JP3870616B2

JP3870616B2 - Fe-Cr-Si alloy and method for producing the same

Info

Publication number: JP3870616B2
Application number: JP20759999A
Authority: JP
Inventors: 修近藤; 明博松崎; 重彰高城
Original assignee: JFE Steel Corp
Current assignee: JFE Steel Corp
Priority date: 1999-07-22
Filing date: 1999-07-22
Publication date: 2007-01-24
Anticipated expiration: 2019-07-22
Also published as: JP2001032054A

Description

【０００１】
【発明の属する技術分野】
この発明は、商用周波数よりも高い周波数において電磁鋼板として用いる場合に良好な鉄損特性を有するFe−Cr−Si系合金及びその製造方法に関する。
【０００２】
【従来の技術】
Fe−Si合金は、軟質磁気特性に優れる材料として知られていて、なかでもSi量が3.5 wt％以下のFe−Si合金は、電磁鋼板として商用周波数用の各種鉄心を中心に多用されている。しかし、使用周波数が商用周波数よりも高い場合には、かかるSi量3.5 wt％以下の電磁鋼板では鉄損が大きくなる不利がある。そのため、このような商用周波数よりも高い周波域で用いられる用途においては、鉄損特性を改善するために、更に電気抵抗の高い材料が求められている。
【０００３】
一般に、鋼中のSi量を増やせば電気抵抗が増大するから、上記のような高周波域での鉄損を低減する上で好都合である。しかし、その一方で、Si量が3.5 wt％を超えると、合金が極めて硬く脆くなり、加工性が劣ってしまうので圧延による製造、加工が困難となる。特にSi量が5.0 wt％を超える場合には、冷間加工はもちろんのこと、温間加工も不可能になってしまう。
【０００４】
この高Si鋼の加工性を改良し、6.5 wt％程度のSiを含有しても工業的に鋼板を製造できる技術としては、特開昭６１−１６６９２３号公報に開示されている低温強圧下の熱間圧延による方法、特開昭６２−２２７０７８号公報に開示されているSiの拡散浸透処理による方法が代表的である。
【０００５】
【発明が解決しようとする課題】
しかし、前者の特開昭６１−１６６９２３号公報に開示された技術は、合金としての脆性を見かけ上改善するために圧延組織を微妙に調整しなければならない。したがって、製造過程で厳密な制御を行わなければならず、工業的に安定して生産するのは非常に困難である。一方、後者の特開昭６２−２２７０７８号公報に開示された技術では、特殊な拡散浸透法を用いるため、工業的な製造を行う場合にはコストにおいて極めて不利である。また、良好な高周波磁気特性を得るためにSi量をこれらの方法で増量しても、電気抵抗の増加には限界がある。
また、通常の工業的な圧延法で製造できる3.5 wt％以下のSi量の場合には、50μΩcm台までの比抵抗しか得られなかった。
また、これらのFe−Si合金は、耐食性が劣る点も鉄心などの用途においては問題とされる。
【０００６】
ところで、Alは磁気特性の観点でSiと同様に電気抵抗を増大させる効果があり、しかもSiほどは加工性を劣化させない。そこで、Siの一部をAlで置換することにより、加工性が改善されることが知られている。Alは、Siよりもコスト高になり、磁束密度の減少が大きいなどの不利があるが、例えばほぼ同等の電気抵抗を得られるSi：3 wt％、Al：0.7 wt％の組成の鋼と、Si：3.7 wt％の組成の鋼とでは、Alを0.7 wt％含有する前者の鋼が加工性、冷延性が良好である。また、磁気特性もほぼ同等となる。
しかし、Si：3 wt％以上の鋼において、SiとAlとの合計量が４wt％以上になる場合は、冷間圧延が不能となり、更に、SiとAlとの合計量が６wt％を超える場合には、温間圧延でさえも困難になっていた。また、この成分系の場合においても、工業的には60μΩcm未満の比抵抗しか得られていなかった。
【０００７】
結局のところ、単にSi量やAl量を増加させることにより高周波域での鉄損低減を図るよりも、本質的に加工性の改善された新規な成分系の合金によって、高周波域にわたる鉄損特性と共に、加工性をも確保し、更に、耐食性などを満たすことが望ましい。
【０００８】
なお、Fe−Si合金の耐食性に関しては、このFe−Si合金の耐食性を改善する手段として、Crを一定量添加する方法が、特開昭５２−２４１１７号公報及び特開昭６１−２７２３５２号公報に開示されている。このように、Crの添加により耐食性を向上させた合金は知られている。しかし、これらの公報に開示された合金はいずれも、磁気特性としては従来の合金と同程度で、格段の改良を加えたものではなかった。
【０００９】
この発明は、上記の問題点を解決するものであり、加工性の改善された成分系を素材として、優れた製造時や使用時の加工性等を有するとともに、高い電気抵抗と良好な高周波鉄損特性を有し、さらに耐食性も良好なFe−Cr−Si系合金を、その有利な製造方法とともに提案することを目的とする。
【００１０】
【課題を解決するための手段】
発明者らは上記目的を達成すべく鋭意研究を行った結果、次のような知見を得た。まず、加工性（ほぼ靱性によって評価することができる。）の確保に関して、Fe−Si合金やFe−Si−Al合金の靱性向上のためには予想外にもCrを共存させることが効果があることを見いだした。すなわち、これまではCrを添加するほど靱性は劣化すると考えられてきたが、Siが3 wt％以上又はAlが1 wt％以上の含有量であっても、Ｃ＋Ｎの含有量を十分に低減した上で、一定量以上のCrを含有させることにより、むしろ高い靱性が得られることを見出した。
しかも、更にSi量又はAl量が低いFe−Cr−Si系合金（Fe−Cr−Si合金の他、Fe−Cr−Si−Al合金も含む。以下同じ。）であって、比抵抗が60μΩcm以上となる成分系においても、Ｃ＋Ｎの含有量を十分に低減すれば、同等の比抵抗をもつFe−Si合金やFe−Si−Al合金よりも加工性が大幅に向上することを見出したのである。
【００１１】
また、磁気特性については、Cr、Si又はAlを同時に含有させることにより、電気抵抗の増大に相乗的な効果が現れることを見いだした。その結果、特に高周波域での鉄損を、SiやAlのみを含有するFe−Si合金、Fe−Al合金、更にはFe−Si−Al合金に比べて格段に低減することができるに至った。
しかも、このようにCrを添加すれば、このCrの効果によって耐食性は従来のFe−Si系に比べて確実に向上する。
【００１２】
更に、上述した成分に加えて、Mn、Ｐ、Sb、Sn、Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ又はCoを含有させることにより、鉄損特性や加工性、耐食性などを更に向上し得ることを見出した。
【００１３】
この発明は上記の知見に立脚するものである。
すなわち、この発明のFe−Cr−Si系合金は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Sb、Snから選ばれる１種又は２種を、それぞれ１wt％以下
で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１４】
この発明の他の態様は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは５wt％以下、Mn及びＰはそれぞれ１wt％以下の範囲で含有し、
Sb、Snから選ばれる１種又は２種を、それぞれ１wt％以下
で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１５】
この発明の他の態様は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは５wt％以下、Cu、La及びＶは１wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１６】
この発明の他の態様は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは５wt％以下、Mn及びＰはそれぞれ１wt％以下の範囲で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは５wt％以下、Cu、La及びＶは１wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１７】
この発明の他の態様は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Sb、Snから選ばれる１種又は２種を、それぞれ１wt％以下
で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは５wt％以下、Cu、La及びＶは１wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１８】
この発明の他の態様は、
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは５wt％以下、Mn及びＰはそれぞれ１wt％以下の範囲で含有し、
Sb、Snから選ばれる１種又は２種を、それぞれ１wt％以下
で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは５wt％以下、Cu、La及びＶは１wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなり、比抵抗が60μΩcm以上であることを特徴とする Fe−Cr−Si系合金である。
【００１９】
この発明のFe−Cr−Si系合金の製造方法は、下記に示す６種の合金素材をそれぞれ熱間圧延し、次いで必要に応じて熱延板焼鈍を行った後、１回又は中間焼鈍を含む２回以上の冷間圧延又は温間圧延を施して最終板厚とし、更に、仕上げ焼鈍を施すことを特徴とする。
記
(1)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Sb、Snから選ばれる１種又は２種を、それぞれ1 wt％以下
で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
(2)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは5 wt％以下、Mn及びＰはそれぞれ1wt％以下の範囲で含有し、
Sb、Snから選ばれる１種又は２種を、それぞれ1 wt％以下
で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
(3)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは5 wt％以下、Cu、La及びＶは1 wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
(4)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは5 wt％以下、Mn及びＰはそれぞれ1wt％以下の範囲で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは5 wt％以下、Cu、La及びＶは1 wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
(5)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Sb、Snから選ばれる１種又は２種を、それぞれ1 wt％以下
で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは5 wt％以下、Cu、La及びＶは1 wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
(6)
Cr：1.5 wt％以上20wt％以下及び
Si：2.5 wt％以上10wt％以下
を含み、
Alよりなる群、ならびに、
Mn及びＰから選ばれる１種又は２種よりなる群
のいずれか一方又は双方の群の成分を、Alは5 wt％以下、Mn及びＰはそれぞれ1wt％以下の範囲で含有し、
Sb、Snから選ばれる１種又は２種を、それぞれ1 wt％以下
で含有し、
Ni、Cu、Mo、Ｗ、La、Ｖ、Nb、Ti、Ｙ、Zr、Ｂ及びCoから選ばれる１種又は２種以上を、Ni、Mo、Ｗ及びCoは5 wt％以下、Cu、La及びＶは1 wt％以下、Nb、Ti、Ｙ、Zr及びＢは0.1 wt％以下の範囲で含有し、
Ｃ及びＮを合計量で100 wtppm 以下
に低減し、残部は鉄及び不可避的不純物からなる合金素材。
【００２０】
【発明の実施の形態】
この発明における合金素材の成分組成範囲について数値限定した理由について説明する。
まず、Crは、Si及び／又はAlとの相乗効果によって電気抵抗を大幅に向上させて高周波域での鉄損を低減し、更には耐食性を向上させる基本的な合金成分である。しかも、3.5 wt％以上のSi含有量の場合、又は3 wt％以上のSi含有量かつ1wt％を超えるAl含有量の場合であっても温間圧延可能な程度の靱性を得るのに極めて有効であり、その観点からはCrは2 wt％以上を要する。Si量やAl量が上記の場合よりも少ないときには、Cr量を更に減じても加工性が確保できるが、Crの加工性向上効果を発揮させ、かつ、合金の比抵抗を60μΩcm以上とするためには、1.5 wt％以上のCrが必須である。一方、20wt％を超えると靱性向上の効果が飽和するとともに、コスト上昇を招くので、Crの含有量は1.5 wt％以上、20wt％以下、好ましくは2 wt％以上、10wt％以下、より好ましくは、3 wt％以上、7 wt％以下とする。
【００２１】
Siは、Crとの相乗効果によって電気抵抗を大幅に上昇させ、高周波域での鉄損を低減するのに有効な成分である。Si量が2.5 wt％未満ではCrやAlを併用しても磁束密度をあまり犠牲にせずに60μΩcm以上の比抵抗を得るには至らない。一方、10wt％を超えるとCrを含有させても温間圧延可能なまでの靱性が確保できないので、Siの含有量は2.5 wt％以上、10wt％以下、好ましくは3 wt％以上、7 wt％以下、より好ましくは3.5 wt％以上、5 wt％以下と規定する。
【００２２】
Sb及びSnは、いずれも集合組織を改善する作用を有し、それにより製品の鉄損特性の向上に寄与する。したがって、この発明では、Sb及びSnから選ばる１種又は２種を、それぞれ1 wt％以下の範囲で添加させることができる。Sb量やSn量が1 wt％を超えると、効果は薄れ、また、コストの上昇を招くことから、Sb量、Sn量の上限は1 wt％とする。なお、Sb量、Sn量の下限は特に限定するものではないが、前述したSb、Snの添加効果を十分に発揮させるためには、それぞれ、0.01wt％以上を添加することが好ましい。
【００２３】
Alは、Siと同様、Crとの相乗効果によって電気抵抗を大幅に向上させ、高周波域での鉄損を低減するのに有効な成分であるので、この発明では必要に応じてAlを含有させることができる。しかし、Al量が5 wt％を超えるとコスト上昇を招く上に、この発明のようにSi量が2.5 wt％以上含有されている場合にCrを含有させても温間圧延可能なまでの靱性が確保できないので、Alの含有量は5 wt％以下とする。Alの下限は特に限定する必要がないが、脱酸や結晶粒成長性の改善のために0.005 〜0.3 wt％程度を含有させることがある。更に、Alを積極的に電気抵抗の増大のために活用するときには、この発明のようにSiが2.5 wt％以上含有されている合金ではAlが0.5 wt％未満では電気抵抗を更に上昇させるに十分な効果が得られない。したがって、この好ましくはAlの含有量は0.005 wt％以上、5 wt％以下、より好ましくは0.5 wt％以上、3 wt％以下と規定する。
【００２４】
Mn及びＰは、Fe−Cr−Si系合金に更に添加することにより、一層の電気抵抗の上昇を与える。これらの成分の添加により、この発明の趣旨を損うことなく、更なる鉄損の低減が達成できる。そこで、この発明では、Mn、Ｐの中から選ばれる１種又は２種を含有させることができる。とはいえ、これらの成分を大量に添加するとコスト上昇を招くので、それぞれの添加量は1 wt％を上限とする。より好ましくは0.5 wt％以下が良い。なお、Mn量、Ｐ量の下限は特に限定するものではないが、前述したMn、Ｐの添加効果を十分に発揮させるためにはそれぞれ、Mnについては0.1 wt％以上、Ｐについては0.05wt％以上を含有させることが好ましい。
【００２５】
Ni及びCuは、いずれも製品の耐食性、耐候性を改善する作用を有する。また、延性−脆性遷移温度を下げて、加工性を向上させる。更に、結晶粒を細粒化する作用を有するため、渦電流損を低減させる効果がある。したがって、この発明では、所望の諸特性に応じて、NiやCuを含有させることができる。Ni量が5 wt％を超える場合、Cu量が1 wt％を超える場合は、いずれも、前述の効果が飽和し、また、延性を劣化させ、また、コスト上昇を招くことから、Ni、Cuの含有量の上限はそれぞれ5 wt％、1 wt％とする。なお、Ni量、Cu量の下限は特に限定するものではないが、前述したNi、Cuの添加効果を十分に発揮させるためには、それぞれ、0.01wt％以上を含有させことが好ましい。
【００２６】
Mo、Ｗは、いずれも製品の耐食性、耐候性を改善する作用を有する。したがって、この発明では、必要に応じてMoやＷを含有させて、耐食性、耐候性の更なる向上を図ることができる。Mo量、Ｗ量が5 wt％を超える場合は、いずれも、前述の効果が飽和し、また、コスト上昇も招くことから、Mo、Ｗの含有量の上限はそれぞれ5 wt％とする。なお、Mo量、Ｗ量の下限は特に限定するものではないが、前述したMo、Ｗの添加効果を十分に発揮させるためには、それぞれ、0.005 wt％以上を含有させことが好ましい。
【００２７】
La、Ｖ、Nb、Ti、Ｙ、Zr及びＢは、いずれも製品の耐食性、耐候性を改善する作用を有する。したがって、この発明では、必要に応じてMoやＷを含有させて、耐食性、耐候性の更なる向上を図ることができる。La量、Ｖ量が1 wt％を超える場合、Nb量、Ti量、Ｙ量、Zr量又はＢ量が0.1 wt％を超える場合は、いずれも、前述の効果が飽和し、また、コスト上昇も招くことから、La量、Ｖ量の上限はそれぞれ1 wt％、Nb量、Ti量、Ｙ量、Zr量又はＢ量の上限は0.1 wt％とする。なお、これら成分の下限は特に限定するものではないが、これらの添加効果を十分に発揮させるためには、0.005 wt％以上を含有させことが好ましい。
【００２８】
Coは、磁束密度を高め、製品の磁気特性を向上させる作用を有する。したがって、この発明では、Coを含有させることができる。Co量が5 wt％を超える場合、コスト上昇を招くことから、Co含有量の上限は5 wt％とする。なお、Co量の下限は特に限定するものではないが、前述した添加効果を十分に発揮させるためには、0.005 wt％以上を含有させことが好ましい。
【００２９】
Ｃ及びＮは、Fe−Cr−Si系合金の靱性を劣化させるためにできる限り低減するのが好ましく、その許容量はこの発明のCr量、Si量の場合には、高靱性を確保するために合計量で100 wtppm 以下に抑える必要がある。すなわち、先に述べたとり、この発明では、Ｃ＋Ｎの含有量を100 wtppm 以下に低減した上で、一定量以上のCrを含有させることにより、たとえSiを多量に (3.5 wt％を超える量) で含有させる場合であっても、優れた高い靱性が得られ、製造時及び製品加工時の加工性が改善されるとともに、高周波鉄損特性が格段に向上するのである。Ｃ＋Ｎの含有量は、好ましくは60wtppm 以下、より好ましくは30wtppm 以下である。なお、Ｃ又はＮの各々は、Ｃが50wtppm 以下、Ｎが80wtppm 以下が良く、より好ましくはＣが30wtppm 以下、Ｎが50wtppm 以下が良い。更に好ましくは、Ｃが10wtppm 以下、Ｎが20wtppm 以下がよい。
また、Ｃ、Ｎ以外の不純物量は特に限定されないが、Ｓ：20wtppm 以下、好ましくは10wtppm 以下、より好ましくは5 wtppm 以下がよい。Ｏ：50wtppm 以下、好ましくは30wtppm 以下、より好ましくは15wtppm 以下が良い。又は、不純物Ｃ＋Ｓ＋Ｎ＋Ｏの合計量で120 wtppm 以下が好ましく、より好ましくは50wtppm 以下が良い。
【００３０】
この発明のFe−Cr−Si系合金薄板は、Ｃ及びＮ合計量を100 wtppm 以下にするように、原料として純度99.9wt％以上の高純度の電解鉄、電解クロム、金属Si、金属Alを用い、Mn、Ｐその他の添加元素を添加する場合には、これらも高純度原料を用いて製造できる。あるいは、転炉法で製造する場合には、所定の純度にまで十分に精錬し、かつ、後工程での汚染を受けないようにして製造することができる。
溶製に際しては、転炉法の他、例えば、高真空（10^-3Torr以下の圧力）の真空溶解炉を用いることもできる。
【００３１】
前述した成分組成範囲に調整された合金素材は、連続鋳造又は造塊−分塊圧延によりスラブとすることができる。また、薄スラブ連続鋳造法を用いて、板厚の薄いスラブを製造することもできる。得られたスラブは、加熱保持後に熱間圧延に供するか、また、CC-DR 法やHCR 法のように、連続鋳造時の顕熱を保持したまま加熱することなく熱間圧延に供することができる。
【００３２】
その後の熱間圧延は、極力薄く圧延することによって、次工程の冷間圧延ないしは温間圧延における加工性、すなわち圧延性を良好にすることができる。これは、この発明のFe−Cr−Si系合金組成の場合には、熱延板の表面部分の方が中心部分よりも靱性が高く、加工性が優れているとの新知見に基づくものである。そのための熱延板の厚みは3 mm以下、好ましくは2.5 mm以下、より好ましくは1.5mm以下とする。
【００３３】
熱間圧延後は、必要に応じて熱延板焼鈍を行う。熱延板焼鈍を行うことにより、圧延された素材の集合組織が改善され、鉄損特性の向上に有利に作用する。また、熱延板焼鈍を行うことにより、圧延素材を軟化できるため、引き続いて行う冷間圧延や温間圧延の作業性を改善することができる。
この熱延板焼鈍条件は、例えば、温度700 〜1100℃、時間1 秒〜2 時間で行う。焼鈍温度が高い場合や焼鈍時間が長い場合は、焼鈍効果が飽和して鉄損特性の一層の改善が見込めないこと及びコスト上昇の要因となること、焼鈍温度が低い場合や焼鈍時間が短い場合は鉄損特性の向上効果が小さいことから、これらの作用効果を考慮して上記の範囲内で定めれば良い。
【００３４】
熱延板焼鈍後は、酸洗もしくはショットブラスト等により熱延スケールを除去した後に、冷間圧延や温間圧延を行う。熱延板の靱性が改善されているため、更に温間や冷間で圧延して0.4 mm以下の厚みの薄板とすることができる。一般に、板厚を減じると、とりわけ高周波において渦電流損が有利に抑制され、低鉄損になることは周知である。しかし、これまでは高電気抵抗の材料は圧延性が悪く、通常の圧延法によっては0.5 mm程度までしか減厚されていなかった。また、単に厚みを減じてもヒステリシス損失のために、十分な鉄損低減ができないとされてきた。この点、この発明では、素材成分と純度を調整することにより、減厚した場合の特性の効果を促進し得る。かかる減厚の効果を得るためには、板厚を0.4mm以下とすることが有効である。もっとも、0.01mmよりも薄くするには、コスト上、工業的に無理があるので、板厚の範囲を0.01〜0.4 mm、好ましくは0.03〜0.35mmとする。
【００３５】
以上のような冷間圧延や温間圧延は、１回の圧延又は途中焼鈍を含む２回以上の圧延により行う。途中焼鈍を行うことは、圧延材の集合組織の改善を通じて鉄損特性の向上に有利に作用する。また、この冷間圧延や温間圧延の作業性を改善することができる。途中焼鈍の条件は、例えば、温度600 〜1100℃で時間1 秒〜10分の範囲とする。焼鈍温度が低い場合や焼鈍時間が短い場合は鉄損特性の向上効果が小さいこと、焼鈍温度が高い場合や焼鈍時間が長い場合は、焼鈍効果が飽和して鉄損特性の一層の改善が見込めないこと及びコスト上昇の要因となることから、これらの作用効果を考慮して上記の範囲内で定めれば良い。
ここで、冷間圧延及び温間圧延は、コストの面からできるだけ低い温度とすることが好ましい。温間圧延を行う場合は、300 ℃程度以下の温度とすることが望ましい。
【００３６】
冷間圧延、温間圧延の後は、仕上げ焼鈍を施し、更に絶縁被膜を被成して製品とする。これらの仕上げ焼鈍の条件、絶縁被膜の被成条件に関しては、通常の電磁鋼板や電磁ステンレス鋼板で常用される方法と同様にすればよい。
【００３７】
【実施例】
（実施例１）
表１に示す成分組成を含み、残部は実質的に鉄の組成よりなる種々の鋼を溶製し、連続鋳造によりスラブとした。これらのスラブを1100℃に加熱してから、熱間粗圧延とそれに引き続き熱間仕上げ圧延を行って板厚1.6 mmとした。
【００３８】
【表１】

【００３９】
熱延後は、熱延板焼鈍を行うことなく脱スケール処理をした後、１回の冷間圧延又は温間圧延を行って最終板厚0.1 mmとした。熱延後、850 ℃の仕上げ焼鈍を行い、絶縁被膜を表面に被成させて製品とした。
かくして得られた製品の機械的特性、磁気特性について調べた結果を表２に示す。なお、表中、延性−脆性遷移温度は、熱延板からＶノッチのシャルピー試験片を圧延方向と平行に採取し、25℃おきの温度でシャルピー衝撃値を測定して、脆性破面率が50％になる温度、すなわち延性−脆性遷移温度を靱性の指標として求めた。また、鉄損特性は、エプスタイン試験片を調製して周波数10kHz 、磁束密度0.1 T における鉄損値を測定した。また、同じ製品の絶縁被膜を被成しない合金から、幅30mm、長さ280 mmの試験片を切り出して、四端子法によって比抵抗を測定した。
【００４０】
【表２】

【００４１】
表２に示された鋼のうち、番号１の鋼は、Si量が2.5 wt％に満たないため、比抵抗が低く、鉄損特性が良好でない。番号６の鋼は、Ｃ＋Ｎ量が100 wtppm を超えているため、延性−脆性遷移温度が高い。番号２，７の鋼は、Sn、Sbを含有しないため鉄損特性が良好でない。。
これに対して、この発明の成分組成範囲内にある番号3 〜5 、8 〜13の鋼は、靱性も鉄損も良好であって磁性材料として極めて優秀である。特に、SbやSnを添加することによって、Sb、Sn無添加の番号2 や7 の鋼と比較して、磁気特性が改善されていることが分かる。
【００４２】
（実施例２）
表３に示す種々の成分を含み、残部は実質的に鉄の組成よりなる鋼を溶製し、連続鋳造によりスラブとした。これらのスラブを1100℃に加熱してから、熱間圧延を行って板厚2.0 mmとした。
熱延後は、熱延板焼鈍を行うことなく脱スケール処理をした後、１回の冷間圧又は温間圧延を行って、最終板厚0.2 mmになる鋼板を得た。その後、950 ℃の仕上げ焼鈍を行い、絶縁被膜を表面に被成させて製品とした。
【００４３】
【表３】

【００４４】
かくして得られた製品の機械的特性、鉄損特性及び耐食性について調べた結果を表４に示す。また、耐食性はJIS Z2371 に準拠した塩水噴霧試験を2 時間行い、板表面の錆発生面積率が20％以下なら「良」、20％を超え80％以下なら「中」、80％超えなら「劣」と判定した。なお、耐食性の評価は、絶縁被膜を被成しない合金について行った。また、鉄損特性の評価法は、実施例１と同じであり、表４中、耐食性が最良とは、板表面の錆発生面積率が5 ％以下の場合である。
【００４５】
【表４】

表４より、この発明に従い種々の成分組成を有する鋼は、Si、Crのみを含有する比較例に比べて、機械的特性、鉄損特性又は耐食性に優れることが明らかである。
【００４６】
（実施例３）
表５に示す種々の成分を含み、残部は実質的に鉄の組成よりなる鋼を溶製し、連続鋳造によりスラブとした。これらのスラブを1050℃に加熱してから、熱間圧延を行って板厚2.6 mmとした。
熱延後は、熱延板焼鈍を行うことなく脱スケール処理をした後、900 ℃、2 分間の中間焼鈍を含む２回の冷間圧延又は温間圧延を行って、最終板厚0.1 mmになる鋼板を得た。その後、820 ℃の仕上げ焼鈍を行い、絶縁被膜を表面に被成させて製品とした。
【００４７】
【表５】

【００４８】
かくして得られた製品の機械的特性、磁気特性について調べた結果を表６に示す。磁束密度は、磁化力 H：5000A/m のときの磁束密度B₅₀ を測定した。
表６より、この発明に従いCoを有する鋼は、Si、Crのみを含有する比較例に比べて、磁気特性に優れることが明らかである。特に、Coを含有することにより、磁束密度が良好となる。
【００４９】
【表６】

【００５０】
（実施例４）
表７に示す種々の成分組成を含み、残部は実質的に鉄の組成よりなる鋼を溶製し、連続鋳造によりスラブとした。これらのスラブを1050℃に加熱してから、熱間圧延を行って板厚2.0 mmとした。
【００５１】
熱延後は、熱延板焼鈍を行う場合と熱延板焼鈍を行わない場合との２条件を行い（熱延板焼鈍を行う場合は、1000℃、1 分間）、次いで脱スケール処理をした後、表８に示すように１回又は中間焼鈍（850 ℃、20秒）を含む２回の冷間圧延を行って、最終板厚0.1 mmの鋼板を得た。その後、820 ℃の仕上げ焼鈍を行い、絶縁被膜を表面に被成させて製品とした。
【００５２】
【表７】

【００５３】
かくして得られた製品の磁気特性について調べた結果を表８に併記する。
表７及び表８より、同一鋼種、同一板厚であっても、熱延板焼鈍を施さない鋼に比べて、熱延板焼鈍を施した鋼は、鉄損が改善されていることが分かる。また、同一鋼種の場合は、中間焼鈍の回数が多いほど鉄損の低い製品が得られることがわかる。
【００５４】
【表８】

【００５５】
（実施例５）
表３及び表９に示す成分組成を含み、残部は実質的に鉄の組成よりなる種々の鋼を溶製し、連続鋳造によりスラブとした。これらのスラブを1050℃に加熱してから、熱間圧延を行って板厚1.8 mmとした。
熱延後は、1000℃で120 秒の熱延板焼鈍を行った後、脱スケール処理をした後、900 ℃で30秒の途中焼鈍を含む２回の冷間圧延を行って最終板厚0.1 mmとした。熱延後、820 ℃の仕上げ焼鈍を行い、絶縁被膜を表面に被成させて製品とした。
【００５６】
かくして得られた製品の磁気特性について調べた結果を表１０に示す。表１０から、この発明に従う成分組成範囲を有する鋼は、磁気特性に優れることが明らかである。
【００５７】
【表９】

【００５８】
【表１０】

【００５９】
【発明の効果】
かくして、この発明によれば、従来のSi量6.5 wt％までのFe−Si合金やFe−Al合金に比べて格段に優れた鉄損特性を、良好な加工性とともに確保することかできる。しかも、耐食性や製造コスト面からも有利であり、総合的に極めて優秀な磁性材料を与えるものである。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to an Fe—Cr—Si alloy having good iron loss characteristics when used as an electromagnetic steel sheet at a frequency higher than a commercial frequency, and a method for producing the same.
[0002]
[Prior art]
Fe-Si alloys are known as materials with excellent soft magnetic properties. Among them, Fe-Si alloys with an Si content of 3.5 wt% or less are widely used as electromagnetic steel sheets, mainly for various iron cores for commercial frequencies. . However, when the operating frequency is higher than the commercial frequency, there is a disadvantage that the iron loss is increased in the electrical steel sheet having the Si content of 3.5 wt% or less. Therefore, in applications that are used in a frequency range higher than the commercial frequency, a material having a higher electrical resistance is required to improve the iron loss characteristics.
[0003]
In general, increasing the amount of Si in steel increases the electrical resistance, which is advantageous in reducing iron loss in the high frequency range as described above. However, on the other hand, if the Si content exceeds 3.5 wt%, the alloy becomes extremely hard and brittle, and the workability is inferior, making it difficult to manufacture and process by rolling. In particular, when the Si content exceeds 5.0 wt%, not only cold working but also warm working becomes impossible.
[0004]
As a technique for improving the workability of this high-Si steel and industrially producing a steel sheet even if it contains about 6.5 wt% of Si, it is under the low-temperature strong pressure disclosed in JP-A-61-166923. A typical method is a method using hot rolling, and a method using a diffusion and permeation treatment of Si disclosed in JP-A-62-227078.
[0005]
[Problems to be solved by the invention]
However, the technique disclosed in the former Japanese Patent Application Laid-Open No. 61-166923 has to finely adjust the rolling structure in order to apparently improve brittleness as an alloy. Therefore, strict control must be performed in the manufacturing process, and it is very difficult to produce industrially stably. On the other hand, the technique disclosed in the latter Japanese Patent Application Laid-Open No. 62-227078 uses a special diffusion permeation method, which is extremely disadvantageous in terms of cost in industrial production. Even if the Si amount is increased by these methods in order to obtain good high-frequency magnetic characteristics, there is a limit to the increase in electrical resistance.
In addition, when the amount of Si was 3.5 wt% or less that could be produced by a normal industrial rolling method, only a specific resistance of the order of 50 μΩcm was obtained.
Moreover, the point that these Fe-Si alloys are inferior in corrosion resistance is also a problem in applications such as iron cores.
[0006]
By the way, Al has the effect of increasing electrical resistance in the same manner as Si in terms of magnetic properties, and does not deteriorate workability as much as Si. Thus, it is known that workability is improved by replacing part of Si with Al. Al has disadvantages such as higher cost and greater decrease in magnetic flux density than Si, but for example, steel with a composition of Si: 3 wt%, Al: 0.7 wt%, which can obtain almost the same electrical resistance, Si: With steel having a composition of 3.7 wt%, the former steel containing 0.7 wt% of Al has good workability and cold-rollability. Also, the magnetic characteristics are almost equivalent.
However, when the total amount of Si and Al is 4 wt% or more in a steel with Si: 3 wt% or more, cold rolling becomes impossible, and the total amount of Si and Al exceeds 6 wt%. In some cases, even warm rolling became difficult. Even in the case of this component system, only a specific resistance of less than 60 μΩcm was obtained industrially.
[0007]
After all, rather than simply reducing the iron loss in the high frequency range by simply increasing the amount of Si or Al, the iron loss characteristics over the high frequency range are achieved by a new component-based alloy with essentially improved workability. At the same time, it is desirable to ensure processability and to satisfy corrosion resistance and the like.
[0008]
Regarding the corrosion resistance of the Fe-Si alloy, as a means for improving the corrosion resistance of the Fe-Si alloy, a method of adding a certain amount of Cr is disclosed in Japanese Patent Laid-Open Nos. 52-24117 and 61-272352. Is disclosed. Thus, alloys whose corrosion resistance is improved by the addition of Cr are known. However, all of the alloys disclosed in these publications have the same magnetic properties as those of conventional alloys and have not been improved significantly.
[0009]
The present invention solves the above-mentioned problems, and has excellent workability at the time of manufacture and use, etc., using a component system with improved processability as a raw material, and also has high electrical resistance and good high-frequency iron. An object of the present invention is to propose an Fe—Cr—Si alloy having good loss resistance and good corrosion resistance together with its advantageous production method.
[0010]
[Means for Solving the Problems]
As a result of intensive studies to achieve the above object, the inventors have obtained the following knowledge. First, regarding the securing of workability (which can be roughly evaluated by toughness), unexpectedly coexisting Cr is effective for improving the toughness of Fe-Si alloys and Fe-Si-Al alloys. I found out. That is, until now it was thought that the toughness deteriorated as Cr was added, but even if the content of Si was 3 wt% or more or Al was 1 wt% or more, the content of C + N was sufficiently reduced. From the above, it was found that rather high toughness can be obtained by containing a certain amount or more of Cr.
Moreover, it is a Fe-Cr-Si alloy having a lower Si content or Al content (including Fe-Cr-Si-Al alloys in addition to Fe-Cr-Si alloys, the same shall apply hereinafter) with a specific resistance of 60 μΩcm. Even in the above component system, it has been found that if the C + N content is sufficiently reduced, the workability is greatly improved over Fe-Si alloys and Fe-Si-Al alloys having the same specific resistance. is there.
[0011]
In addition, regarding magnetic properties, it was found that a synergistic effect appears in increasing electrical resistance by simultaneously containing Cr, Si or Al. As a result, the iron loss particularly in the high frequency range can be significantly reduced compared to Fe-Si alloys, Fe-Al alloys, and even Fe-Si-Al alloys containing only Si and Al. .
In addition, if Cr is added in this way, the corrosion resistance is reliably improved by the effect of Cr as compared with the conventional Fe-Si system.
[0012]
Furthermore, in addition to the above-described components, iron loss characteristics and the like can be obtained by adding Mn, P, Sb, Sn, Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B or Co. It has been found that processability, corrosion resistance and the like can be further improved.
[0013]
  The present invention is based on the above findings.
  That is, the Fe-Cr-Si alloy of this invention is
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  1 or less each of one or two selected from Sb and Sn
Contained in
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0014]
  Another aspect of the present invention is:
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  A group of Al, and
  A group consisting of one or two selected from Mn and P
The components of either one or both groups are contained within a range of 5 wt% or less for Al and 1 wt% or less for Mn and P, respectively.
  1 or less each of one or two selected from Sb and Sn
Contained in
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0015]
  Another aspect of the present invention is:
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0016]
  Another aspect of the present invention is:
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  A group of Al, and
  A group consisting of one or two selected from Mn and P
The components of either one or both groups are contained within a range of 5 wt% or less for Al and 1 wt% or less for Mn and P, respectively.
  One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0017]
  Another aspect of the present invention is:
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  1 or less each of one or two selected from Sb and Sn
Contained in
  One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0018]
  Another aspect of the present invention is:
  Cr: 1.5 wt% to 20 wt%
  Si: 2.5 wt% to 10 wt%
Including
  A group of Al, and
  A group consisting of one or two selected from Mn and P
The components of either one or both groups are contained within a range of 5 wt% or less for Al and 1 wt% or less for Mn and P, respectively.
  1 or less each of one or two selected from Sb and Sn
Contained in
  One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in 0.1 wt% or less,
  100 wtppm or less in total for C and N
The balance is made of iron and inevitable impurities, and the specific resistance is 60 μΩcm or more.Ru Fe-Cr-Si alloy.
[0019]
In the manufacturing method of the Fe—Cr—Si alloy of the present invention, the following six kinds of alloy materials are each hot-rolled, and then hot-rolled sheet annealing is performed as necessary, and then one time or intermediate annealing is performed. It is characterized in that it is subjected to cold rolling or warm rolling twice or more to obtain a final sheet thickness and further subjected to finish annealing.
Record
(1)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
1 wt% or less of one or two selected from Sb and Sn
Contained in
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
(2)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
A group of Al, and
A group consisting of one or two selected from Mn and P
The component of either one or both of the groups, Al is 5 wt% or less, Mn and P are each in the range of 1 wt% or less,
1 wt% or less of one or two selected from Sb and Sn
Contained in
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
(3)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La And V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in a range of 0.1 wt% or less,
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
(Four)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
A group of Al, and
A group consisting of one or two selected from Mn and P
The component of either one or both of the groups, Al is 5 wt% or less, Mn and P are each in the range of 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La And V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in a range of 0.1 wt% or less,
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
(Five)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
1 wt% or less of one or two selected from Sb and Sn
Contained in
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La And V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in a range of 0.1 wt% or less,
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
(6)
Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% to 10 wt%
Including
A group of Al, and
A group consisting of one or two selected from Mn and P
The component of either one or both of the groups, Al is 5 wt% or less, Mn and P are each in the range of 1 wt% or less,
1 wt% or less of one or two selected from Sb and Sn
Contained in
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La And V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in a range of 0.1 wt% or less,
100 wtppm or less in total for C and N
Alloy material consisting of iron and inevitable impurities.
[0020]
DETAILED DESCRIPTION OF THE INVENTION
The reason why the component composition range of the alloy material in the present invention is numerically limited will be described.
First, Cr is a basic alloy component that greatly improves electrical resistance by a synergistic effect with Si and / or Al, reduces iron loss in a high frequency region, and further improves corrosion resistance. Moreover, it is extremely effective in obtaining toughness that can be warm-rolled even when the Si content is 3.5 wt% or more, or even when the Si content is 3 wt% or more and the Al content exceeds 1 wt%. From that point of view, Cr needs 2 wt% or more. When the amount of Si or Al is less than the above case, workability can be secured even if the Cr amount is further reduced, but the workability improvement effect of Cr is exhibited and the specific resistance of the alloy is set to 60 μΩcm or more. For Cr, 1.5 wt% or more of Cr is essential. On the other hand, if it exceeds 20 wt%, the effect of improving toughness will be saturated and the cost will increase, so the Cr content is 1.5 wt% or more and 20 wt% or less, preferably 2 wt% or more and 10 wt% or less, more preferably 3 wt% or more and 7 wt% or less.
[0021]
Si is an effective component for greatly increasing electric resistance and reducing iron loss in a high frequency range by a synergistic effect with Cr. If the amount of Si is less than 2.5 wt%, even if Cr or Al is used together, a specific resistance of 60 μΩcm or more cannot be obtained without sacrificing the magnetic flux density. On the other hand, if it exceeds 10 wt%, the toughness until warm rolling cannot be secured even if Cr is contained, the Si content is 2.5 wt% or more, 10 wt% or less, preferably 3 wt% or more, 7 wt% Hereinafter, it is defined as 3.5 wt% or more and more preferably 5 wt% or less.
[0022]
Sb and Sn both have the effect of improving the texture, thereby contributing to the improvement of the iron loss characteristics of the product. Therefore, in this invention, 1 type or 2 types chosen from Sb and Sn can be added in the range of 1 wt% or less, respectively. If the amount of Sb or Sn exceeds 1 wt%, the effect is reduced and the cost is increased. Therefore, the upper limit of the amount of Sb and Sn is set to 1 wt%. In addition, although the minimum of Sb amount and Sn amount is not specifically limited, in order to fully exhibit the addition effect of Sb and Sn mentioned above, it is preferable to add 0.01 wt% or more, respectively.
[0023]
Al, like Si, is an effective component for greatly improving electrical resistance and reducing iron loss in the high frequency range due to a synergistic effect with Cr. Therefore, in the present invention, Al is contained as necessary. be able to. However, if the Al content exceeds 5 wt%, the cost will increase, and if the Si content is 2.5 wt% or more as in the present invention, the toughness until warm rolling is possible even if Cr is included Therefore, the Al content should be 5 wt% or less. The lower limit of Al is not particularly limited, but may be contained in an amount of about 0.005 to 0.3 wt% for deoxidation and improvement of crystal grain growth. Furthermore, when Al is actively used to increase the electrical resistance, an alloy containing Si of 2.5 wt% or more as in the present invention is sufficient to further increase the electrical resistance if Al is less than 0.5 wt%. The effect is not obtained. Therefore, the Al content is preferably defined as 0.005 wt% or more and 5 wt% or less, more preferably 0.5 wt% or more and 3 wt% or less.
[0024]
Further addition of Mn and P to the Fe—Cr—Si alloy gives a further increase in electrical resistance. Addition of these components can achieve further reduction of iron loss without detracting from the spirit of the present invention. Therefore, in the present invention, one or two selected from Mn and P can be contained. Nonetheless, adding these components in large amounts increases costs, so the upper limit of each added amount is 1 wt%. More preferably, 0.5 wt% or less is good. In addition, although the lower limit of the amount of Mn and P is not specifically limited, in order to fully demonstrate the addition effect of Mn and P mentioned above, 0.1% by weight or more for Mn and 0.05% by weight for P, respectively. It is preferable to contain the above.
[0025]
Both Ni and Cu have the effect of improving the corrosion resistance and weather resistance of the product. In addition, the ductility-brittle transition temperature is lowered to improve workability. Furthermore, since it has the effect | action which makes a crystal grain fine, it has the effect of reducing an eddy current loss. Therefore, in this invention, Ni and Cu can be contained according to various desired properties. When the Ni content exceeds 5 wt%, and the Cu content exceeds 1 wt%, the above-mentioned effects are saturated, ductility is degraded, and costs are increased. The upper limit of the content of is 5 wt% and 1 wt%, respectively. In addition, although the minimum of Ni amount and Cu amount is not specifically limited, in order to fully exhibit the addition effect of Ni and Cu mentioned above, it is preferable to contain 0.01 wt% or more, respectively.
[0026]
Both Mo and W have the effect of improving the corrosion resistance and weather resistance of the product. Therefore, according to the present invention, Mo and W can be contained as necessary to further improve the corrosion resistance and weather resistance. When the amount of Mo and the amount of W exceed 5 wt%, the above-described effects are saturated and the cost increases, so the upper limit of the contents of Mo and W is 5 wt% respectively. In addition, although the minimum of Mo amount and W amount is not specifically limited, in order to fully exhibit the addition effect of Mo and W mentioned above, it is preferable to contain 0.005 wt% or more, respectively.
[0027]
La, V, Nb, Ti, Y, Zr and B all have an action of improving the corrosion resistance and weather resistance of the product. Therefore, according to the present invention, Mo and W can be contained as necessary to further improve the corrosion resistance and weather resistance. If the amount of La and V exceeds 1 wt%, the amount of Nb, Ti, Y, Zr, or B exceeds 0.1 wt%, the effects will be saturated and the cost will increase. Therefore, the upper limit of La amount and V amount is 1 wt%, and the upper limit of Nb amount, Ti amount, Y amount, Zr amount or B amount is 0.1 wt%. In addition, although the minimum of these components is not specifically limited, In order to fully exhibit these addition effects, it is preferable to contain 0.005 wt% or more.
[0028]
Co has the effect of increasing the magnetic flux density and improving the magnetic properties of the product. Therefore, in this invention, Co can be contained. If the Co content exceeds 5 wt%, the cost will increase, so the upper limit of the Co content is 5 wt%. The lower limit of the amount of Co is not particularly limited, but it is preferable to contain 0.005 wt% or more in order to sufficiently exhibit the above-described addition effect.
[0029]
C and N are preferably reduced as much as possible in order to degrade the toughness of the Fe-Cr-Si alloy, and the allowable amount is in the case of the Cr amount and Si amount of the present invention in order to ensure high toughness. It is necessary to keep the total amount below 100 wtppm. That is, as described above, in the present invention, the content of C + N is reduced to 100 wtppm or less, and by adding a certain amount or more of Cr, a large amount of Si (amount exceeding 3.5 wt%) Even if it is contained, excellent high toughness is obtained, workability at the time of manufacturing and product processing is improved, and high-frequency iron loss characteristics are remarkably improved. The content of C + N is preferably 60 wtppm or less, more preferably 30 wtppm or less. Each of C and N may have C of 50 wtppm or less and N of 80 wtppm or less, more preferably C of 30 wtppm or less and N of 50 wtppm or less. More preferably, C is 10 wtppm or less and N is 20 wtppm or less.
The amount of impurities other than C and N is not particularly limited, but S: 20 wtppm or less, preferably 10 wtppm or less, more preferably 5 wtppm or less. O: 50 wtppm or less, preferably 30 wtppm or less, more preferably 15 wtppm or less. Alternatively, the total amount of impurities C + S + N + O is preferably 120 wtppm or less, more preferably 50 wtppm or less.
[0030]
The Fe-Cr-Si alloy thin plate of the present invention is made of high-purity electrolytic iron, electrolytic chromium, metallic Si, and metallic Al with a purity of 99.9 wt% or more as raw materials so that the total amount of C and N is 100 wtppm or less. When Mn, P and other additive elements are added, these can also be produced using high-purity raw materials. Or when manufacturing by a converter method, it can manufacture, refining enough to predetermined purity, and not receiving the contamination in a post process.
In melting, in addition to the converter method, for example, high vacuum (10^-3A vacuum melting furnace having a pressure equal to or lower than Torr can also be used.
[0031]
The alloy material adjusted to the component composition range described above can be made into a slab by continuous casting or ingot-bundling rolling. Moreover, a thin slab can be manufactured using a thin slab continuous casting method. The obtained slab can be used for hot rolling after being heated, or it can be used for hot rolling without heating while maintaining the sensible heat during continuous casting, as in the CC-DR method and HCR method. it can.
[0032]
Subsequent hot rolling can improve the workability in the next step of cold rolling or warm rolling, that is, rollability, by rolling as thinly as possible. This is based on the new knowledge that in the case of the Fe-Cr-Si alloy composition of the present invention, the surface portion of the hot-rolled sheet has higher toughness and excellent workability than the central portion. is there. For this purpose, the thickness of the hot-rolled sheet is 3 mm or less, preferably 2.5 mm or less, more preferably 1.5 mm or less.
[0033]
After hot rolling, hot-rolled sheet annealing is performed as necessary. By performing hot-rolled sheet annealing, the texture of the rolled material is improved, which advantageously works to improve iron loss characteristics. Moreover, since a rolling raw material can be softened by performing hot-rolled sheet annealing, the workability of the cold rolling and warm rolling performed subsequently can be improved.
The hot-rolled sheet annealing conditions are, for example, a temperature of 700 to 1100 ° C. and a time of 1 second to 2 hours. When the annealing temperature is high or when the annealing time is long, the annealing effect is saturated and no further improvement of the iron loss property can be expected, and the cost increases. When the annealing temperature is low or the annealing time is short Since the effect of improving the iron loss characteristic is small, it may be determined within the above range in consideration of these effects.
[0034]
After hot-rolled sheet annealing, the hot-rolled scale is removed by pickling or shot blasting, and then cold rolling or warm rolling is performed. Since the toughness of the hot-rolled sheet is improved, it can be further rolled hot or cold to form a thin sheet having a thickness of 0.4 mm or less. In general, it is well known that reducing the plate thickness advantageously suppresses eddy current loss, especially at high frequencies, resulting in low iron loss. However, until now, materials with high electrical resistance have poor rollability, and the thickness has been reduced only to about 0.5 mm by a normal rolling method. Further, it has been said that even if the thickness is simply reduced, sufficient iron loss cannot be reduced due to hysteresis loss. In this respect, in the present invention, by adjusting the material component and the purity, the effect of the characteristics when the thickness is reduced can be promoted. In order to obtain such a thickness reduction effect, it is effective to set the plate thickness to 0.4 mm or less. However, in order to make the thickness thinner than 0.01 mm, it is industrially impossible for cost reasons. Therefore, the thickness range is set to 0.01 to 0.4 mm, preferably 0.03 to 0.35 mm.
[0035]
The cold rolling and warm rolling as described above are performed by two or more rollings including one rolling or annealing. Performing annealing in the middle works advantageously to improve iron loss characteristics through improvement of the texture of the rolled material. Moreover, the workability of this cold rolling and warm rolling can be improved. The conditions for the intermediate annealing are, for example, a temperature of 600 to 1100 ° C. and a time of 1 second to 10 minutes. If the annealing temperature is low or the annealing time is short, the effect of improving the iron loss characteristics is small.If the annealing temperature is high or the annealing time is long, the annealing effect is saturated and the iron loss characteristics can be further improved. Therefore, it may be determined within the above range in consideration of these effects.
Here, it is preferable that the cold rolling and the warm rolling be as low as possible in terms of cost. When performing warm rolling, the temperature is preferably about 300 ° C. or lower.
[0036]
After cold rolling and warm rolling, finish annealing is performed, and an insulating film is further formed to obtain a product. These finish annealing conditions and insulating film deposition conditions may be the same as those commonly used for ordinary electromagnetic steel sheets and electromagnetic stainless steel sheets.
[0037]
【Example】
Example 1
Various steels having the composition shown in Table 1 and the balance being substantially composed of iron were melted, and slabs were formed by continuous casting. These slabs were heated to 1100 ° C., followed by hot rough rolling and subsequent hot finish rolling to a thickness of 1.6 mm.
[0038]
[Table 1]

[0039]
After hot rolling, descaling was performed without performing hot rolling sheet annealing, and then a single cold rolling or warm rolling was performed to a final thickness of 0.1 mm. After hot rolling, finish annealing at 850 ° C. was performed, and an insulating film was formed on the surface to obtain a product.
Table 2 shows the results of examining the mechanical and magnetic properties of the product thus obtained. In the table, the ductile-brittle transition temperature is determined by taking a V-notch Charpy test piece from a hot-rolled sheet in parallel with the rolling direction and measuring the Charpy impact value at a temperature of every 25 ° C. The temperature at 50%, that is, the ductile-brittle transition temperature was determined as an indicator of toughness. For the iron loss characteristics, an Epstein test piece was prepared, and the iron loss value at a frequency of 10 kHz and a magnetic flux density of 0.1 T was measured. In addition, a test piece having a width of 30 mm and a length of 280 mm was cut out from an alloy that did not form an insulating coating of the same product, and the specific resistance was measured by a four-terminal method.
[0040]
[Table 2]

[0041]
Among the steels shown in Table 2, steel No. 1 has a low specific resistance and poor iron loss characteristics because the Si content is less than 2.5 wt%. Steel No. 6 has a high ductile-brittle transition temperature because the amount of C + N exceeds 100 wtppm. Since the steels of Nos. 2 and 7 do not contain Sn and Sb, the iron loss characteristics are not good. .
On the other hand, the steels of Nos. 3 to 5 and 8 to 13 within the component composition range of the present invention have excellent toughness and iron loss, and are extremely excellent as magnetic materials. In particular, it can be seen that the addition of Sb or Sn improves the magnetic properties as compared with steels of Nos. 2 and 7 with no addition of Sb and Sn.
[0042]
(Example 2)
Various components shown in Table 3 were included, and the balance was made by melting steel substantially composed of iron, and was made into a slab by continuous casting. These slabs were heated to 1100 ° C. and then hot rolled to a thickness of 2.0 mm.
After hot rolling, the steel sheet was descaled without performing hot-rolled sheet annealing, and then subjected to a single cold pressure or warm rolling to obtain a steel sheet having a final thickness of 0.2 mm. Then, finish annealing at 950 ° C. was performed, and an insulating film was formed on the surface to obtain a product.
[0043]
[Table 3]

[0044]
Table 4 shows the results of examining the mechanical characteristics, iron loss characteristics, and corrosion resistance of the products thus obtained. In addition, the corrosion resistance is a salt spray test in accordance with JIS Z2371 for 2 hours. If the area of rust on the plate surface is 20% or less, it is “good”, if it exceeds 20% and 80% or less, “medium”, and if it exceeds 80%, “ It was judged as “poor”. NaOh,The corrosion resistance was evaluated for an alloy that does not form an insulating coating. Moreover, the evaluation method of the iron loss characteristic is the same as that of Example 1. In Table 4, the corrosion resistance is the best when the rust generation area ratio on the plate surface is 5% or less.
[0045]
[Table 4]

From Table 4, it is clear that steels having various component compositions according to the present invention are superior in mechanical characteristics, iron loss characteristics, or corrosion resistance as compared with comparative examples containing only Si and Cr.
[0046]
(Example 3)
Various components shown in Table 5 were included, and the balance was made by melting steel substantially composed of iron and was made into a slab by continuous casting. These slabs were heated to 1050 ° C. and then hot-rolled to a thickness of 2.6 mm.
After hot rolling, after descaling without hot-rolled sheet annealing, two cold rollings or warm rolling processes including intermediate annealing at 900 ° C for 2 minutes are performed to a final sheet thickness of 0.1 mm. A steel plate was obtained. Thereafter, finish annealing at 820 ° C. was performed, and an insulating film was formed on the surface to obtain a product.
[0047]
[Table 5]

[0048]
Table 6 shows the results of examining the mechanical and magnetic properties of the product thus obtained. The magnetic flux density is the magnetic flux density B when the magnetizing force H is 5000A / m.₅₀ Was measured.
From Table 6, it is clear that the steel having Co according to the present invention is superior in magnetic properties as compared with the comparative example containing only Si and Cr. In particular, the magnetic flux density is improved by containing Co.
[0049]
[Table 6]

[0050]
(Example 4)
The various components composition shown in Table 7 was included, and the balance was made by melting steel substantially composed of iron and made into a slab by continuous casting. These slabs were heated to 1050 ° C. and then hot-rolled to a thickness of 2.0 mm.
[0051]
After hot-rolling, two conditions were performed: hot-rolled sheet annealing and non-hot-rolled sheet annealing (when hot-rolled sheet annealing was performed, 1000 ° C, 1 minute), and then descaling was performed. Thereafter, as shown in Table 8, one or two cold rollings including intermediate annealing (850 ° C., 20 seconds) were performed to obtain a steel sheet having a final thickness of 0.1 mm. Thereafter, finish annealing at 820 ° C. was performed, and an insulating film was formed on the surface to obtain a product.
[0052]
[Table 7]

[0053]
The results of examining the magnetic properties of the products thus obtained are also shown in Table 8.
From Tables 7 and 8, it can be seen that even if the steel type and thickness are the same, steel subjected to hot-rolled sheet annealing has improved iron loss compared to steel not subjected to hot-rolled sheet annealing. . Moreover, in the case of the same steel type, it turns out that a product with a low iron loss is obtained, so that the number of intermediate annealing is large.
[0054]
[Table 8]

[0055]
(Example 5)
Various steels including the composition of components shown in Tables 3 and 9 were melted, and the remainder was substantially made of iron, and slabs were formed by continuous casting. These slabs were heated to 1050 ° C. and then hot-rolled to a thickness of 1.8 mm.
After hot rolling, after hot-rolled sheet annealing at 1000 ° C for 120 seconds, descaling was performed, and then cold rolling was performed twice at 900 ° C including 30-second annealing for a final sheet thickness of 0.1 mm. After hot rolling, final annealing at 820 ° C. was performed, and an insulating coating was formed on the surface to obtain a product.
[0056]
Table 10 shows the results of examining the magnetic properties of the products thus obtained. From Table 10, it is clear that the steel having the component composition range according to the present invention is excellent in magnetic properties.
[0057]
[Table 9]

[0058]
[Table 10]

[0059]
【The invention's effect】
Thus, according to the present invention, it is possible to ensure iron loss characteristics that are markedly superior to those of conventional Fe—Si alloys and Fe—Al alloys up to a Si content of 6.5 wt%, as well as good workability. In addition, it is advantageous in terms of corrosion resistance and manufacturing cost, and provides a comprehensively excellent magnetic material.

Claims

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in 0.1 wt% or less,
C and N reduced in a total amount to 100 wtppm or less, the balance being iron and unavoidable impurities, specific resistance you characterized in that at least 60μΩcm Fe -Cr-Si based alloy.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.

Cr: 1.5 wt% to 20 wt%
Si: 2.5 wt% or more and 10 wt% or less
A group of Al, and
A component of either one or both of the group consisting of one or two selected from Mn and P, Al is contained in a range of 5 wt% or less, Mn and P are each contained in a range of 1 wt% or less,
1 type or 2 types selected from Sb and Sn, each containing 1 wt% or less,
One or more selected from Ni, Cu, Mo, W, La, V, Nb, Ti, Y, Zr, B and Co. Ni, Mo, W and Co are 5 wt% or less, Cu, La and V is 1 wt% or less, Nb, Ti, Y, Zr and B are contained in the range of 0.1 wt% or less,
C and N are reduced to 100 wtppm or less in the total amount, and the balance is hot-rolled with an alloy material consisting of iron and inevitable impurities, and then hot-rolled sheet annealing is performed as necessary, then once or intermediate annealing to a final thickness is subjected to between two or more cold rolling or warm rolling containing, further, the manufacturing method of the Fe -Cr-Si alloy you characterized by applying finish annealing.