JP7180694B2 - 方向性電磁鋼板の製造方法 - Google Patents
方向性電磁鋼板の製造方法 Download PDFInfo
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- JP7180694B2 JP7180694B2 JP2020566459A JP2020566459A JP7180694B2 JP 7180694 B2 JP7180694 B2 JP 7180694B2 JP 2020566459 A JP2020566459 A JP 2020566459A JP 2020566459 A JP2020566459 A JP 2020566459A JP 7180694 B2 JP7180694 B2 JP 7180694B2
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Description
本願は、2019年01月16日に、日本に出願された特願2019-005060号に基づき優先権を主張し、その内容をここに援用する。
0.01≦P1≦0.15 (式1)
0.01≦P2≦0.15 (式2)
P1>P2 (式3)
本発明者らは、このような課題を解決するために種々の実験を行った。その結果、鋼成分としてSnおよび/またはSbを適量含有させることによって、脱炭を良好に実施しつつ磁気特性の良好な方向性電磁鋼板を製造することができることを見出した。さらに、脱炭焼鈍工程の加熱帯および均熱帯の雰囲気ガスの酸化度(PH2O/PH2)を制御することで、上記の効果が向上することも見出した。
また、以下の実施形態の独立した各要素は、本発明の範囲において、互いに組み合わせ可能であることも自明である。
また、特に断りのない限り、以下の実施形態における化学成分の「%」は「質量%」を意味する。
Siは、含有量を多くすると電気抵抗が高くなり、鉄損特性が改善される。しかし、Si含有量が7.0%を超えると冷延が極めて困難となり、圧延時に鋼素材が割れてしまう。そのため、Si含有量の上限を7.0%とする。Si含有量の上限は好ましくは4.5%、さらに好ましくは4.0%である。
また、Si含有量が0.8%より少ないと、仕上げ焼鈍時にγ変態が生じ、鋼板の結晶方位が損なわれてしまう。そのため、Si含有量の下限を0.8%とする。Si含有量の下限は、好ましくは2.0%、さらに好ましくは2.5%である。
珪素鋼素材のC含有量が0.085%より多いと、脱炭焼鈍時間が長くなり、工業生産における生産性が損なわれてしまう。そのため、C含有量の上限を0.085%とする。C含有量の上限は、より好ましくは0.070%である。
酸可溶性Al含有量の下限は、好ましくは0.020%、さらに好ましくは0.025%である。酸可溶性Al含有量の上限は、好ましくは0.040%、さらに好ましくは0.030%である。
また、Sはその一部をSeで置き換えることができる。そのため、Seを含む場合、S+Se:0.050%以下であることが好ましく、Mn/(S+Se)≧4となる範囲であることが好ましい。
これらの選択元素は、その目的に応じて含有させればよい。よって、これらの選択元素の下限を限定する必要がなく、下限が0%でもよい。また、これらの選択元素が不純物として含有されても、上記効果は損なわれない。
Cu(銅)は、電気抵抗を高めて鉄損を低減するのに有効な元素である。従って、Cuを0.4%以下の含有量の範囲で含有させてもよい。Cu含有量が0.4%を超えると、鉄損低減効果が飽和してしまうとともに、熱間圧延時に“カッパーヘゲ”という表面疵の原因になることがある。Cu含有量の下限は、0.05%であることが好ましく、0.1%であることがより好ましい。Cu含有量の上限は、0.3%であることが好ましく、0.2%であることがより好ましい。
P(燐)は、電気抵抗を高めて鉄損を低減するのに有効な元素である。従って、Pを0.5%以下の含有量の範囲で含有させてもよい。P含有量が0.5%を超えると、珪素鋼板の圧延性に問題が生じることがある。P含有量の下限は、0.005%であることが好ましく、0.01%であることがより好ましい。P含有量の上限は、0.2%であることが好ましく、0.15%であることがより好ましい。
Ni(ニッケル)は、電気抵抗を高めて鉄損を低減するのに有効な元素である。また、Niは、熱延板の金属組織を制御して、磁気特性を高めるうえで有効な元素である。従って、Niを1.0%以下の含有量の範囲で含有させてもよい。Ni含有量が1.0%を超えると、二次再結晶が不安定になることがある。Ni含有量の下限は、0.01%であることが好ましく、0.02%であることがより好ましい。Ni含有量の上限は、0.2%であることが好ましく、0.1%であることがより好ましい。
B(ボロン)は、BNとしてインヒビター効果を発揮する有効な元素である。従って、Bを0.008%以下の含有量の範囲で含有させてもよい。B含有量が0.008%を超えると、磁気特性が劣化するおそれがある。B含有量の下限は、0.0005%であることが好ましく、0.001%であることがより好ましい。B含有量の上限は、0.005%であることが好ましく、0.003%であることがより好ましい。
Nb:0%以上0.20%以下
Ti:0%以上0.015%以下
V(バナジウム)、Nb(ニオブ)、及びTi(チタン)は、NやCと結合してインヒビターとして機能する、有効な元素である。従って、Vを0.15%以下、Nbを0.20%以下、および/またはTiを0.015%以下の含有量の範囲で含有させてもよい。これらの元素が最終製品に残留して、V含有量が0.15%を超え、Nb含有量が0.20%を超え、またはTi含有量が0.015%を超えると、磁気特性が劣化するおそれがある。
V含有量の下限は、0.002%であることが好ましく、0.01%であることがより好ましい。V含有量の上限は、0.10%であることが好ましく、0.05%であることがより好ましい。
Nb含有量の下限は、0.005%であることが好ましく、0.02%であることがより好ましい。Nb含有量の上限は、0.10%であることが好ましく、0.08%であることがより好ましい。
Ti含有量の下限は、0.002%であることが好ましく、0.004%であることがより好ましい。Ti含有量の上限は、0.010%であることが好ましく、0.008%であることがより好ましい。
Mo(モリブデン)も、電気抵抗を高めて鉄損を低減するのに有効な元素である。従って、Moを0.10%以下の範囲で含有させてもよい。Mo含有量が0.10%を超えると、鋼板の圧延性に問題が生じることがある。Mo含有量の下限は、0.005%であることが好ましく、0.01%であることがより好ましい。Mo含有量の上限は、0.08%であることが好ましく、0.05%であることがより好ましい。
Bi(ビスマス)は、硫化物等の析出物を安定化してインヒビターとしての機能を強化するのに有効な元素である。従って、Biを0.010%以下の範囲で含有させてもよい。Bi含有量が0.010%を超えると、磁気特性が劣化することがある。Bi含有量の下限は、0.001%であることが好ましく、0.002%であることがより好ましい。Bi含有量の上限は、0.008%であることが好ましく、0.006%であることがより好ましい。
上述した化学組成の珪素鋼素材から{110}<001>方位に発達した集合組織を有する方向性電磁鋼板を製造するためには、次のような工程を経る。
熱延板焼鈍工程(S104)における焼鈍は、750~1200℃の温度域で30秒~30分間行われてもよい。
0.01≦P1≦0.15 (式1)
0.01≦P2≦0.15 (式2)
脱炭焼鈍工程(S108)における加熱帯の雰囲気ガスの酸化度P1及び酸化度P2を上記の式1および式2で規定することで、Snおよび/またはSbが、加熱時に表面に偏析して最表面の初期酸化膜を変質させ、脱炭性が改善されると考えられる。
P1>P2 (式3)
たとえば、窒化処理工程(S110)は、小松等による(Al,Si)Nを主インヒビターとして用いる製造法(特公昭62-45285号公報)等)の窒化処理が好ましく用いられる。
仕上げ焼鈍では、酸化層を有する鋼板の表面に、上記のアルミナを主成分とする焼鈍分離剤を塗布して乾燥させ、乾燥後、コイル状に巻き取って、仕上げ焼鈍(二次再結晶焼鈍)に供する。
仕上げ焼鈍は例えば水素及び窒素を含有する雰囲気ガス中で、1150~1250℃まで昇温し、10~30時間焼鈍する条件で行えばよいが、窒化物や硫化物の純化等を行う場合、二次再結晶完了後、100%水素で1100℃以上の温度で焼鈍することが好ましい。
鋳造によって得られた質量で、Si:3.3%、Mn:0.14%、C:0.05%、S:0.007%、酸可溶性Al:0.027%、N:0.008%を含有し、残部Feおよび不純物からなる珪素鋼スラブを加熱後、板厚2.0mmまで熱間圧延した。この熱延板を1100℃に加熱後900℃に降温して30秒保持する焼鈍を実施した後、最終板厚が0.22mmとなるように1回の冷間圧延を行った。
また、酸化度が0.20以上の湿潤ガス雰囲気下で焼鈍した場合は、鋼中炭素量は0.0030%以下となるが、良好な鉄損は得られていない。
実施例1の結果より、鉄系酸化物が形成しないような低酸化度雰囲気ガス中で焼鈍すると、一般に鋼板表面のシリカは稠密な膜状で生成し脱炭を阻害するものと考えられる。
シリカ形成反応に及ぼす表面偏析形成元素や酸化物形成元素の影響について検討を行った。その結果を実施例2として以下に説明する。
表2より、酸化度が0.01~0.15の湿潤ガス(水蒸気-水素-窒素混合ガス)雰囲気下で焼鈍した場合は、良好な鉄損が得られると共に、鋼中炭素量が0.0030%以下となることが分かる。
実施例3では、実施例2において、Sn及びSb(偏析元素)とともにCrを適量含有させた場合の脱炭反応の安定化について検討した。
表3より、酸化度が0.01~0.20の湿潤ガス(水蒸気-水素-窒素混合ガス)雰囲気下で焼鈍した場合は、良好な鉄損が得られると共に、鋼中炭素量が0.0030%以下となることが分かる。Crを含有させることにより、酸化度裕度の上限を広げることができる。含有されたCrは、SnやSbとは異なり、脱炭焼鈍の加熱過程で酸化物を形成することによって、膜状シリカの生成に影響を及ぼし、脱炭反応を促進しているものと推定される。
実施例4では、加熱帯の酸化度と均熱帯の酸化度とを変更した場合の脱炭反応の安定化について検討した。
さらに、冷間圧延工程について検討した。その結果を実施例5として以下に説明する。
以上の工程により作製された試料につき、水洗、試料剪断の後、さらに歪取り焼鈍を行い、さらに、鋼板に張力を与える絶縁被膜を形成した(張力コーティングを施した)後、レーザー照射を行い、SST法にて磁気測定を行った。
脱炭焼鈍後の炭素量及び上記磁気測定によって得られた鉄損(W17/50)の値を表5に示す。
表5に示す通り、いずれの工程を経た場合でも、脱炭後の鋼中炭素量が0.0030%(30ppm)以下となるとともに、良好な鉄損が得られた。
表6に示す成分を含有し、残部Feおよび不純物からなる、鋳造によって得られた珪素鋼スラブを加熱後、板厚2.3mmまで熱間圧延した。この熱延板を1100℃で60秒保持する焼鈍を実施した後、最終板厚が0.22mmとなるように1回の冷間圧延を行った。
Claims (5)
- 珪素鋼素材を製造する珪素鋼素材製造工程と、
前記珪素鋼素材を熱間圧延して熱延板を得る熱間圧延工程と、
前記熱延板に一回の冷間圧延もしくは中間焼鈍を挟む複数回の冷間圧延を施して最終板厚の鋼板を得る冷間圧延工程と、
前記鋼板に脱炭焼鈍を施す脱炭焼鈍工程と、
前記鋼板に、アルミナを主成分とする焼鈍分離剤を塗布し、仕上げ焼鈍を施す仕上げ焼鈍工程と、を含み、
前記珪素鋼素材が、質量%で、
Si:0.8~7.0%、
C:0.085%以下、
酸可溶性Al:0.010~0.065%、
N:0.004~0.012%、
Mn:1.00%以下、
S:0.050%以下、および
SnとSbの一方あるいは双方を総量で0.01~0.20%、
を含有し、残部がFe及び不純物からなり、
前記脱炭焼鈍工程では、加熱帯と均熱帯とを備える脱炭焼鈍炉を用いて前記脱炭焼鈍を行い、
前記加熱帯の雰囲気ガスの酸化度P1が下記の式1を満足し、
前記均熱帯の雰囲気ガスの酸化度P2が下記の式2を満足し、
前記P1、および前記P2が下記の式3を満足する
ことを特徴とする方向性電磁鋼板の製造方法。
0.01≦P1≦0.15 (式1)
0.01≦P2≦0.15 (式2)
P1>P2 (式3) - 前記珪素鋼素材が、質量%で、Cr:0.02~0.50%をさらに含有することを特徴とする請求項1に記載の方向性電磁鋼板の製造方法。
- 前記珪素鋼素材が、さらに、質量%で、
Cu:0%以上0.4%以下、
P:0%以上0.5%以下、
Ni:0%以上1.0%以下、
B:0%以上0.008%以下、
V:0%以上0.15%以下、
Nb:0%以上0.20%以下、
Mo:0%以上0.10%以下、
Ti:0%以上0.015%以下、及び
Bi:0%以上0.010%以下、
を含有する
ことを特徴とする請求項1または2に記載の方向性電磁鋼板の製造方法。 - 前記脱炭焼鈍工程の前から前記仕上げ焼鈍工程での二次再結晶発現前までに、窒化処理工程をさらに含む
ことを特徴とする請求項1から3のいずれか1項に記載の方向性電磁鋼板の製造方法。 - 前記熱間圧延工程の後、かつ前記冷間圧延工程の前に、前記熱間圧延工程で得られた前記熱延板を焼鈍する熱延板焼鈍工程をさらに含む
ことを特徴とする請求項1から4のいずれか1項に記載の方向性電磁鋼板の製造方法。
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DE102015114358B4 (de) * | 2015-08-28 | 2017-04-13 | Thyssenkrupp Electrical Steel Gmbh | Verfahren zum Herstellen eines kornorientierten Elektrobands und kornorientiertes Elektroband |
RU2698042C1 (ru) * | 2015-12-04 | 2019-08-21 | ДжФЕ СТИЛ КОРПОРЕЙШН | Способ производства текстурированной электротехнической листовой стали |
JP7046329B2 (ja) | 2017-06-22 | 2022-04-04 | Funfam株式会社 | ランチョンマット |
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JP2002060843A (ja) | 2000-08-09 | 2002-02-28 | Nippon Steel Corp | 磁束密度の高い鏡面一方向性電磁鋼板の製造方法 |
JP2003268452A (ja) | 2002-03-15 | 2003-09-25 | Nippon Steel Corp | 磁気特性の良好な鏡面方向性電磁鋼板の製造方法 |
JP2008001980A (ja) | 2006-05-24 | 2008-01-10 | Nippon Steel Corp | 鏡面方向性電磁鋼板の製造方法 |
JP2010236013A (ja) | 2009-03-31 | 2010-10-21 | Jfe Steel Corp | 方向性電磁鋼板の製造方法 |
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BR112021013632A2 (pt) | 2021-09-14 |
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US20220098694A1 (en) | 2022-03-31 |
CN113272456B (zh) | 2023-03-14 |
EP3913093A1 (en) | 2021-11-24 |
CN113272456A (zh) | 2021-08-17 |
EP3913093A4 (en) | 2022-10-05 |
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