JPH01263218A - Production of high magnetic permeability alloy of ni-fe system - Google Patents
Production of high magnetic permeability alloy of ni-fe systemInfo
- Publication number
- JPH01263218A JPH01263218A JP9159988A JP9159988A JPH01263218A JP H01263218 A JPH01263218 A JP H01263218A JP 9159988 A JP9159988 A JP 9159988A JP 9159988 A JP9159988 A JP 9159988A JP H01263218 A JPH01263218 A JP H01263218A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- cold rolling
- present
- magnetic permeability
- magnetic properties
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 27
- 239000000956 alloy Substances 0.000 title claims abstract description 27
- 230000035699 permeability Effects 0.000 title abstract description 29
- 238000004519 manufacturing process Methods 0.000 title description 4
- 238000000137 annealing Methods 0.000 claims abstract description 39
- 238000005097 cold rolling Methods 0.000 claims abstract description 36
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 10
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 6
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 6
- 230000009467 reduction Effects 0.000 claims description 19
- 238000005096 rolling process Methods 0.000 claims description 13
- 230000004907 flux Effects 0.000 abstract description 6
- 229910052759 nickel Inorganic materials 0.000 abstract description 5
- 229910003271 Ni-Fe Inorganic materials 0.000 abstract description 4
- 229910052796 boron Inorganic materials 0.000 abstract description 4
- 229910000831 Steel Inorganic materials 0.000 abstract description 2
- 239000010959 steel Substances 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract 1
- 239000000463 material Substances 0.000 description 23
- 229910000889 permalloy Inorganic materials 0.000 description 16
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 9
- 229910052739 hydrogen Inorganic materials 0.000 description 9
- 239000001257 hydrogen Substances 0.000 description 9
- 230000000694 effects Effects 0.000 description 6
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 241000251468 Actinopterygii Species 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910000846 In alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- -1 and found that C2S Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000011162 core material Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006735 deficit Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 230000005381 magnetic domain Effects 0.000 description 1
- 230000005415 magnetization Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 150000003568 thioethers Chemical class 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【発明の詳細な説明】
「発明の目的」
本発明はＮｉ −Ｆｅ系高透磁率合金の製造方法に係り
、直流磁気特性の優れたＮｉ−Ｆｅ系超高透磁率合金を
適切に製造することのできる方法を提供しようとするも
のである。DETAILED DESCRIPTION OF THE INVENTION [Object of the Invention] The present invention relates to a method for producing a Ni-Fe based high magnetic permeability alloy, and an object thereof is to appropriately produce a Ni-Fe based super high magnetic permeability alloy having excellent direct current magnetic properties. The aim is to provide a method that allows for
（産業上の利用分野）
Ｎｉ−Ｆｅ系高透磁率合金の磁気特性を改善するための
製造方法。(Industrial Application Field) A manufacturing method for improving the magnetic properties of a Ni-Fe based high magnetic permeability alloy.
（従来の技術）
パーマロイは１量によって得られる磁気性質が変化する
。すなわち、ＪＩＳ ＰＣ相当のパーマロイはＮｉを約
７８％含み、透磁率が極めて高く、優れた材料であるが
、飽和磁束密度が低く、また高価であるという欠点を有
している。これに対してＪＩＳＰＢ相当のパーマロイは
Ｎｉを約４５％含み、上記のＰＣパーマロイに比べて飽
和磁束密度が２倍はど高く、かつ低価格であるが透磁率
は低い。このようにＰＣパーマロイとＰＢパーマロイで
はそれぞれ長所はあるが、短所も有していた。(Prior Art) The magnetic properties of permalloy vary depending on the amount. That is, permalloy equivalent to JIS PC contains about 78% Ni and has extremely high magnetic permeability, making it an excellent material, but it has the drawbacks of low saturation magnetic flux density and being expensive. On the other hand, permalloy equivalent to JISPB contains about 45% Ni, has a saturation magnetic flux density twice as high as the above-mentioned PC permalloy, and is low in price, but has low magnetic permeability. As described above, PC permalloy and PB permalloy each have advantages, but they also have disadvantages.
しかるに、昨今のエレクトロニクスの発達から、各種機
器の小型高性能化が進行し、上記のＰＢ、 ＰＣパーマ
ロイの欠点を補い合うような、高透磁率、高飽和磁束密
度かつ低価格の材料が望まれている。However, with the recent development of electronics, various devices have become smaller and more sophisticated, and there is a desire for materials with high magnetic permeability, high saturation magnetic flux density, and low cost that can compensate for the drawbacks of PB and PC permalloy. There is.
このような要求に対して、ＰＳパーマロイでの透Ｉｆｆ
率の向上を意図した特開昭６２−１４２７４９及び特開
昭６２−２２７０６５の如き提案がなされている。即ち
、前者の特開昭６１−１４２７４９ではＯ，Ｓの低減、
後者の特開昭６２−２２７０６５では、Ｐ、Ｓの低減に
加え、Ｍｏの添加をそれぞれ行なうことにより磁気特性
の向上を図ろうとしている。In response to such requests, transparent If in PS Permalloy
Proposals such as JP-A-62-142749 and JP-A-62-227065 have been made with the intention of improving the efficiency. That is, in the former Japanese Patent Application Laid-Open No. 61-142749, reduction of O, S,
The latter, JP-A No. 62-227065, attempts to improve magnetic properties by reducing P and S and adding Mo.
（発明が解決しようとする課題）
上記した特開昭６２−２２７０６５の技術で特徴として
いる不純物元素の低減、Ｍｏの添加によっても最終の水
素雰囲気での熱処理（１１００°Ｃ×３時間）後の初透
磁率は高々６，０００である。−方、特開昭６２−１４
２７４９で特徴としている不純物元素の低減によっても
最終の水素雰囲気での熱処理（１１００℃×１時間）後
の最大透磁率はせいぜい１５０，０００である。即ちこ
のような透磁率を越えたレベルの磁気特性が要求された
場合においてはこれら２つの提案は不適とならざるを得
なかった。このようにＰＢＳパーマロイ透磁率が不十分
な場合には、ＰＣパーマロイの極めて高い透磁率は必要
ないにしても、やむを得ずＰＣパーマロイを使用するこ
とが必要で、コスト高になる。(Problem to be solved by the invention) The reduction of impurity elements, which is featured in the technique of JP-A-62-227065 mentioned above, and the addition of Mo can also be applied after the final heat treatment in a hydrogen atmosphere (1100°C x 3 hours). The initial permeability is at most 6,000. -, JP-A-62-14
Even with the reduction of impurity elements, which is a feature of 2749, the maximum magnetic permeability after the final heat treatment in a hydrogen atmosphere (1100° C. x 1 hour) is at most 150,000. That is, in cases where magnetic properties at a level exceeding such magnetic permeability are required, these two proposals are unsuitable. If the magnetic permeability of PBS permalloy is insufficient as described above, even though the extremely high magnetic permeability of PC permalloy is not required, it is necessary to use PC permalloy, which increases the cost.
なお、上記した、前者のものでは、Ｂの添加が行なわれ
ているが、この場合のＢの添加は熱間加工性及び打抜き
性を改善するために行なうものであり、この発明で意図
するＢの添加だけでは磁気特性の明らかな向上はみられ
ず、逆に劣化する場合も見られる。In addition, in the former case mentioned above, B is added, but in this case, B is added to improve hot workability and punching property, and B is not intended to be used in this invention. No obvious improvement in magnetic properties is observed with just the addition of , and on the contrary, some cases of deterioration are observed.
「発明の構成」
（課題を解決するための手段）
本発明は上記したような従来のものの問題点を解決する
ように検討して創案されたものであって、その要旨とす
るところは、
Ｎｉ：４３．Ｏ〜４８．０智Ｌ％、 Ｃ： ０．０１
０ ｗｔ％以下、Ｓ ： ０．０００５〜０．００２
ｗｔ％、 Ｐ ： ０．００６ ｗｔ％以下、０ ：
０．００３ｗｔ％以下、 Ｎ ： ０．００１５ｗｔ
％以下、であって、かつ、
Ｂ ： ０．００１５〜０．００５０ｗｔ％を含有し、
残部は基本的にＦｅからなるＦｅ−Ｎｉ合金である薄鋼
帯の製造に際して前記合金の熱間加工後の冷延を中間焼
鈍をはさみ２回行い、かつ１回目の冷延での圧下率を５
０〜９８％、２回目の冷延での圧下率を７５〜９８％、
中間焼鈍を７３０〜９００°Ｃでそれぞれ行うことを特
徴とるすＮｉ −Ｆｅ系高透磁率合金の製造方法である
。"Structure of the Invention" (Means for Solving the Problems) The present invention was developed after consideration to solve the problems of the conventional products as described above, and its gist is as follows: :43. O ~ 48.0 Wisdom L%, C: 0.01
0 wt% or less, S: 0.0005-0.002
wt%, P: 0.006 wt% or less, 0:
0.003wt% or less, N: 0.0015wt
% or less, and contains B: 0.0015 to 0.0050 wt%,
In producing a thin steel strip, which is an Fe-Ni alloy, the remainder of which is basically Fe, the alloy is cold-rolled twice with an intermediate annealing in between after hot working, and the reduction rate in the first cold-rolling is 5
0 to 98%, the rolling reduction in the second cold rolling to 75 to 98%,
This is a method for producing a Ni--Fe based high magnetic permeability alloy, characterized in that intermediate annealing is performed at 730 to 900°C.
（作用）
本発明で対象とするＰＢ級パーマロイであって、４％（
以下単に％という）で、Ｎｉが４３．０〜４８．０％の
範囲ではＰＢＳパーマロイ所要の透磁率、飽和磁束密度
を有している。Ｎｉが４３．０％未満では透磁率が低く
なり、一方４８．０％を越えると飽和磁束密度が低くな
るので４３．０〜４８．０％と定めた。(Function) The PB class permalloy targeted by the present invention is 4% (
In the range of 43.0 to 48.0% Ni, PBS Permalloy has the required magnetic permeability and saturation magnetic flux density. If Ni is less than 43.0%, the magnetic permeability will be low, while if it exceeds 48.0%, the saturation magnetic flux density will be low, so it was set at 43.0 to 48.0%.
ところで本発明者等は、ＰＢＳパーマロイ磁気特性を向
上すべく数々の実験を重ねたところ、Ｃ２Ｓ、Ｐ、Ｏ，
Ｎの容量を制御し、かつＢを微量添加した合金がある特
定の冷延、焼鈍条件を経たときに磁気特性が飛躍的に向
上することを見出した。By the way, the present inventors conducted numerous experiments to improve the magnetic properties of PBS permalloy, and found that C2S, P, O,
It has been found that when an alloy in which the amount of N is controlled and a small amount of B is added is subjected to certain cold rolling and annealing conditions, the magnetic properties are dramatically improved.
即ちこれらの成分についての規定理由は以下の如くであ
る。That is, the reasons for specifying these components are as follows.
Ｃは、０．０１％を越えると、熱間加工性が劣化し、か
つ磁気特性も劣化するので０．０１０％を上限とした。If C exceeds 0.01%, hot workability and magnetic properties will deteriorate, so the upper limit was set at 0.010%.
なお下限は特に定めないが溶製時の経済性から好ましく
は０．００１０％である。Although the lower limit is not particularly determined, it is preferably 0.0010% from the economical point of view of melting.
Ｐは、本発明で対象とするＦｅ −Ｎｉ合金に有害であ
り、又最終の水素焼鈍時の立方体集合組織の形成傾向を
弱める元素である。このＰが０．００６％を越えると立
方体集合組織が弱まって高い透磁率が得られず、又熱間
加工性が悪くなるためその上限を０．００６％とした。P is an element that is harmful to the Fe--Ni alloy targeted by the present invention, and also weakens the tendency to form a cubic texture during the final hydrogen annealing. If the P content exceeds 0.006%, the cubic texture will be weakened, making it impossible to obtain high magnetic permeability and causing poor hot workability, so the upper limit was set at 0.006%.
なお下限については溶製時の経済性から０．００１％と
した。The lower limit was set at 0.001% from the economical point of view of melting.
Ｓは、熱間加工性に有害であり、かつ硫化物の形成を通
じて最終の水素焼鈍時における粒成長を阻害し、焼鈍後
の粒径が小さいため保磁力が大きくなったり、磁化物に
より磁区が移動しにくくなるため透磁率が低くなり、磁
気特性に対しても極めて有害な元素である。このＳ量が
０．００２０％を越えると、以下に示すようなり添加お
よび特定の冷延、焼鈍条件採用によっても本発明で意図
する磁気特性の飛躍的改善を計ることができず、熱間加
工性も著しく悪くなるためＯ，ＯＯ２０％を上限とした
。なお下限は溶製時の経済性から０．０００５％とした
。S is harmful to hot workability, inhibits grain growth during final hydrogen annealing through the formation of sulfides, and increases the coercive force due to the small grain size after annealing, and causes magnetic domains to form due to magnetization. Since it becomes difficult to move, magnetic permeability decreases, and it is an extremely harmful element to magnetic properties. If the amount of S exceeds 0.0020%, it will not be possible to dramatically improve the magnetic properties as intended by the present invention, even by addition and specific cold rolling and annealing conditions as shown below, and hot processing The upper limit was set at 20% of O and OO, since the properties were also significantly deteriorated. Note that the lower limit was set to 0.0005% from the economical point of view of melting.
Ｂは、その適量添加のもとて熱間加工性の改善効果があ
り、かつ、固溶状態で、本発明の対象とする合金の集合
組織を、磁気特性に有利な方向に変える働きがある。こ
のＢ量が０．００１５％未満では本発明で意図する磁気
特性の向上が図れず、一方０．００５０％を越えると、
Ｂの金属間加工物が形成され磁気特性が劣化するため、
０．００１５％を下限、０．００５０％を上限と定めた
。When added in an appropriate amount, B has the effect of improving hot workability, and in a solid solution state, B has the effect of changing the texture of the alloy targeted by the present invention in a direction favorable to magnetic properties. . If the amount of B is less than 0.0015%, the magnetic properties intended in the present invention cannot be improved, while if it exceeds 0.0050%,
Since an intermetallic workpiece of B is formed and the magnetic properties deteriorate,
The lower limit was set at 0.0015%, and the upper limit was set at 0.0050%.
Ｎは、Ｂ添加を基本とした合金においては、Ｂと容易に
結合し、ＢＮを形成するため、有効Ｂ量が低下する。ま
た形成されたＢＮにより磁気特性が著しく劣化するなど
の理由より、合金中に多く・含まれる時、著しい悪影響
を及ぼす。即ちこのＮが０．００１５％を越えると上記
の理由により、磁気特性の劣化が著しくなるので、Ｎの
上限は０．００１５％と定めた。In alloys based on B addition, N easily combines with B to form BN, resulting in a decrease in the effective amount of B. In addition, since the magnetic properties are significantly deteriorated due to the formed BN, when a large amount of BN is contained in the alloy, it has a significant adverse effect. That is, if this N exceeds 0.0015%, the magnetic properties will deteriorate significantly for the above-mentioned reasons, so the upper limit of N was set at 0.0015%.
さて、本発明で意図する高い磁気特性を有するＦｅ−Ｎ
ｉ合金はこれまで述べたＣ、Ｓ、Ｐ、０．Ｎといった不
純物元素の低減及び微量Ｂの添加といった成分的配慮の
みでは達成されず、熱間加工後の冷延、焼鈍条件の適正
化がなされた時はじめて製造し得る。Now, Fe-N having high magnetic properties as intended in the present invention
The i alloys are C, S, P, 0. This cannot be achieved only by considering the components such as reducing impurity elements such as N and adding a small amount of B, but it can only be produced when cold rolling and annealing conditions after hot working are optimized.
第１図には、後述する第１表のＮ１１ｌ材（本発明合金
）の熱延板を用いて、数々の冷延条件にて作製した板厚
０．２ ｉｎの薄板サンプルより外径４５龍。Figure 1 shows an outer diameter of 45 mm from a thin plate sample with a thickness of 0.2 inches produced under various cold rolling conditions using a hot-rolled plate of N11l material (invention alloy) shown in Table 1 below. .
内径３３龍のＪＩＳ リングに打抜いて、試料とし、そ
れらを水素雰囲気中で１１００℃×１時間の熱処理を施
し、１００℃／ｈｒで冷却したサンプルのμｉ及びμｍ
を測定した結果を冷延条件で整理して示した。即ち、２
回冷延材の場合の中間焼鈍は７３０〜９００℃の範囲内
で行なっている。２回冷延材のうち、１次冷延率が５０
％以上、かつ２次冷延率が７５％以上の時、μｉは２６
，０００以上で、μｍも１７０，０００以上であり、優
れた直流特性が得られていることがわかる。なお、１回
冷延材で得られるμｉ及びμｍはそれぞれ上記のレベル
に比較して明らかに低い。なお、１次冷延率及び２次冷
延率の上限は、冷延時のエッヂ割れや、ミル負荷の点か
らそれぞれ９８％と定めた。Samples were punched into JIS rings with an inner diameter of 33mm, heat treated at 1100°C for 1 hour in a hydrogen atmosphere, and cooled at 100°C/hr. μi and μm
The measurement results are summarized and shown according to cold rolling conditions. That is, 2
Intermediate annealing in the case of re-cold rolled material is carried out within the range of 730 to 900°C. Among the twice cold rolled materials, the first cold rolling rate is 50
% or more and when the secondary cold rolling rate is 75% or more, μi is 26
,000 or more, and the μm is also 170,000 or more, indicating that excellent DC characteristics are obtained. Note that μi and μm obtained from the once cold-rolled material are clearly lower than the above levels. The upper limits of the primary cold rolling rate and the secondary cold rolling rate were each set at 98% in view of edge cracking during cold rolling and mill load.
本発明で意図する高透磁率材料は上記のような冷延条件
に加えて、焼鈍条件を適正としなければ達成されない。The high magnetic permeability material intended by the present invention cannot be achieved unless the annealing conditions are appropriate in addition to the cold rolling conditions described above.
第２図は、後述する第１表の阻１材（本発明合金）の熱
延板を６５％の圧下率にて冷延し、引き続く中間焼鈍の
のちに８０％の圧下率にて冷延した板厚０．２鶴の薄板
サンプルより外径４５１鳳、内径３３１１のＪＩＳリン
グに打抜いて試料とし、それらを水素雰囲気中で１１０
０°ｃｘ１時間の熱処理を施し、１００℃／ｈｒで冷却
したサンプルのμｉ及びμｍを測定した結果を中間焼鈍
温度で整理したものである。中間焼鈍温度が７３０〜９
００℃の範囲であるとμｉが２６． ＯＯ０以上で、μ
ｍも約１７０，０００を越えており、優れた磁気特性を
有している。中間焼鈍温度がこの範囲の時に最終の水素
焼鈍後で磁気特性が優れているのは、中間焼鈍後で１０
０％再結晶していること、かつその再結晶オーステナイ
トが細粒であり、また再結晶後に磁気特性に有利な集合
！！Ｊ１ｍが強く形成されていることなどが、最終焼鈍
時に形成される磁気特性に有利な集合ｍ織の集積を著し
く強める因子として働らいているためと考えられる。な
お、中間焼鈍温度が上記の範囲の場合でも、１次冷延率
及び２次冷延率が本発明規定範囲内でなければ、本発明
で意図する磁気特性の向上が図られないことは第１図に
関して述べた通りである。また、上記のように１次冷延
での圧下率、２次冷延での圧下率及び中間焼鈍温度が本
発明規定を満たした場合でも、成分が本発明範囲内でな
ければ、本発明で意図する磁気特性の向上が図られない
ことは、以下の実施例で示す通りである。以上が中間焼
鈍温度を本発明範囲に規定した理由である。Figure 2 shows a hot-rolled sheet of material No. 1 (invention alloy) in Table 1, which will be described later, which is cold-rolled at a rolling reduction of 65%, followed by intermediate annealing, and then cold-rolled at a rolling reduction of 80%. A JIS ring with an outer diameter of 451mm and an inner diameter of 3311mm was punched out from a thin plate sample with a thickness of 0.2mm.
The results of measuring μi and μm of a sample heat-treated at 0°C x 1 hour and cooled at 100°C/hr are summarized by intermediate annealing temperature. Intermediate annealing temperature is 730~9
In the range of 00°C, μi is 26. OO0 or more, μ
m also exceeds about 170,000, and has excellent magnetic properties. When the intermediate annealing temperature is in this range, the magnetic properties are excellent after the final hydrogen annealing when the intermediate annealing temperature is 10
0% recrystallization, and the recrystallized austenite is fine-grained, and after recrystallization, it aggregates advantageously for magnetic properties! ! This is thought to be because the strong formation of J1m acts as a factor that significantly strengthens the accumulation of aggregated m-weave, which is advantageous for magnetic properties, and is formed during final annealing. Incidentally, even if the intermediate annealing temperature is within the above range, unless the primary cold rolling rate and the secondary cold rolling rate are within the range specified by the present invention, the magnetic properties intended by the present invention cannot be improved. This is as stated regarding Figure 1. Furthermore, even if the rolling reduction ratio in the first cold rolling, the rolling reduction ratio in the secondary cold rolling, and the intermediate annealing temperature satisfy the provisions of the present invention as described above, if the components are not within the range of the present invention, the present invention is not applicable. The fact that the intended magnetic properties were not improved is shown in the following examples. The above is the reason why the intermediate annealing temperature is defined within the range of the present invention.
なお、中間焼鈍温度が７３０℃未満の時に透磁率が低い
のは、この温度域では、焼鈍後に１００％再結晶せず、
続く冷延及び最終焼鈍で磁気特性に好ましい集合組織が
十分発達しないためと思われる。The reason why the magnetic permeability is low when the intermediate annealing temperature is less than 730°C is because in this temperature range, 100% recrystallization does not occur after annealing.
This seems to be because the texture favorable for magnetic properties is not sufficiently developed during the subsequent cold rolling and final annealing.
一方、中間焼鈍温度が９００℃を越えて透磁率が低下す
るのは、中間焼鈍後のオーステナイト粒径が大きくなる
ため、引き続く冷延ののちに行なわれる水素焼鈍時に形
成される集合組織が全体的にランダム化するため、磁気
特性に有利な集合組織が十分に発達しないためと認めら
れる。On the other hand, the reason why the magnetic permeability decreases when the intermediate annealing temperature exceeds 900°C is because the austenite grain size increases after the intermediate annealing, and the texture formed during the hydrogen annealing performed after the subsequent cold rolling is It is recognized that this is because the texture, which is advantageous for magnetic properties, is not sufficiently developed due to the randomization.
（実施例）
本発明によるものの具体的な実施例について説明すると
以下の如くである。(Example) Specific examples of the present invention will be described below.
実施例１゜
次の第１表に示すような化学成分を有するＦｅ −Ｎｉ
合金である本発明合金および比較合金を真空溶解で溶製
し、熱間加工、脱スケールを施して冷延素材を準備した
。即ち魚１〜３は何れも本発明範囲を満足するのに対し
阻４はＳが０．００３５％、隘６はＰが０．０１０％と
高く、又Ｎ０．６の比較合金は０が０．００６０％と本
発明範囲より高＜、１１ｈ７はＮが０．００３０％と高
＜１ｔｋｔ８はＢを含有せず隘９はＢを含有していると
しても０．０００９％と本発明のＢ含有範囲の下限０．
００１５％に達せず、阻１０は反対にＢが０．００６５
％と高（、阻１１はＣが０．０１５％と本発明の上限範
囲より高いものである。Example 1 Fe-Ni having chemical components as shown in Table 1 below
The alloys of the present invention and comparative alloys were melted by vacuum melting, hot worked, and descaled to prepare cold rolled materials. That is, while Fish 1 to 3 all satisfy the range of the present invention, the S content of Ni 4 is high at 0.0035%, the P content of Fish 6 is high at 0.010%, and the comparison alloy with N0.6 has a high content of 0. .0060% is higher than the present invention range, 11h7 has N of 0.0030% and is higher than 1tkt8 does not contain B, and even if 9 does contain B, it is 0.0009%, which is the B content of the present invention. Lower limit of range 0.
0015% is not reached, and B is 0.0065 on the contrary.
% and high (11 has a C content of 0.015%, which is higher than the upper limit range of the present invention.
これらの素材はまず６５％の圧下率にて冷延し、次に８
００ ’Ｃにて焼鈍し、そののちに８０％の圧下率で冷
延した板厚０．２０の薄板サンプルより外径４５ｍｍ、
内径３３鶴のＪＩＳ リングに打抜き、試料とした。These materials were first cold rolled at a reduction rate of 65% and then rolled at a rolling reduction of 8%.
An outer diameter of 45 mm was obtained from a thin plate sample with a thickness of 0.20 that was annealed at 00'C and then cold rolled at a rolling reduction of 80%.
A JIS ring with an inner diameter of 33 mm was punched out and used as a sample.
上記のようにして得られた各試料を、水素雰囲気中で１
１００℃×１時間の熱処理を施し、１００”Ｃ／ｈｒで
冷却したものについての直流磁気特性を調べた。次の第
２表にＮｉ、μｍ、 Ｈｃ及びＢＩＧの各量の測定結果
を示すが、合金魚１．２の各村は、Ｃ，Ｐ、Ｓ、Ｎ、Ｏ
，Ｂの容量とも本発明成分範囲の合金であり、この実施
例の如く、冷延・焼鈍条件が本発明規定範囲内の場合は
初透磁率μｉは２６．０００以上、最大ｉ！ ６５ｉ率
μｍも１７０，０００以上、保磁力Ｈｃは、０．０２（
Φｅ）より小さ（優れた直流磁気特性を示している。ま
た、合金Ｎ１１３材はＣ，Ｐ、Ｓ、Ｎ、Ｏ，Ｂの容量が
本発明成分範囲内にあり、かつ熱間加工性の向上を意図
して微量のＣａ添加を行った合金であるが、この場合も
μｉ２μｍ、 Ｈｃは漱１．２の各村とほぼ同じレベル
ムこある。このようにｉｔのＣａ添加が行われた合金に
おいても、本発明の効果は十分に発揮されることがわか
る。Each sample obtained as above was heated for 1 hour in a hydrogen atmosphere.
The DC magnetic properties of the specimens were heat-treated at 100°C for 1 hour and cooled at 100"C/hr. Table 2 below shows the measurement results for the amounts of Ni, μm, Hc, and BIG. , each village of Alloy Fish 1.2 is C, P, S, N, O.
, B are both alloys within the composition range of the present invention, and when the cold rolling and annealing conditions are within the range specified by the present invention as in this example, the initial magnetic permeability μi is 26.000 or more, and the maximum i! The 65i ratio μm is also over 170,000, and the coercive force Hc is 0.02 (
Φe) (showing excellent DC magnetic properties.Also, the alloy N113 material has C, P, S, N, O, and B capacities within the composition range of the present invention, and has improved hot workability. In this alloy, a trace amount of Ca was added with the intention of It can be seen that the effects of the present invention are also fully exhibited.
第 ２ 表 一方、合金魚４〜７の各村はそれぞれ、ｓ、 ｐ。Table 2 On the other hand, each village of alloy fish 4 to 7 has s and p, respectively.
０、Ｎの容量が本発明成分範囲を超えることば前記の如
くで、階８及び患９はＢｆｆｉが本発明規定の下限未満
であり、階１０はＢｌが本発明規定の上限を越えるもの
であって隘１１はＣが高いことは上記の如くであり、か
つ各村ともその他の成分は本発明規定範囲内にある場合
であるが、いずれの場合でもＮｉはほぼ１０，０００以
下、μｍは高々９０．０００であり、Ｈｃは０．０３
（５ｅ）より大きく、直流磁気特性は、本発明で得られ
たものより劣っている。なお、Ｎｌｌｌ０材はＮｉ、Ｂ
、Ｓ、Ｐの容量が特開昭６２−２２７０６５の発明規定
範囲を満たすものであるが、この材料の磁気特性は、上
記の如く、本発明例に比べて明らかに劣り、本発明で目
的とする磁気特性の向上は、この特開昭６２−２２７０
６５の発明では達成されないことがわかる。As mentioned above, the capacity of 0 and N exceeds the component range of the present invention, and the Bffi of floors 8 and 9 is less than the lower limit defined by the present invention, and the Bl of floor 10 exceeds the upper limit defined by the present invention. As mentioned above, in case 11, C is high, and other components in each village are within the range specified by the present invention, but in all cases, Ni is approximately 10,000 or less, and μm is at most 90.000 and Hc is 0.03
(5e), and the DC magnetic properties are inferior to those obtained in the present invention. Note that the Nlll0 material is Ni, B
, S, and P satisfy the range stipulated in the invention of JP-A No. 62-227065, but the magnetic properties of this material are clearly inferior to those of the examples of the present invention, as described above, and are not suitable for the purpose of the present invention. The improvement of the magnetic properties was achieved in this Japanese Patent Application Laid-open No.
It can be seen that this cannot be achieved with the invention of No. 65.
以上のように、本発明の目的とする磁気特性は、冷延・
焼鈍条件を本発明規定内しても、成分が本発明範囲でな
ければ達成されないことが理解される。As described above, the magnetic properties that are the object of the present invention can be obtained by cold rolling.
It is understood that even if the annealing conditions are within the specifications of the present invention, the results will not be achieved unless the components are within the range of the present invention.
実施例２゜
本発明規定内の成分を有する前記第１表の合金嵐１材に
ついての冷延素材を次の第３表に示すような冷延・焼鈍
条件により作製した板厚０．２ ｍｍの薄板サンプルよ
り、外径４５ｍ、内径３３ｍのＪＩＳリングを打ち抜き
、試料とした。Example 2 A cold-rolled material of Alloy Arashi 1 material in Table 1 having components within the specifications of the present invention was prepared under the cold-rolling and annealing conditions shown in Table 3 below, with a thickness of 0.2 mm. A JIS ring with an outer diameter of 45 m and an inner diameter of 33 m was punched out from the thin plate sample and used as a sample.
試料を、水素雰囲気中で１１００℃×１時間の熱処理を
施し、１００°Ｃ／ｈｒで冷却したサンプルの直流磁気
特性を調べた。即ち第３表の後段に示すようなμｉ１μ
ｍ、 Ｈｃ及びＢ１゜の各量の測定結果が得られた。The sample was heat-treated at 1100° C. for 1 hour in a hydrogen atmosphere and cooled at 100° C./hr. The DC magnetic properties of the sample were investigated. In other words, μi1μ as shown in the latter part of Table 3
Measurement results for each amount of m, Hc and B1° were obtained.
即ち供試材階１〜３の各供試材は、１次冷延での圧下率
、２次冷延での圧下率および中間焼鈍温度が何れも本発
明の規定範囲内のものであって、Ｎｉは２６，０００以
上でμｍも１７０，０００以上であり、一方Ｈｃは０．
０２（ｂｅ）未満と優れた直流磁気特性を示している。That is, each of the test materials of test material grades 1 to 3 has a rolling reduction ratio in the primary cold rolling, a rolling reduction ratio in the secondary cold rolling, and an intermediate annealing temperature that are all within the specified range of the present invention. , Ni is 26,000 or more and μm is 170,000 or more, while Hc is 0.
It shows excellent DC magnetic properties with less than 0.02 (be).
これに対し、１Ｖｈ４材は２冷延での圧下率が本発明規
定の下限未満のもの、ＮＱ５材は中間焼鈍温度が本発明
規定の下限に達しないもの、寛６材は中間焼鈍温度の上
限を超えるもの、魚７材は１次冷延での圧下率が本発明
規定の下限未満のものであり、階８材は１次冷延のみの
ものであって、その他の条件はそれぞれ本発明の規定範
囲内のものであるが、Ｎｉは何れもせいぜい１９，００
０、μｍで高々１５０，０００． Ｈｃも０．０２５
（ｂｅ）より大きく、直流磁気特性は本発明例に見られ
るものに比較して劣っている。On the other hand, the 1Vh4 material has a rolling reduction ratio in the second cold rolling that is less than the lower limit specified by the present invention, the NQ5 material has an intermediate annealing temperature that does not reach the lower limit specified by the present invention, and the Kan6 material has an upper limit of the intermediate annealing temperature. In the case of the fish material 7, the rolling reduction ratio in the first cold rolling is less than the lower limit defined by the present invention, and in the case of the material No. 8, the reduction ratio in the first cold rolling is less than the lower limit defined by the present invention, and the other conditions are as follows. However, Ni is within the specified range of 19,00 at most.
0, μm at most 150,000. Hc is also 0.025
(be), and the DC magnetic properties are inferior to those seen in the examples of the present invention.
即ち本発明の目的とする磁気特性は単に成分が本発明規
定内であっても、冷延・焼鈍条件が本発明条件を満さな
ければ達成されないことが理解される。That is, it is understood that the magnetic properties aimed at by the present invention cannot be achieved unless the cold rolling and annealing conditions satisfy the conditions of the present invention, even if the components are within the specifications of the present invention.
「発明の効果」
以上説明したような本発明によるときは、Ｆｅ−Ｎｉ系
の高透磁率磁性合金における磁気特性の改良が図られ、
特に直流磁気特性が従来の同じ成分系であるＪＩＳ Ｐ
Ｂパーマロイよりも飛躍的に優れ、ＪＩＳＰＣパーマロ
イに準じた直流磁気特性を有せしめ、その用途は高磁界
において従来より高いシールド特性が求められる各種磁
気シールド材をはじめ、継鉄や直流重畳の変成器用鉄心
材料など栂めて広い利用範囲に対しを利に提供し得るも
のであって、工業的にその効果の大きい発明である。"Effects of the Invention" According to the present invention as explained above, the magnetic properties of a Fe-Ni-based high permeability magnetic alloy are improved,
In particular, JIS P whose direct current magnetic properties are the same component system as conventional
It is dramatically superior to B permalloy and has DC magnetic properties similar to JISPC permalloy, and its applications include various magnetic shielding materials that require higher shielding properties than conventional ones in high magnetic fields, as well as yoke and DC superposition transformers. This invention can be advantageously applied to a wide range of applications such as iron core materials, and has great industrial effects.
図面は本発明の技術的内容を示すものであって、第１図
は冷延条件と初透磁率および最大透磁率の関係を示した
図表、第２図は最大透磁率および初透磁率の中間焼鈍温
度による変化状態を要約して示した図表である。
第 ／ 圓
（Ｑ）４ＪＪｆｋＸｋｆ７１．、ｍｌ
（１−）最欠＄並率よThe drawings show the technical content of the present invention. Figure 1 is a chart showing the relationship between cold rolling conditions, initial magnetic permeability and maximum magnetic permeability, and Figure 2 is a diagram showing the relationship between the maximum magnetic permeability and the initial magnetic permeability. It is a chart summarizing the state of change depending on the annealing temperature. No. / En (Q) 4JJfkXkf71. , ml (1-) Most deficit $ average rate
Claims (1)
％以下、Ｓ：０．０００５〜０．００２ｗｔ％、Ｐ：０
．００６ｗｔ％以下、Ｏ：０．００３ｗｔ％以下、Ｎ：
０．００１５ｗｔ％以下、であって、かつ、 Ｂ：０．００１５〜０．００５０ｗｔ％ を含有し、残部は基本的にＦｅからなるＦｅ−Ｎｉ合金
である薄鋼帯の製造に際して前記合金の熱間加工後の冷
延を中間焼鈍をはさみ２回行い、かつ１回目の冷延での
圧下率を５０〜９８％、２回目の冷延での圧下率を７５
〜９８％、中間焼鈍を７３０〜９００℃でそれぞれ行う
ことを特徴とするＮｉ−Ｆｅ系高透磁率合金の製造方法
。[Claims] Ni: 43.0 to 48.0 wt%, C: 0.010 wt%
% or less, S: 0.0005-0.002wt%, P: 0
．． 006wt% or less, O: 0.003wt% or less, N:
0.0015 wt% or less, and contains B: 0.0015 to 0.0050 wt%, and the balance is basically Fe-Ni alloy. Cold rolling after rough working is performed twice with intermediate annealing in between, and the rolling reduction in the first cold rolling is 50 to 98%, and the rolling reduction in the second cold rolling is 75%.
98% and intermediate annealing at 730 to 900°C, respectively.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63091599A JPH0759741B2 (en) | 1988-04-15 | 1988-04-15 | Fe-Ni-based high permeability alloy and method for producing the same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63091599A JPH0759741B2 (en) | 1988-04-15 | 1988-04-15 | Fe-Ni-based high permeability alloy and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01263218A true JPH01263218A (en) | 1989-10-19 |
| JPH0759741B2 JPH0759741B2 (en) | 1995-06-28 |
Family
ID=14031021
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP63091599A Expired - Lifetime JPH0759741B2 (en) | 1988-04-15 | 1988-04-15 | Fe-Ni-based high permeability alloy and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0759741B2 (en) |
Cited By (5)
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|---|---|---|---|---|
| JPH02225621A (en) * | 1989-02-27 | 1990-09-07 | Daido Steel Co Ltd | Production of high permeability magnetic material |
| JP2015034329A (en) * | 2013-08-09 | 2015-02-19 | 日本冶金工業株式会社 | Fe-Ni-BASED PERMALLOY ALLOY AND PRODUCTION METHOD THEREOF |
| CN105929344A (en) * | 2015-02-26 | 2016-09-07 | 精工半导体有限公司 | Magnetic sensor and method of manufacturing the same |
| TWI675500B (en) * | 2015-02-26 | 2019-10-21 | 日商艾普凌科有限公司 | Magnetic sensor and method of manufacturing the same |
| CN116377284A (en) * | 2023-03-08 | 2023-07-04 | 北京北冶功能材料有限公司 | Iron-nickel-based soft magnetic alloy foil and preparation method and application thereof |
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| JPS6033337A (en) * | 1983-08-05 | 1985-02-20 | Nisshin Steel Co Ltd | High ni-fe alloy for electronic parts |
| JPS60159157A (en) * | 1984-01-30 | 1985-08-20 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy having excellent hot workability |
| JPS60248865A (en) * | 1984-05-23 | 1985-12-09 | Nippon Gakki Seizo Kk | High magnetic permeability alloy |
| JPS62142749A (en) * | 1985-12-18 | 1987-06-26 | Nippon Mining Co Ltd | High permeability pb permalloy having superior suitability to press blanking |
| JPS62227065A (en) * | 1986-03-28 | 1987-10-06 | Sumitomo Special Metals Co Ltd | High permeability magnetic alloy excellent in workability |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6033337A (en) * | 1983-08-05 | 1985-02-20 | Nisshin Steel Co Ltd | High ni-fe alloy for electronic parts |
| JPS60159157A (en) * | 1984-01-30 | 1985-08-20 | Nippon Yakin Kogyo Co Ltd | Fe-ni alloy having excellent hot workability |
| JPS60248865A (en) * | 1984-05-23 | 1985-12-09 | Nippon Gakki Seizo Kk | High magnetic permeability alloy |
| JPS62142749A (en) * | 1985-12-18 | 1987-06-26 | Nippon Mining Co Ltd | High permeability pb permalloy having superior suitability to press blanking |
| JPS62227065A (en) * | 1986-03-28 | 1987-10-06 | Sumitomo Special Metals Co Ltd | High permeability magnetic alloy excellent in workability |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02225621A (en) * | 1989-02-27 | 1990-09-07 | Daido Steel Co Ltd | Production of high permeability magnetic material |
| JP2015034329A (en) * | 2013-08-09 | 2015-02-19 | 日本冶金工業株式会社 | Fe-Ni-BASED PERMALLOY ALLOY AND PRODUCTION METHOD THEREOF |
| CN105929344A (en) * | 2015-02-26 | 2016-09-07 | 精工半导体有限公司 | Magnetic sensor and method of manufacturing the same |
| US20170294577A1 (en) * | 2015-02-26 | 2017-10-12 | Sii Semiconductor Corporation | Magnetic sensor and method of manufacturing the same |
| TWI675500B (en) * | 2015-02-26 | 2019-10-21 | 日商艾普凌科有限公司 | Magnetic sensor and method of manufacturing the same |
| CN116377284A (en) * | 2023-03-08 | 2023-07-04 | 北京北冶功能材料有限公司 | Iron-nickel-based soft magnetic alloy foil and preparation method and application thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0759741B2 (en) | 1995-06-28 |
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