JPS62124262A - Method for modifying magnetic characteristic of high permeability amorphous alloy - Google Patents
Method for modifying magnetic characteristic of high permeability amorphous alloyInfo
- Publication number
- JPS62124262A JPS62124262A JP61144002A JP14400286A JPS62124262A JP S62124262 A JPS62124262 A JP S62124262A JP 61144002 A JP61144002 A JP 61144002A JP 14400286 A JP14400286 A JP 14400286A JP S62124262 A JPS62124262 A JP S62124262A
- Authority
- JP
- Japan
- Prior art keywords
- less
- alloy
- amorphous
- magnetic
- amorphous alloy
- 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.)
- Pending
Links
- 230000005291 magnetic effect Effects 0.000 title claims abstract description 97
- 229910000808 amorphous metal alloy Inorganic materials 0.000 title claims abstract description 39
- 230000035699 permeability Effects 0.000 title claims description 43
- 238000000034 method Methods 0.000 title claims description 21
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 39
- 239000000956 alloy Substances 0.000 claims abstract description 39
- 238000001816 cooling Methods 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052779 Neodymium Inorganic materials 0.000 claims abstract description 5
- 229910052777 Praseodymium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052726 zirconium Inorganic materials 0.000 claims abstract 3
- 238000000137 annealing Methods 0.000 claims description 24
- 238000002425 crystallisation Methods 0.000 claims description 10
- 230000008025 crystallization Effects 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 5
- 229910052693 Europium Inorganic materials 0.000 claims description 4
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 4
- 229910052772 Samarium Inorganic materials 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052790 beryllium Inorganic materials 0.000 claims description 4
- 229910052797 bismuth Inorganic materials 0.000 claims description 4
- 230000005294 ferromagnetic effect Effects 0.000 claims description 4
- 229910052732 germanium Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052715 tantalum Inorganic materials 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052692 Dysprosium Inorganic materials 0.000 claims description 3
- 229910052771 Terbium Inorganic materials 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 239000004615 ingredient Substances 0.000 claims description 2
- 229910052689 Holmium Inorganic materials 0.000 claims 2
- 230000004048 modification Effects 0.000 claims 1
- 238000012986 modification Methods 0.000 claims 1
- 229910052751 metal Inorganic materials 0.000 abstract description 14
- 239000002184 metal Substances 0.000 abstract description 14
- 238000010438 heat treatment Methods 0.000 abstract description 13
- 239000000463 material Substances 0.000 abstract description 9
- 239000005300 metallic glass Substances 0.000 abstract description 5
- 239000010453 quartz Substances 0.000 abstract description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 5
- 229910052759 nickel Inorganic materials 0.000 abstract description 4
- 230000005307 ferromagnetism Effects 0.000 abstract description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 19
- 239000000203 mixture Substances 0.000 description 17
- 230000007423 decrease Effects 0.000 description 8
- 230000004907 flux Effects 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 230000005389 magnetism Effects 0.000 description 6
- 239000007769 metal material Substances 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 238000005260 corrosion Methods 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 5
- 230000005415 magnetization Effects 0.000 description 5
- 239000011162 core material Substances 0.000 description 4
- 150000002739 metals Chemical class 0.000 description 4
- 239000010949 copper Substances 0.000 description 3
- -1 Pm Inorganic materials 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 229910000889 permalloy Inorganic materials 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 238000006467 substitution reaction Methods 0.000 description 2
- 229910001017 Alperm Inorganic materials 0.000 description 1
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 230000005330 Barkhausen effect Effects 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910017061 Fe Co Inorganic materials 0.000 description 1
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000009760 electrical discharge machining Methods 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000007712 rapid solidification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229910000702 sendust Inorganic materials 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 229910002058 ternary alloy Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Soft Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、高透磁率アモルファス合金（特にＦｅ含有量
の少ない合金）の磁気特性改質方法、特に用途に応じて
履歴曲線の形状を調整できる方法に関する。Detailed Description of the Invention (Industrial Application Field) The present invention relates to a method for modifying the magnetic properties of a high magnetic permeability amorphous alloy (especially an alloy with a low Fe content), and particularly for adjusting the shape of a hysteresis curve depending on the application. Regarding how it can be done.
（従来の技術）
従来結晶構造を有する高透磁率金属材料として、Ｆｅ−
３ｉ合金、Ｆｒ−Ｎｉ合金、Ｆｅ−Ａ１合金、Ｆｅ−３
ｉ−Ａ１合金などがあり、それぞれの特性に応じて多く
の分野で使用されているが、これらの合金にはなおそれ
ぞれ特性上および使用上の欠点がある。(Prior art) Fe-
3i alloy, Fr-Ni alloy, Fe-A1 alloy, Fe-3
There are i-A1 alloys, etc., which are used in many fields depending on their properties, but each of these alloys still has drawbacks in terms of properties and use.
Ｆｅ−５ｉ合金は、変圧器、モータ等の鉄心として高透
磁率金属材料２４に使用されているが製造工程が複雑で
あり、これを製造するのに要する燃料ならびに電力も多
大であるから、終局的には原材料費の割合には高価な合
金となっている。Fe-5i alloy is used as a high magnetic permeability metal material 24 as an iron core for transformers, motors, etc., but the manufacturing process is complicated, and the amount of fuel and electricity required to manufacture it is large, so it cannot be used in the end. In terms of raw material cost, it is an expensive alloy.
Ｆｅ−Ｎ ｉ合金は、弱電関係の鉄心として使用されて
おり、なかでもＮｉ ７８％を含有するパーマロイは透
磁率が非常に高く、変成器、磁気ヘッド用として、また
デルタマックス（Ｎｉ ５０％と鉄を含有する磁性合金
の商品名）は履歴曲線が急峻な角形性を有するので、磁
気増幅器等の鉄心として使用さされている。しかし製造
方法はＦｅ−３ｉ合金と同様に複雑である上に高価なＮ
ｉを多量に使用するので非常に高価な材料である点で実
用上難点がある。Fe-Ni alloys are used as iron cores for weak electrical equipment, and permalloy, which contains 78% Ni, has extremely high magnetic permeability and is used for transformers, magnetic heads, and deltamax (with 50% Ni). The iron-containing magnetic alloy (trade name) has a steep angular hysteresis curve and is therefore used as an iron core for magnetic amplifiers and the like. However, the manufacturing method is complicated like that of Fe-3i alloy, and expensive N
Since a large amount of i is used, it is a very expensive material, which is a practical problem.
Ｆｅ−Ａｌ合金であるアルパームはＡＩ約１６％を含有
する高透磁率合金であるが、塑性加工が非常に困難であ
り、またＦｅ−３ｉ−Ａ１合金であるセンダスト（Ｆｅ
−１０％Ｓｉ−５％ＡＩ）は全く塑性加工ができないと
いう欠点があるので、特に高い硬度と高い固有抵抗を有
しているという特性が生かされる特殊な用途に限って特
殊加工の上使用されている。すなわち前者は録画用磁気
ヘッドとして温間加工により製作され、後者はカードリ
ーダー用の磁気ヘッドとして放電加工或いは研削加工に
よって製作されているから、前記欠点のためその用途は
自から制限されている。Alperm, an Fe-Al alloy, is a high permeability alloy containing about 16% AI, but it is extremely difficult to plastically work, and Sendust (Fe-3i-A1 alloy)
-10%Si-5%AI) has the disadvantage that it cannot be plastically worked at all, so it is only used after special processing in special applications where its characteristics of high hardness and high specific resistance are utilized. ing. That is, the former is manufactured by warm processing as a recording magnetic head, and the latter is manufactured by electrical discharge machining or grinding as a magnetic head for a card reader, so the above-mentioned drawbacks limit its use.
これら結晶質金属材料の前記欠点を改善するものとして
、非晶質（アモルファス）金属材料が注目を集めてきた
。しかし、未だ実用化研究はその緒についたところであ
り、ホー・ソー・チェノらの研究もあるが、未だ前記欠
点を十分には改善しておらず、特に用途に応じて非晶質
合金の履歴曲線の形状を調整することによって結晶質金
属材料の持つ前記欠点を十分に改善するには至ってなか
った（特開昭４９−９１０１４号公報参照）。Amorphous metal materials have been attracting attention as a means of improving the above-mentioned drawbacks of these crystalline metal materials. However, research on practical application is still in its infancy, and although research by Ho, Soe, and Cheno et al. It has not been possible to sufficiently improve the above-mentioned drawbacks of crystalline metal materials by adjusting the shape of the curve (see Japanese Patent Laid-Open No. 49-91014).
（発明が解決しようとする問題点）
すなわち、従来の結晶質金属材料の前記欠点を克服し、
なお且つ用途に応じて履歴曲線の形状を調整する技術は
未熟であり、産業界の要望に応えられるものではなかっ
た。(Problems to be solved by the invention) That is, to overcome the drawbacks of conventional crystalline metal materials,
Furthermore, the technology for adjusting the shape of the hysteresis curve depending on the application is still underdeveloped and has not been able to meet the demands of the industrial world.
そこで、本発明は組成を特定したアモルファス合金の熱
処理方法を工夫して磁気特性を用途に応じて改質する方
法を提供することを目的とする。Therefore, an object of the present invention is to provide a method for modifying the magnetic properties of an amorphous alloy according to the intended use by devising a heat treatment method for an amorphous alloy having a specified composition.
（問題点を解決するための手段）
本発明は、従来用いられている高透磁率金属材料が有す
る前記諸欠点のない新規な高透磁率率アモルファス合金
の磁気特性の改質方法を提供することを目的とし、Ｂの
み又はＢとＣとの合計で７〜３５原子％を含み残部常温
で強磁性を有するＣ。(Means for Solving the Problems) The present invention provides a method for modifying the magnetic properties of a novel high permeability amorphous alloy that does not have the above-mentioned drawbacks of conventionally used high permeability metal materials. C containing 7 to 35 atomic percent of B alone or the total of B and C, with the remainder being ferromagnetic at room temperature.
（但し、一部を２．１ ％未満のＦｅで置換）よりなる
アモルファス合金、またはこれに更に原子％で（イ）Ｎ
ｉ ２０％以下−（用途によって添加しないことがある
。）、（ロ）Ｓｉ２５％以下、（ハ） ＣｒおよびＭｏ
の少なくとも１種１５％以下、（ニ） Ｍｏ、 ２ｒ、
Ｔ ｌ。(However, a portion is replaced with less than 2.1% Fe), or an amorphous alloy consisting of (a) N
i 20% or less - (may not be added depending on the application), (b) Si 25% or less, (c) Cr and Mo
15% or less of at least one of (d) Mo, 2r,
Tl.
Ａｌ、 Ｖ、 Ｎｂ、 Ｔａ、 Ｗ、 Ｃｕ、 Ｇｅ、
ＢｅおよびＢｉのうちから選ばれた何れか１種または
２種以上を１０％以下、ならびに（ホ）Ｐｒ、 Ｎｄ、
Ｐｍ、 Ｓｍ、 Ｅｕ、 Ｇｄ、 ’Ｔｂ、 Ｄｙ
およびＨＯのうちから選ばれた何れか１種または２種以
上を５％以下、の前記（イ）、（ロ）、（ハ）。Al, V, Nb, Ta, W, Cu, Ge,
10% or less of one or more selected from Be and Bi, and (e) Pr, Nd,
Pm, Sm, Eu, Gd, 'Tb, Dy
and HO in an amount of 5% or less of any one or two or more selected from (a), (b), and (c) above.
（ニ）および（ホ）のうちから選ばれた何れか１または
２以上の成分を合計５０％以下で含有するアモルファス
合金を結晶温度以下で焼鈍処理を磁場中で行い、 歴曲
線の形状を変化調整させることによってその目的を達成
することができる。An amorphous alloy containing one or more components selected from (d) and (e) in a total amount of 50% or less is annealed in a magnetic field at a temperature below the crystallization temperature to change the shape of the history curve. This goal can be achieved by making adjustments.
（作 用）
通常金属は固体状態では結晶状態であるが、ある特殊な
条件（合金の組成、急冷凝固）下では固体状態でも液体
に類似した結晶構造をもたない原子構造が得られ、この
ような金属又は合金はアモルファス金属（又は非晶質金
属）と呼ばれている。(Function) Normally, metals are in a crystalline state in the solid state, but under certain special conditions (alloy composition, rapid solidification), even in the solid state, an atomic structure that does not have a crystalline structure similar to that of a liquid can be obtained. Such metals or alloys are called amorphous metals (or amorphous metals).
本発明者等は先に新規なアモルファス合金ならびにその
新規な製造方法を発明し、アモルファス合金の中にはそ
の成分組成によって特に機械特性、耐食性が驚異的に優
れたものがあることを新規に知見することができた。The present inventors previously invented a new amorphous alloy and a new method for producing the same, and newly found that some amorphous alloys have surprisingly excellent mechanical properties and corrosion resistance depending on their composition. We were able to.
またさらに、本発明者等は前記特定の成分組成を有する
アモルファス合金が極めて優れた透磁性を有することを
新規に知見した。第１表にそれらの一部の合金の成分組
成ならびに磁気特性中膜大透磁率および保持力を示す。Furthermore, the present inventors have newly discovered that an amorphous alloy having the above-mentioned specific composition has extremely excellent magnetic permeability. Table 1 shows the composition and magnetic properties of some of these alloys, including their large magnetic permeability and coercive force.
なお第１表には従来知られた高透磁率金属材料の磁気特
性を併記する。Table 1 also lists the magnetic properties of conventionally known high magnetic permeability metal materials.
Ｆｅ系、Ｃｏ系、Ｆｅ−Ｃｏ系アモルファス合金のＦｅ
およびまたはＣｏを前記種々の元素をもって部分的に置
換することによって機械特性ならびに耐食性を向上させ
ることができると共に、優れた磁気特性を有せしめるこ
とが判る。特にＣｒ、 Ｎｉ、 ５ｉｌｔＦｅ系および
Ｃｏ系アモルファス合金の透磁率を向上させるに有効な
成分元素であり、また前記各種元素成分を添加すること
により固有抵抗が高くなり、高周波特性が非常に向上す
る。Fe in Fe-based, Co-based, and Fe-Co-based amorphous alloys
It has been found that mechanical properties and corrosion resistance can be improved by partially substituting Co and/or Co with the various elements mentioned above, as well as excellent magnetic properties. It is a component element that is particularly effective in improving the magnetic permeability of Cr, Ni, 5iltFe-based and Co-based amorphous alloys, and addition of the various elemental components increases the specific resistance and greatly improves high frequency characteristics.
第１表
次に前記成分組成のアモルファス合金を製造する方法の
１例を図面により説明する。Table 1 Next, one example of a method for manufacturing an amorphous alloy having the above-mentioned composition will be explained with reference to the drawings.
第１図は前記アモルファス合金を製造する装置の一例を
示す概略図である。図において、１は下方先端に水平方
向に噴出するノズル２を有する石英管で、その中には原
料金属３が装入され、溶解される。４は原料金属３を加
熱するための加熱炉であり、５はモーター６により高速
度、例えば５０００ ｒ、ｐ、ｍ、 で回転される回
転ドラムで、これは、ドラムの回転による遠心力負荷を
できるだけ小さくするため、軽量で熱伝導性の良い金属
、例えばアルミニウム合金よりなり、内面には更に熱伝
導性の良い金属、例えば銅板７で内張すされている。FIG. 1 is a schematic diagram showing an example of an apparatus for producing the amorphous alloy. In the figure, 1 is a quartz tube having a nozzle 2 at its lower end that ejects water in a horizontal direction, into which raw metal 3 is charged and melted. 4 is a heating furnace for heating the raw metal 3; 5 is a rotating drum rotated by a motor 6 at a high speed, for example, 5000 r, p, m; In order to make it as small as possible, it is made of a lightweight metal with good heat conductivity, such as an aluminum alloy, and the inner surface is lined with a metal with good heat conductivity, such as a copper plate 7.
８は石英管ｌを支持して上下に移動するためのエアピス
トンである。原料金属は、先ず石英管１の送入口１ａよ
り流体搬送等により装入され加熱炉４の位置で加熱溶解
され、次いでエアピストン８により、ノズル２が回転ド
ラム５の内面に対向する如く、石英管１が図に示す位置
に下降され、次いで上昇を開始するとほぼ同時に溶融金
属３にガス圧が加えられて、金属が回転ドラムの内面に
向って噴流される。石英管内部へは金Ｒ３の酸化を防ぐ
ため絶えず不活性ガス、例えばアルゴンガス９を送入し
て不活性雲囲気としておくものとする。8 is an air piston for supporting the quartz tube l and moving it up and down. The raw metal is first charged through the inlet 1a of the quartz tube 1 by fluid conveyance, heated and melted in the heating furnace 4, and then heated and melted by the air piston 8 so that the nozzle 2 faces the inner surface of the rotating drum 5. The tube 1 is lowered to the position shown in the figure and then, at about the same time as it begins to rise, gas pressure is applied to the molten metal 3, causing the metal to be jetted against the inner surface of the rotating drum. In order to prevent the oxidation of gold R3, an inert gas such as argon gas 9 is constantly fed into the quartz tube to create an inert cloud atmosphere.
回転ドラム内面に噴流された金属は高速回転による遠心
力のため、回転ドラム内面に強く接触せしめられること
により、超高速冷却が与えられてアモルファス金属とな
る。The metal jetted onto the inner surface of the rotating drum is brought into strong contact with the inner surface of the rotating drum due to the centrifugal force caused by the high speed rotation, and is cooled at an ultra-high speed to become an amorphous metal.
本発明は、急冷状態において、前記第１表に示した如く
既に高い透磁率を有しているアモルファス合金に特殊な
熱処理を施すことによりさらに高透磁率と低保磁力とな
すことができると共に履歴曲線を用途に応じた形状に調
整できる磁気特性の改質方法を新規に知見したことに基
づくもので、前記高透磁率アモルファス合金を組成ある
いは形状に対応した適当な磁場中で結晶化する温度以下
に加熱した後組成に対応した適当な速度で冷却して磁場
中焼鈍することにより、履歴曲線の形状を調整すること
ができる。The present invention is capable of achieving even higher magnetic permeability and lower coercive force by subjecting an amorphous alloy, which already has high magnetic permeability as shown in Table 1, to special heat treatment in a rapidly cooled state. This is based on the discovery of a new method for modifying magnetic properties that allows the curve to be adjusted to a shape appropriate for the application, and is based on the discovery that the high magnetic permeability amorphous alloy can be adjusted to a temperature below the crystallization temperature in an appropriate magnetic field corresponding to the composition or shape. The shape of the hysteresis curve can be adjusted by heating the material to a temperature, then cooling it at an appropriate rate corresponding to the composition and annealing it in a magnetic field.
本発明の発明者等が発明した高透磁率アモルファス合金
は一般のアモルファス合金と同じくその成分組成に応じ
である温度で結晶性金属または合金に変化する結晶化温
度をもっている。アモルファス合金が結晶化すると、ア
モルファス合金としての特性が失われることになるので
、本発明の方法において熱処理温度は前記高透磁率アモ
ルファス合金の結晶化温度以下でなければならない。第
２表に前記高透磁率アモルファス合金の成分組成と結晶
化温度の数例を示す。The high magnetic permeability amorphous alloy invented by the inventors of the present invention, like general amorphous alloys, has a crystallization temperature at which it changes to a crystalline metal or alloy at a certain temperature depending on its component composition. When an amorphous alloy crystallizes, it loses its properties as an amorphous alloy, so in the method of the present invention, the heat treatment temperature must be below the crystallization temperature of the high magnetic permeability amorphous alloy. Table 2 shows several examples of the composition and crystallization temperature of the high magnetic permeability amorphous alloy.
第２表
第２表により判る如く、アモルファス合金はその組成に
より結晶化温度が異なるので、本発明の方法においても
、成分組成に応じた熱処理温度を選択することが必要で
ある。As can be seen from Table 2, the crystallization temperature of amorphous alloys differs depending on their composition, and therefore, in the method of the present invention, it is also necessary to select the heat treatment temperature according to the component composition.
本発明によれば、第１表に示す急冷状態の高透磁率アモ
ルファス合金を結晶化温度以下の比較的低温の焼鈍すな
わち３００〜４００℃で１０〜３５０分間保持すること
によって保磁力が約半分に減少する。According to the present invention, the coercive force is reduced by about half by annealing the rapidly cooled high permeability amorphous alloy shown in Table 1 at a relatively low temperature below the crystallization temperature, that is, by holding it at 300 to 400°C for 10 to 350 minutes. Decrease.
また、磁場中焼鈍によってさらに磁気特性を向上させる
ことができる。Furthermore, magnetic properties can be further improved by annealing in a magnetic field.
本発明方法の研究において、急冷状態、種々の熱処理状
態での履歴曲線と漸近飽和の領域の磁化曲線さらにそれ
らの磁場中焼鈍効果を調べた。In researching the method of the present invention, we investigated the hysteresis curves and magnetization curves in the asymptotic saturation region under rapid cooling conditions and various heat treatment conditions, as well as their annealing effects in a magnetic field.
（１）急冷状態のヒステリシス特性とその熱処理効果厚
さ約３０μｍ、幅約０．５ｍｍ、長さ３０ｃｍのＣｏ−
１３％Ｂ−７％Ｃの急冷状態のヒステリシスルーブヲＣ
１ｏｆｆｉ型のＢ−Ｈループ積分器で約２０層にリボン
を重ね巻きしたトロイダルコア試料の場合および１枚の
試料の場合についてＢ−８曲線を測定した。これらの履
歴曲線は大きなバルクハウゼン効果を持つ角型ヒステリ
シスループが特徴である。１枚で測定する場合は数段の
バルクハウゼン飛躍であるが、それが生ずる磁場は試料
各部で少し異なっている。平均の保磁力（Ｈｃ）は約０
．０８０ｅで良く吟味された純鉄の場合に匹敵し軟磁性
に属する。Ｃｏ−Ｂ−３ｉのＨｃはさ゛らに小さく約０
．０３０ｅである。このような軟磁性は非晶質の等方的
性質に起因しているものと思われる。(1) Hysteresis characteristics in quenched state and its heat treatment effect Co-
Hysteresis tube in quenching state of 13%B-7%C
B-8 curves were measured using a 1offi type B-H loop integrator for a toroidal core sample in which ribbons were wound in approximately 20 layers and for a single sample. These hysteresis curves are characterized by a square hysteresis loop with a large Barkhausen effect. When measuring with one sample, there is a Barkhausen leap of several steps, but the magnetic field generated is slightly different in each part of the sample. The average coercive force (Hc) is approximately 0
．． It is comparable to the case of pure iron, which was carefully examined in 080e, and belongs to soft magnetism. The Hc of Co-B-3i is even smaller, about 0.
．． It is 030e. Such soft magnetism is thought to be due to the isotropic nature of the amorphous material.
しかし、残留磁気（Ｂｒ）は急冷状態では必ずしも大き
くはない。Ｃｏ−Ｂ−Ｃの残留磁気（Ｂｒ）は約５６０
０ Ｇ で飽和磁気（ａｓ） １３９４０の約４０％
にすぎない。つまり６０％の磁化は磁場に対して大きな
抵抗力を示し１００〜２０００ｅでないと飽和しない。However, the residual magnetism (Br) is not necessarily large in the rapidly cooled state. The residual magnetism (Br) of Co-B-C is approximately 560
Approximately 40% of saturation magnetism (as) 13940 at 0 G
It's nothing more than that. In other words, 60% magnetization has a large resistance to the magnetic field and does not saturate unless it is 100 to 2000 e.
非晶質状態を保持できる比較的低温の焼鈍（３００℃Ｘ
３５０ｍ１ｎ）によって保磁力（Ｈｃ）は約１７２に減
少し同時に磁化は１０００程度で飽和に達するようにな
る。原子配列の無秩序性を理由に対称性から生ずる結晶
磁気異方性を無視したとして、なお残る抗磁力の原因を
磁歪を通じての磁気弾性効果と仮定すると、焼鈍による
保磁力（Ｈｃ）の減少は潜在的内部応力の緩和によると
考えられる。Relatively low-temperature annealing (300°C
350 m1n), the coercive force (Hc) decreases to about 172, and at the same time the magnetization reaches saturation at about 1000. If we ignore the magnetocrystalline anisotropy caused by symmetry due to the disorder of atomic arrangement, and if we assume that the cause of the remaining coercive force is the magnetoelastic effect through magnetostriction, then the decrease in coercive force (Hc) due to annealing is latent. This is thought to be due to the relaxation of internal stress.
さらに進んだ熱処理（３５０℃×２日）で非晶質状態は
体心立方晶に変わり、保磁力（Ｈｃ）は０．５〜１００
ｅ と大きくなる。Further heat treatment (350℃ x 2 days) changes the amorphous state to a body-centered cubic crystal, and the coercive force (Hc) is 0.5 to 100.
It becomes large as e.
（２）磁場中焼鈍効果
４００口ｅの磁場中で最高温度２８５℃から２４時間／
２６５℃の一定冷却速度を持って常温まで磁場中冷却し
たＦｅ−Ｂ−Ｃのヒステリシスループを測定した。この
場合も急冷状態に比較して保磁力（）ｌｃ）が大幅に減
少する。(2) Magnetic field annealing effect 24 hours/24 hours at a maximum temperature of 285°C in a 400-e magnetic field
The hysteresis loop of Fe-B-C cooled to room temperature in a magnetic field with a constant cooling rate of 265°C was measured. In this case as well, the coercive force () lc) is significantly reduced compared to the rapidly cooled state.
以上のごと＜、Ｃｏ系の非晶質金属は磁化過程において
顕著な軟磁特性を示すことが分った。As described above, it has been found that the Co-based amorphous metal exhibits remarkable soft magnetic properties during the magnetization process.
本発明方法に適するアモルファス合金における各成分の
含有量を限定する理由は次の如くである。The reason for limiting the content of each component in the amorphous alloy suitable for the method of the present invention is as follows.
ＢおよびＣはアモルファス組織とすることを助成する元
素であるが、これ等のうち少なくとも１種の含有量が７
原子％未渦の場合と、３５％を越えた場合にはアモルフ
ァス合金の製造が困難になり、かつ合金を脆化するので
７〜３５原子％の範囲内にする必要があり、Ｂのみまた
はＢとＣとの含有量はいずれも多いほど透磁率を高くす
るが、飽和磁束密度を低下するので、これ等の合計が２
０〜２５原子％の程度とするのが最良の結果を与える。B and C are elements that help form an amorphous structure, and the content of at least one of these is 7.
It is difficult to produce an amorphous alloy when there is no vortex, and when it exceeds 35 atomic %, it becomes difficult to manufacture an amorphous alloy and the alloy becomes brittle, so it is necessary to keep it within the range of 7 to 35 atomic %. The larger the content of C and C, the higher the magnetic permeability, but the lower the saturation magnetic flux density, so the total of these is 2.
A range of 0 to 25 atom % gives best results.
ＦｅとＣｏは常温で強磁性を示し、互いに全量置換でき
る元素であるが、Ｃｏ系の場合にはＣｏをＦｅで置換し
て行くと、飽和磁束密度が増大し、また保磁力は著しく
減少し約２原子％で極小（０，０１０ｅ）となる。Fe and Co are elements that exhibit ferromagnetism at room temperature and can be completely replaced with each other, but in the case of Co-based materials, when Co is replaced with Fe, the saturation magnetic flux density increases and the coercive force decreases significantly. It becomes minimum (0,010e) at about 2 atomic %.
したがって要求される特性に応じてＣｏ量をＦｅ２，１
％以下で置換することができる。すなわち、Ｆｅ置換に
伴ってＴｃ（キュリ一温度）が低下するので、耐熱性、
経時安定性を充分に必要とされる可飽和リアクトル等の
用途には、Ｆｅ置換量が２．１％未満であることが望ま
しい。Therefore, depending on the required characteristics, the amount of Co may be changed to Fe2,1
% or less can be substituted. In other words, as Tc (Curi temperature) decreases with Fe substitution, heat resistance,
For applications such as saturable reactors that require sufficient stability over time, it is desirable that the Fe substitution amount be less than 2.1%.
Ｎ＋は、透磁率を向上させる元素であるが２０原子％を
越えても透磁率はそれほど向上せず飽和磁束密度を減少
させるだけであるので２０原子％以下にする必要がある
。なお、用途によっては高価なＮｉを含有させなくても
よい。N+ is an element that improves magnetic permeability, but if it exceeds 20 atomic %, the magnetic permeability does not improve much and only decreases the saturation magnetic flux density, so it is necessary to limit it to 20 atomic % or less. Note that depending on the application, expensive Ni may not be included.
Ｓｌは透磁率を高め、保磁力を減少させる有効な元素で
あるがとくにＣｏ基アモルファス合金の場合に顕著な効
果がある。しかし、２５原子％を越えてもそれほど透磁
率を向上せず、飽和磁束密度を減少させるだけであるの
で２５原子％以下にする必要がある。Sl is an effective element for increasing magnetic permeability and decreasing coercive force, and has a particularly remarkable effect in the case of Co-based amorphous alloys. However, even if it exceeds 25 atom %, the magnetic permeability does not improve much and only the saturation magnetic flux density decreases, so it is necessary to keep it below 25 atom %.
ＣｒおよびＭｎを１５原子％以下とする理由は、Ｃｒは
透磁率を高め、保磁力を減少させ、さらに硬さ、耐食性
を向上させる有効な元素であり、またＭｎは透磁率、保
磁力を害せずにアモルファス合金を硬化させる元素であ
るがいずれも１５原子％を越えると飽和磁束密度を著し
く低下させるからである。The reason why Cr and Mn are set at 15 atomic % or less is that Cr is an effective element that increases magnetic permeability, reduces coercive force, and further improves hardness and corrosion resistance, and Mn harms magnetic permeability and coercive force. This is because, although they are elements that harden an amorphous alloy without carbon, if their content exceeds 15 at %, the saturation magnetic flux density will be significantly lowered.
Ｍｏ、 ｈ、 Ｔｉ、 Ａｌ、 Ｖ、 Ｎｂ、 Ｔａ、
Ｗ、 Ｃｕ、 Ｇｅ、 ＢｅおよびＢｉを１０原子％
以下とする理由は、これ等の元素はアモルファス構造の
安定化、硬さ、耐食性に有効な元素であるが、１０原子
％以下の場合にはこれらの特性を余り害せずに磁気特性
の改善の効果があるからである。Mo, h, Ti, Al, V, Nb, Ta,
W, Cu, Ge, Be and Bi at 10 atomic%
The reason for the following is that these elements are effective for stabilizing the amorphous structure, hardness, and corrosion resistance, but if the content is less than 10 atomic percent, they can improve the magnetic properties without significantly impairing these properties. This is because it has the effect of
Ｐｒ、 Ｎｄ、 Ｐｍ、 Ｓｍ、 Ｅｕ、 Ｇｄ、 Ｔ
ｂ、 Ｄｙ、 Ｎｏを５原子％以下とする理由は、５原
子％以下の場合は磁気特性を改善しかつアモルファス合
金を製造できるが、５原子％を越えるとアモルファス合
金の製造が困難になるからである。Pr, Nd, Pm, Sm, Eu, Gd, T
The reason why b, Dy, and No are kept at 5 atomic % or less is that if the content is 5 atomic % or less, the magnetic properties can be improved and an amorphous alloy can be manufactured, but if it exceeds 5 atomic %, it becomes difficult to manufacture an amorphous alloy. It is.
なお特許請求の範囲記載のアモルファス合金において（
イ）（ロ）（ハ）および（ニ）、又は（イ）（ロ）（ハ
）（ニ）および（ホ）のうちから選ばれた何れか１また
は２以上の成分を合計５０％以下とする理由は、これら
の成分合計が５０％を越えると飽和磁気が低下するから
である。In addition, in the amorphous alloy described in the claims (
A) (B) (C) and (D), or (A) (B) (C) (D) and (E) Any one or more ingredients selected from the following must be contained in a total of 50% or less. The reason for this is that if the total of these components exceeds 50%, the saturation magnetism decreases.
（実施例）
次に本発明の方法を実施例についてさらに詳細に説明す
る。(Example) Next, the method of the present invention will be described in more detail with reference to Examples.
実施例１
原子％でＢ １３％、Ｃ７％、残部Ｃｏよりなるアモル
ファス合金を製造し、１７．９ ｋｇ／ ｍｍ ２の張
力を加えながら３００℃で１時間焼鈍すると、保磁力０
．０５０ｅ、最大透磁率１３００００ 、角形性０．９
５の特性が得られた。Example 1 An amorphous alloy consisting of 13% B, 7% C, and the balance Co in terms of atomic percent was produced and annealed at 300°C for 1 hour while applying a tension of 17.9 kg/mm2, resulting in a coercive force of 0.
．． 050e, maximum permeability 130000, squareness 0.9
5 characteristics were obtained.
実施例２
実施例１の組成と同じアモルファス合金を４０００ｅの
磁場中で３３０℃まで加熱後直ちに２時間かけて常温ま
で磁場中冷却すると保磁力０．０１８、最大透磁率１８
００００ 、角形性０．３６の特性が得られた。Example 2 When an amorphous alloy having the same composition as in Example 1 is heated to 330°C in a magnetic field of 4000e and immediately cooled to room temperature over 2 hours in a magnetic field, the coercive force is 0.018 and the maximum permeability is 18.
0000 and squareness of 0.36.
第６図は同組成アモルファス合金に磁場中焼鈍を施した
際の最大透磁率と焼鈍温度、冷却速度との関係を示す図
、第７図は保磁力と焼鈍温度、冷却速度との関係を示す
図であり、高い最大透磁率でかつ小さな保磁力の優れた
高透磁率特性を得る。Figure 6 shows the relationship between maximum magnetic permeability, annealing temperature, and cooling rate when an amorphous alloy with the same composition is annealed in a magnetic field, and Figure 7 shows the relationship between coercive force, annealing temperature, and cooling rate. As shown in the figure, excellent high magnetic permeability characteristics with high maximum magnetic permeability and small coercive force are obtained.
なお、磁場中焼鈍の最適条件は、約２５０〜３５０℃の
アモルファス状態が安定に存在し得る温度範囲で磁化の
飽和に要する２００〜４０００ｅの範囲の磁場中で、５
０〜５００分／１００℃の冷却速度で冷却することによ
って得られる。The optimum conditions for annealing in a magnetic field are approximately 250 to 350°C, a temperature range where an amorphous state can stably exist, and a magnetic field of 200 to 4000 e, which is required for saturation of magnetization.
Obtained by cooling at a cooling rate of 0 to 500 minutes/100°C.
実施例３
実施例１と同じ組成のアモルファス合金に張力を約４０
ｋｇ／ｍｍ’およびねじり力（最大せん断芯力４ ｋｇ
／ ｍｍりを加えると保磁力０．１６０ｅ 、最大透
磁率８１０００、残留磁束密度１２９００ガウスでがっ
完全矩形履歴曲線の特性が得られた。なお高い残留磁束
密度でかつ小さな保磁力の優れた高透磁率特性を有する
張力範囲は約５〜４５ｋｇ＃ｕｎ２の間にある。Example 3 An amorphous alloy with the same composition as Example 1 was subjected to a tension of approximately 40
kg/mm' and torsional force (maximum shear core force 4 kg
/ mm, a perfectly rectangular hysteresis curve was obtained with a coercive force of 0.160e, a maximum permeability of 81000, and a residual magnetic flux density of 12900 Gauss. Furthermore, the tension range having excellent high magnetic permeability characteristics with high residual magnetic flux density and small coercive force is between about 5 and 45 kg#un2.
以上３つの実施例で得た本発明方法のアモルファス合金
の磁気特性をデルタマックスおよび７８バーマロイトと
比較すると第３表の如くである。The magnetic properties of the amorphous alloys produced by the method of the present invention obtained in the above three examples are compared with those of Deltamax and 78 vermaloid as shown in Table 3.
第３表
同表から明らかな如く、本発明方法による高透磁率合金
の実施例１，３の合金はデルタマックスに匹敵する磁気
特性を有し、また実施例２の合金は７８パーマロイに匹
敵する磁気特性を有する。As is clear from Table 3, the high magnetic permeability alloys produced by the method of the present invention in Examples 1 and 3 have magnetic properties comparable to Deltamax, and the alloy in Example 2 has magnetic properties comparable to 78 Permalloy. Has magnetic properties.
実施例４
原子％でＣ０７８％、Ｓｉ ５ ％ 、８１５％ 、
残部Ｆｅよりなるアモルファス合金を製造し、４０００
ｅの磁場中で３２０℃で１０分間焼鈍後、１時間１００
℃の割合で磁場中冷却すると、飽和磁束密度１１ＫＧ、
保磁力０．００９０ｅ 、最大透磁率２２０００００、
鉄損０、０８ Ｌ３７ｓｏ（Ｗａｔｔ／ｋｇ）が得られ
た。Example 4 C078%, Si 5%, 815% in atomic %,
An amorphous alloy consisting of the remainder Fe is produced, and 4000
After annealing for 10 min at 320 °C in a magnetic field of e, 100 °C for 1 h
When cooled in a magnetic field at a rate of ℃, the saturation magnetic flux density is 11KG,
Coercive force 0.0090e, maximum permeability 2200000,
An iron loss of 0.08 L37so (Watt/kg) was obtained.
実施例５
原子％で下記に示すＣｏ−３ｉ−Ｂ系合金を用いてアモ
ルファス合金を製造し、２５００ｅの磁場中で３００℃
から３６０℃で１０〜６０分間焼鈍後１時間１００ｔの
割合で冷却すると第４表に示す特性が得られた。Example 5 An amorphous alloy was produced using the Co-3i-B alloy shown below in atomic %, and heated at 300°C in a magnetic field of 2500e.
After annealing at 360° C. for 10 to 60 minutes and cooling at a rate of 100 tons for 1 hour, the properties shown in Table 4 were obtained.
実施例６
Ｃｏ−３ｉ−８の三元合金を溶融状態から圧延急冷法に
より厚さ３０μｍ、幅１．５＋＋＋ｍ、長さ数ｍの試料
を作製した。アモルファス合金はＣｏが８１−７３原子
％、Ｓｉが５〜１５原子％、Ｂが８〜１５原子％の範囲
で容易に得られた。これらの合金の中で（’ｏ ７８
％、８１１２％、８１０％の合金が優秀な磁気特性を示
した。Example 6 A sample having a thickness of 30 μm, a width of 1.5 +++ m, and a length of several meters was prepared from a molten Co-3i-8 ternary alloy by rolling quenching. Amorphous alloys were easily obtained with Co in the range of 81-73 at.%, Si in the range of 5-15 at.%, and B in the range of 8-15 at.%. Among these alloys ('o 78
%, 8112%, and 810% alloys exhibited excellent magnetic properties.
その結果を第５表に示す。The results are shown in Table 5.
第５表
本発明の方法によれば、急冷状態のアモルファス合金は
、アモルファス状態を保持できる比較的低温焼鈍によっ
て保磁力は約半分に減少するが、応力下焼鈍、磁場中焼
鈍或いはこれらを組合せ応力下磁場中焼鈍によってさら
に磁気特性を向上させることができる。応力下焼鈍の場
合が正の合金には張力を、負の合金には圧縮を加える必
要がある。また応力の大きさは合金組成に対応した最適
の範囲があり、必要以上に大きな応力を加えると保磁力
は急冷状態よりも大きくなる。合金組成に対応した最適
な応力下焼鈍を行うと、保磁力は半分以下に減少し、履
歴曲線は著しく急峻な角形性となる。またねじり応力に
より履歴曲線は完全な矩形になる。磁場中焼鈍あるいは
応力下磁場中焼鈍によって保磁力を下げ、透磁率を上げ
ることができるが、磁場中焼鈍の場合には角形性は余り
良くない。Table 5 According to the method of the present invention, the coercive force of an amorphous alloy in a rapidly cooled state is reduced to about half by annealing at a relatively low temperature that can maintain the amorphous state, but the coercive force is reduced by about half by annealing under stress, annealing in a magnetic field, or a combination of these. The magnetic properties can be further improved by annealing in a lower magnetic field. In the case of stress annealing, it is necessary to apply tension to alloys that are positive, and compression to alloys that are negative. Furthermore, the magnitude of stress has an optimum range depending on the alloy composition, and if a stress larger than necessary is applied, the coercive force becomes larger than that in the rapidly cooled state. When the stress annealing is performed optimally according to the alloy composition, the coercive force is reduced by more than half, and the hysteresis curve becomes extremely steep and square. Also, due to torsional stress, the hysteresis curve becomes a perfect rectangle. Magnetic field annealing or stress annealing in a magnetic field can lower the coercive force and increase magnetic permeability, but in the case of magnetic field annealing, the squareness is not very good.
磁気増幅器の鉄心の場合には急峻な角形性を、また磁気
ヘッドの場合には透磁率、保磁力が重要でむしろ角形性
の悪い材料が要求される。このように要求される履歴曲
線の形状は用途によって異なるので、それぞれの用途に
応じて磁気特性改質熱処理方法を選択する必要がある。In the case of the iron core of a magnetic amplifier, a material with steep squareness is required, and in the case of a magnetic head, magnetic permeability and coercive force are important, so a material with rather poor squareness is required. Since the shape of the required hysteresis curve differs depending on the application, it is necessary to select a heat treatment method for modifying magnetic properties according to each application.
以上本発明方法によれは、急冷状態で強度、耐摩耗性、
固有電気抵抗が非常に太き（、かつ耐食性の優れた高透
磁率アモルファス合金を用途に応じた履歴曲線の形状に
調整することだできるという特徴を有しているので、従
来の金属系高透磁率材料が使用されている変圧器、モー
タおよび磁気増幅器等の鉄心、あるいは音声用、録画用
およびカードリーダー用等の磁気ヘッドのコア材として
非常に好適な材料を提供することができる。As described above, the method of the present invention improves strength, abrasion resistance, and
The high permeability amorphous alloy has a very high specific electrical resistance (and excellent corrosion resistance) and can be adjusted to the shape of the hysteresis curve depending on the application, so it is different from conventional metallic high permeability. It is possible to provide a material that is very suitable for the core material of transformers, motors, magnetic amplifiers, etc. in which magnetic materials are used, or the core material of magnetic heads for audio, video recording, card readers, etc.
第１図はアモルファス合金を製造する装置の一例を示す
概略図である。FIG. 1 is a schematic diagram showing an example of an apparatus for manufacturing an amorphous alloy.
Claims (1)
含み、残部常温で強磁性を有するＣｏ（但し、一部を２
．１％未満のＦｅで置換）よりなる高透磁率アモルファ
ス合金を溶融状態より急冷し、アモルファス化する工程
と、これを結晶化温度以下、磁場中で焼鈍処理する工程
との結合を特徴とする高透磁率アモルファス合金の磁気
特性改質方法。 ２、原子％でＢのみ又はＢとＣとの合計で７〜３５％含
み、残部常温で強磁性を有するＣｏ（但し、一部を２．
１％未満のＦｅで置換）よりなり副成分として、 （イ）Ｓｉ２５％以下 （ロ）Ｃｒ及びＭｎの少なくとも１種１５％以下（ハ）
Ｍｏ、Ｚｒ、Ｔｉ、Ａｌ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｃｕ、
Ｇｅ、Ｂｅ及びＢｉのうちから選ばれた何れか１種また
は２種以上を１０％以下、 ならびに （ニ）Ｐｒ、Ｎｄ、Ｐｍ、Ｓｍ、Ｅｕ、Ｇｄ、Ｔｂ、Ｄ
ｙ及びＨｏのうちから選ばれた何れか１種ま たは２種以上を５％以下 の前記（イ）、（ロ）、（ハ）および（ニ）のうちから
選ばれた何れか１種または２種以上の成分を合計で５０
％以下で含有する合金を溶融状態より急冷し、アモルフ
ァス化する工程と、これを結晶化温度以下、磁場中で焼
鈍処理する工程との結合を特徴とする高透磁率アモルフ
ァス合金の磁気特性改質方法。 ３、原子％でＢのみ又はＢとＣとの合計で７〜３５％含
み、残部常温で強磁性を有するＣｏ（但し、一部を２．
１％未満のＦｅで置換）よりなり副成分として原子％で
、 （イ）Ｎｉ２０％以下 （ロ）Ｓｉ２５％以下 （ハ）Ｃｒ及びＭｎの少なくとも１種１５％以下（ニ）
Ｍｏ、Ｚｒ、Ｔｉ、Ａｌ、Ｖ、Ｎｂ、Ｔａ、Ｗ、Ｃｕ、
Ｇｅ、Ｂｅ及びＢｉのうちから選ばれた何れか１種また
は２種以上を１０％以下 （ホ）ならびにＰｒ、Ｎｄ、Ｐｍ、Ｓｍ、Ｅｕ、Ｇｄ、
Ｔｂ、Ｄｙ及びＨｏのうちから選ばれた何 れか１種または２種以上を５％以下 の前記（イ）、（ロ）、（ハ）（ニ）および（ホ）のう
ちから選ばれた何れか１種または２種以上の成分を合計
で５０％以下で含有する合金を溶融状態より急冷し、ア
モルファス化する工程と、これを結晶化温度以下、磁場
中で焼鈍処理する工程との結合を特徴とする高透磁率ア
モルファス合金の磁気特性改質方法。[Claims] 1. Contains B alone or a total of 7 to 35% of B and C in atomic %, and the remainder is Co which is ferromagnetic at room temperature (however, a part is 2
．． A high magnetic permeability amorphous alloy consisting of a high permeability amorphous alloy (substituted with less than 1% Fe) is rapidly cooled from a molten state to become amorphous, and annealing is performed in a magnetic field at a temperature below the crystallization temperature. Method for modifying magnetic properties of permeability amorphous alloys. 2. Contains B alone or a total of 7 to 35% of B and C in atomic %, and the remainder is Co which is ferromagnetic at room temperature (however, 2.
(substituted with less than 1% Fe) as a subcomponent, (a) 25% or less of Si (b) 15% or less of at least one of Cr and Mn (c)
Mo, Zr, Ti, Al, V, Nb, Ta, W, Cu,
10% or less of any one or more selected from Ge, Be and Bi, and (d) Pr, Nd, Pm, Sm, Eu, Gd, Tb, D
Any one or two selected from y and Ho with 5% or less of any one or two selected from the above (a), (b), (c), and (d). A total of 50 ingredients over seeds
Modification of the magnetic properties of a high magnetic permeability amorphous alloy, characterized by a combination of a step of rapidly cooling an alloy containing % or less from a molten state to make it amorphous, and a step of annealing it in a magnetic field at a temperature below the crystallization temperature. Method. 3. Contains only B or a total of 7 to 35% of B and C in atomic %, and the remainder is Co which is ferromagnetic at room temperature (however, a part is 2.
(substituted with less than 1% Fe) as a subcomponent in atomic %, (a) Ni 20% or less (b) Si 25% or less (c) at least 15% or less of at least one of Cr and Mn (d)
Mo, Zr, Ti, Al, V, Nb, Ta, W, Cu,
10% or less of any one or two or more selected from Ge, Be and Bi (e) and Pr, Nd, Pm, Sm, Eu, Gd,
Any one or more selected from Tb, Dy, and Ho with 5% or less of any one selected from the above (a), (b), (c), (d), and (e). A combination of a step of rapidly cooling an alloy containing one or more of the following components in a total amount of 50% or less from a molten state to make it amorphous, and a step of annealing it in a magnetic field at a temperature below the crystallization temperature. A method for modifying the magnetic properties of high magnetic permeability amorphous alloys.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61144002A JPS62124262A (en) | 1974-12-24 | 1986-06-21 | Method for modifying magnetic characteristic of high permeability amorphous alloy |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP751509A JPS5929644B2 (en) | 1974-12-24 | 1974-12-24 | Method for modifying magnetic properties of high magnetic permeability amorphous alloy |
| JP61144002A JPS62124262A (en) | 1974-12-24 | 1986-06-21 | Method for modifying magnetic characteristic of high permeability amorphous alloy |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP751509A Division JPS5929644B2 (en) | 1974-12-24 | 1974-12-24 | Method for modifying magnetic properties of high magnetic permeability amorphous alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62124262A true JPS62124262A (en) | 1987-06-05 |
Family
ID=26334728
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61144002A Pending JPS62124262A (en) | 1974-12-24 | 1986-06-21 | Method for modifying magnetic characteristic of high permeability amorphous alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62124262A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011058080A (en) * | 2009-09-14 | 2011-03-24 | Sanyo Special Steel Co Ltd | Co-BASED ALLOY EXCELLENT IN ABRASION RESISTANCE AND LUBRICITY, METHOD FOR PRODUCING THE SAME, AND SINTERED COMPACT THEREOF |
| JP2018076587A (en) * | 2016-11-11 | 2018-05-17 | ザ・スウォッチ・グループ・リサーチ・アンド・ディベロップメント・リミテッド | Co-BASED HIGH-STRENGTH AMORPHOUS ALLOY AND USE THEREOF |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5165395A (en) * | 1974-10-21 | 1976-06-05 | Western Electric Co | |
| JPS5929644A (en) * | 1982-08-12 | 1984-02-16 | ウエラ・アクチエンゲゼルシヤフト | 1,3-diamino-4-(2',2',2'-trifluoroethoxy)-benzole, manufacture and hair dye |
-
1986
- 1986-06-21 JP JP61144002A patent/JPS62124262A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5165395A (en) * | 1974-10-21 | 1976-06-05 | Western Electric Co | |
| JPS5929644A (en) * | 1982-08-12 | 1984-02-16 | ウエラ・アクチエンゲゼルシヤフト | 1,3-diamino-4-(2',2',2'-trifluoroethoxy)-benzole, manufacture and hair dye |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011058080A (en) * | 2009-09-14 | 2011-03-24 | Sanyo Special Steel Co Ltd | Co-BASED ALLOY EXCELLENT IN ABRASION RESISTANCE AND LUBRICITY, METHOD FOR PRODUCING THE SAME, AND SINTERED COMPACT THEREOF |
| JP2018076587A (en) * | 2016-11-11 | 2018-05-17 | ザ・スウォッチ・グループ・リサーチ・アンド・ディベロップメント・リミテッド | Co-BASED HIGH-STRENGTH AMORPHOUS ALLOY AND USE THEREOF |
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