JP2009068055A - Non-oriented electrical steel sheet - Google Patents
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Abstract
【課題】靭性に優れたクロムフリーの絶縁被膜が形成された無方向性電磁鋼板を提供する。
【解決手段】質量%で、C:0.005%以下、Si:1.0〜4.0%、Al:2.0%以下、Mn:0.1〜1.0%、P:0.03%以下、B:0.0003〜0.01%、Sn:0.1%以下、残部がFeおよび不可避的不純物からなり、下記の式(1)を満足することを特徴とするCr量が1質量%以下の絶縁被膜が形成された無方向性電磁鋼板；[Sn]≧-0.02×log10[B]-0.04・・・(1)、ただし、[Sn]、[B]は鋼板中のSn、Bの含有量を表す。
【選択図】図1A non-oriented electrical steel sheet provided with a chromium-free insulating coating having excellent toughness is provided.
SOLUTION: In mass%, C: 0.005% or less, Si: 1.0 to 4.0%, Al: 2.0% or less, Mn: 0.1 to 1.0%, P: 0.03% or less, B: 0.0003 to 0.01%, Sn: 0.1 % Non-oriented electrical steel sheet with an insulating coating having a Cr content of 1% by mass or less, characterized in that the balance is Fe and inevitable impurities and satisfies the following formula (1): [Sn] ≧ −0.02 × log 10 [B] −0.04 (1), where [Sn] and [B] represent the contents of Sn and B in the steel sheet.
[Selection] Figure 1
Description
本発明は、無方向性電磁鋼板、特に、クロムフリーの絶縁被膜が形成された無方向性電磁鋼板に関する。 The present invention relates to a non-oriented electrical steel sheet, and more particularly to a non-oriented electrical steel sheet on which a chromium-free insulating coating is formed.
モータや変圧器の積鉄心として使用される無方向性電磁鋼板には、渦電流損失を低減させて電流効率を高めるためや、積層された鋼板間に電流が流れてジュール熱が発生することによるモータ効率の低下を防ぐために、その表面に絶縁被膜が形成されている。 Non-oriented electrical steel sheets used as cores for motors and transformers are used to reduce eddy current loss and increase current efficiency, or because current flows between laminated steel sheets and Joule heat is generated. In order to prevent a reduction in motor efficiency, an insulating coating is formed on the surface.
この絶縁被膜には、本来の目的である高い絶縁性に加えて、鋼板との密着性、溶接性、耐食性、打ち抜き性や、加工歪を除去して磁気特性の向上を図るために行われる歪取焼鈍時において鋼板同士の融着(スティッキング)が起こりにくい性質などが要求されている。 In addition to high insulation, which is the original purpose, this insulating coating includes adhesion to the steel sheet, weldability, corrosion resistance, punchability, and strain that is applied to improve the magnetic properties by removing processing strain. There is a demand for properties such that steel sheets are less likely to be fused (sticking) during annealing.
こうした特性を有する絶縁被膜としては、これまで、クロム酸塩を主体とする無機有機系被膜が広く使用されている。例えば、特許文献1には、少なくとも1種の2価金属を含む重クロム酸塩系水溶液に酢酸ビニル/ベオバの樹脂エマルジョンおよび有機還元剤を配合した処理液を塗布して形成した絶縁被膜が、また、特許文献2には、クロム酸とAl、Mgなどの酸化物と粒子径が0.2〜0.5μmの有機樹脂エマルジョンおよび粒子径が1〜50μmの有機樹脂エマルジョンとからなる処理液を塗布して形成した絶縁被膜が開示されている。 As an insulating film having such characteristics, inorganic organic films mainly composed of chromate have been widely used so far. For example, Patent Document 1 includes an insulating film formed by applying a treatment liquid containing a vinyl acetate / veova resin emulsion and an organic reducing agent to a dichromate aqueous solution containing at least one divalent metal. In Patent Document 2, a treatment liquid composed of chromic acid, an oxide such as Al and Mg, an organic resin emulsion having a particle size of 0.2 to 0.5 μm, and an organic resin emulsion having a particle size of 1 to 50 μm is applied. A formed insulating coating is disclosed.
しかし、特許文献1や2に記載の絶縁被膜形成のための処理液には6価クロムが含まれており、環境負荷の観点から、クロムを含有しない、すなわちクロムフリーの絶縁被膜が望まれている。そこで、例えば、特許文献3には、リン化合物を含む第1層とケイ酸塩および粒子径が0.3〜2.5μmの有機樹脂エマルジョンを含む第2層とからなるクロムフリーの絶縁被膜が形成された電磁鋼板が提案されている。
しかしながら、本発明者等が、特許文献3に記載のクロムフリーの絶縁被膜が形成された電磁鋼板を用いて、モータの鉄心を試作し、歪取焼鈍(750℃、2時間、乾燥N2雰囲気)を行ったところ、鋼板が脆化して割れやすくなるという現象が確認された。なお、クロムを含有した従来の絶縁被膜を用いた場合には、このような問題は生じなかった。 However, the inventors made a prototype of the motor core using the magnetic steel sheet on which the chromium-free insulating film described in Patent Document 3 was formed, and then applied the strain relief annealing (750 ° C., 2 hours, dry N 2 atmosphere). ), The phenomenon that the steel sheet becomes brittle and easily breaks was confirmed. Such a problem did not occur when a conventional insulating film containing chromium was used.
本発明は、歪取焼鈍により脆化することのない、すなわち靭性に優れたクロムフリーの絶縁被膜が形成された無方向性電磁鋼板を提供することを目的とする。なお、本発明では、クロムフリーの絶縁被膜とは、便宜上、被膜中のCr量が1質量%以下の絶縁被膜と定義する。 An object of the present invention is to provide a non-oriented electrical steel sheet in which a chromium-free insulating coating that is not embrittled by strain relief annealing, that is, excellent in toughness, is formed. In the present invention, the chromium-free insulating film is defined as an insulating film having a Cr content of 1% by mass or less for convenience.
本発明者等は、歪取焼鈍により脆化することのないクロムフリーの絶縁被膜が形成された無方向性電磁鋼板について鋭意検討したところ、SnとBを添加し、その量を適正化することにより歪取焼鈍による脆化を防止できることを見出した。 The inventors of the present invention have intensively studied a non-oriented electrical steel sheet on which a chromium-free insulating coating that does not become brittle by strain relief annealing has been formed, and adding Sn and B to optimize the amount thereof. It was found that embrittlement due to strain relief annealing can be prevented.
本発明は、このような知見に基づきなされたもので、質量%で、C:0.005%以下、Si:1.0〜4.0%、Al:2.0%以下、Mn:0.1〜1.0%、P:0.03%以下、B:0.0003〜0.01%、Sn:0.1%以下、残部がFeおよび不可避的不純物からなり、下記の式(1)を満足することを特徴とするCr量が1質量%以下の絶縁被膜が形成された無方向性電磁鋼板を提供する。
[Sn]≧-0.02×log10[B]-0.04 ・・・(1)
ただし、[Sn]、[B]は鋼板中のSn、Bの含有量を表す。
The present invention has been made based on such knowledge, in mass%, C: 0.005% or less, Si: 1.0-4.0%, Al: 2.0% or less, Mn: 0.1-1.0%, P: 0.03% or less B: 0.0003-0.01%, Sn: 0.1% or less, the balance is Fe and unavoidable impurities, and satisfies the following formula (1). An oriented non-oriented electrical steel sheet is provided.
[Sn] ≧ -0.02 × log 10 [B] -0.04 (1)
However, [Sn] and [B] represent the contents of Sn and B in the steel sheet.
本発明の無方向性電磁鋼板では、質量%で、Al:0.3%以上であることが好ましい。 In the non-oriented electrical steel sheet of the present invention, it is preferable that Al is 0.3% or more by mass%.
本発明により、歪取焼鈍により脆化することのない、すなわち靭性に優れたクロムフリーの絶縁被膜が形成された無方向性電磁鋼板を製造できるようになった。そのため、環境負荷の低減や、高速回転の際に鋼板が割れて飛散するような危惧もなくモータ効率の向上を図れるようになった。 The present invention makes it possible to manufacture a non-oriented electrical steel sheet that is not embrittled by strain relief annealing, that is, is formed with a chromium-free insulating coating excellent in toughness. For this reason, it has become possible to improve the motor efficiency without reducing the environmental load and without fear that the steel sheet will crack and scatter during high-speed rotation.
以下、成分含有量の単位を表す「%」は、特に断らない限り「質量%」を意味する。 Hereinafter, “%” representing a unit of component content means “% by mass” unless otherwise specified.
本発明者等は、クロムフリーの絶縁被膜が形成された無方向性電磁鋼板の歪取焼鈍による脆化の原因について以下のような詳細な調査を行った。まず、C:0.0027%、Si:3.2%、Al:0.42%、Mn:0.21%、P:0.02%、残部Feおよび不可避的不純物を含む鋼を真空溶製してスラブを作製し、1100℃で30分間スラブを加熱処理後熱間圧延を行い、板厚1.7mmの熱延板とした。得られた熱延板に1000℃で1分間の熱延板熱処理を施した後、酸洗・冷間圧延を行って0.35mmの冷延板とし、1000℃で30秒間の仕上焼鈍を行った。そして、焼鈍後の鋼板に、表１に示す組成のNo.1〜4の処理液を塗布後、焼付けを行って、絶縁被膜を形成した。絶縁被膜の目付量は全て1.0g/m2とした。得られた鋼板に対し、幾つかの歪取焼鈍炉を用い、N2雰囲気中で750℃で2時間の歪取焼鈍を行ったところ、このうち１つの焼鈍炉ではクロムフリーの絶縁被膜(No.2〜4)を形成した鋼板に脆化割れが発生することが分かった。 The present inventors conducted the following detailed investigation on the cause of embrittlement due to strain relief annealing of a non-oriented electrical steel sheet on which a chromium-free insulating coating was formed. First, C: 0.0027%, Si: 3.2%, Al: 0.42%, Mn: 0.21%, P: 0.02%, the steel containing the balance Fe and unavoidable impurities is vacuum-melted to produce a slab at 1100 ° C The slab was heat-treated for 30 minutes and then hot-rolled to obtain a hot-rolled sheet having a thickness of 1.7 mm. The obtained hot-rolled sheet was subjected to hot-rolled sheet heat treatment at 1000 ° C. for 1 minute, and then pickled and cold-rolled to form a 0.35 mm cold-rolled sheet, and was subjected to finish annealing at 1000 ° C. for 30 seconds . And after apply | coating the processing liquid of No. 1-4 of the composition shown in Table 1 to the steel plate after annealing, it baked and formed the insulating film. The weight per unit area of the insulating coating was 1.0 g / m 2 . The obtained steel sheet was subjected to strain relief annealing for 2 hours at 750 ° C. in N 2 atmosphere using several strain relief annealing furnaces. It was found that embrittlement cracks occur in the steel sheets formed with 2-4).
脆化割れした鋼板の断面をSEMで観察したところ、表面に厚さ1μm程度の内部酸化層が形成されていることが判明した。そこで、脆化割れが発生した歪取焼鈍炉の雰囲気を分析したところ、均熱開始の時点で雰囲気中に約1%のO2が含まれていることが判明した。これに対し、脆化割れが発生しない焼鈍炉の雰囲気中のO2濃度は0.1%以下であった。 When the cross section of the embrittled cracked steel sheet was observed by SEM, it was found that an internal oxide layer having a thickness of about 1 μm was formed on the surface. Therefore, when analyzing the atmosphere of the stress relief annealing furnace in which embrittlement cracking occurred, it was found that the atmosphere contained about 1% O 2 at the start of soaking. On the other hand, the O 2 concentration in the atmosphere of the annealing furnace where no brittle cracking occurred was 0.1% or less.
また、脆化割れの破面をSEMで観察したところ、破面がほとんど粒界破面であることが判明した。さらに、真空中で脆化割れした鋼板と脆化割れしなかった鋼板を破壊し、粒界破面をAES(オージェ電子分光)で分析したところ、脆化割れしなかった鋼板の粒界にはCが強く偏析しているのに対し、脆化割れした鋼板の粒界にはCの偏析が弱く、Pの偏析が強いことが判明した。Cは粒界強化元素、Pは粒界脆化元素として知られており、粒界破壊の原因は粒界Cの減少と粒界Pの増加であると考えられる。また、クロムフリーの絶縁被膜が形成された鋼板で粒界にCの偏析が弱いのは、絶縁被膜のO2に対するバリア性が低く、粒界で脱炭が進行しやすくなったためと考えられる。一方、クロムを含有した絶縁被膜が形成された鋼板で粒界にCが強く偏析するのは、高O2ポテンシャル雰囲気下では鋼板-被膜界面にFe-Cr-O系の強固なバリア層が形成され、粒界で脱炭が進行しにくくなったためと考えられる。 Further, when the fracture surface of the embrittlement crack was observed by SEM, it was found that the fracture surface was almost a grain boundary fracture surface. Furthermore, when the steel plate that was embrittled cracked in vacuum and the steel plate that was not embrittled cracked were broken, and the grain boundary fracture surface was analyzed by AES (Auger electron spectroscopy), In contrast to the strong segregation of C, the segregation of C was weak and the segregation of P was strong at the grain boundaries of the brittle cracked steel sheet. C is known as a grain boundary strengthening element and P is known as a grain boundary embrittlement element. The cause of grain boundary fracture is thought to be a decrease in grain boundary C and an increase in grain boundary P. The reason why the segregation of C at the grain boundary is weak in the steel sheet on which the chromium-free insulating film is formed is considered to be that the barrier property against O 2 of the insulating film is low and decarburization easily proceeds at the grain boundary. On the other hand, the strong segregation of C at the grain boundaries occurs in steel plates with chromium-containing insulation coatings. A strong barrier layer of Fe-Cr-O system is formed at the steel plate-coating interface in a high O 2 potential atmosphere. This is thought to be because decarburization is less likely to proceed at the grain boundaries.
歪取焼鈍の雰囲気中にO2が含まれることはしばしばみられ、例えば、打抜き加工時の加工油を除去する油焼き処理のO2が残留したり、炉の密封性が悪く大気が混入したりして起こる。また、鉄心をモーターケースに焼きばめする際の熱処理は大気中で行われるので、O2が含まれることになる。本発明者等は、クロムフリーの絶縁被膜が形成された無方向性電磁鋼板を広く普及させるためには、このような雰囲気の焼鈍炉を用いても鋼板が脆化しないようにする必要があると考え、その検討を行った。 O 2 is often included in the atmosphere of strain relief annealing.For example, O 2 of oil baking treatment that removes processing oil at the time of punching processing remains, or the furnace seal is poor and air is mixed in. Happens. In addition, since the heat treatment when the iron core is shrink-fitted in the motor case is performed in the atmosphere, O 2 is included. In order to widely disseminate the non-oriented electrical steel sheet on which the chromium-free insulating film is formed, the present inventors need to prevent the steel sheet from becoming brittle even when using an annealing furnace in such an atmosphere. I thought that.
その結果、B:0.0003〜0.01%、Sn:0.1%以下を添加し、かつB含有量[B]とSn含有量[Sn]を、上記式(1)、すなわち
[Sn]≧-0.02×log10[B]-0.04 ・・・(1)
を満足させれば、図1に示すように、鋼板の脆化を防止できることが明らかになった。なお、図1の結果は、脆化をJIS C2550で規定されている繰り返し曲げ試験により求めたもので、○は10回以上繰り返し曲げを行っても脆化割れが発生しない、△は3〜9回繰り返し曲げを行うと脆化割れが発生する、×は2回以下の繰り返し曲げを行うと脆化割れが発生する、を表している。また、試験に供した鋼板の成分の含有量は、BとSn以外は本発明範囲内としている。
As a result, B: 0.0003-0.01%, Sn: 0.1% or less was added, and B content [B] and Sn content [Sn], the above formula (1),
[Sn] ≧ -0.02 × log 10 [B] -0.04 (1)
As shown in FIG. 1, it was clarified that embrittlement of the steel sheet can be prevented if the above is satisfied. In addition, the result of FIG. 1 was obtained by the repeated bending test stipulated in JIS C2550, ○ indicates that no brittle cracking occurs even after repeated bending 10 times or more, and △ 3-9 When repeated bending is performed, embrittlement cracking occurs. × indicates that embrittlement cracking occurs when bending is repeated twice or less. Moreover, the content of the components of the steel sheet subjected to the test is within the scope of the present invention except for B and Sn.
Snが脆化を抑制するメカニズムは明確ではないが、何らかのメカニズムでPの偏析を妨げているか、鋼中へのO2の侵入を妨げて、粒界における脱炭の進行を抑制していると考えられる。また、Bは粒界に偏析して粒界脆化を防止しているものと考えられる。 The mechanism by which Sn suppresses embrittlement is not clear, but some mechanism prevents P segregation or prevents O 2 from penetrating into the steel to suppress the progress of decarburization at grain boundaries. Conceivable. Further, B is considered to segregate at the grain boundary and prevent grain boundary embrittlement.
B量の上限を0.01%とし、Sn量の上限を0.1%としたのは、これらの上限を超えると粒成長を阻害し、磁気特性を劣化させるためである。 The reason why the upper limit of the B content is set to 0.01% and the upper limit of the Sn content is set to 0.1% is that when these upper limits are exceeded, grain growth is inhibited and the magnetic properties are deteriorated.
以下に、BとSn以外の成分の含有量の限定理由を説明する。 The reason for limiting the content of components other than B and Sn will be described below.
C:0.005%以下
Cは、粒界を強化し、脆化防止に効果的な元素である。しかし、磁気時効による磁気特性の劣化を招きやすいため、C量は0.005%以下とする。
C: 0.005% or less
C is an element that strengthens grain boundaries and is effective in preventing embrittlement. However, the amount of C is set to 0.005% or less because magnetic characteristics are likely to deteriorate due to magnetic aging.
Si:1.0〜4.0%
Siは、鋼板の比抵抗を増加させるので、鉄損低減のために有効な元素である。また、高温酸化を抑制するので、クロムフリーの絶縁被膜の密着性を向上させる上でも効果的な元素である。このような効果を発揮するには、Si量を1.0%以上、好ましくは2.0%以上とする必要がある。しかし、Si量が4.0%を超えるとコスト高になる。したがって、Si量は1.0〜4.0%、好ましくは2.0〜4.0%とする。
Si: 1.0-4.0%
Since Si increases the specific resistance of the steel sheet, it is an effective element for reducing iron loss. Moreover, since high temperature oxidation is suppressed, it is an element effective also in improving the adhesiveness of a chromium-free insulating film. In order to exert such an effect, the Si amount needs to be 1.0% or more, preferably 2.0% or more. However, when the Si amount exceeds 4.0%, the cost becomes high. Therefore, the Si content is 1.0 to 4.0%, preferably 2.0 to 4.0%.
Al:2.0%以下
Alは、鋼板の比抵抗を増加させるので、鉄損低減のために有効な元素である。また、Bの粒界偏析を促進させ、脆化割れを防ぐ役割も有する。しかし、Al量が2.0%を超えるとコスト高になるため、Al量は2.0%以下とする。
Al: 2.0% or less
Al increases the specific resistance of the steel sheet and is therefore an effective element for reducing iron loss. It also has the role of promoting grain boundary segregation of B and preventing embrittlement cracking. However, if the Al amount exceeds 2.0%, the cost increases, so the Al amount is set to 2.0% or less.
また、図2に例示すように、Al量を0.3%以上添加すると、上述した繰り返し曲げ試験における脆化割れが発生する繰り返し曲げ回数が増加し、鋼板の脆化をより効果的に抑制することができる。Al量を0.3%以上添加すると、N活量を低減させてB活量を高め、Bの粒界偏析が促進されると推察される。 Also, as shown in FIG. 2, when Al content is added 0.3% or more, the number of repeated bending that causes embrittlement cracking in the above-described repeated bending test increases, and the embrittlement of the steel sheet is more effectively suppressed. Can do. It is presumed that when 0.3% or more of Al is added, the N activity is reduced to increase the B activity and the grain boundary segregation of B is promoted.
Mn:0.1〜1.0%
Mnは、熱間圧延での割れを防止するために有効な元素であり、この効果を得るためにはMn量を少なくとも0.1%以上とする必要がある。しかし、Mn量が1.0%を超えるとコスト高になる。したがって、Mn量は0.1〜1.0%とする。
Mn: 0.1-1.0%
Mn is an element effective for preventing cracking in hot rolling, and in order to obtain this effect, the amount of Mn needs to be at least 0.1% or more. However, if the amount of Mn exceeds 1.0%, the cost becomes high. Therefore, the amount of Mn is 0.1 to 1.0%.
P:0.03%以下
Pは、粒界脆化元素であるので、その量は0.03%以下とする必要があるが、できるだけ少ないほど好ましい。
P: 0.03% or less
Since P is an intergranular embrittlement element, its amount needs to be 0.03% or less, but it is preferably as small as possible.
残部はFeおよび不可避的不純物であるが、特に微細な析出物を形成する元素は、焼鈍中の粒成長を阻害し、鉄損を増大させるので、できるだけ低減することが望ましい。例えば、S、N、Oは0.005%以下に、V、Tiは0.002%以下にすることが望ましい。これに対し、Cu、Cr、Ni等の元素は、磁気特性にそれほど影響せず、また、除去の難しい元素であるので、意図的に低減する必要もなく、例えば0.01〜0.05%程度に制御されていれば十分である。 The balance is Fe and inevitable impurities, but the elements that form fine precipitates in particular inhibit grain growth during annealing and increase iron loss, so it is desirable to reduce them as much as possible. For example, S, N, and O are preferably 0.005% or less, and V and Ti are preferably 0.002% or less. On the other hand, elements such as Cu, Cr, and Ni do not affect the magnetic characteristics so much and are difficult to remove, and therefore do not need to be reduced intentionally, and are controlled to about 0.01 to 0.05%, for example. It is enough.
本発明の無方向性電磁鋼板の製造方法については、通常の方法を用いることができる。すなわち、転炉・脱ガスにて成分調整した後に鋳造し、熱間圧延、熱延板焼鈍、冷間圧延、仕上焼鈍、絶縁被膜の塗布・焼付けという工程で製造することができる。冷間圧延は、中間焼鈍を挟む2回の冷間圧延で置き換えることもできる。鉄損低減の観点から、全ての焼鈍はα単相域で行うことが望ましい。絶縁被膜は、例えば上記の表1に示すようなクロムフリーの処理液を通常の方法で塗布・焼付けすれば形成できる。歪取焼鈍後も被膜特性を保つためには、無機成分が主体の被膜にする必要があることは言うまでもない。 A normal method can be used about the manufacturing method of the non-oriented electrical steel sheet of this invention. That is, it can be cast after the components are adjusted by converter and degassing, and can be manufactured by the steps of hot rolling, hot-rolled sheet annealing, cold rolling, finish annealing, and application / baking of an insulating coating. The cold rolling can be replaced with two cold rollings that sandwich the intermediate annealing. From the viewpoint of reducing iron loss, it is desirable to perform all annealing in the α single phase region. The insulating coating can be formed, for example, by applying and baking a chromium-free processing solution as shown in Table 1 in the usual manner. Needless to say, in order to maintain the film characteristics even after strain relief annealing, it is necessary to make the film mainly composed of inorganic components.
表2に示す成分を有する鋼を転炉・脱ガスで溶製・鋳造してスラブとした後、1100℃で30分間のスラブ加熱を行ってから熱間圧延を行い、厚さ1.8mmの熱延板とし、1000℃で30秒間の熱延板焼鈍を行った。焼鈍後の熱延板を酸洗し、冷間圧延を行い厚さ0.35mmの冷延板とし、1000℃で30秒間の仕上焼鈍を行い、表2に示す成分の絶縁被膜を塗布・焼付けにより形成して無方向性電磁鋼板を作製した。このとき、絶縁被膜の目付量は1.0g/m2とした。得られた電磁鋼板を1%O2-99%N2雰囲気中で750℃で2時間の歪取焼鈍を行った後、上述したJIS C2550に規定された繰り返し曲げ試験と以下に示す絶縁被膜の密着性試験を行った。
絶縁被膜の密着性試験：曲げR20mmφで、180°曲げ戻し試験後の被膜剥離率(剥離部分の面積率)により、次のように評価した。
◎：剥離なし
○：〜剥離20%未満
△：剥離20%以上40%未満
×：剥離40%以上
結果を表2に示す。本発明範囲であるクロムフリーの絶縁被膜が形成された無方向性電磁鋼板は、歪取焼鈍を行っても脆化割れが発生せず、また、良好な絶縁被膜の密着性を示すことがわかる。
Steel with the components shown in Table 2 was melted and cast in a converter and degassed to form a slab, followed by slab heating at 1100 ° C for 30 minutes, followed by hot rolling to produce a 1.8 mm thick heat The sheet was rolled and annealed at 1000 ° C. for 30 seconds. The hot-rolled sheet after annealing is pickled, cold-rolled to form a cold-rolled sheet with a thickness of 0.35 mm, finish-annealed at 1000 ° C for 30 seconds, and an insulating coating of the components shown in Table 2 is applied and baked The non-oriented electrical steel sheet was formed by forming. At this time, the basis weight of the insulating coating was 1.0 g / m 2 . The obtained electrical steel sheet was subjected to strain relief annealing at 750 ° C. for 2 hours in a 1% O 2 -99% N 2 atmosphere, then the repeated bending test specified in JIS C2550 and the insulating coating shown below. An adhesion test was performed.
Insulation film adhesion test: Evaluation was carried out as follows according to the film peeling rate (area ratio of the peeled portion) after the 180 ° bending return test at a bending R of 20 mmφ.
A: No peeling O: ~ Less than 20% peeling Δ: Peeling 20% or more and less than 40% X: Peeling 40% or more The results are shown in Table 2. It can be seen that the non-oriented electrical steel sheet on which the chromium-free insulating coating within the scope of the present invention is formed does not cause embrittlement cracking even when strain relief annealing is performed, and also shows good adhesion of the insulating coating. .
Claims (2)
[Sn]≧-0.02×log10[B]-0.04 ・・・(1)
ただし、[Sn]、[B]は鋼板中のSn、Bの含有量を表す。 In mass%, C: 0.005% or less, Si: 1.0 to 4.0%, Al: 2.0% or less, Mn: 0.1 to 1.0%, P: 0.03% or less, B: 0.0003 to 0.01%, Sn: 0.1% or less, balance Is a non-oriented electrical steel sheet on which an insulating film having a Cr content of 1% by mass or less is formed, which comprises Fe and inevitable impurities and satisfies the following formula (1):
[Sn] ≧ -0.02 × log 10 [B] -0.04 (1)
However, [Sn] and [B] represent the contents of Sn and B in the steel sheet.
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2012126975A (en) * | 2010-12-16 | 2012-07-05 | Kobe Steel Ltd | Soft magnetic steel component superior in ac magnetic property, and manufacturing method therefor |
| JP2018178198A (en) * | 2017-04-14 | 2018-11-15 | 新日鐵住金株式会社 | Non-oriented electrical steel sheet and method of manufacturing the same |
| WO2022210864A1 (en) * | 2021-03-31 | 2022-10-06 | 日本製鉄株式会社 | Non-oriented electromagnetic steel sheet, production method for non-oriented electromagnetic steel sheet, electric motor, and production method for electric motor |
| JPWO2023063369A1 (en) * | 2021-10-13 | 2023-04-20 |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03274247A (en) * | 1990-03-22 | 1991-12-05 | Sumitomo Metal Ind Ltd | Nonoriented silicon steel sheet excellent in magnetic property |
| JP2001323351A (en) * | 2000-05-15 | 2001-11-22 | Kawasaki Steel Corp | Non-oriented electrical steel sheet with excellent workability and recyclability, low iron loss and high magnetic flux density |
| JP2005240078A (en) * | 2004-02-25 | 2005-09-08 | Jfe Steel Kk | Oriented electrical steel sheet with low magnetic field magnetic properties and excellent stability over time and method for producing the same |
-
2007
- 2007-09-12 JP JP2007236118A patent/JP2009068055A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03274247A (en) * | 1990-03-22 | 1991-12-05 | Sumitomo Metal Ind Ltd | Nonoriented silicon steel sheet excellent in magnetic property |
| JP2001323351A (en) * | 2000-05-15 | 2001-11-22 | Kawasaki Steel Corp | Non-oriented electrical steel sheet with excellent workability and recyclability, low iron loss and high magnetic flux density |
| JP2005240078A (en) * | 2004-02-25 | 2005-09-08 | Jfe Steel Kk | Oriented electrical steel sheet with low magnetic field magnetic properties and excellent stability over time and method for producing the same |
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| JP2012126975A (en) * | 2010-12-16 | 2012-07-05 | Kobe Steel Ltd | Soft magnetic steel component superior in ac magnetic property, and manufacturing method therefor |
| JP2018178198A (en) * | 2017-04-14 | 2018-11-15 | 新日鐵住金株式会社 | Non-oriented electrical steel sheet and method of manufacturing the same |
| WO2022210864A1 (en) * | 2021-03-31 | 2022-10-06 | 日本製鉄株式会社 | Non-oriented electromagnetic steel sheet, production method for non-oriented electromagnetic steel sheet, electric motor, and production method for electric motor |
| JPWO2022210864A1 (en) * | 2021-03-31 | 2022-10-06 | ||
| JP7231115B2 (en) | 2021-03-31 | 2023-03-01 | 日本製鉄株式会社 | Non-oriented electrical steel sheet, method for manufacturing non-oriented electrical steel sheet, electric motor, and method for manufacturing electric motor |
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