JPH07180003A - Fe-ni magnetic alloy excellent in hot workability and magnetic property - Google Patents
Fe-ni magnetic alloy excellent in hot workability and magnetic propertyInfo
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- JPH07180003A JPH07180003A JP32283493A JP32283493A JPH07180003A JP H07180003 A JPH07180003 A JP H07180003A JP 32283493 A JP32283493 A JP 32283493A JP 32283493 A JP32283493 A JP 32283493A JP H07180003 A JPH07180003 A JP H07180003A
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、熱間圧延時に発生する
耳割れ現象を実操業上問題にならない程度に低減改善
し、しかも磁気特性にも優れたＦｅ−Ｎｉ系磁性合金に
関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a Fe-Ni-based magnetic alloy which has reduced and improved edge cracking phenomenon that occurs during hot rolling to the extent that it does not pose a problem in actual operation and has excellent magnetic properties. .
【０００２】[0002]
【従来の技術】Ｆｅ−Ｎｉ系磁性合金は、いわゆるパー
マロイと呼ばれ、磁気ヘッドや磁気シールド等の軟質磁
性材料として広く使用されている。このような用途には
薄板或いは箔が使用され、スラブを熱間圧延し、次いで
冷間圧延して製造される。2. Description of the Related Art Fe-Ni magnetic alloys are so-called permalloys and are widely used as soft magnetic materials for magnetic heads and magnetic shields. Sheets or foils are used for such applications and are manufactured by hot rolling and then cold rolling slabs.
【０００３】しかしながら、Ｆｅ−Ｎｉ系磁性合金を熱
間圧延すると、熱間加工性が悪いので耳割れが発生する
ことがある。熱間圧延合金板及び帯に耳割れが存在する
と、後工程の冷間圧延時に板破断するので冷間圧延前に
トリミングを行う必要がある。このことは、歩留りを著
しく低下させる原因となっている。その対策として本出
願人は、熱間加工性低下の原因となるＳの粒界偏析を防
止するために、Ｓの低減化及びＢの適量添加が有効であ
ることを特開平２−１１１８３８号公報により提案して
いる。しかしながら、Ｂの添加はコストが高くなり、経
済性に劣るといった短所がある。However, when the Fe-Ni magnetic alloy is hot-rolled, the hot workability is poor and ear cracking may occur. If the hot-rolled alloy sheet and the strip have edge cracks, the sheet is broken during cold rolling in the subsequent process, and therefore it is necessary to perform trimming before cold rolling. This causes a significant decrease in yield. As a countermeasure against this, the applicant of the present invention discloses that reduction of S and addition of an appropriate amount of B are effective in order to prevent segregation of S in grain boundaries, which causes deterioration of hot workability. Is proposed by. However, the addition of B has the disadvantages of high cost and poor economic efficiency.
【０００４】また、従来の製造法では、原料としてスク
ラップが使用されている。近年、製造コストの低減化を
目的に低価格のスクラップが大量に使われる傾向にあ
る。この場合、スクラップ中に存在する不純物元素の材
質特性に及ぼす影響を考慮する必要がある。これまで鋼
中のＰｂ，Ｂｉ，Ｓｎ，Ｚｎ，Ｓ等の不純物元素濃度が
上昇すると、熱間加工時に割れが発生すると言われてき
た。Further, in the conventional manufacturing method, scrap is used as a raw material. In recent years, a large amount of low-priced scrap tends to be used for the purpose of reducing the manufacturing cost. In this case, it is necessary to consider the influence of the impurity elements present in the scrap on the material properties. Up to now, it has been said that when the concentration of impurity elements such as Pb, Bi, Sn, Zn and S in steel increases, cracking occurs during hot working.
【０００５】これまで本出願人は、特願平４−３４９５
２８号において、Ｓｎを添加したオーステナイト系ステ
ンレス鋼において、不純物元素量を規制して材質特性の
劣化を抑え、さらにＡｌ，Ｃａにより脱硫を強化した熱
間加工性の優れたオーステナイト系ステンレス鋼を提案
してきた。しかしながら、Ｆｅ−Ｎｉ系磁性合金にＡｌ
を添加することは、磁性焼鈍後にＡｌ2 Ｏ3 が製品表面
に濃化し白濁現象を起こしたり、またＳｎを添加するこ
とは、磁気特性を劣化させることになり有効ではない。Up to now, the present applicant has filed Japanese Patent Application No. 4-3495.
No. 28 proposes an austenitic stainless steel with excellent hot workability in which austenitic stainless steel containing Sn is regulated by controlling the amount of impurity elements to suppress deterioration of material properties, and desulfurization is strengthened by Al and Ca. I've been However, the Fe--Ni magnetic alloy has Al
Addition of Al causes Al 2 O 3 to concentrate on the surface of the product after magnetic annealing to cause a clouding phenomenon, and addition of Sn deteriorates the magnetic properties and is not effective.
【０００６】一方、本出願人は、特願平５−７０２０２
号において、６５〜８５％Ｎｉ−Ｆｅ系合金にＢ及びＭ
ｏを添加し、さらに、不純物元素量を規制した熱間加工
性及び磁性特性の優れたＦｅ−Ｎｉ系磁性合金を提案し
てきた。しかしながら、３０〜５５％程度のＮｉを含む
Ｎｉ−Ｆｅ系合金では、Ｂの添加による熱間加工性の改
善あるいは、Ｍｏの添加による磁気特性の改善はあまり
認められないことが知られている。On the other hand, the present applicant has filed Japanese Patent Application No. 5-70202.
No. 65-85% Ni-Fe alloys with B and M
In addition, Fe-Ni-based magnetic alloys have been proposed, in which O is added and the amount of impurity elements is regulated and hot workability and magnetic properties are excellent. However, it is known that in a Ni—Fe based alloy containing about 30 to 55% Ni, improvement of hot workability by addition of B or improvement of magnetic properties by addition of Mo is not observed so much.
【０００７】従来、耳割れ現象を防止し熱間加工性を向
上させるためには、Ｍｎ，Ｔｉ，Ｍｇ等の元素を添加さ
せる方法が知られている。しかしＭｎ，Ｔｉ，Ｍｇ等の
過度の添加は磁気特性を低下させる一方、最終工程であ
る磁性焼鈍時に表面に白濁現象が発生し製品の意匠性を
損なうために問題がある。磁気特性の点からは、磁気ヘ
ッド、磁気シールド材等の使用周波数域の上昇に伴い、
ますます高い磁気特性が要求されている。Conventionally, in order to prevent the ear cracking phenomenon and improve the hot workability, a method of adding elements such as Mn, Ti and Mg has been known. However, while excessive addition of Mn, Ti, Mg, etc. deteriorates the magnetic properties, a white turbid phenomenon occurs on the surface during the final step of magnetic annealing, which impairs the design of the product, which is a problem. From the viewpoint of magnetic characteristics, as the operating frequency range of magnetic heads and magnetic shield materials increases,
Increasingly high magnetic properties are required.
【０００８】従って、熱間圧延時に発生する耳割れ現象
のない、熱間加工性及び磁気特性に優れたＦｅ−Ｎｉ系
磁性合金が強く要望されている。Therefore, there is a strong demand for an Fe-Ni-based magnetic alloy which is free from the edge cracking phenomenon that occurs during hot rolling and is excellent in hot workability and magnetic properties.
【０００９】[0009]
【発明が解決しようとする課題】本発明は、以上のよう
な熱間圧延時に発生する耳割れ現象を、実操業上問題に
ならない程度に低減改善し、しかも磁気特性にも優れた
Ｆｅ−Ｎｉ系磁性合金を提供することを目的とする。SUMMARY OF THE INVENTION The present invention reduces and improves the edge cracking phenomenon that occurs during hot rolling as described above to the extent that it does not pose a problem in actual operation, and is also excellent in magnetic characteristics. An object of the present invention is to provide a magnetic alloy.
【００１０】[0010]
【課題を解決するための手段、作用】本発明は、この目
的のために熱間加工性に及ぼすＰｂ，Ｂｉ，Ｓｎ，Ｚ
ｎ，Ｓ等不純物元素の影響を詳細に調査し、その他の成
分も種々検討した結果、下記のように成分を限定するこ
とにより達成されたものである。すなわち本発明の要旨
は、重量％にて、Ｎｉ：３０〜５５％、Ｃ：０．０３％
以下、Ｓｉ：０．０５〜１．０％、Ｍｎ：２．０％以
下、Ｔｉ：０．０５％以下、Ｍｇ：０．０５％以下、Ａ
ｌ：０．０５％以下、Ｏ：０．００８％以下、Ｎ：０．
００８％以下とし、更にＰｂ，Ｂｉ，Ｓｎ，Ｚｎ，Ｓの
含有量が、重量ｐｐｍで、Ｐｂ：１５ｐｐｍ以下、Ｂ
ｉ：１５ｐｐｍ以下、Ｓｎ：２００ｐｐｍ以下、Ｚｎ：
２０ｐｐｍ以下、Ｓ：５０ｐｐｍ以下であり、かつ１式
で規定されるＣＶの値が２５ｐｐｍ以下であり、残部が
Ｆｅおよび不可避的不純物からなることを特徴とする熱
間加工性及び磁気特性に優れたＦｅ−Ｎｉ系磁性合金に
ある。For the purpose of the present invention, the present invention has an effect on the hot workability of Pb, Bi, Sn, Z.
As a result of detailed investigation of the influence of impurity elements such as n and S, and various investigations on other components, it was achieved by limiting the components as described below. That is, the gist of the present invention is, in% by weight, Ni: 30 to 55%, C: 0.03%.
Hereinafter, Si: 0.05 to 1.0%, Mn: 2.0% or less, Ti: 0.05% or less, Mg: 0.05% or less, A
1: 0.05% or less, O: 0.008% or less, N: 0.
008% or less, and the content of Pb, Bi, Sn, Zn, S is ppm by weight, Pb: 15 ppm or less, B
i: 15 ppm or less, Sn: 200 ppm or less, Zn:
20 ppm or less, S: 50 ppm or less, the CV value defined by the formula 1 was 25 ppm or less, and the balance being Fe and inevitable impurities, and was excellent in hot workability and magnetic properties. Fe-Ni magnetic alloy.
【００１１】 ＣＶ＝Ｐｂ＋Ｂｉ＋０．０３Ｓｎ＋０．６３Ｚｎ＋０．２１Ｓ １式 以下、本発明合金の化学成分の限定理由について詳細に
説明する。Ｎｉは、本合金の基本成分であり、Ｎｉが３
０％未満の場合、または５５％を超える場合は合金の磁
気特性が低下して、軟質磁性材料としての特性を発揮で
きなくなる。従って、Ｎｉの範囲は３０〜５５％とし
た。CV = Pb + Bi + 0.03Sn + 0.63Zn + 0.21S 1 Formula Hereinafter, the reasons for limiting the chemical components of the alloy of the present invention will be described in detail. Ni is a basic component of this alloy, and Ni is 3
If it is less than 0% or exceeds 55%, the magnetic properties of the alloy are deteriorated and the properties as a soft magnetic material cannot be exhibited. Therefore, the range of Ni is set to 30 to 55%.
【００１２】Ｃは、含有量が多くなりすぎると合金中に
炭化物を形成し、熱間加工性や磁気特性を劣化させるた
め、その上限を０．０３％とした。Ｓｉは、脱酸剤とし
て有効な成分であり、０．０５％未満ではその効果が少
なく、また１．０％を超える場合は、ＳｉＯ2 が顕著に
生成するために磁気特性が劣化する。従って、Ｓｉの範
囲は０．０５〜１．０％とした。さらに好ましくは、
０．２０〜０．５０％が良い。If the content of C is too large, it forms carbides in the alloy and deteriorates hot workability and magnetic properties, so the upper limit was made 0.03%. Si is an effective component as a deoxidizing agent, and if it is less than 0.05%, its effect is small, and if it exceeds 1.0%, SiO 2 is remarkably generated and the magnetic properties are deteriorated. Therefore, the range of Si is set to 0.05 to 1.0%. More preferably,
0.20 to 0.50% is good.
【００１３】Ｍｎは、２．０％を超えると熱間加工性を
飽和させるために、その上限を２．０％とした。Ｔｉ
は、熱間加工性を向上させ、また脱酸剤としても有効な
成分であるが、０．０５％を超えると磁性焼鈍後にＴｉ
Ｏ2 が製品表面に偏析し白濁現象を起こすので、その上
限を０．０５％とした。さらに好ましくは、０．０３％
以下が良い。When Mn exceeds 2.0%, the hot workability is saturated, so the upper limit was made 2.0%. Ti
Is a component that improves hot workability and is also effective as a deoxidizing agent. However, if it exceeds 0.05%, Ti after magnetic annealing is
O 2 segregates on the surface of the product and causes a white turbidity phenomenon, so the upper limit was made 0.05%. More preferably, 0.03%
The following is good.
【００１４】Ｍｇは、熱間加工性を向上させるために有
効な成分であるが、０．０５％を超えると磁性焼鈍後に
ＭｇＯが製品表面に偏析し白濁現象を起こすので、その
上限を０．０５％とした。さらに好ましくは、０．０３
％以下が良い。Ａｌは、脱酸剤として有効な成分である
が、０．０５％を超えると磁性焼鈍後にＡｌ2 Ｏ3 が製
品表面に濃化し白濁現象を起こすので、その上限を０．
０５％とした。さらに好ましくは、０．０３％以下が良
い。Mg is an effective component for improving hot workability, but if it exceeds 0.05%, MgO segregates on the product surface after magnetic annealing to cause a clouding phenomenon, so the upper limit is set to 0. It was set to 05%. More preferably, 0.03
% Or less is good. Al is an effective component as a deoxidizing agent, but if it exceeds 0.05%, Al 2 O 3 concentrates on the product surface after magnetic annealing and causes a clouding phenomenon, so the upper limit is set to 0.
It was set to 05%. More preferably, it is 0.03% or less.
【００１５】Ｏは、含有量が多くなりすぎると酸化物が
析出し磁気特性を劣化させるので、その上限を０．００
８％とした。さらに好ましくは、０．００３％以下が良
い。Ｎは、含有量が多くなりすぎると窒化物が析出し磁
気特性を劣化させるので、その上限を０．００８％とし
た。さらに好ましくは、０．００３％以下が良い。Ｐ
ｂ，Ｚｎ，Ｂｉは凝固時の溶質濃化により偏析しやす
く、かつ粒界で低融点相を形成しやすいため、熱間加工
性を著しく低下させる。このため、Ｐｂ，Ｂｉの上限を
１５ｐｐｍ、Ｚｎの上限を２０ｐｐｍとした。If the content of O is too large, an oxide precipitates and deteriorates the magnetic properties, so the upper limit is 0.00.
8%. More preferably, it is 0.003% or less. If the content of N is too large, nitride precipitates and deteriorates the magnetic properties, so the upper limit was made 0.008%. More preferably, it is 0.003% or less. P
b, Zn, and Bi are likely to segregate due to solute concentration during solidification, and easily form a low melting point phase at grain boundaries, so that the hot workability is significantly reduced. Therefore, the upper limits of Pb and Bi are set to 15 ppm, and the upper limit of Zn is set to 20 ppm.
【００１６】Ｓｎ，Ｓは、Ｐｂ，Ｚｎ，Ｂｉに比較して
影響は少ないものの、高濃度では熱間加工性を劣化させ
る傾向があるため、それぞれ上限を２００、５０ｐｐｍ
とした。これらの不純物元素は先に述べたように特に凝
固時の溶質濃化により偏析しやすく、かつ粒界において
低融点相を形成しやすい。１式における各元素の係数は
偏析および低融点相の形成能の２つの要因により決定さ
れる。Although Sn and S have less influence than Pb, Zn and Bi, they tend to deteriorate hot workability at high concentrations, so the upper limits are 200 and 50 ppm, respectively.
And As described above, these impurity elements are likely to segregate due to the solute concentration during solidification and to form a low melting point phase at grain boundaries. The coefficient of each element in Formula 1 is determined by two factors, segregation and the ability to form a low melting point phase.
【００１７】ＣＶの値は、熱間加工性に及ぼす不純物元
素含有量の影響を表す指標である。Ｐｂ，Ｂｉ，Ｓｎ，
Ｚｎ及びＳはスクラップ及び合金原料より混入するもの
である。Ｐｂ，Ｂｉ，Ｚｎは高蒸気圧成分であり、精錬
時間のコントロールによる高温下での蒸発反応により除
去可能である。一方、Ｓｎは、Ｐｂ，Ｂｉ，Ｚｎに比較
して蒸気圧が低いため、蒸発反応によっても除去しにく
く、現状の大量生産工程においては原料を選択する以外
にない。一方、Ｓはスラグ精錬による除去が可能であ
り、例えば高塩基度スラグを用いた脱硫処理がなされ
る。The value of CV is an index showing the influence of the content of the impurity element on the hot workability. Pb, Bi, Sn,
Zn and S are mixed from scrap and alloy raw materials. Pb, Bi, and Zn are high vapor pressure components and can be removed by an evaporation reaction under high temperature by controlling the refining time. On the other hand, since Sn has a lower vapor pressure than Pb, Bi, and Zn, it is difficult to remove Sn even by an evaporation reaction, and in the current mass production process, there is no choice but to select a raw material. On the other hand, S can be removed by slag refining, and for example, desulfurization treatment using high basicity slag is performed.
【００１８】本発明では原料選択，蒸発反応，スラグ精
錬を利用して、ＣＶの値が２５ｐｐｍ以下になるように
制御することにより、安定して熱間加工性の優れた材料
を得ることが可能となるものである。図１に熱間引張破
断時の絞り値、熱延板の表面疵発生ランクとＣＶの値の
関係を示す。ＣＶの値が２５ｐｐｍを超えた場合、熱間
加工性が著しく低下し、熱間圧延にて表面及び端部に疵
発生が観察された。そこで、ＣＶの値を２５ｐｐｍ以下
と限定した。また、絞り値は高値ほど熱間加工性が良好
であり、本発明では約８０％以上であれば割れ等の欠陥
を発生することなく熱間圧延が可能であった。In the present invention, it is possible to stably obtain a material having excellent hot workability by controlling the CV value to 25 ppm or less by utilizing the raw material selection, the evaporation reaction and the slag refining. It will be. FIG. 1 shows the relationship between the drawing value at the time of hot tensile rupture, the surface flaw generation rank of the hot rolled sheet, and the CV value. When the value of CV exceeded 25 ppm, the hot workability was remarkably deteriorated, and flaws were observed on the surface and the edges during hot rolling. Therefore, the value of CV is limited to 25 ppm or less. Further, the higher the drawing value is, the better the hot workability is. In the present invention, if it is about 80% or more, hot rolling can be performed without generating defects such as cracks.
【００１９】[0019]
【実施例】次に、本発明の優位性を実施例と比較例を用
いて、具体的に説明する。表１および表２（表１のつづ
き）に本発明例と比較例の化学成分及び熱間加工性、磁
気特性を示す。表１、表２に示すような本発明合金と比
較合金を、真空誘導溶解炉で溶製し、連続鋳造法により
スラブとした。その後１２５０℃×２時間加熱後熱間圧
延を行った。また、各特性の評価は下記の方法で行っ
た。EXAMPLES Next, the superiority of the present invention will be specifically described with reference to Examples and Comparative Examples. Tables 1 and 2 (continued from Table 1) show the chemical components, hot workability and magnetic properties of the examples of the present invention and the comparative examples. The alloys of the present invention and the comparative alloys shown in Tables 1 and 2 were melted in a vacuum induction melting furnace and made into slabs by a continuous casting method. Then, after heating at 1250 ° C. for 2 hours, hot rolling was performed. Moreover, evaluation of each characteristic was performed by the following method.
【００２０】（１）熱間加工性 １２５０℃加熱後冷却過程において高速引張試験を実施
した。熱間加工性の評価は冷却過程の１１００℃におけ
る引張破断部の熱間絞り値（％）で評価した。また、熱
延を行いその時の熱延板の表面疵及び耳割れ発生を以下
のようにランク評価した。(1) Hot workability A high-speed tensile test was carried out in the cooling process after heating at 1250 ° C. The hot workability was evaluated by the hot drawing value (%) of the tensile fracture portion at 1100 ° C in the cooling process. Further, hot rolling was performed, and the surface flaws and the occurrence of edge cracks of the hot rolled sheet at that time were ranked as follows.
【００２１】○ 表面疵及び耳割れ発生なし △ 一部表面疵及び耳割れ発生 × 全面表面疵及び耳割れ発生 （２）磁気特性 熱延板端部をスリットし表面の疵取りを行い、冷間圧
延、中間焼鈍を繰り返し板厚０．５ｍｍの冷延薄板を得
た後、外径４５ｍｍ×内径３３ｍｍのＪＩＳ規格に基づ
いたリング片を採取した。その後、磁性焼鈍（１１００
℃×３時間、水素雰囲気中、露点：５５℃）を行い、最
大比透磁率を測定した。○ No surface flaws and edge cracks occurred △ Partial surface flaws and edge cracks occurred × Whole surface surface flaws and edge cracks occurred (2) Magnetic characteristics The edges of the hot-rolled sheet were slit to remove surface flaws, and then cold After rolling and intermediate annealing were repeated to obtain a cold-rolled thin plate having a plate thickness of 0.5 mm, a ring piece having an outer diameter of 45 mm and an inner diameter of 33 mm based on the JIS standard was sampled. Then, magnetic annealing (1100
The maximum relative magnetic permeability was measured by performing dew point: 55 ° C. in a hydrogen atmosphere at 3 ° C. for 3 hours.
【００２２】Ｎｏ．１〜８は本発明例、Ｎｏ．９〜２７
は比較例である。各元素の量もしくはＣＶ値が本発明範
囲を外れている場合、熱間加工性及び磁気特性は本発明
例に比べて劣っている。比較例Ｎｏ．９、１０はＮｉ量
が本発明範囲を超えるものであり、この場合において
は、磁気特性が著しく低下している。比較例Ｎｏ．１１
はＣ量が本発明範囲を超えるものであり、熱間加工性及
び磁気特性が劣っている。比較例Ｎｏ．１２はＳｉ量が
本発明範囲未満であり、脱酸効果が少なく、磁気特性が
劣っている。比較例Ｎｏ．１３はＳｉ量が本発明範囲を
超えるものであり、磁気特性が劣っている。比較例Ｎ
ｏ．１４はＭｎ量が本発明範囲を超えるものであり、熱
間加工性への効果が飽和する傾向にあり、コスト面から
好ましくない。比較例Ｎｏ．１５はＴｉ量が、Ｎｏ．１
６はＭｇ量が、Ｎｏ．１７はＡｌ量が高く、本発明範囲
を超えているために磁性焼鈍後に製品表面に白濁現象が
発生した。比較例Ｎｏ．１８はＯ量が、Ｎｏ．１９はＮ
量が高く、本発明範囲を超えているために磁気特性が劣
っている。比較例Ｎｏ．２０はＰｂ量が、Ｎｏ．２１は
Ｂｉ量が、Ｎｏ．２２はＳｎ量が、Ｎｏ．２３はＺｎ量
が、Ｎｏ．２４はＳ量が高く、ＣＶ値の本発明範囲を単
一で超えるものであり、熱間加工性が劣り、熱延時にお
いて割れが発生している。また、比較例Ｎｏ．２５はＰ
ｂ，Ｂｉが、Ｎｏ．２６はＳｎ，Ｚｎが高く、ＣＶ値が
本発明範囲を超えるものであり、この場合においても熱
間加工性が著しく劣り、熱延時において割れが多発して
いる。No. Nos. 1 to 8 are examples of the present invention. 9-27
Is a comparative example. When the amount of each element or the CV value is outside the range of the present invention, the hot workability and magnetic properties are inferior to those of the examples of the present invention. Comparative Example No. In Nos. 9 and 10, the amount of Ni exceeds the range of the present invention, and in this case, the magnetic properties are remarkably deteriorated. Comparative Example No. 11
Has an amount of C exceeding the range of the present invention and is inferior in hot workability and magnetic properties. Comparative Example No. In No. 12, the amount of Si is less than the range of the present invention, the deoxidizing effect is small, and the magnetic properties are poor. Comparative Example No. In No. 13, the Si content exceeds the range of the present invention, and the magnetic properties are inferior. Comparative Example N
o. No. 14 has an Mn content exceeding the range of the present invention, and the effect on hot workability tends to be saturated, which is not preferable in terms of cost. Comparative Example No. No. 15 has a Ti content of No. 1
No. 6 has a Mg content of No. 6 Sample No. 17 has a high Al content, which exceeds the range of the present invention, and thus the white turbidity phenomenon occurred on the product surface after magnetic annealing. Comparative Example No. No. 18 has the O amount. 19 is N
The amount is high and the magnetic properties are inferior because it exceeds the range of the present invention. Comparative Example No. No. 20 has a Pb amount of No. 20. No. 21 has a Bi content of No. 21. No. 22 has a Sn content of No. 22. No. 23 has a Zn content of No. 23. No. 24, which has a high S content and exceeds the CV value of the present invention range alone, is inferior in hot workability and cracks are generated during hot rolling. In addition, Comparative Example No. 25 is P
b and Bi are No. No. 26 has a high Sn and Zn and a CV value exceeding the range of the present invention, and also in this case, the hot workability is remarkably inferior and cracks frequently occur during hot rolling.
【００２３】また、比較例Ｎｏ．２７は、不純物元素Ｐ
ｂ，Ｂｉ，Ｓｎ，Ｚｎ，Ｓ量は本発明範囲内ではある
が、ＣＶ値が本発明範囲を超えるものであり、この場合
においても熱間加工性が著しく劣り、熱延時において割
れが多発している。Further, in Comparative Example No. 27 is an impurity element P
The amounts of b, Bi, Sn, Zn, and S are within the range of the present invention, but the CV value exceeds the range of the present invention. Also in this case, hot workability is remarkably inferior and cracks frequently occur during hot rolling. ing.
【００２４】[0024]
【表１】 [Table 1]
【００２５】[0025]
【表２】 [Table 2]
【００２６】[0026]
【発明の効果】以上のことから明らかなように、本発明
によるＦｅ−Ｎｉ系磁性合金は、熱間圧延時に発生する
耳割れ現象を実操業上問題にならない程度に低減改善
し、しかも磁気特性にも優れたものである。As is apparent from the above, the Fe-Ni-based magnetic alloy according to the present invention reduces and improves the ear cracking phenomenon that occurs during hot rolling to such an extent that it does not pose a problem in actual operation, and has magnetic characteristics. It is also excellent.
【図１】熱間引張破断時の絞り値、熱延板の表面疵及び
耳割れ発生ランクとＣＶ値の関係を示す図である。FIG. 1 is a diagram showing a relationship between a drawing value at the time of hot tensile rupture, a surface flaw of a hot-rolled sheet, and a crack generation rank of an edge crack, and a CV value.
Claims (1)
０．０３％以下、Ｓｉ：０．０５〜１．０％、Ｍｎ：
２．０％以下、Ｔｉ：０．０５％以下、Ｍｇ：０．０５
％以下、Ａｌ：０．０５％以下、Ｏ：０．００８％以
下、Ｎ：０．００８％以下とし、さらにＰｂ，Ｂｉ，Ｓ
ｎ，Ｚｎ，Ｓの含有量が、重量ｐｐｍで、Ｐｂ：１５ｐ
ｐｍ以下、Ｂｉ：１５ｐｐｍ以下、Ｓｎ：２００ｐｐｍ
以下、Ｚｎ：２０ｐｐｍ以下、Ｓ：５０ｐｐｍ以下であ
り、かつ１式で規定されるＣＶの値が２５ｐｐｍ以下で
あり、残部がＦｅおよび不可避的不純物からなることを
特徴とする熱間加工性及び磁気特性に優れたＦｅ−Ｎｉ
系磁性合金。 ＣＶ＝Ｐｂ＋Ｂｉ＋０．０３Ｓｎ＋０．６３Ｚｎ＋０．２１Ｓ・・・１式1. Ni: 30-55%, C:% by weight
0.03% or less, Si: 0.05 to 1.0%, Mn:
2.0% or less, Ti: 0.05% or less, Mg: 0.05
% Or less, Al: 0.05% or less, O: 0.008% or less, N: 0.008% or less, and further Pb, Bi, S
The content of n, Zn, S is ppm by weight, and Pb: 15p
pm or less, Bi: 15 ppm or less, Sn: 200 ppm
Hereinafter, Zn: 20 ppm or less, S: 50 ppm or less, the value of CV defined by the formula 1 is 25 ppm or less, and the balance is Fe and unavoidable impurities. Fe-Ni with excellent characteristics
Series magnetic alloy. CV = Pb + Bi + 0.03Sn + 0.63Zn + 0.21S ... 1 formula
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32283493A JPH07180003A (en) | 1993-12-21 | 1993-12-21 | Fe-ni magnetic alloy excellent in hot workability and magnetic property |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32283493A JPH07180003A (en) | 1993-12-21 | 1993-12-21 | Fe-ni magnetic alloy excellent in hot workability and magnetic property |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH07180003A true JPH07180003A (en) | 1995-07-18 |
Family
ID=18148130
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32283493A Withdrawn JPH07180003A (en) | 1993-12-21 | 1993-12-21 | Fe-ni magnetic alloy excellent in hot workability and magnetic property |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07180003A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103938030A (en) * | 2014-04-29 | 2014-07-23 | 王杨 | Method for preparing nickel-based soft magnetic material |
-
1993
- 1993-12-21 JP JP32283493A patent/JPH07180003A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103938030A (en) * | 2014-04-29 | 2014-07-23 | 王杨 | Method for preparing nickel-based soft magnetic material |
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| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Withdrawal of application because of no request for examination |
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