JPH02225621A - Production of high permeability magnetic material - Google Patents
Production of high permeability magnetic materialInfo
- Publication number
- JPH02225621A JPH02225621A JP1048314A JP4831489A JPH02225621A JP H02225621 A JPH02225621 A JP H02225621A JP 1048314 A JP1048314 A JP 1048314A JP 4831489 A JP4831489 A JP 4831489A JP H02225621 A JPH02225621 A JP H02225621A
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- annealing
- cold working
- Prior art date
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Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
（産業上の利用分野）
本発明は、高透磁率磁性材料（軟質磁性材料）の製造方
法に関し、例えば、トランス用コア、モーター用コア、
リレー用鉄心、磁気ヘッド、磁気シールド材、磁気増幅
器などの素材として利用される高透磁率磁性材料を製造
するのに適した高透磁率磁性材料の製造方法に関するも
のである。
（従来の技術）
従来、上記した用途に利用される高透磁率磁性材料とし
ては、電磁軟鉄、ケイ素鋼板、パーマロイ、センダスト
、パーミンバー、イソバーム。
フェライト、各種アモルファス合金などがありパーマロ
イには、Ｎｉ含有量が７０〜８０重址％のパーマロイＡ
級（ＦＡパーマロイ）、Ｎｉ含有量が４０〜５０重量％
のパーマロ４８級（ＰＥパーマロイ）、Ｎｉ含有量が７
０〜８０重量％でその他に特殊成分を含むパーマロ４０
級（ＰＣパーマロイ）、Ｎｉ含有量が３５〜４０重量％
のパーマロ４０級（ＦＤパーマロイ）、Ｎｌ含有量が４
５〜５５重量％のパーマロイＥｊｌ （ＰＥパーマロイ
）など（例えば、ＪＩＳ Ｃ２５３１）があって１本
発明は、これらのうちＰＥパーマロイ系の高透磁率磁性
材料の製造方法の改良に関するものである。
従来、この種の高透磁率磁性材料を製造するに際しては
、所定成分に溶解したのち造塊して得たインゴットを熱
間鍛造および熱間圧延し１次いで冷間圧延（その他律線
加工等の冷間加工）を行い、この冷間圧延の間に１００
０℃前後ないしはそれ以上の温度での完全焼鈍を施して
冷間加工な容易なものにすると共に必要な冷間加工率が
確保されるようにし１次いで打抜き、深絞り、巻線。
冷間鍛造などによって所望の製品形状に加工し。
その後水素ないしは真空とした非酸化性雰囲気中におい
て９００−１２００℃で磁気焼鈍を行うことによって透
磁率の向上が実現されるようにしていた。
（発明が解決しようとする課題）
しかしながら、従来の高透磁率磁性材料の製造方法によ
る場合には、磁気特性とくに透磁率の向」二がいまだ十
分でないという課題を有していた。
（発明の目的）
本発明はこのような従来の課題にかんがみてなされたも
ので、磁気特性、とくに初透磁率（路、）および最大透
磁率（ｇｍ）で表わされる透磁率（ＪＬ）が大きな値を
示すＰＥパーマロイ系の高透磁率磁性材料を提供するこ
とを目的とじている。(Industrial Application Field) The present invention relates to a method for manufacturing a high magnetic permeability magnetic material (soft magnetic material), such as a core for a transformer, a core for a motor,
The present invention relates to a method for manufacturing a high permeability magnetic material suitable for manufacturing a high permeability magnetic material used as a material for relay cores, magnetic heads, magnetic shielding materials, magnetic amplifiers, etc. (Prior Art) High permeability magnetic materials conventionally used for the above-mentioned purposes include electromagnetic soft iron, silicon steel plate, permalloy, sendust, perminvar, and isobalm. Permalloy includes ferrite and various amorphous alloys, including Permalloy A with a Ni content of 70 to 80% by weight.
grade (FA permalloy), Ni content is 40-50% by weight
Permalloy grade 48 (PE permalloy), Ni content is 7
Permallo 40 containing 0 to 80% by weight and other special ingredients
grade (PC permalloy), Ni content is 35-40% by weight
Permalloy grade 40 (FD Permalloy), Nl content is 4
There are permalloy Ejl (PE permalloy) with a content of 5 to 55% by weight (for example, JIS C2531), and the present invention relates to an improvement in the manufacturing method of PE permalloy-based high permeability magnetic materials. Conventionally, when manufacturing this type of high permeability magnetic material, an ingot obtained by melting it into a predetermined component and forming an ingot was hot-forged and hot-rolled, and then cold-rolled (and subjected to other processes such as wire processing). cold working), and during this cold rolling, 100
Complete annealing is performed at a temperature of around 0°C or higher to make cold working easier and to ensure the necessary cold working rate.Then, the wire is punched, deep drawn, and wound. Processed into the desired product shape by cold forging etc. Thereafter, magnetic annealing was performed at 900-1200° C. in a non-oxidizing atmosphere of hydrogen or vacuum, thereby improving the magnetic permeability. (Problems to be Solved by the Invention) However, the conventional method for manufacturing high permeability magnetic materials has had the problem that the magnetic properties, particularly the direction of magnetic permeability, are still insufficient. (Objective of the Invention) The present invention has been made in view of the above-mentioned conventional problems. The object of the present invention is to provide a PE permalloy-based high permeability magnetic material that exhibits high permeability.
（課題を解決するための手段）
本発明に係る高透磁率磁性材料の製造方法は、Ｎｉが３
４重量％以上６５重量％以下、Ｓｉが１．０重量％以下
、Ｍｎが１．０重量％以下、必要に応じてＭｏ、Ｃ：ｕ
、Ｃｒ、Ｖ、Ｎｂ、Ｔａ。
Ｗ 、 Ｔ Ｉ 、 Ｚ ｒのうちから選ばれる１種ま
たは２種以上の合計が１０重量％以下、残部がＦｅおよ
び６不純物からなる素材を冷間加工する際の必要に応じ
て中間焼鈍を行う場合の中間焼鈍温度を９５０℃以下に
すると共に最終冷間加工率を９０％以上にして磁気焼鈍
前の硬さをビッカース硬さでＨｖ２５０以上とし、磁気
焼鈍を施して磁気焼鈍後の平均結晶粒径を０．２５ｍｍ
以上とする構成としたことを特徴としており、このよう
な高透磁率磁性材料の製造方法の構成を上述した従来の
課題を解決するための手段としている。
本発明が適用される高透磁率磁性材料は、Ｎｉが３４重
量％以上６５重量％以下、Ｓｉが１．０重量％以下、Ｍ
ｎが１．０重量％以下、必要に応じてＭｏ、Ｃｕ、Ｃｒ
、Ｖ、Ｎｂ、Ｔａ、Ｗ。
ＴＩ、Ｚｒのうちから選ばれる１種または２種以上の合
計が１０重量％以下、残部がＦｅおよび不純物からなる
ものであるが、このような成分組成に限定した理由につ
いて説明する。
Ｎｉ：
Ｎｉはこの種のパーマロイ系高透磁率磁性材料にとって
主要な元素であり、３４重量％未満ではキュリー点が室
温近くにまで低下すると共に、磁気特性の温度依存性が
大きくなるため実用的なものにならず、飽和磁束密度も
低いものとなるので好ましくなく、６５重量％超過では
飽和磁束密度が低下すると共に素材自体のコストが著し
く上昇するので、Ｎｉ含有量は３４重量％以上６５重量
％以下の範囲とした。
Ｓｉ：
Ｓｔは溶製時の脱＃成分として添加されるが、Ｎｉ含有
量が多くなると磁気特性の低下を招くので１．０重量％
以下とする必要がある。
Ｍｎ：
Ｍｎは溶製時の脱酸−脱硫成分として添加されるが、Ｍ
ｎ含有量が多くなると磁気特性の低下を招くので１．０
重量％以下とする必要がある。
Ｍｏ、Ｃｕ、Ｃｒ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｔｉ。
Ｚｒ：
これらの元素はこの種の高透磁率磁性材料の磁気特性を
向上させるのに有効な元素であるので。
これらの１種または２Ｉ！以上を必要に応じて添加する
のもよい、そして、Ｖ、Ｎｂ、Ｔａ、Ｗ。
Ｔｉ、Ｚｒ、Ｎｏ、Ｃｒは微細な炭化物や窒化物を形成
して結晶粒の一次成長を妨げ、磁気焼鈍時の二次成長を
容易にして結晶粒を粗大化させることにより磁気特性を
改善し、透磁率を向上させる。また、ａｔ械的特性や耐
摩耗性を改善し、磁気焼鈍前の硬さがピンカース硬さで
Ｈｖ２５０以上が得られるのを容易にする。さらに、Ｃ
ｕは電気抵抗を向上し、さらにＭＯとともにヒステリシ
スの低下、最大透磁率の向上に効果がある。
しかし、これらの元素の含有量が、多すぎるとかえって
磁気特性を低下させるので、添加するとしてもＭ ｏ
、 Ｃｕ 、 Ｃｒ 、 Ｖ 、 Ｎ ｂ 、 Ｔ ａ
、 Ｗ 。
Ｔｉ、Ｚｒのうちから選ばれる１種または２種以上の合
計で１０重量％以下の含有量とすることが必要である。
Ｃ：
Ｃは磁気特性の低下を招く元素であるので、その含有量
は少ない方がよく、０゜０２重量％以下とすることが望
ましいが、炭化物形成元素が含有されているときには微
細な炭化物を形成して結晶粒の成長時に一次結晶粒成長
を妨げ、二次結晶粒成長を起しやすくして磁気焼鈍後の
結晶粒を粗大化することにより透磁率を向上するのに寄
与すると共に、冷間加工後磁気焼鈍前の硬さがＨｖ２５
０以上となるのを容易にする。しかし、多すぎると結晶
粒粗大化作用を小さくしてかえって磁気特性の低下を招
くので、０．０３５重量％以下とすることが望ましい。
Ｎ：
Ｎは溶製時にブローホールを生じたり、磁気特性の低下
を招いたりする元素であるので、その含有量は少ない方
がよく、０．００５重量％以下とするのが望ましいが、
窒化物形成元素が含有されているときには微細な窒化物
を形成して結晶粒の成長時に一次結晶粒成長を妨げ、二
次結晶粒成長を起しやすくして磁気焼鈍後に結晶粒を粗
大化することにより透磁率を向上するのに寄与すると共
に、冷間加工後磁気焼鈍前の硬さが）（ｖ２５０以上と
なるのを容易にする。しかし、多すぎると結晶粒粗大化
作用を小さくしてかえって磁気特性の低下を招くので０
．０１０重量％以下とすることが望ましい。
Ｆｅ：
Ｆｅはこの種のパーマロイ系高透磁率磁性材料にとって
主要な元素であるので残部とした。
本発明に係る高透磁率磁性材料の製造方法は、上記組成
になるＦｅ−Ｎｉ系合金を素材とし、この素材に対して
冷間圧延や冷間引抜きなどの冷間加工を行うに際して最
終冷間加工率が９０％以上となるようにし、冷間加工を
行いがたいとぎや冷間加工率を大きなものとしたいとき
などに必要に応じて中間焼鈍を行う場合には中間焼鈍温
度を９５０℃以下（下限は中間焼鈍が可能である温度（
例えば６００℃程度）以上）にし、磁気焼鈍前の硬さが
ビッカース硬さでＨｖ２５０以上となるようにしている
。この場合、最終冷間加工率が９０％よりも小さいと、
磁気焼鈍後に平均結晶粒径を０．２５ｍｎｎ以上のもの
とするのが困難となる。また、中間焼鈍を行う場合にお
いてその焼鈍温度が９５０℃を超えるとその後の冷間加
工にとっては有利となるものの加工歪が残留しないもの
となり、磁気焼鈍後に平均結晶粒径を０．２５ｍｍ以上
のものとするのが困難となるので、中間焼鈍温度を９５
０℃以下として、加工歪を残しておくことによって磁気
焼鈍後に平均結晶粒径が０．２５ｍｍ以上となるように
する。
また、ａｉ磁気焼鈍前硬さがビー２カース硬さでＨｖ２
５０よりも低いと、磁気鏡Ｍ後の平均結晶粒径を０．２
５ｍｍ以上とするのが困難となるので、磁気焼鈍前の硬
さをＨｖ２５０以上とすることによって磁気焼鈍後の平
均結晶粒径を０．２５ｍｍ以上とするのがより確実なも
のになるようにする。
このように、冷間加工を行う際の最終冷間加工率を９０
％以上とし、冷間加工を行うに際して中間焼鈍を実施す
る必要がある場合には中間焼鈍温度を９５０℃以下とし
、打抜き、深絞り１巻線。
冷１１Ｊ１鍛造などを行うことによって製品形状に加工
し２磁気焼鈍前の硬さがＨｖ２５０以上とした状態で、
水素または真空等の非酸化性雰囲気中において９００〜
１２００℃で磁気焼鈍を行い、ビット炉、連続炉などの
炉中で冷却して所定形状の高透磁率磁性材料を得る。
これによって、磁気焼鈍後には平均結晶粒径が０．２５
ｍｍ以上のものが得られるようにし、磁気特性、とくに
透磁率の大きい高透磁率磁性材料な得る。
（発明の作用）
本発明に係る高透磁率磁性材料の製造方法では、所定の
成分組成を有するＦｅ−Ｎｉ系素材の冷間加工時におけ
る最終冷間加工率を９０％以上にし２冷間加工の際に中
間焼鈍を必要とする場合には中間焼鈍温度を９５０℃以
下とし、磁気焼鈍前の硬さがＨｖ２５０以上であるよう
にし、磁気焼鈍後の平均結晶粒径が０．２５ｍｍ以上と
なるようにしているので、結晶粒の粗大化による透磁率
の自重が実現され、磁気特性の優れたものとなる作用が
もたらされる。
（実施例）
第１表に示す成分組成の合゛金を溶製したのち造塊して
各々インゴットとし、各インゴットに対して８００〜１
３５０℃の温度で熱間鍛造を行って厚さ３０ｍｍのビレ
ットとし、続いて８００〜１３５０℃の温度で熱間圧延
を行って厚さ２．０ｍｍの帯板とし１次いで冷間圧延（
冷間加工）を行った。そして、この冷間圧延に際して中
間焼鈍を必要とする場合に同じく第１表に示す中間焼鈍
温度で中間焼鈍温度い、最終冷間圧延（加工）率を同じ
く第１表に示す値にして冷間圧延（冷間加工）を終了し
、最終的に厚さ０．１０〜０．５０ｍｍの薄帯にした。
この冷間圧延後（磁気焼鈍前）の硬さは同じく第１表に
示すとおりであった。
次いで、各薄帯に対し水素気流中で１１００℃、２時間
の磁気焼鈍を行い、平均結晶粒径を調べるとともに初透
磁率（、Ｗ−）および最大透磁率（延）を測定した、こ
れらの結果を同じく第１表に示す。
第１表に示すように１本発明の各構成要件を満足する実
施例間、１〜１４では、初透磁率および最大透磁率であ
られされる透磁率が大きな値を示していることが認めら
れた。これに対して本発明の各構成要件を満足しない比
較例Ｎｏ、 １ 、２では透磁率がかなり少ない値しか
有していないものであることが認められた。(Means for Solving the Problems) The method for producing a high magnetic permeability magnetic material according to the present invention is characterized in that Ni is 3
4% by weight or more and 65% by weight or less, Si is 1.0% by weight or less, Mn is 1.0% by weight or less, Mo, C: u as necessary
, Cr, V, Nb, Ta. Intermediate annealing is performed as necessary when cold working a material in which the total of one or more selected from W, TI, and Zr is 10% by weight or less, and the balance is Fe and 6 impurities. In this case, the intermediate annealing temperature is set to 950°C or lower, the final cold working rate is set to 90% or higher, the hardness before magnetic annealing is set to Hv250 or higher in terms of Vickers hardness, and magnetic annealing is performed to improve the average grain size after magnetic annealing. Diameter 0.25mm
The present invention is characterized by the above structure, and the structure of the method for producing a high magnetic permeability magnetic material is a means for solving the above-mentioned conventional problems. The high permeability magnetic material to which the present invention is applied includes Ni of 34% by weight or more and 65% by weight or less, Si of 1.0% by weight or less, M
n is 1.0% by weight or less, Mo, Cu, Cr as necessary
, V, Nb, Ta, W. The total amount of one or more selected from TI and Zr is 10% by weight or less, and the remainder is Fe and impurities. The reason for limiting the composition to this will be explained. Ni: Ni is a major element for this type of permalloy-based high permeability magnetic material, and if it is less than 34% by weight, the Curie point will drop to near room temperature and the temperature dependence of magnetic properties will increase, making it impractical for practical use. Ni content is undesirable because it becomes undesirable and the saturation magnetic flux density becomes low.If it exceeds 65% by weight, the saturation magnetic flux density decreases and the cost of the material itself increases significantly, so the Ni content should be 34% by weight or more and 65% by weight. The range was as follows. Si: St is added as a de#ing component during melting, but if the Ni content increases, the magnetic properties will deteriorate, so add 1.0% by weight.
It is necessary to do the following. Mn: Mn is added as a deoxidizing and desulfurizing component during melting, but Mn
If the n content increases, the magnetic properties will deteriorate, so 1.0
It is necessary to keep it below % by weight. Mo, Cu, Cr, V, Nb, Ta, W, Ti. Zr: These elements are effective for improving the magnetic properties of this type of high permeability magnetic material. One or two of these! It is also good to add the above as necessary, and V, Nb, Ta, and W. Ti, Zr, No, and Cr form fine carbides and nitrides that impede the primary growth of crystal grains, facilitate secondary growth during magnetic annealing, and coarsen the crystal grains, thereby improving magnetic properties. , improve magnetic permeability. It also improves mechanical properties and wear resistance, and makes it easier to obtain a Pinkers hardness of Hv250 or more before magnetic annealing. Furthermore, C
U improves electrical resistance and, together with MO, is effective in reducing hysteresis and increasing maximum magnetic permeability. However, if the content of these elements is too large, it will actually reduce the magnetic properties, so even if they are added, Mo
, Cu, Cr, V, Nb, Ta
,W. It is necessary that the total content of one or more selected from Ti and Zr be 10% by weight or less. C: Since C is an element that causes deterioration of magnetic properties, the lower its content is, the better, preferably 0.02% by weight or less, but when a carbide-forming element is contained, fine carbides may be formed. It forms and hinders primary grain growth during grain growth, facilitates secondary grain growth, and coarsens the grains after magnetic annealing, contributing to improving magnetic permeability. Hardness after machining and before magnetic annealing is Hv25
Make it easy to reach 0 or more. However, if the amount is too large, the crystal grain coarsening effect will be reduced and the magnetic properties will be deteriorated, so it is preferable that the amount is 0.035% by weight or less. N: N is an element that causes blowholes during melting and reduces magnetic properties, so it is better to have a lower content, preferably 0.005% by weight or less.
When a nitride-forming element is contained, fine nitrides are formed, inhibiting primary crystal grain growth during crystal grain growth, facilitating secondary crystal grain growth, and coarsening the crystal grains after magnetic annealing. This contributes to improving the magnetic permeability, and also makes it easier to achieve a hardness of v250 or more after cold working and before magnetic annealing.However, if it is too large, the grain coarsening effect is reduced. 0 as it will actually cause a decrease in magnetic properties.
．． It is desirable that the content be 0.010% by weight or less. Fe: Since Fe is a major element for this type of permalloy-based high permeability magnetic material, it was left as the remainder. The method for manufacturing a high permeability magnetic material according to the present invention uses an Fe-Ni alloy having the above composition as a raw material, and when performing cold working such as cold rolling or cold drawing on this material, the final cold The processing rate should be 90% or more, and if intermediate annealing is performed as necessary, such as when it is difficult to perform cold working or when it is desired to increase the cold working rate, the intermediate annealing temperature should be 950°C or less. (The lower limit is the temperature at which intermediate annealing is possible (
For example, the temperature is about 600° C.) or higher), and the hardness before magnetic annealing is set to Hv250 or higher in terms of Vickers hardness. In this case, if the final cold working rate is less than 90%,
It becomes difficult to make the average crystal grain size 0.25 mnn or more after magnetic annealing. In addition, when intermediate annealing is performed, if the annealing temperature exceeds 950°C, it is advantageous for subsequent cold working, but no processing strain remains. Therefore, the intermediate annealing temperature is set to 95
The temperature is set to 0° C. or lower, and processing strain is left so that the average crystal grain size becomes 0.25 mm or more after magnetic annealing. In addition, the hardness before ai magnetic annealing is Hv2 in Beakers hardness.
If it is lower than 50, the average grain size after the magnetic mirror M is 0.2
Since it is difficult to set the average grain size to 5 mm or more, by setting the hardness before magnetic annealing to Hv250 or more, it becomes more reliable to set the average grain size after magnetic annealing to 0.25 mm or more. . In this way, the final cold working rate when performing cold working is set to 90
% or more, and if it is necessary to perform intermediate annealing during cold working, the intermediate annealing temperature is 950°C or less, and one winding is punched and deep drawn. Processed into a product shape by performing cold 11J1 forging etc. 2 to have a hardness of Hv250 or more before magnetic annealing,
900~ in a non-oxidizing atmosphere such as hydrogen or vacuum
Magnetic annealing is performed at 1200° C. and cooled in a furnace such as a bit furnace or continuous furnace to obtain a high permeability magnetic material in a predetermined shape. This results in an average grain size of 0.25 after magnetic annealing.
mm or more, and obtain a high permeability magnetic material with high magnetic properties, especially magnetic permeability. (Function of the invention) In the method for producing a high magnetic permeability magnetic material according to the present invention, the final cold working rate during cold working of a Fe-Ni material having a predetermined component composition is set to 90% or more, and two cold workings are performed. If intermediate annealing is required, the intermediate annealing temperature should be 950°C or less, the hardness before magnetic annealing should be Hv250 or more, and the average grain size after magnetic annealing should be 0.25 mm or more. As a result, the self-weighting of magnetic permeability due to coarsening of crystal grains is achieved, resulting in the effect of providing excellent magnetic properties. (Example) An alloy having the composition shown in Table 1 was melted and then ingot made into ingots.
Hot forging was carried out at a temperature of 350°C to form a billet with a thickness of 30 mm, followed by hot rolling at a temperature of 800 to 1350°C to form a strip with a thickness of 2.0 mm, and then cold rolling (
cold working). If intermediate annealing is required during this cold rolling, the intermediate annealing temperature is set to the intermediate annealing temperature shown in Table 1, and the final cold rolling (processing) rate is set to the value shown in Table 1. The rolling (cold working) was completed, and a ribbon having a thickness of 0.10 to 0.50 mm was finally obtained. The hardness after cold rolling (before magnetic annealing) was also as shown in Table 1. Next, each ribbon was magnetically annealed at 1100°C for 2 hours in a hydrogen stream, and the average crystal grain size was examined, as well as the initial magnetic permeability (,W-) and maximum magnetic permeability (magnitude) were measured. The results are also shown in Table 1. As shown in Table 1, among Examples 1 to 14 that satisfy each component of the present invention, it is recognized that the magnetic permeability calculated by the initial magnetic permeability and the maximum magnetic permeability shows a large value. Ta. On the other hand, it was found that Comparative Examples Nos. 1 and 2, which did not satisfy each of the constituent requirements of the present invention, had only a considerably small value of magnetic permeability.
本発明に係る高透磁率磁性材料の製造方法は、ＮＩが３
４重量％以Ｊ：、６５重量％以下、Ｓｔが１．０重量％
以下、Ｍｎが１．０重量％以下、必要に応じ−（Ｍｏ、
Ｃｕ、Ｃｒ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｔｊ、Ｚｒのうちか
ら選ばれる１種または２種以上の合計が１０重量％以下
、残部がＦｅおよび不純物からなる素材を冷間加工する
際の必要に応じて中間焼鈍を行う場合の中間焼鈍温度を
９５０℃以下にすると共に最終冷間加工率を９０％以上
にして磁気焼鈍前の硬さをビッカース硬さでＨｖ２５０
以上とし、磁気焼鈍を施して磁気焼鈍後の平均結晶粒径
を０．２５ｍｍ以上とする構成としたから、磁気特性、
とくに初透磁率および最大透磁率であられされる透磁率
の値が大きなものとなり、トランス用コア、モーター用
コア、リレー用コア、リレー用鉄心、磁気ヘッド、？！
！気シールド材、Ｆｊｉ気増幅器等々の素材として優れ
た高透磁率磁性材料を提供することが可能であるという
著大なる効果がもたらされる。
特許出願人 大同特殊鋼株式会社The method for producing a high permeability magnetic material according to the present invention has an NI of 3
4% by weight or more J:, 65% by weight or less, St 1.0% by weight
Hereinafter, Mn is 1.0% by weight or less, -(Mo,
Necessary when cold working a material in which the total of one or more selected from Cu, Cr, V, Nb, Ta, W, Tj, and Zr is 10% by weight or less, and the balance is Fe and impurities. When performing intermediate annealing according to
As described above, since magnetic annealing is performed and the average grain size after magnetic annealing is set to 0.25 mm or more, the magnetic properties,
In particular, the value of magnetic permeability expressed by initial permeability and maximum magnetic permeability becomes large, and it is used for transformer cores, motor cores, relay cores, relay cores, magnetic heads, etc. !
! This brings about the great effect that it is possible to provide a magnetic material with high magnetic permeability that is excellent as a material for a magnetic shield material, an Fji amplifier, and the like. Patent applicant: Daido Steel Co., Ltd.
Claims (1)
．０重量％以下、Ｍｎが１．０重量％以下、残部がＦｅ
および不純物からなる素材を冷間加工する際の最終冷間
加工率を９０％以上にして磁気焼鈍前の硬さをビッカー
ス硬さでＨｖ２５０以上とし、磁気焼鈍を施して磁気焼
鈍後の平均結晶粒径を０．２５ｍｍ以上とすることを特
徴とする高透磁率磁性材料の製造方法。 （２）Ｎｉが３４重量％以上６５重量％以下、Ｓｉが１
．０重量％以下、Ｍｎが１．０重量％以下、残部がＦｅ
および不純物からなる素材を冷間加工する際の中間焼鈍
温度を９５０℃以下にすると共に最終冷間加工率を９０
％以上にして磁気焼鈍前の硬さをビッカース硬さでＨｖ
２５０以上とし、磁気焼鈍を施して磁気焼鈍後の平均結
晶粒径を０．２５ｍｍ以上とすることを特徴とする高透
磁率磁性材料の製造方法。 （３）Ｎｉが３４重量％以上６５重量％以下、Ｓｉが１
．０重量％以下、Ｍｎが１．０重量％以下、Ｍｏ、Ｃｕ
、Ｃｒ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｔｉ、Ｚｒのうちから選
ばれる１種または２種以上の合計が１０重量％以下、残
部がＦｅおよび不純物からなる素材を冷間加工する際の
最終冷間加工率を９０％以上にして磁気焼鈍前の硬さを
ビッカース硬さでＨｖ２５０以上とし、磁気焼鈍を施し
て磁気焼鈍後の平均結晶粒径を０．２５ｍｍ以上とする
ことを特徴とする高透磁率磁性材料の製造方法。 （４）Ｎｉが３４重量％以上６５重量％以下、Ｓｉが１
．０重量％以下、Ｍｎが１．０重量％以下、Ｍｏ、Ｃｕ
、Ｃｒ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｔｉ、Ｚｒのうちから選
ばれる１種または２種以上の合計が１０重量％以下、残
部がＦｅおよび不純物からなる素材を冷間加工する際の
中間焼鈍温度を９５０℃以下にすると共に最終冷間加工
率を９０％以上にして磁気焼鈍前の硬さをビッカース硬
さでＨｖ２５０以上とし、磁気焼鈍を施して磁気焼鈍後
の平均結晶粒径を０．２５ｍｍ以上とすることを特徴と
する高透磁率磁性材料の製造方法。 （５）Ｃが０．０３５重量％以下、Ｎが ０．０１０重量％以下であることを特徴とする請求項第
（３）項または第（４）項に記載の高透磁率磁性材料の
製造方法。[Claims] (1) Ni is 34% by weight or more and 65% by weight or less, Si is 1
．． 0% by weight or less, Mn is 1.0% by weight or less, the balance is Fe
When cold working a material consisting of impurities, the final cold working rate is set to 90% or more, the hardness before magnetic annealing is set to Hv250 or more in terms of Vickers hardness, and the average crystal grain after magnetic annealing is applied. A method for manufacturing a high permeability magnetic material, characterized in that the diameter is 0.25 mm or more. (2) Ni is 34% by weight or more and 65% by weight or less, Si is 1
．． 0% by weight or less, Mn is 1.0% by weight or less, the balance is Fe
When cold working materials containing impurities, the intermediate annealing temperature should be 950°C or lower, and the final cold working rate should be 90°C.
% or more, the hardness before magnetic annealing is expressed as Vickers hardness (Hv)
250 or more, and magnetic annealing is performed so that the average crystal grain size after magnetic annealing is 0.25 mm or more. (3) Ni is 34% by weight or more and 65% by weight or less, Si is 1
．． 0% by weight or less, Mn 1.0% by weight or less, Mo, Cu
, Cr, V, Nb, Ta, W, Ti, Zr in total of 10% by weight or less, the balance being Fe and impurities. High quality steel characterized by having a spacing rate of 90% or more, a Vickers hardness of Hv250 or more before magnetic annealing, and an average grain size of 0.25 mm or more after magnetic annealing by performing magnetic annealing. Method of manufacturing magnetic permeability magnetic material. (4) Ni is 34% by weight or more and 65% by weight or less, Si is 1
．． 0% by weight or less, Mn 1.0% by weight or less, Mo, Cu
, Cr, V, Nb, Ta, W, Ti, Zr in total of 10% by weight or less of one or more selected from among them, with the balance being Fe and impurities. Intermediate annealing when cold working a material. The temperature is set to 950°C or lower, the final cold working rate is set to 90% or higher, the hardness before magnetic annealing is set to Hv250 or higher in terms of Vickers hardness, and magnetic annealing is performed to reduce the average grain size after magnetic annealing to 0. A method for manufacturing a high permeability magnetic material, characterized in that the thickness is 25 mm or more. (5) Production of a high permeability magnetic material according to claim (3) or (4), characterized in that C is 0.035% by weight or less and N is 0.010% by weight or less. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1048314A JP2760013B2 (en) | 1989-02-27 | 1989-02-27 | Method for producing high permeability magnetic material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1048314A JP2760013B2 (en) | 1989-02-27 | 1989-02-27 | Method for producing high permeability magnetic material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02225621A true JPH02225621A (en) | 1990-09-07 |
| JP2760013B2 JP2760013B2 (en) | 1998-05-28 |
Family
ID=12799953
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1048314A Expired - Fee Related JP2760013B2 (en) | 1989-02-27 | 1989-02-27 | Method for producing high permeability magnetic material |
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| Country | Link |
|---|---|
| JP (1) | JP2760013B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH046249A (en) * | 1990-04-24 | 1992-01-10 | Nippon Steel Corp | Fe-ni magnetic alloy excellent in magnetic property and surface characteristic and its production |
| EP0818551A1 (en) * | 1996-07-12 | 1998-01-14 | Krupp VDM GmbH | Use of an iron-nickel-alloy for electromagnetic parts |
| WO1998038725A1 (en) * | 1997-02-26 | 1998-09-03 | Seiko Instruments Inc. | Stepper motor |
| US7226515B2 (en) | 2000-09-29 | 2007-06-05 | Hippon Yakin Kogyo Co., Ltd. | Fe—Ni based permalloy and method of producing the same and cast slab |
| JP2015034329A (en) * | 2013-08-09 | 2015-02-19 | 日本冶金工業株式会社 | Fe-Ni permalloy alloy and method for producing the same |
| JP2015196838A (en) * | 2014-03-31 | 2015-11-09 | Ｄｏｗａメタルテック株式会社 | Fe-Ni alloy material manufacturing method, soft magnetic component manufacturing method, Fe-Ni alloy and soft magnetic component material |
| JP2018031061A (en) * | 2016-08-25 | 2018-03-01 | 大同特殊鋼株式会社 | Fe-Ni ALLOY, SOFT MAGNETIC RAW MATERIAL, SOFT MAGNETIC MATERIAL AND METHOD FOR PRODUCING SOFT MAGNETIC MATERIAL |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6452021A (en) * | 1987-08-20 | 1989-02-28 | Nippon Yakin Kogyo Co Ltd | Manufacture of fe-ni alloy |
| JPH01263218A (en) * | 1988-04-15 | 1989-10-19 | Nkk Corp | Production of high magnetic permeability alloy of ni-fe system |
| JPH01272716A (en) * | 1988-04-22 | 1989-10-31 | Nkk Corp | Fe-Ni-based high permeability magnetic alloy and its manufacturing method |
-
1989
- 1989-02-27 JP JP1048314A patent/JP2760013B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6452021A (en) * | 1987-08-20 | 1989-02-28 | Nippon Yakin Kogyo Co Ltd | Manufacture of fe-ni alloy |
| JPH01263218A (en) * | 1988-04-15 | 1989-10-19 | Nkk Corp | Production of high magnetic permeability alloy of ni-fe system |
| JPH01272716A (en) * | 1988-04-22 | 1989-10-31 | Nkk Corp | Fe-Ni-based high permeability magnetic alloy and its manufacturing method |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH046249A (en) * | 1990-04-24 | 1992-01-10 | Nippon Steel Corp | Fe-ni magnetic alloy excellent in magnetic property and surface characteristic and its production |
| EP0818551A1 (en) * | 1996-07-12 | 1998-01-14 | Krupp VDM GmbH | Use of an iron-nickel-alloy for electromagnetic parts |
| WO1998038725A1 (en) * | 1997-02-26 | 1998-09-03 | Seiko Instruments Inc. | Stepper motor |
| US7226515B2 (en) | 2000-09-29 | 2007-06-05 | Hippon Yakin Kogyo Co., Ltd. | Fe—Ni based permalloy and method of producing the same and cast slab |
| US7419634B2 (en) | 2000-09-29 | 2008-09-02 | Nippon Yakin Kogyo Co., Ltd. | Fe-Ni based permalloy and method of producing the same and cast slab |
| US7435307B2 (en) | 2000-09-29 | 2008-10-14 | Nippon Yakin Kogyo Co., Ltd | Fe-Ni based permalloy and method of producing the same and cast slab |
| JP2015034329A (en) * | 2013-08-09 | 2015-02-19 | 日本冶金工業株式会社 | Fe-Ni permalloy alloy and method for producing the same |
| JP2015196838A (en) * | 2014-03-31 | 2015-11-09 | Ｄｏｗａメタルテック株式会社 | Fe-Ni alloy material manufacturing method, soft magnetic component manufacturing method, Fe-Ni alloy and soft magnetic component material |
| JP2018031061A (en) * | 2016-08-25 | 2018-03-01 | 大同特殊鋼株式会社 | Fe-Ni ALLOY, SOFT MAGNETIC RAW MATERIAL, SOFT MAGNETIC MATERIAL AND METHOD FOR PRODUCING SOFT MAGNETIC MATERIAL |
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| Publication number | Publication date |
|---|---|
| JP2760013B2 (en) | 1998-05-28 |
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