JP6192291B2 - Non-oriented electrical steel sheet for spiral core and manufacturing method thereof - Google Patents
Non-oriented electrical steel sheet for spiral core and manufacturing method thereof Download PDFInfo
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Description
自動車用交流発電機（オルタネータ）などのステータには、鋼板をヘリカル加工により平面曲げし、とぐろ状に巻き積層する「らせんコア」が使われることが多い。本発明は、らせんコアに適した無方向性電磁鋼板に関するものである。 A stator such as an alternator for automobiles is often used with a “spiral core” in which a steel plate is bent in a plane by helical processing and wound in a round shape. The present invention relates to a non-oriented electrical steel sheet suitable for a helical core.
らせんコア用無方向性電磁鋼板に関し、従来次のような技術が提案されている。
特許文献１には、らせんコアの鉄損を向上させるため、素材として従来使われてきた冷延鋼板に変えて無方向性電磁鋼板を使うことが提案されている。しかし、スキンパス圧延を施した状態で使用するため、鉄損は通常の無方向性電磁鋼板に比べて劣位である。
これに対して特許文献２には、スキンパス圧延の伸び率を低く限定し、鉄損と加工性を改善する提案がなされている。しかしスキンパス圧延による鉄損劣化は依然として課題となっている。
The following technologies have been proposed for non-oriented electrical steel sheets for spiral cores.
On the other hand,
本発明は、上記従来技術に鑑み、ヘリカル加工性が良好で、かつ低い鉄損をもつ無方向性電磁鋼板を提供することを目的とする。 In view of the above prior art, an object of the present invention is to provide a non-oriented electrical steel sheet having good helical workability and low iron loss.
本発明は、鋼板の成分組成と組織制御により、降伏応力ＹＰ、引張強さＴＳ、降伏比ＹＲ（ＹＰ／ＴＳ）、伸びＥＬの機械的特性をヘリカル加工に適した特性範囲とし、同時に低い鉄損を満足したものである。
その要旨は下記の通りである。
According to the present invention, the mechanical properties of the yield stress YP, tensile strength TS, yield ratio YR (YP / TS) , and elongation EL are set in the characteristic range suitable for the helical processing, and at the same time, low iron The loss is satisfied.
The summary is as follows.
（１）質量％で、Ｃ：０〜０．０１％、Ｓｉ：０．５〜１．１％、Ａｌ：０〜０．７％、Ｓｉ＋Ａｌ：０．６〜１．１％、Ｍｎ：０．０５〜０．６％を含有し、残部Ｆｅおよび不可避不純物からなり、金属組織がフェライト単相組織であり、前記フェライト相の平均結晶粒径が１０〜６０μｍであり、降伏応力ＹＰ：３２０ＭＰａ以下、引張強さＴＳ：４００ＭＰａ以下、降伏比ＹＲ（ＹＰ／ＴＳ）：０．８２以下、伸びＥＬ：３０〜４０％であることを特徴とするらせんコア用無方向性電磁鋼板。
（２）前記（１）に記載の成分組成を有する熱延板を冷延後、再結晶焼鈍する電磁鋼板の製造方法において、再結晶焼鈍を７００〜９００℃の温度範囲で、かつ、次式で決められるＬＭＰを１７０００〜２１０００の範囲で行うことを特徴とする前記（１）に記載の無方向性電磁鋼板の製造方法。
ＬＭＰ＝Ｔ×（２０＋Ｌｏｇ（ｔ））
ここで、Ｔ：焼鈍温度（Ｋ）、ｔ：焼鈍時間（時間）である。
(1) By mass%, C: 0 to 0.01%, Si: 0.5 to 1.1%, Al: 0 to 0.7%, Si + Al: 0.6 to 1.1%, Mn: 0 0.05 to 0.6%, the balance being Fe and unavoidable impurities, the metal structure being a ferrite single phase structure, the average crystal grain size of the ferrite phase being 10 to 60 μm, and the yield stress YP: 320 MPa or less A non-oriented electrical steel sheet for a spiral core, characterized by tensile strength TS: 400 MPa or less, yield ratio YR (YP / TS): 0.82 or less , and elongation EL: 30 to 40% .
(2) In the manufacturing method of the electrical steel sheet which carries out recrystallization annealing after cold-rolling the hot-rolled sheet which has a component composition as described in said (1), recrystallization annealing is 700-900 degreeC, and following Formula The method for producing a non-oriented electrical steel sheet according to the above (1) , wherein the LMP determined by 1 is performed in the range of 17000 to 21000.
LMP = T × (20 + Log (t))
Here, T: annealing temperature (K), t: annealing time (hour).
本発明によれば、ヘリカル加工性が良好で、かつ低い鉄損をもつ無方向性電磁鋼板を提供することができる。 ADVANTAGE OF THE INVENTION According to this invention, the non-oriented electrical steel sheet which has favorable helical workability and has a low iron loss can be provided.
以下、本発明を構成する要件について順次説明する。
＜成分組成＞
本発明の無方向性電磁鋼板の成分組成の限定理由について説明する。以下で含有量の％は、質量％を意味する。
（Ｃ：０〜０．０１％）
Ｃは鉄損を劣化させ、磁気時効の原因にもなる有害な元素なので、上限を０．０１％とし、下限を０％とする。好ましくは０〜０．００５％以下である。
（Ｓｉ：０．１〜２．０％）
Ｓｉは脱酸剤として有効であり、鋼の固有抵抗を増加させ鉄損を低下させるため、０．１％以上が必要である。一方、多すぎると磁束密度が低下するため、上限を２．０％とする。最適な範囲は０．１〜２．０％であり、好ましくは０．５〜１．０％である。なお、特許請求の範囲では、Ｓｉの下限を好ましい値の０．５％とし、上限をＳｉ＋Ａｌ量の上限から求められる１．１％とした。
Hereinafter, requirements constituting the present invention will be sequentially described.
<Ingredient composition>
The reason for limiting the component composition of the non-oriented electrical steel sheet of the present invention will be described. Below,% of content means the mass%.
(C: 0 to 0.01%)
C is a harmful element that deteriorates iron loss and causes magnetic aging, so the upper limit is made 0.01% and the lower limit is made 0%. Preferably it is 0 to 0.005% or less.
(Si: 0.1-2.0%)
Since Si is effective as a deoxidizer and increases the specific resistance of steel and lowers iron loss, 0.1% or more is necessary. On the other hand, if the amount is too large, the magnetic flux density decreases, so the upper limit is made 2.0%. The optimum range is 0.1 to 2.0%, preferably 0.5 to 1.0%. In the claims, the lower limit of Si is set to 0.5% of a preferable value, and the upper limit is set to 1.1% obtained from the upper limit of the amount of Si + Al.
（Ａｌ：０〜０．７％）
Ａｌも脱酸剤として有効であり、固有抵抗を増加させるので、添加してもよい。しかし磁束密度の低下にはＳｉよりも影響が大きい。また理由は不明であるが、Ａｌ量が増えると降伏比が大きくなる傾向がある。従ってＡｌの範囲を０〜０．７％とする。好ましくは０〜０．３％である。
(Al: 0 to 0.7%)
Al is also effective as a deoxidizing agent and increases the specific resistance, so it may be added. However, the effect of lowering the magnetic flux density is greater than that of Si. The reason is unknown, but the yield ratio tends to increase as the Al content increases. Therefore, the range of Al is made 0 to 0.7%. Preferably it is 0 to 0.3%.
（Ｓｉ＋Ａｌ：０．３〜２．５％）
ＳｉとＡｌは上記の作用の他に、降伏応力ＹＰや引張強さＴＳなどの機械的強度を高め、降伏比ＹＲ（ＹＰ／ＴＳ）にも影響を与える。図1〜３に、フェライト粒の平均結晶粒径が２０μmである場合の、ＳｉとＡｌの合計添加量（Ｓｉ＋Ａｌ）とＹＰ、ＴＳ、ＹＲとの関係を示す。
後述するが、良好なヘリカル加工性を持つには、ＹＰ、ＴＳ、ＹＲがそれぞれ３２０ＭＰａ以下、４００ＭＰａ以下、０．８２以下を満足することが必要である。これらの条件を満足させるＳｉ＋Ａｌ量は、図1〜３の場合、ＹＰでは１．８％以下、ＴＳでは１．１％以下、ＹＲでは０．６％以上である。
このように、良好なヘリカル加工性を得るにはＳｉ＋Ａｌ量には適正な範囲があることが確認されたので、フェライト粒の平均結晶粒径が他の場合についても、さらに検討した結果、Ｓｉ＋Ａｌを０．３〜２．５％の範囲にするとよいことが確認された。より好ましいＳｉ＋Ａｌの範囲は０．５〜１．５％であり、更に好ましくは０．５〜１．０％である。なお、特許請求の範囲では、上記ＴＳ、ＹＲについての記載に基づき０．６〜１．１％とした。
(Si + Al: 0.3-2.5%)
In addition to the above-described effects, Si and Al increase mechanical strength such as yield stress YP and tensile strength TS, and affect the yield ratio YR (YP / TS). 1 to 3 show the relationship between the total addition amount of Si and Al (Si + Al) and YP, TS, and YR when the average grain size of ferrite grains is 20 μm.
As will be described later, in order to have good helical workability, it is necessary that YP, TS, and YR satisfy 320 MPa or less, 400 MPa or less, and 0.82 or less, respectively. In the case of FIGS. 1 to 3, the amount of Si + Al that satisfies these conditions is 1.8% or less for YP, 1.1% or less for TS, and 0.6% or more for YR.
As described above, since it was confirmed that there is an appropriate range for the amount of Si + Al in order to obtain good helical workability, further investigation was conducted even when the average crystal grain size of the ferrite grains was other than that. It was confirmed that the content should be in the range of 0.3 to 2.5%. A more preferable range of Si + Al is 0.5 to 1.5%, still more preferably 0.5 to 1.0%. In the claims, the content is set to 0.6 to 1.1% based on the description of the TS and YR.
（Ｍｎ：０．０５〜０．６％）
Ｍｎは熱間加工性の改善や硫化物の粗大化にも効果があるため下限を０．０５％とし、過剰な添加はコスト増になるため、Ｍｎの範囲を０．０５〜０．６％とする。好ましくは０．１〜０．３％である。
(Mn: 0.05-0.6%)
Since Mn is effective in improving hot workability and coarsening of sulfides, the lower limit is set to 0.05%, and excessive addition increases costs, so the Mn range is 0.05 to 0.6%. And Preferably it is 0.1 to 0.3%.
（その他の成分）
前記以外のその他の元素は特に規定しないが、下記の様に制御することが有効であることを確認している。
Ｐは打ち抜きのかえりの防止に効果があるが、凝固偏析によって鉄損が劣化しやすいため０．１％以下が好ましい。
Ｓ、Ｎ、ＯおよびＴｉ、Ｎｂ、Ｖ、Ｚｒ、Ｍｇなどは析出物を形成して鉄損を劣化させるので、すべて０．０１％以下が好ましい。
またＳを無害化させるべく、Ｃａ、ＲＥＭなどの添加（約０．０００５〜０．００５％）により、粗大なオキシサルファイドを鋳造での冷却段階で析出させる公知の技術を採用することも有効である。
さらに磁気特性を改善するためにＣｕ、Ｓｎ、Ｓｂ、Ｎｉ、Ｃｒ、Ｂなどを添加しても良いが、添加コストの面から０．５％以下が好ましい。
(Other ingredients)
Other elements other than the above are not particularly defined, but it has been confirmed that the following control is effective.
P is effective in preventing punching burr, but is preferably 0.1% or less because iron loss is likely to deteriorate due to solidification segregation.
Since S, N, O and Ti, Nb, V, Zr, Mg, etc. form precipitates and deteriorate iron loss, all are preferably 0.01% or less.
In order to render S harmless, it is also effective to adopt a known technique in which coarse oxysulfide is precipitated at the cooling stage in casting by adding Ca, REM, etc. (about 0.0005 to 0.005%). is there.
Further, Cu, Sn, Sb, Ni, Cr, B or the like may be added to improve the magnetic characteristics, but 0.5% or less is preferable from the viewpoint of the addition cost.
＜鋼板組織＞
本発明の鋼板の組織は、未再結晶組織を含まないフェライト単相組織とし、その平均粒径を１０μｍ〜６０μｍとする。未再結晶組織を含んだり、平均粒径が１０μm未満だったりすると、鉄損が劣化し、ＹＰ、ＴＳ、ＹＲも上昇する。６０μｍより大きくなると、ヘリカル加工性が劣化する。更に打ち抜きの際、端面のダレも大きくなる。好ましくは１０〜３０μｍである。
<Steel structure>
The structure of the steel sheet of the present invention is a ferrite single-phase structure that does not include an unrecrystallized structure, and the average particle size is 10 μm to 60 μm. If an unrecrystallized structure is included or the average particle size is less than 10 μm, the iron loss deteriorates and YP, TS, and YR also increase. If it exceeds 60 μm, the helical processability deteriorates. Further, when punching, the sagging of the end surface increases. Preferably it is 10-30 micrometers.
＜機械的特性＞
機械的特性とヘリカル加工性との関係を次のような試験を行って評価して、ヘリカル加工性を確保するために必要な機械的特性の要件を得た。
まず、機械特性の異なる無方向性電磁鋼板のヘリカル加工性を評価するために、鋼板から幅１０ｍｍ、長さ１０００ｍｍの試料を切り出し、直径３００ｍｍの丸鋼に１ターンをヘリカル巻きつけし、外周または内周に発生したしわの個数をカウントした。
<Mechanical properties>
The relationship between mechanical properties and helical workability was evaluated by conducting the following tests to obtain the requirements for mechanical properties necessary to ensure helical workability.
First, in order to evaluate the helical workability of non-oriented electrical steel sheets having different mechanical properties, a sample having a width of 10 mm and a length of 1000 mm is cut out from the steel sheet, and one turn is helically wound around a round steel having a diameter of 300 mm. The number of wrinkles that occurred on the inner circumference was counted.
含有成分とフェライト結晶粒径を調整して機械特性変化させた場合の、ＹＰ、ＴＳとしわの数の関係を図４、５に示す。ＹＰ、ＴＳが小さくなるほどしわの数は少なく、ヘリカル加工性が良好になることが分かる。これらの図から、良好なヘリカル加工性を得るために、鋼板の降伏点ＹＰを３２０ＭＰａ以下、引張強さＴＳ４００ＭＰａ以下とする。ただし加工時の座屈防止の観点からＹＰは２５０ＭＰａ以上、ＴＳは３５０ＭＰａ以上が好ましい。また、伸びＥＬは、大きい方がヘリカル加工性は良くなるので３０％以上とする。大きすぎると打ち抜き時のダレが大きくなるので、４０％以下とする。
FIGS. 4 and 5 show the relationship between YP, TS, and the number of wrinkles when the mechanical properties are changed by adjusting the contained component and the ferrite crystal grain size. It can be seen that the smaller YP and TS, the smaller the number of wrinkles and the better the helical processability. From these figures, in order to obtain good helical workability, the yield point YP of the steel sheet is set to 320 MPa or less and the tensile strength TS is 400 MPa or less. However, from the viewpoint of preventing buckling during processing, YP is preferably 250 MPa or more, and TS is preferably 350 MPa or more. Further, the elongation EL is 30% or more because the larger helical workability is improved. Since too large sag during punching increases to 40% or less.
次に、０．００３％Ｃ、０．７％Ｓｉ、０．２％Ｍｎ、Ａｌ-ｔｒの成分組成を持つ鋼を用いて結晶粒径を変化させ降伏比の異なる鋼板を用意しヘリカル加工性を評価した。ＹＰは２９０〜３２０ＭＰa、ＴＳは３５０〜４００ＭＰaの範囲で降伏比ＹＲを変化させることができた。ＹＲとしわの数の変化を図６に示す。降伏比ＹＲは０．８２以下とすることで、しわの数は顕著に減少し、加工性が良好となるので、本発明においては、降伏比を０．８２以下とする。一方小さすぎると、打ち抜き時のダレが大きくなるので０．６５以上が好ましい。 Next, using steel with a composition of 0.003% C, 0.7% Si, 0.2% Mn, and Al-tr, steel sheets with different yield ratios are prepared by changing the grain size, and helical workability Evaluated. Yield ratio YR could be changed in the range of 290 to 320 MPa for YP and 350 to 400 MPa for TS. The change in the number of YRs and wrinkles is shown in FIG. By setting the yield ratio YR to 0.82 or less, the number of wrinkles is remarkably reduced and the workability is improved. Therefore, in the present invention, the yield ratio is 0.82 or less. On the other hand, if it is too small, sagging at the time of punching becomes large, so 0.65 or more is preferable.
＜製造方法＞
本発明の無方向電磁鋼板の製造方法は下記の通りである。
先に示した鋼組成を有するスラブに対して熱間圧延を施し、酸洗、冷間圧延を施し、その後再結晶のための仕上げ焼鈍を施す。仕上げ焼鈍以外は一般的な無方向性電磁鋼板の製造方法で製造できる。仕上げ焼鈍は結晶粒径の均一化のために連続焼鈍で行うことが好ましく、鋼板組織を粒径１０〜６０μｍのフェライト単相とするため、温度は７００〜９００℃とする。ただしバッチ焼鈍も可能であり、その場合、次式で決められるＬＭＰを１７０００〜２１０００の範囲に制御することで、最適な結晶粒径を得ることができる。
ＬＭＰ＝Ｔ×（２０＋Ｌｏｇ（ｔ））
ここで、Ｔ：焼鈍温度（Ｋ）、ｔ：焼鈍時間（時間）である。
その後、通常の絶縁皮膜を塗布乾燥してもよいし、コスト面から省略することも可能である。
<Manufacturing method>
The manufacturing method of the non-oriented electrical steel sheet of the present invention is as follows.
The slab having the steel composition shown above is hot-rolled, pickled and cold-rolled, and then subjected to finish annealing for recrystallization. Except for finish annealing, it can be manufactured by a general method for manufacturing non-oriented electrical steel sheets. The finish annealing is preferably performed by continuous annealing to make the crystal grain size uniform, and the temperature is set to 700 to 900 ° C. in order to make the steel sheet structure a ferrite single phase having a grain size of 10 to 60 μm. However, batch annealing is also possible, and in that case, an optimal crystal grain size can be obtained by controlling the LMP determined by the following formula within a range of 17000 to 21000.
LMP = T × (20 + Log (t))
Here, T: annealing temperature (K), t: annealing time (hour).
Thereafter, a normal insulating film may be applied and dried, or may be omitted from the viewpoint of cost.
以下、実施例により本発明の実施可能性及び効果についてさらに示す。
＜実施例１＞
表１に示す各種成分を含有する鋼塊を供試材として、加熱温度を１１５０℃として熱延を行い、２．５ｍｍ厚の熱延板を得た。この熱延板を酸洗し、冷延して０．５ｍｍとした。脱脂してから、８５０℃で３０秒均熱の連続焼鈍を施し、電磁鋼板を得た。
得られた電磁鋼板の粒径はＪＩＳ Ｇ ０５５２に基づき測定した。磁気測定は、Ｌ、Ｃ方向に５５ｍｍ×５５ｍｍの単板試料を切り出し、ＪＩＳ Ｃ ２５５６に基づき行った。引張試験は、Ｌ、Ｃ方向にＪＩＳ５号試験片を切り出し、ＪＩＳ Ｚ ２２４１に基づき行った。またヘリカル加工性を評価するために、鋼板から幅１０ｍｍ、長さ１０００ｍｍの試料を切り出し、直径３００ｍｍの丸鋼に１ターンをヘリカル巻きつけし、外周または内周に発生したしわの個数をカウントした。結果を表１に示す。機械特性、磁気特性はＬＣの平均値である。
本発明例においては、良好なヘリカル加工性と低い鉄損が同時に得られる。
The following examples further illustrate the feasibility and effects of the present invention.
<Example 1>
Using a steel ingot containing various components shown in Table 1 as a test material, hot rolling was performed at a heating temperature of 1150 ° C. to obtain a 2.5 mm thick hot rolled sheet. This hot-rolled sheet was pickled and cold-rolled to 0.5 mm. After degreasing, continuous annealing was performed at 850 ° C. for 30 seconds to obtain a magnetic steel sheet.
The particle size of the obtained electrical steel sheet was measured based on JIS G 0552. Magnetic measurement was performed based on JIS C 2556 by cutting out a single plate sample of 55 mm × 55 mm in the L and C directions. The tensile test was performed based on JIS Z 2241 by cutting out JIS No. 5 test pieces in the L and C directions. In addition, in order to evaluate the helical workability, a sample having a width of 10 mm and a length of 1000 mm was cut out from a steel plate, wound one turn on a round steel having a diameter of 300 mm, and the number of wrinkles generated on the outer periphery or the inner periphery was counted. . The results are shown in Table 1. Mechanical properties and magnetic properties are average values of LC.
In the example of the present invention, good helical workability and low iron loss can be obtained at the same time.
＜実施例２＞
質量％で、Ｃ：０．００３％、Ｓｉ：０．７％、Ｍｎ：０．１８％、Ｐ：０．０７３％、Ａｌ：０．００１％の成分組成の鋼塊を供試材として、加熱温度１１５０℃の熱延を行い、２．５ｍｍ厚の熱延板を得た。この熱延板を酸洗し、冷延して０．５ｍｍとした。脱脂してから、表２に示す条件で仕上げ焼鈍を行った。実施例１と同様に粒径、磁気特性、機械的特性、ヘリカル加工性を評価した。結果を表２に示す。
本発明例においては、良好なヘリカル加工性と低い鉄損が同時に得られる。
<Example 2>
A steel ingot having a component composition of C: 0.003%, Si: 0.7%, Mn: 0.18%, P: 0.073%, Al: 0.001% in mass% was used as a test material. Hot rolling was performed at a heating temperature of 1150 ° C. to obtain a 2.5 mm thick hot rolled sheet. This hot-rolled sheet was pickled and cold-rolled to 0.5 mm. After degreasing, finish annealing was performed under the conditions shown in Table 2. Similar to Example 1, the particle size, magnetic properties, mechanical properties, and helical processability were evaluated. The results are shown in Table 2.
In the example of the present invention, good helical workability and low iron loss can be obtained at the same time.
Claims (2)
Ｃ：０〜０．０１％、
Ｓｉ：０．５〜１．１％、
Ａｌ：０〜０．７％、
Ｓｉ＋Ａｌ：０．６〜１．１％、
Ｍｎ：０．０５〜０．６％
を含有し、残部Ｆｅおよび不可避不純物からなり、金属組織がフェライト単相組織であり、前記フェライト相の平均結晶粒径が１０〜６０μｍであり、降伏応力ＹＰ：３２０ＭＰａ以下、引張強さＴＳ：４００ＭＰａ以下、降伏比ＹＲ（ＹＰ／ＴＳ）：０．８２以下、伸びＥＬ：３０〜４０％であることを特徴とするらせんコア用無方向性電磁鋼板。 % By mass
C: 0 to 0.01%
Si: 0.5 to 1.1%
Al: 0 to 0.7%,
Si + Al: 0.6 to 1.1%
Mn: 0.05 to 0.6%
The balance is composed of Fe and unavoidable impurities, the metal structure is a ferrite single phase structure, the average crystal grain size of the ferrite phase is 10 to 60 μm, the yield stress YP: 320 MPa or less, the tensile strength TS: 400 MPa A non-oriented electrical steel sheet for a spiral core, characterized in that the yield ratio YR (YP / TS) is 0.82 or less and the elongation EL is 30 to 40% .
ＬＭＰ＝Ｔ×（２０＋Ｌｏｇ（ｔ））
ここで、Ｔ：焼鈍温度（Ｋ）、ｔ：焼鈍時間（時間）である。 In the manufacturing method of the electrical steel sheet which carries out recrystallization annealing after cold-rolling the hot-rolled sheet which has the component composition of the said Claim 1, recrystallization annealing is determined in the temperature range of 700-900 degreeC, and following Formula. LMP is performed in the range of 17000-21000, The manufacturing method of the non-oriented electrical steel sheet according to claim 1 characterized by things.
LMP = T × (20 + Log (t))
Here, T: annealing temperature (K), t: annealing time (hour).
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