JPH11233328A - Non-oriented magnetic steel sheet having superior fatigue characteristic - Google Patents
Non-oriented magnetic steel sheet having superior fatigue characteristicInfo
- Publication number
- JPH11233328A JPH11233328A JP10046305A JP4630598A JPH11233328A JP H11233328 A JPH11233328 A JP H11233328A JP 10046305 A JP10046305 A JP 10046305A JP 4630598 A JP4630598 A JP 4630598A JP H11233328 A JPH11233328 A JP H11233328A
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- steel sheet
- less
- fatigue
- flux density
- magnetic flux
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Abstract
Description
【0001】[0001]
【従来の技術】従来における一般の産業用モータにおい
ては、加減速の回数が少ないため、モータのコア材が疲
労破壊を起こすことは少なく、これまで、疲労特性に注
目した電磁鋼板の検討は、なされていなかった。2. Description of the Related Art In conventional general industrial motors, the number of times of acceleration / deceleration is small, so that the core material of the motor rarely causes fatigue failure. Had not been done.
【0002】[0002]
【発明が解決しようとする課題】しかしながら、電気自
動車用モータのような、車の加減速に伴いモータの回転
数が大きく変動するモータにおいては、コア材として使
用される電磁鋼板の疲労特性が優れていることが要求さ
れている。また、一方でモータ高効率化の観点から、高
周波領域で低鉄損であることも求められている。このよ
うな特性は、電気自動車用モータだけでなくインバータ
により可変速運転が行われる高効率エアコン用モータ等
においても要求されている。However, in a motor such as a motor for an electric vehicle, in which the number of revolutions of the motor greatly fluctuates as the vehicle is accelerated or decelerated, the magnetic steel sheet used as a core material has excellent fatigue characteristics. Is required. On the other hand, from the viewpoint of increasing the efficiency of the motor, low iron loss in a high frequency region is also required. Such characteristics are required not only for motors for electric vehicles, but also for motors for high-efficiency air conditioners in which variable speed operation is performed by an inverter.
【0003】疲労特性を向上させるためには、結晶粒の
細粒化が有効であるが、細粒化は鉄損を増大させるため
電磁鋼板における疲労特性の改善手法としては望ましく
ない。このため、磁気特性を劣化させることなく疲労特
性を改善する手法が望まれている。[0003] In order to improve the fatigue properties, it is effective to refine the crystal grains. However, the refinement of the crystal grains increases the iron loss, which is not desirable as a technique for improving the fatigue properties of the magnetic steel sheet. For this reason, a method for improving fatigue characteristics without deteriorating magnetic characteristics is desired.
【0004】本発明は、このような事情に鑑みてなされ
たもので、優れた磁気特性(低鉄損、高磁束密度)を保
ち、かつ疲労特性に優れた無方向性電磁鋼板を提供する
ことを課題とする。The present invention has been made in view of such circumstances, and provides a non-oriented electrical steel sheet which has excellent magnetic properties (low iron loss, high magnetic flux density) and excellent fatigue properties. As an issue.
【0005】[0005]
【課題を解決するための手段】本発明の骨子は、鋼板断
面にて観察される鋼中の5μm以上の粗大な酸化物量を1
0個/mm2以下とすることにより、磁気特性と疲労特性が
共に良好な無方向性電磁鋼板を得ることにある。(ここ
に、個/mm2という単位は、試料を切断、又は研磨して切
断、研磨の表面を観察するとき、試料断面1mm2当たり
に観察される個数を示す。)Means for Solving the Problems The gist of the present invention is to reduce the amount of coarse oxides of 5 μm or more in the steel observed in the cross section of the steel sheet.
An object of the present invention is to obtain a non-oriented electrical steel sheet having good magnetic properties and good fatigue properties by controlling the number to 0 pieces / mm 2 or less. (Here, the unit of “pieces / mm 2 ” indicates the number observed per 1 mm 2 of the cross section of the sample when the sample is cut or polished and the cut and polished surface is observed.)
【0006】すなわち、前記課題は、重量%で、C:0.
005%以下、Si:1.0〜4.0%、Mn:0.05〜1.5%、P:0.
2%以下、N:0.005%以下(0を含む)、Al:0.004%
以下又は0.1〜1.0%、S:0.01%以下(0を含む)を含
有し、残部が実質的にFeからなり、鋼板断面にて観察さ
れる直径5μm以上の酸化物の個数が、10個/mm2以下で
あることを特徴とする疲労特性に優れた無方向性電磁鋼
板により解決される。[0006] That is, the above-mentioned problem is expressed by:
005% or less, Si: 1.0-4.0%, Mn: 0.05-1.5%, P: 0.
2% or less, N: 0.005% or less (including 0), Al: 0.004%
Or 0.1 to 1.0%, S: 0.01% or less (including 0), the balance is substantially composed of Fe, and the number of oxides having a diameter of 5 μm or more observed in the cross section of the steel sheet is 10 / The problem is solved by a non-oriented electrical steel sheet having excellent fatigue characteristics characterized by being not more than mm 2 .
【0007】(発明に至る経緯と酸化物量の限定理由)
本発明者らは、優れた磁気特性(低鉄損、高磁束密度)
を保ち、かつ疲労特性に優れた無方向性電磁鋼板を得る
ために鋭意検討を行った。以下、本発明を実験結果に基
づいて詳細に説明する。(History leading to the invention and reasons for limiting the amount of oxides)
We have excellent magnetic properties (low iron loss, high magnetic flux density)
We studied diligently to obtain non-oriented electrical steel sheet which has excellent fatigue characteristics. Hereinafter, the present invention will be described in detail based on experimental results.
【0008】最初に、高グレード電磁鋼板の疲労限を調
査するため、実機にてC:0.0020%、Si:2.85%、Mn:
0.18%、P:0.01%、S:0.004%、Al:0.30%、N:
0.0021%の成分の鋼を20チャージ溶解し、熱延後、酸洗
し、830℃×3hrの熱延板焼鈍を行い、板厚0.35mmまで
冷間圧延を行った。引き続き10%H2-90%N2雰囲気に
て1000℃×1min間の仕上焼鈍を行った。First, in order to investigate the fatigue limit of a high-grade electrical steel sheet, C: 0.0020%, Si: 2.85%, Mn:
0.18%, P: 0.01%, S: 0.004%, Al: 0.30%, N:
Twenty charges of steel having a composition of 0.0021% were melted, hot-rolled, pickled, hot-rolled at 830 ° C. for 3 hours, and cold-rolled to a thickness of 0.35 mm. Subsequently, finish annealing was performed at 1000 ° C. for 1 minute in a 10% H 2 -90% N 2 atmosphere.
【0009】疲労試験は仕上焼鈍材より平行部の幅5m
m、長さ150mmのサンプルを切り出し、平行部を800番の
エメリー紙で研磨したのち、応力比0.1、周波数20Hzの
部分片振り(引張り-引張り)で行った。その結果、疲
労限は35kgf/mm2〜40kgf/mm2と大きくばらつくことが判
明した。ここで、疲労限は繰り返し数107回において破
壊が生じない応力振幅のことである。In the fatigue test, the width of the parallel portion was 5 m from the finish annealed material.
A sample having a length of 150 mm and a length of 150 mm was cut out, and the parallel portion was polished with No. 800 emery paper, followed by partial pulsating (tensile-tensile) at a stress ratio of 0.1 and a frequency of 20 Hz. As a result, it was found that the fatigue limit varied widely from 35 kgf / mm 2 to 40 kgf / mm 2 . Here, the fatigue limit is that stress amplitude breakdown does not occur in repeated several 10 7 times.
【0010】このように電磁鋼板の疲労限が大きく異な
る原因を調査するため、光学顕微鏡にて鋼板断面の組織
観察を行った。その結果、疲労限の低いサンプルにおい
ては直径5μm以上の粗大な酸化物が多く認められた。
このことから、粗大酸化物の存在が疲労限の低下の原因
ではないかと考えた。そこで、疲労限と5μm以上の粗
大酸化物の個数との関係を調査した。図1にその結果を
示す。図1より、疲労限は、鋼板断面における酸化物量
が10個/mm2以下の場合には高い値を保ち、酸化物量が10
個/mm2を超えた場合に低下することがわかる。これは、
酸化物量が10個/mm2以下の場合には疲労亀裂のイニシエ
ーションサイトが減少したためと考えられる。[0010] In order to investigate the cause of the large difference in the fatigue limit of the magnetic steel sheet, the structure of the cross section of the steel sheet was observed with an optical microscope. As a result, in the sample having a low fatigue limit, many coarse oxides having a diameter of 5 μm or more were observed.
From this, it was considered that the presence of the coarse oxide might be the cause of the decrease in fatigue limit. Therefore, the relationship between the fatigue limit and the number of coarse oxides of 5 μm or more was investigated. FIG. 1 shows the results. From FIG. 1, the fatigue limit maintains a high value when the amount of oxide in the steel sheet cross section is 10 or less / mm 2,
It can be seen that the value decreases when the number of pieces / mm 2 is exceeded. this is,
It is considered that when the amount of oxide was 10 / mm 2 or less, the number of initiation sites for fatigue cracks decreased.
【0011】次に、図1のサンプルの鉄損を測定した結
果を図2に示す。ここで、磁気測定は25cmエプスタイン
法により行った。図2より、鉄損には粗大酸化物の影響
はほとんど認められないことがわかる。これは、このよ
うな粗大酸化物は粒成長性にほとんど影響を及ぼさない
ためである。Next, FIG. 2 shows the result of measuring the iron loss of the sample of FIG. Here, the magnetic measurement was performed by a 25 cm Epstein method. From FIG. 2, it is understood that the influence of the coarse oxide is hardly recognized on the iron loss. This is because such a coarse oxide hardly affects the grain growth.
【0012】以上のことより、鋼板断面にて観察される
5μm以上の粗大酸化物の個数を10個/mm2以下とするこ
とにより、磁気特性を劣化させることなく疲労特性を向
上させることができることがわかる。よって、本発明に
おいては、鋼板断面にて観察される直径5μm以上の酸
化物の個数を、10個/mm2以下に限定する。From the above, it is observed in the cross section of the steel sheet.
It can be seen that by setting the number of coarse oxides of 5 μm or more to 10 / mm 2 or less, fatigue properties can be improved without deteriorating magnetic properties. Therefore, in the present invention, the number of oxides having a diameter of 5 μm or more observed in the cross section of the steel sheet is limited to 10 / mm 2 or less.
【0013】(鋼中成分の含有量の限定理由)次に、鋼
中の成分の含有量の限定理由について説明する。 C: Cは含有量が多い場合には炭化物を形成し、磁気
特性を劣化させるだけでなく疲労特性も劣化させるため
0.005%以下とする。 Si: Siは鋼板の固有抵抗を上げるために有効な元素で
あるため1.0%以上含有させる。一方、4.0%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4.0%とする。 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、1.5%以上になると磁束密度を
低下させるので0.05〜1.5%とする。(Reason for Limiting the Content of Components in Steel) Next, the reason for limiting the content of components in steel will be described. C: When C is contained in a large amount, it forms carbides, which not only deteriorates magnetic properties but also fatigue properties.
0.005% or less. Si: Since Si is an element effective for increasing the specific resistance of the steel sheet, it is contained in an amount of 1.0% or more. On the other hand, if it exceeds 4.0%, the magnetic flux density decreases as the saturation magnetic flux density decreases, so the upper limit is set to 4.0%. Mn: Mn is 0.1% to prevent red hot brittleness during hot rolling.
It is required to be at least 05%, but if it is at least 1.5%, the magnetic flux density will be reduced.
【0014】P: Pは鋼板の打ち抜き性を改善するた
めに必要な元素であるが、0.2%を超えて添加すると鋼
板が脆化するため0.2%以下とする。 N: Nは含有量が多い場合にはAlNの析出量が多くな
り、鉄損を増大させるだけでなく疲労特性も劣化させる
ため0.005%以下とする。 Al: Alは少量添加した場合には、微細なAlNを形成し
結晶粒径の成長を阻害するために磁束密度を低下させ鉄
損も多くなる、このため0.004%以下とする。また0.1%
以上と多く添加した場合には、AlNが粗大化するために
結晶粒径の成長を阻害せず、かつ固有抵抗を上昇させ
る。一方、1%超えでは、磁束密度を低下させるので1%
以下とする。従って、0.004%以下又は0.1〜1%とす
る。P: P is an element necessary for improving the punching property of the steel sheet, but if added in excess of 0.2%, the steel sheet becomes brittle, so that the content is set to 0.2% or less. N: When N content is large, the precipitation amount of AlN increases, and not only increases iron loss but also deteriorates fatigue characteristics, so that the content of N is set to 0.005% or less. Al: When a small amount of Al is added, fine AlN is formed to inhibit the growth of the crystal grain size, so that the magnetic flux density is reduced and the iron loss is increased. 0.1%
When a large amount is added as described above, AlN becomes coarse, so that the growth of the crystal grain size is not hindered, and the specific resistance increases. On the other hand, if it exceeds 1%, the magnetic flux density will decrease, so 1%
The following is assumed. Therefore, the content is set to 0.004% or less or 0.1 to 1%.
【0015】(製造方法)粗大酸化物の個数を所定の範
囲内とする手法はどのようなものでもよいが、例えば、
RHの溶鋼還流時間を長くし、粗大酸化物の浮上分離を
十分に行ってから鋳造を行うことにより達成できる。鋳
造後の製造方法は通常の無方向性電磁鋼板を製造する方
法でかまわない。すなわち、スラブを再加熱後、熱間圧
延を行う。熱間圧延時の仕上温度、巻取り温度は特に規
定する必要はなく、無方向性電磁鋼板を製造する通常の
温度でかまわない。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、仕上焼鈍を行う。(Manufacturing method) Any method may be used for controlling the number of coarse oxides within a predetermined range.
This can be achieved by extending the molten steel reflux time of the RH and sufficiently performing flotation separation of the coarse oxide before casting. The method of manufacturing after casting may be a method of manufacturing a normal non-oriented electrical steel sheet. That is, hot rolling is performed after reheating the slab. The finishing temperature and the winding temperature during hot rolling do not need to be particularly defined, and may be normal temperatures for producing a non-oriented electrical steel sheet. In addition, hot-rolled sheet annealing after hot-rolling may be performed, but is not essential. Next, finish annealing is performed after a predetermined thickness is obtained by one cold rolling or two or more cold rollings sandwiching intermediate annealing.
【0016】[0016]
【実施例】表1に示す鋼(成分値は重量%)を用い、転
炉で吹練した後にRHの還流時間を変化させた鋼を鋳造
し、スラブを1110℃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800℃とした。巻
取り温度は610℃とし、巻取り後、酸洗し830℃×3hrの
熱延板焼鈍を施した。その後、板厚0.35mmまで冷間圧延
を行い、1000℃×2minの仕上焼鈍を行った。EXAMPLES Using the steel shown in Table 1 (component values are% by weight), steel was blown in a converter and the RH reflux time was changed, then the slab was heated at 1110 ° C. for 1 hour. Hot rolling was performed to a thickness of 2.0 mm. The hot rolling finishing temperature was 800 ° C. The winding temperature was 610 ° C., after the winding, pickling was performed, and hot-rolled sheet annealing at 830 ° C. × 3 hours was performed. Thereafter, cold rolling was performed to a sheet thickness of 0.35 mm, and finish annealing at 1000 ° C. for 2 minutes was performed.
【0017】磁気測定は25cmエプスタイン法により行っ
た。疲労試験は平行部の幅5mm、長さ150mmのサンプル
を切り出し、平行部を800番のエメリー紙で研磨したの
ち、応力比0.1、周波数20Hzの部分片振り(引張り-引張
り)で行った。各鋼板の磁気特性および疲労特性を表1
に併せて示す。The magnetic measurement was performed by the 25 cm Epstein method. The fatigue test was performed by cutting out a sample having a parallel portion having a width of 5 mm and a length of 150 mm, polishing the parallel portion with No. 800 emery paper, and performing partial pulsation (tensile-tensile) at a stress ratio of 0.1 and a frequency of 20 Hz. Table 1 shows the magnetic and fatigue properties of each steel sheet.
Are shown together.
【0018】表1より、鋼板成分および酸化物量を本発
明の範囲内に制御した場合(No.1〜No.4の本発明鋼)
に、磁気特性(鉄損と磁束密度)を劣化させることなく
疲労特性に優れた鋼板が得られることがわかる。From Table 1, when the steel sheet composition and the amount of oxide are controlled within the range of the present invention (No. 1 to No. 4 of the present invention)
In addition, it can be seen that a steel sheet having excellent fatigue properties can be obtained without deteriorating the magnetic properties (iron loss and magnetic flux density).
【0019】これに対し、No.5の鋼板は、酸化物量が
本発明の範囲を超えているので、疲労限が低くなってい
る。No.6の鋼板は、C含有量が本発明の範囲を超えて
いるので、疲労限が低くなると共に、鉄損が高く、磁束
密度が低くなっている。No.7の鋼板は、Si含有量が本
発明の範囲を超えているために、疲労限がやや低くな
り、磁束密度が極端に低くなっている。No.8の鋼板
は、Mn含有量が本発明の範囲を超えているために、疲労
限は本発明鋼なみであるが、磁束密度が低くなってい
る。On the other hand, the steel sheet No. 5 has a low fatigue limit because the amount of oxides exceeds the range of the present invention. Since the C content exceeds the range of the present invention, the steel sheet of No. 6 has a low fatigue limit, a high iron loss, and a low magnetic flux density. No. 7 steel sheet has a slightly lower fatigue limit and extremely low magnetic flux density because the Si content exceeds the range of the present invention. The steel sheet of No. 8 has a fatigue limit similar to that of the steel of the present invention because the Mn content exceeds the range of the present invention, but has a low magnetic flux density.
【0020】No.9の鋼板は、Al含有量が本発明の範囲
を下回っているために、疲労限は本発明鋼なみであるが
鉄損が高く、磁束密度が低くなっている。No.10の鋼板
は、Al含有量が本発明の範囲を超えているために、疲労
限は本発明鋼なみであるが、磁束密度が低くなってい
る。No.11の鋼板は、S含有量が本発明の範囲を超えて
いるため、疲労限がやや低く、鉄損が高く、かつ磁束密
度が低くなっている。No.12の鋼板は、N含有量が本発
明の範囲を超えているため、疲労限がやや低く、鉄損が
高く、かつ磁束密度が低くなっている。[0020] The steel sheet No. 9 has a fatigue limit similar to that of the steel of the present invention but a high iron loss and a low magnetic flux density because the Al content is below the range of the present invention. The steel sheet No. 10 has a fatigue limit similar to that of the steel of the present invention because the Al content exceeds the range of the present invention, but has a low magnetic flux density. Since the S content exceeds the range of the present invention, the steel sheet No. 11 has a slightly lower fatigue limit, a higher iron loss, and a lower magnetic flux density. Since the N content exceeds the range of the present invention, the steel sheet No. 12 has a slightly lower fatigue limit, a higher iron loss, and a lower magnetic flux density.
【0021】[0021]
【表1】 [Table 1]
【0022】[0022]
【発明の効果】以上説明したように、本発明に係る無方
向性電磁鋼板は、重量%で、C:0.005%以下、Si:1.0
〜4.0%、Mn:0.05〜1.5%、P:0.2%以下、N:0.005
%以下(0を含む)、Al:0.004%以下又は0.1〜1.0
%、S:0.01%以下(0を含む)を含有し、残部が実質
的にFeからなり、鋼板断面にて観察される直径5μm以
上の酸化物の個数が、10個/mm2以下であることを特徴と
するものであるので、優れた磁気特性(低鉄損、高磁束
密度)を保ち、かつ疲労特性に優れている。As described above, the non-oriented electrical steel sheet according to the present invention has a C content of 0.005% or less and a Si content of 1.0% by weight.
-4.0%, Mn: 0.05-1.5%, P: 0.2% or less, N: 0.005
% Or less (including 0), Al: 0.004% or less or 0.1 to 1.0
%, S: 0.01% or less (including 0), the balance is substantially composed of Fe, and the number of oxides having a diameter of 5 μm or more observed in the cross section of the steel plate is 10 / mm 2 or less. Therefore, it has excellent magnetic properties (low iron loss, high magnetic flux density) and excellent fatigue properties.
【0023】この無方向性電磁鋼板は、電気自動車用モ
ータのコア材等、優れた疲労特性を必要とする電気材料
に広く使用するのに好適である。This non-oriented electrical steel sheet is suitable for being widely used for electrical materials requiring excellent fatigue properties, such as core materials for electric vehicle motors.
【図1】 酸化物量と疲労限との関係を示す図である。FIG. 1 is a diagram showing the relationship between the amount of oxide and the fatigue limit.
【図2】 酸化物量と鉄損との関係を示す図である。FIG. 2 is a diagram showing a relationship between an oxide amount and iron loss.
Claims (1)
4.0%、Mn:0.05〜1.5%、P:0.2%以下、N:0.005%
以下(0を含む)、Al:0.004%以下又は0.1〜1.0%、
S:0.01%以下(0を含む)を含有し、残部が実質的に
Feからなり、鋼板断面にて観察される直径5μm以上の
酸化物の個数が、10個/mm2以下であることを特徴とする
疲労特性に優れた無方向性電磁鋼板。C .: 0.005% or less by weight, Si: 1.0 to
4.0%, Mn: 0.05-1.5%, P: 0.2% or less, N: 0.005%
Or less (including 0), Al: 0.004% or less or 0.1 to 1.0%,
S: 0.01% or less (including 0) is contained, and the balance is substantially
A non-oriented electrical steel sheet having excellent fatigue properties, characterized in that the number of oxides having a diameter of 5 μm or more and observed in a steel sheet cross section is 10 or less / mm 2 .
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10046305A JPH11233328A (en) | 1998-02-13 | 1998-02-13 | Non-oriented magnetic steel sheet having superior fatigue characteristic |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10046305A JPH11233328A (en) | 1998-02-13 | 1998-02-13 | Non-oriented magnetic steel sheet having superior fatigue characteristic |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH11233328A true JPH11233328A (en) | 1999-08-27 |
Family
ID=12743493
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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JP10046305A Pending JPH11233328A (en) | 1998-02-13 | 1998-02-13 | Non-oriented magnetic steel sheet having superior fatigue characteristic |
Country Status (1)
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JP (1) | JPH11233328A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPWO2021084785A1 (en) * | 2019-10-29 | 2021-05-06 |
-
1998
- 1998-02-13 JP JP10046305A patent/JPH11233328A/en active Pending
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPWO2021084785A1 (en) * | 2019-10-29 | 2021-05-06 | ||
WO2021084785A1 (en) * | 2019-10-29 | 2021-05-06 | Jfeスチール株式会社 | Non-oriented electromagnetic steel sheet and method for producing same |
CN114555848A (en) * | 2019-10-29 | 2022-05-27 | 杰富意钢铁株式会社 | Non-oriented electromagnetic steel sheet and method for producing same |
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