焼鈍を行った。図２に、Ｐ量と鉄損Ｗ15/50の関
係を示す。Next, in order to investigate the optimum addition amount of P, C:
0.0020%, Si: 1.87%, Mn: 0.20%, Al: 0.30%, S:
A steel containing 0.0003%, N: 0.0017% and the P content varied in the range of tr. To 0.20% was melted in a laboratory, hot rolled, and then pickled. Continue to apply this hot rolled sheet at 75% H 2 -25% N 2 atmosphere for 800
The sheet was annealed at 300 ° C. for 3 hours, then cold-rolled to a sheet thickness of 0.5 mm, and subjected to finish annealing at 930 ° C. for 2 minutes in a 10% H 2 -90% N 2 atmosphere. FIG. 2 shows the relationship between the P content and the iron loss W 15/50 .
【００２５】図２より、Ｐ添加量が0.03％以上の領域で
鉄損が低下し、Ｗ15/50＝2.5Ｗ／kgが達成されることが
わかる。しかし、Ｐをさらに添加し、Ｐ＞0.10％となっ
た場合には、鉄損は再び増大することもわかる。FIG. 2 shows that the iron loss is reduced in the region where the P content is 0.03% or more, and W 15/50 = 2.5 W / kg is achieved. However, when P is further added and P> 0.10%, the iron loss increases again.
【００２６】このＰ＞0.10％の領域での鉄損増大原因を
調査するため、光学顕微鏡による組織観察を行った。そ
の結果、表層細粒組織は認められなかったものの、平均
結晶粒径が若干小さくなっていた。この原因は明確では
ないが、Ｐが粒界に偏析しやすい元素であるため、Ｐの
粒界ドラッグ効果により粒成長性が低下したものと考え
られる。また、Ｐを0.15％超添加した場合には、冷間圧
延性が著しく低下した。以上のことよりＰは0.03％以上
とし、冷間圧延性の問題から上限を0.15％とする。また
鉄損の観点より、望ましくは0.04％以上、0.10％以下と
する。In order to investigate the cause of the increase in iron loss in the region where P> 0.10%, the structure was observed with an optical microscope. As a result, although the surface layer fine grain structure was not recognized, the average crystal grain size was slightly smaller. Although the cause is not clear, it is considered that since P is an element which is easily segregated at the grain boundary, the grain growth property is reduced by the grain boundary drag effect of P. When P was added in excess of 0.15%, the cold rollability was significantly reduced. From the above, P is set to 0.03% or more, and the upper limit is set to 0.15% from the problem of cold rolling property. From the viewpoint of iron loss, the content is desirably 0.04% or more and 0.10% or less.
【００２７】（その他の成分の限定理由）次に、その他
の成分の限定理由について説明する。(Reasons for Limiting Other Components) Next, reasons for limiting other components will be described.
【００２８】Ｃ： Ｃは磁気時効の問題があるため0.00
5％以下とした。C: C is 0.00% because of the problem of magnetic aging.
5% or less.
【００２９】Si： Siは鋼板の固有抵抗を上げるために
有効な元素であり、このため下限を1.5％とした。一
方、3.5％を超えると飽和磁束密度の低下に伴い磁束密
度が低下するため上限を3.5％とした。Si: Si is an element effective for increasing the specific resistance of the steel sheet, and therefore, the lower limit is set to 1.5%. On the other hand, if it exceeds 3.5%, the magnetic flux density decreases as the saturation magnetic flux density decreases, so the upper limit is set to 3.5%.
【００３０】Mn： Mnは熱間圧延時の赤熱脆性を防止す
るために、0.05％以上必要であるが、1.0％以上になる
と磁束密度を低下させるので0.05〜1.0％とした。Mn: Mn is required to be 0.05% or more in order to prevent red-hot brittleness during hot rolling. However, if it exceeds 1.0%, the magnetic flux density is reduced.
【００３１】Ｎ： Ｎは、含有量が多い場合にはAlＮの
析出量が多くなり、鉄損を増大させるため0.005％以下
とした。N: N is set to 0.005% or less in order to increase the amount of AlN and increase iron loss when the content of N is large.
【００３２】Al： AlはSiと同様、固有抵抗を上げるた
めに有効な元素であるが、1.0％を超えると飽和磁束密
度の低下に伴い磁束密度が低下するため上限を1.0％と
した。また、0.1％未満の場合にはAlＮが微細化し粒成
長性が低下するため下限を0.1％とした。Al: Al, like Si, is an element effective for increasing the specific resistance. However, when the content exceeds 1.0%, the magnetic flux density decreases with a decrease in the saturation magnetic flux density. Therefore, the upper limit is set to 1.0%. If it is less than 0.1%, the lower limit is set to 0.1% because AlN becomes finer and the grain growth is reduced.
【００３３】（製造方法）本発明においては、Ｓ、Ｐが
所定の範囲内であれば、製造方法は通常の無方向性電磁
鋼板の製造方法でかまわない。すなわち、転炉で吹練し
た溶鋼を脱ガス処理し所定の成分に調整し、引き続き鋳
造、熱間圧延を行う。熱間圧延時の仕上焼鈍温度、巻取
り温度は特に規定する必要はなく、通常でかまわない。
また、熱延後の熱延板焼鈍は行っても良いが必須ではな
い。次いで一回の冷間圧延、もしくは中間焼鈍をはさん
だ２回以上の冷間圧延により所定の板厚とした後に、最
終焼鈍を行う。(Manufacturing method) In the present invention, as long as S and P are within a predetermined range, the manufacturing method may be a normal non-oriented electrical steel sheet manufacturing method. That is, the molten steel blown in the converter is degassed and adjusted to a predetermined component, and subsequently casting and hot rolling are performed. The finish annealing temperature and the winding temperature during hot rolling do not need to be particularly specified, and may be normal.
In addition, hot-rolled sheet annealing after hot-rolling may be performed, but is not essential. Next, final cold-rolling or cold-rolling two or more times with intermediate annealing to obtain a predetermined sheet thickness is performed, followed by final annealing.
【００３４】[0034]
【実施例】表１に示す鋼を用い、転炉で吹練した後に脱
ガス処理を行うことにより所定の成分に調整後鋳造し、
スラブを1160℃で１hr加熱した後、板厚2.0mmまで熱間
圧延を行った。熱延仕上げ温度は750℃とした。巻取り
温度は610℃とし、表１に示す条件で熱延板焼鈍を施し
た。その後、板厚0.5mmまで冷間圧延を行い、表１に示
す仕上焼鈍条件で焼鈍を行った。EXAMPLES The steels shown in Table 1 were cast into a given component after being degassed after being blown in a converter,
After the slab was heated at 1160 ° C. for 1 hour, hot rolling was performed to a thickness of 2.0 mm. The hot rolling finishing temperature was 750 ° C. The winding temperature was 610 ° C., and the hot-rolled sheet was annealed under the conditions shown in Table 1. Thereafter, cold rolling was performed to a sheet thickness of 0.5 mm, and annealing was performed under finish annealing conditions shown in Table 1.
【００３５】[0035]
【表１】 [Table 1]
【００３６】磁気測定は25cmエプスタイン試験片を用い
て行った。各鋼板の磁気特性を表１に併せて示す。The magnetic measurement was performed using a 25 cm Epstein test piece. Table 1 also shows the magnetic properties of each steel sheet.
【００３７】表１において、No.１〜12の鋼板は、Siの
レベルが1.8％のオーダににあり、No.13〜16の鋼板は、
Siのレベルが2.5％のオーダにある。同じSiのレベル同
士で比較した場合、本発明鋼の方が、鉄損Ｗ15/50が低
い。In Table 1, the steel sheets of Nos. 1 to 12 have the Si level in the order of 1.8%, and the steel sheets of Nos. 13 to 16
Si levels are on the order of 2.5%. When compared at the same Si level, the steel of the present invention has lower iron loss W15 / 50 .
【００３８】これより、鋼板成分を本発明のＳ、Ｐ量に
制御した場合に、仕上焼鈍後の鉄損の非常に低い無方向
性電磁鋼板が得られることがわかる。From this, it can be seen that a non-oriented electrical steel sheet having extremely low iron loss after finish annealing can be obtained when the steel sheet components are controlled to the S and P contents of the present invention.
【００３９】これに対し、No.５とNo.14の鋼板は、Ｓと
Ｐの範囲が共に本発明の範囲を外れているため、鉄損Ｗ
15/50が高くなっている。On the other hand, in the steel sheets No. 5 and No. 14, since the ranges of S and P are out of the range of the present invention, the iron loss W
15/50 is higher.
【００４０】No.６とNo.15の鋼板は、Ｓの範囲が本発明
の上限を外れているため、Ｗ15/50が高くなっている。The steel sheets No. 6 and No. 15 have high W 15/50 because the range of S is outside the upper limit of the present invention.
【００４１】同様、No.７とNo.16の鋼板は、Ｐの範囲が
本発明の下限を外れているため、Ｗ15/50が高くなって
いる。Similarly, for steel sheets No. 7 and No. 16, W 15/50 is high because the range of P is outside the lower limit of the present invention.
【００４２】No.８の鋼板は、Ｐの範囲が本発明の上限
を外れているため、圧延時に板の破断が発生して製品と
することができなかった。In the steel sheet No. 8, since the range of P was out of the upper limit of the present invention, the sheet was broken at the time of rolling and could not be produced.
【００４３】No.９の鋼板は、Ｃが本発明の範囲を超え
ているので、磁気時効の問題がある。The steel sheet No. 9 has a problem of magnetic aging because C exceeds the range of the present invention.
【００４４】No.10の鋼板は、Mnが本発明の範囲を超え
ているので、磁束密度Ｂ50が小さくなっている。[0044] No.10 steel sheet, since Mn is beyond the scope of the present invention, the magnetic flux density B 50 is small.
【００４５】No.11の鋼板は、Alが本発明の範囲を下回
っているので、鉄損Ｗ15/50が高くなっている。The steel sheet No. 11 has a high iron loss W 15/50 because Al is below the range of the present invention.
【００４６】No.12の鋼板は、Ｎが本発明の範囲を超え
ているので、鉄損Ｗ15/50が大きくなっている。In the steel sheet No. 12, since N exceeds the range of the present invention, the iron loss W 15/50 is large.
【００４７】No.17の鋼板は、Siが本発明の範囲を超え
ているので、鉄損Ｗ15/50は低いが、磁束密度Ｂ50が小
さくなっている。The steel sheet No. 17 has a low iron loss W 15/50 but a small magnetic flux density B 50 because Si exceeds the range of the present invention.
【００４８】[0048]
【発明の効果】以上述べたように、本発明は、重量％
で、Ｃ：0.005％以下、Si：1.5〜3.5％、Mn：0.05〜1.0
％、Ｐ：0.03〜0.15％、Ｎ：0.005％以下(０を含む)、A
l：0.1〜1.0％、Ｓ：0.001％以下（０を含む）を含有
し、残部が実質的にFeであることを特徴とするものであ
るので、鉄損の低い無方向性電磁鋼板を得ることができ
る。As described above, according to the present invention, the weight%
And C: 0.005% or less, Si: 1.5 to 3.5%, Mn: 0.05 to 1.0
%, P: 0.03 to 0.15%, N: 0.005% or less (including 0), A
l: 0.1 to 1.0%, S: 0.001% or less (including 0), and the balance is substantially Fe, so that a non-oriented electrical steel sheet with low iron loss is obtained. be able to.
【００４９】本発明に係る無方向性電磁鋼板は、鉄損が
低いことを要求される電気材料として、トランスの鉄
心、モータのコア等、広く種々の用途に使用することが
できる。The non-oriented electrical steel sheet according to the present invention can be used for a wide variety of applications, such as a transformer core and a motor core, as an electrical material required to have low iron loss.
【図１】Ｓ量と仕上焼鈍後の磁気特性との関係を示す図
である。FIG. 1 is a diagram showing the relationship between the amount of S and magnetic properties after finish annealing.
【図２】Ｐ量と仕上焼鈍後の磁気特性との関係を示す図
である。FIG. 2 is a diagram showing the relationship between the amount of P and magnetic properties after finish annealing.
Claims (1)
3.5％、Mn：0.05〜1.0％、Ｐ：0.03〜0.15％、Ｎ：0.00
5％以下(０を含む)、Al：0.1〜1.0％、Ｓ：0.001％以下
（０を含む）を含有し、残部が実質的にFeであることを
特徴とする鉄損の低い無方向性電磁鋼板。(1) C: 0.005% or less by weight, Si: 1.5 to
3.5%, Mn: 0.05-1.0%, P: 0.03-0.15%, N: 0.00
Non-directionality with low iron loss characterized by containing 5% or less (including 0), Al: 0.1 to 1.0%, S: 0.001% or less (including 0), and the balance being substantially Fe Electrical steel sheet.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9186054A JPH1112700A (en) | 1997-06-27 | 1997-06-27 | Non-oriented electrical sheet having low iron loss |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9186054A JPH1112700A (en) | 1997-06-27 | 1997-06-27 | Non-oriented electrical sheet having low iron loss |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH1112700A true JPH1112700A (en) | 1999-01-19 |
Family
ID=16181597
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9186054A Withdrawn JPH1112700A (en) | 1997-06-27 | 1997-06-27 | Non-oriented electrical sheet having low iron loss |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH1112700A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003002777A1 (en) * | 2001-06-28 | 2003-01-09 | Jfe Steel Corporation | Nonoriented electromagnetic steel sheet |
| KR100514785B1 (en) * | 2000-09-01 | 2005-09-15 | 주식회사 포스코 | A method for manufacturing non-oriented electrical steel sheet having low iron loss |
-
1997
- 1997-06-27 JP JP9186054A patent/JPH1112700A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100514785B1 (en) * | 2000-09-01 | 2005-09-15 | 주식회사 포스코 | A method for manufacturing non-oriented electrical steel sheet having low iron loss |
| WO2003002777A1 (en) * | 2001-06-28 | 2003-01-09 | Jfe Steel Corporation | Nonoriented electromagnetic steel sheet |
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