JPH0277560A - Corrosion-resisting alloy with high saturation magnetic flux density - Google Patents
Corrosion-resisting alloy with high saturation magnetic flux densityInfo
- Publication number
- JPH0277560A JPH0277560A JP1094781A JP9478189A JPH0277560A JP H0277560 A JPH0277560 A JP H0277560A JP 1094781 A JP1094781 A JP 1094781A JP 9478189 A JP9478189 A JP 9478189A JP H0277560 A JPH0277560 A JP H0277560A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- flux density
- alloy
- magnetic flux
- magnetic
- 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.)
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Links
- 230000004907 flux Effects 0.000 title claims abstract description 35
- 239000001997 corrosion-resisting alloy Substances 0.000 title abstract 2
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 42
- 239000000956 alloy Substances 0.000 claims abstract description 42
- 238000005260 corrosion Methods 0.000 claims abstract description 25
- 230000007797 corrosion Effects 0.000 claims abstract description 25
- 239000000203 mixture Substances 0.000 claims abstract description 14
- 238000000465 moulding Methods 0.000 abstract description 7
- 230000006866 deterioration Effects 0.000 abstract description 6
- 229910052742 iron Inorganic materials 0.000 abstract description 2
- 230000035699 permeability Effects 0.000 description 12
- 230000007423 decrease Effects 0.000 description 9
- 238000012360 testing method Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 238000000034 method Methods 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 239000000696 magnetic material Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 239000011162 core material Substances 0.000 description 4
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 229910000702 sendust Inorganic materials 0.000 description 3
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 2
- 229910001035 Soft ferrite Inorganic materials 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 210000000078 claw Anatomy 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 229910000889 permalloy Inorganic materials 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000011282 treatment Methods 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」
本発明は磁気ヘッド用などとして好適で、高飽和磁束密
度を示し耐食性に優れた合金に関する。DETAILED DESCRIPTION OF THE INVENTION "Field of Industrial Application" The present invention relates to an alloy suitable for use in magnetic heads, etc., exhibiting a high saturation magnetic flux density and excellent corrosion resistance.
「従来の技術」
磁気ヘッド用材料などに用いられる高飽和磁束密度合金
において、−殻内に要求される磁気特性は、以下の■〜
■に記載する特性である。"Prior art" In high saturation magnetic flux density alloys used as materials for magnetic heads, the magnetic properties required within the shell are as follows:
These are the characteristics described in ①.
■耐摩耗性に優れていること。■It has excellent wear resistance.
■磁束密度が高いこと。■High magnetic flux density.
■透磁率が高いこと。■High magnetic permeability.
■低保磁力であること。■It must have low coercive force.
■耐食性に優れていること。■It has excellent corrosion resistance.
従ってこのような観点から種々の合金系において材料研
究がなされている。Therefore, from this point of view, material research is being conducted on various alloy systems.
ここで従来、磁気ヘッド用の磁性材料において著名なら
のとして、Ｆ ｅ−Ｎ ｉ系合金のパーマロイ、Ｆｅ−
５ｉ−ＡＩ系合金のセンダスト、あるいは、ソフトフェ
ライトなどが知られている。Conventionally, as well-known magnetic materials for magnetic heads, permalloy of Fe-Ni alloy, Fe-
Sendust, a 5i-AI alloy, and soft ferrite are known.
「発明が解決しようとする課題」
しかるに近年、オーディオ用録音機、家庭用ホームビデ
オ、あるいは、磁気カードなどに使用されでいる磁気記
録媒体が徐々に高保磁力化されている関係から、これら
の磁気記録媒体に好適な高性能磁気ヘッド用の磁性材料
が望まれている。``Problem to be solved by the invention'' However, in recent years, the coercive force of magnetic recording media used in audio recorders, household home videos, magnetic cards, etc. has gradually increased, and these magnetic A magnetic material for a high-performance magnetic head suitable for recording media is desired.
ところか前述のＦ ｅ−Ｎ ｉ系合金は、透磁率は比較
的高い乙のの耐摩耗性に劣る問題があり、Ｆｅ−５ｉ−
Ａ ｉ系合金は高飽和密度を示し硬度も高い利点を存す
る反面、加工性に劣る問題があり、ソフトフェライトは
磁束密度が低い問題を有しており、前記いずれの磁性材
料ら総ての面で満足な特性を得ることができるものでは
゛なかった。However, the Fe-Ni alloy mentioned above has a relatively high magnetic permeability and poor wear resistance.
Although A i-based alloys have the advantage of high saturation density and high hardness, they have the problem of poor workability, and soft ferrite has the problem of low magnetic flux density. However, it was not possible to obtain satisfactory characteristics.
なお、最近では、高飽和磁束密度材として前記Ｆ ｅ−
９ｉ−Ａ Ｉ系の合金が主として用いられるようになっ
ているが、この系の合金の磁束密度を更に改仰した上で
面性の各要件を満たしうる磁性合金として本発明者らは
先に、特願昭６３−６４１０号明細吉においてＦ ｅ−
Ｇ ｏ−９ｉ−Ａ Ｉ系の磁性材料を提案した。この磁
性材料は、Ｃｏ ３〜２０重量％、Ｓｉ６〜１２重量％
、ＡＩ ０．１〜３重壜％を含ａし、残部Ｆｅの組成を
有してなるものである。しかしながらこの系の合金は、
磁気記録用のヘッドコア材として優れた特性を何してい
る乙のの、Ｆｅを主体とした合金であるために、高温多
湿などの環境下における耐食性の而では不安かあった。In addition, recently, the above-mentioned Fe-
9i-A I series alloys have come to be mainly used, but the present inventors have previously developed a magnetic alloy that can satisfy the requirements for planarity by further revising the magnetic flux density of this series alloy. , in patent application No. 63-6410, F e-
We proposed a Go-9i-A I-based magnetic material. This magnetic material contains 3-20% by weight of Co and 6-12% by weight of Si.
, 0.1 to 3% of Al, and the balance is Fe. However, this type of alloy is
Although it has excellent properties as a head core material for magnetic recording, since it is an alloy mainly composed of Fe, there were concerns about its corrosion resistance in environments such as high temperature and humidity.
本発明は前記課題に鑑み、本発明者らか先に提案したＦ
ｃ−Ｇ ｏ−５ｉ−Ａ Ｉ基磁性材料の耐食性を向」
ニさせる目的でなされたもので、高飽和磁束密度を示し
、耐食性に優れた合金を提供することを目的とする。In view of the above-mentioned problems, the present invention has been developed by the present inventors.
c-G o-5i-A Improving the corrosion resistance of I-based magnetic materials
The purpose is to provide an alloy that exhibits high saturation magnetic flux density and excellent corrosion resistance.
「課題を解決するだめの手段」
本発明は前記課題を解決するために、
３重重％ ≦ＣＯ≦ ２０重看％、
６重重％ ≦Ｓｉ≦ １２重１％、
０．１重１％ ≦ＡＩ≦ ３重ｒｉ［、■、閤１％ ≦
Ｃｒ≦ ４重量％、
Ｆｅ 残部
の組成を有したものである。"A Means to Solve the Problems" In order to solve the above-mentioned problems, the present invention provides the following: 3 weight%≦CO≦20 weight%, 6 weight%≦Si≦12 weight 1%, 0.1 weight 1%≦AI ≦ Triple ri[, ■, 1% ≦
It has a composition of Cr≦4% by weight and the balance being Fe.
更に本発明では前記課題を解決するために、３重量％
≦Ｃｏ≦ ２０重項％、
６重量％ ≦Ｓｉ≦ １２重量％、
０１重１％ ≦Ａ１≦ ３重重％、
０５重里％ ≦Ｃｒ≦ ４重撹％、
Ｒｕ＜１０重量％、
Ｆｅ 残部
の組成を存したものである。Furthermore, in the present invention, in order to solve the above problems, 3% by weight
≦Co≦ 20 weight %, 6 weight % ≦Si≦ 12 weight %, 01 weight 1% ≦A1≦ 3 weight %, 05 weight % ≦Cr≦ 4 weight %, Ru<10 weight %, Fe Remaining composition It existed.
本発明において、Ｓｌの含有量を６〜１２重１％とした
のは、Ｓｉの含有量か６重量％より小さい値では、Ｆｅ
−Ｃｏ −Ｓ ｉ −Ａ Ｉ系において、零磁歪が存
在しなくなるためであり、Ｓｉ含有量が１２重爪形を超
える値では飽和磁束密度が著しく低下して高飽和磁束密
度材とならないためである。In the present invention, the reason why the Si content is 6 to 12% by weight is that if the Si content is smaller than 6% by weight, Fe
-Co -S i -A This is because zero magnetostriction no longer exists in the I system, and when the Si content exceeds a 12-fold claw shape, the saturation magnetic flux density decreases significantly and a high saturation magnetic flux density material cannot be obtained. be.
また、Ｃｏの含有量を３〜２０重債％に限定したのは、
ＣＯ含有量が３重量％より小さい値では、昔しく脆くな
り、Ｃｏ含汀量が２０重量％を超える値では磁歪がずれ
てＳｉ含有愼を多くしないと磁歪零が存在しなくなり飽
和磁束密度が低下するためである。更に、ＡＩをＯｌ〜
３重量％含仔しているが、この理由は、Ｆｅ−Ｃｏ−５
ｉ系の合金のマクロ組織は柱状晶を示し、極めて脆いも
のであるが、この系の合金に前記組成範囲でＡＩを添加
すると、マクロ組織が等軸晶に変化し、脆さを改善でき
るためである。すなわち、ＡＩの含有ｆｆｌを０．１〜
３重量％とじたのはＡ＋含仔量が０１重量％より小さい
値では柱状晶から等軸品への組織の変化が見られず、Ａ
Ｉ含何量が３重量％を超えろ値では飽和磁束密度の低下
を来すためでめろ。In addition, the reason why the Co content was limited to 3 to 20% was that
When the CO content is less than 3% by weight, it becomes brittle, and when the Co content exceeds 20% by weight, the magnetostriction shifts and zero magnetostriction does not exist unless the Si content is increased, and the saturation magnetic flux density decreases. This is because it decreases. Furthermore, AI
The reason for this is that Fe-Co-5 contains 3% by weight of grains.
The macrostructure of the i-series alloy shows columnar crystals and is extremely brittle, but when AI is added to this alloy in the above composition range, the macrostructure changes to an equiaxed crystal and the brittleness can be improved. It is. That is, the content ffl of AI is 0.1~
3% by weight was used because when the A+ grain content was less than 01% by weight, no change in the structure from columnar crystals to equiaxed products was observed;
If the I content exceeds 3% by weight, the saturation magnetic flux density will decrease.
また本発明において、Ｃｒを単独で含有する場合、Ｃｒ
含ａ量を１．５重里％以下とすると耐食性の向上効果が
見られず、４重里％以上とすると飽和磁束密度が１３０
００Ｇ以下に低下してしまう。Further, in the present invention, when Cr is contained alone, Cr
When the a content is less than 1.5%, no improvement in corrosion resistance is observed, and when it is more than 4%, the saturation magnetic flux density is 130%.
It will drop below 00G.
一方、ＣｒとＲｕを両方含有する場合、Ｃｒ含１が０．
５重１％より小さい値ではその効果が少なく、４重積％
を超えると飽和磁束密度の低下が昔しくなり、Ｒｕ含有
量は５重量％を超えると磁気特性の劣化を生じるが、１
０重量％より少ない頃までは添加しても差し支えない。On the other hand, when both Cr and Ru are contained, the Cr content is 0.
If the value is smaller than 1% of the quintuple, the effect will be small, and the quadruple %
If the Ru content exceeds 5% by weight, the saturation magnetic flux density will deteriorate, and if the Ru content exceeds 5% by weight, the magnetic properties will deteriorate.
It may be added until it is less than 0% by weight.
なお、耐食性の効果に関し、Ｃｒ添加がａ効であり、更
にＲｕをＩＪＯえると耐食性が相乗効果で向上し、しか
も、Ｃｒの添加による飽和磁束密度の低下をＲｕの添加
で抑制することができる。Regarding the effect of corrosion resistance, the addition of Cr has an a-effect, and adding Ru to IJO improves the corrosion resistance with a synergistic effect, and furthermore, the decrease in saturation magnetic flux density due to the addition of Cr can be suppressed by the addition of Ru. .
なお、本発明合金はアーク炉を用いた溶解法、真空溶解
法、粉末冶金法などの常法で製造することができろ。The alloy of the present invention can be manufactured by conventional methods such as a melting method using an arc furnace, a vacuum melting method, and a powder metallurgy method.
「実施例Ｊ
本発明組成の合金３００ｇをアーク溶解炉を用いて溶製
し、放電加工により外径１０ｍｍ、内径６ｍｍ、厚さＩ
ｍｍのリング状の試料を複数得た。また、本発明外の
組成の合金試料を前述の方法と同等の方法で作成した。"Example J 300g of the alloy having the composition of the present invention was melted using an arc melting furnace, and was melted by electric discharge machining into an outer diameter of 10 mm, an inner diameter of 6 mm, and a thickness of I.
A plurality of ring-shaped samples of mm in diameter were obtained. In addition, alloy samples having compositions other than those of the present invention were prepared by a method equivalent to the method described above.
次いでこれらの試料のいくつかを水素雰囲気中において
９００℃で２時間加熱した後に炉冷する焼鈍処理を施し
て磁気特性とビッカース硬さを測定した。なお、磁気特
性については、初期の透磁率およびモールド劣化後の透
磁率と、初期の保磁力およびモールド劣化後の保磁力と
、飽和磁束密度を測定した。また、残りの試料について
は、温度６０℃、湿度９５％の空気中に９６時間放置し
て発錆状況を観察する腐食判定試験を行った。この腐食
判定試験において、全体に錆を発生した試料は第１表に
Ｘ印で示し、少竜の錆が点在的に生じた試料については
Δ印で示し、全く錆を生じない試料については第１表に
○印で示した。Next, some of these samples were subjected to an annealing treatment in which they were heated at 900° C. for 2 hours in a hydrogen atmosphere and then cooled in a furnace, and their magnetic properties and Vickers hardness were measured. Regarding the magnetic properties, the initial magnetic permeability and the magnetic permeability after mold deterioration, the initial coercive force and the coercive force after mold deterioration, and the saturation magnetic flux density were measured. Further, the remaining samples were subjected to a corrosion determination test in which they were left in air at a temperature of 60° C. and a humidity of 95% for 96 hours and the state of rust was observed. In this corrosion determination test, samples with rust all over are indicated with an X mark in Table 1, samples with scattered rust are indicated with a Δ mark, and samples with no rust are indicated with a Δ mark. It is indicated by a circle in Table 1.
以上の測定結果を第１表と第２表に示す。The above measurement results are shown in Tables 1 and 2.
第１表
第１表と第２表から、本発明の合金試料Ｎ ｏ ５〜１
５にあっては、ＣｒあるいはＲｕを添加してぃない合金
試料である比較例３．４に比較して耐食性が向上してい
ることか明らかである。From Table 1 and Table 2, alloy samples of the present invention No. 5 to 1
It is clear that the corrosion resistance of No. 5 is improved compared to Comparative Example 3.4, which is an alloy sample without addition of Cr or Ru.
また、本発明の試料Ｎｏ５〜１５および１８〜２０は、
いずれら１３０００Ｇ以上の飽和磁束密度を示し、一般
に知られるセンダストの飽和磁束密度（１１ｏ００ｃ）
より高い飽和磁束密度を示すことが明らかである。また
、各試料Ｎｏ５〜１５および１８〜２０ともモールド劣
化後の透磁率は十分に高く、又、保磁力は十分に低く、
優れた磁気特性を存している。In addition, samples Nos. 5 to 15 and 18 to 20 of the present invention are
Both exhibit a saturation magnetic flux density of 13000G or more, and the saturation magnetic flux density (11o00c) of the commonly known Sendust
It is clear that it exhibits a higher saturation magnetic flux density. In addition, for each sample No. 5 to 15 and No. 18 to 20, the magnetic permeability after mold deterioration is sufficiently high, and the coercive force is sufficiently low.
It has excellent magnetic properties.
なお、試料Ｎｏ８，９，１２，１３，１５．１６．１８
はＦ ｅ−Ｃｏ−５ｉ−Ａ Ｉ系にＣｒを添加した合金
であるが、Ｃｒを３重重％添加した試料Ｎｏ９において
飽和磁束密度が１３１００に低下している。更に、試料
Ｎｏｌ ６と試料Ｎｏｌ ８を比較して明らかなように
Ｃｒ含有量が１．５重量％から１．０重量％に低下する
と腐食性が低下している。従って本発明ではＣｒ添加俄
の上限を４重量％、下限を１５重■％とした。In addition, sample No. 8, 9, 12, 13, 15.16.18
is an alloy in which Cr is added to the Fe-Co-5i-A I system, but the saturation magnetic flux density decreases to 13,100 in sample No. 9 in which 3% by weight of Cr is added. Furthermore, as is clear from comparing Sample No. 6 and Sample No. 8, when the Cr content decreases from 1.5% by weight to 1.0% by weight, the corrosivity decreases. Therefore, in the present invention, the upper limit before adding Cr is set to 4% by weight, and the lower limit is set to 15% by weight.
また、試料Ｎｏ５，６，７．１０，１１，１４，１７゜
１９．２０はＦ ｅ−Ｃｏ−５ｉ−Ａ Ｉ系にＣｒとＲ
ｕを添加した合金である。Ｒｕに関し、試料Ｎｏ５．７
．Ｉ７に見られるように、Ｒｕ含Ｎｆｆ１５重量％では
各特性に優れているが、１０重量％では透磁率の低下が
著しい。更に、試料ＮＯ２ＯのＣｒ含有↑に見られるよ
うに、Ｃｒを３重量％添加すると飽和磁束密度が１３０
００Ｇに低下している。なお、前記腐食試験結果をＣｒ
添加量とＲｕ添加量の関係についてまとめてみると第１
図に示すようになる。In addition, sample Nos. 5, 6, 7.10, 11, 14, 17°19.20 have Cr and R in the Fe-Co-5i-A I system.
This is an alloy containing u. Regarding Ru, sample No. 5.7
．． As seen in I7, a Ru-containing Nff content of 15% by weight is excellent in each property, but a 10% by weight content shows a significant decrease in magnetic permeability. Furthermore, as seen in the Cr content↑ of sample NO2O, when 3% by weight of Cr is added, the saturation magnetic flux density increases to 130%.
It has dropped to 00G. Note that the above corrosion test results are
To summarize the relationship between the amount of addition and the amount of Ru added, the first
The result will be as shown in the figure.
以上の結果を鑑みてＣｒ含ｑ量を１〜４重量％、Ｒｕ含
有量を１０重里％より少ない量に限定した。In view of the above results, the Cr content was limited to 1 to 4% by weight, and the Ru content was limited to less than 10% by weight.
従って本発明の合金は、磁気へラドコア用として好適で
あり、磁気ヘッドコア用として用いた場合、１３０００
Ｇ以上の優れた飽和磁束密度を示し、透磁率が高く保磁
力か低い上に、モールド後の磁気特性ら優れ、硬度が高
くて摩耗に強く、しかも耐食性に優れた磁気ヘッドを得
ることができる。Therefore, the alloy of the present invention is suitable for magnetic helad cores, and when used for magnetic head cores,
It is possible to obtain a magnetic head that exhibits an excellent saturation magnetic flux density of G or higher, has high magnetic permeability and low coercive force, has excellent magnetic properties after molding, is highly hard, resistant to abrasion, and has excellent corrosion resistance. .
即ち本発明の合金は、磁気記録媒体の高性能化が進めら
れている磁気カード用の磁気ヘット材料、オーディオ録
音機用ヘッド材料、ビデオ装置用ヘッド材料なととして
好適である。That is, the alloy of the present invention is suitable as a magnetic head material for magnetic cards, a head material for audio recorders, a head material for video devices, etc., where the performance of magnetic recording media is being improved.
ところで更に、本発明において限定した組成と比較組成
の合金について、飽和磁束密度と透磁率の検討を行った
。この検討を行う前に、−殻内な組成の合金について磁
気特性の測定を行った。By the way, the saturation magnetic flux density and magnetic permeability of alloys with the composition limited in the present invention and comparative compositions were also investigated. Before conducting this study, the magnetic properties of an alloy with a -shell composition were measured.
まず、出発材料として、電解鉄（純度９９．９％以上）
、電解コバルト（純度９９９％）、Ｓ ｉ（９９。First, as a starting material, electrolytic iron (purity of 99.9% or more)
, electrolytic cobalt (999% purity), Si (99.
９９９％）などを用い、アーク溶解炉によりＡ ｒ雰囲
気中で溶製してインゴットを得た。得られたインゴット
から放電加工等により外１Ｍ１０ｍｍ、内径６ ｍｍ、
厚さ１＋ｎｍのリング状試験片に加工し、Ｌ（ｔガス中
で種々の熱処理を施した。透磁率の測定はトランス法に
より、０．３ ｋＨｚ −１０ｋＨｚの間で行った。磁
気特性は直流Ｂ−Ｈルーブトレーザーにて測定した。飽
和磁束密度の測定はＶＳ〜１（残留側波帯変調）にて行
った。また、耐食性の評価は面紀耐食試験法と同様の耐
湿試験とした。999%), etc., and was melted in an Ar atmosphere in an arc melting furnace to obtain an ingot. The obtained ingot was machined by electric discharge machining etc. to an outer diameter of 1 m and 10 mm, an inner diameter of 6 mm,
It was processed into a ring-shaped test piece with a thickness of 1+ nm and subjected to various heat treatments in L (t gas). The magnetic permeability was measured between 0.3 kHz and 10 kHz using the transformer method. The magnetic properties were measured using direct current. Measured using a B-H Lube laser.Saturation magnetic flux density was measured using VS~1 (residual sideband modulation).Corrosion resistance was evaluated using a moisture resistance test similar to the surface corrosion resistance test method. .
まず第３表に、飽和磁束密度（Ｂ ｓ）と透磁率（μ）
（初期特性と樹脂モールド後の劣化した特性）の測定結
果を示す。First, Table 3 shows the saturation magnetic flux density (B s) and magnetic permeability (μ).
The measurement results (initial characteristics and deteriorated characteristics after resin molding) are shown.
第３表
第３表に示すように飽和磁束密度と透磁率が高く、しか
も樹脂モールドによる劣化ら少ない合金は、Ｆ ｅ−８
Ｃｏ−８Ｓ ｉ合金であるので、以下にこの合金を基に
、耐食性の向上効果について検討した。Table 3 As shown in Table 3, the alloy that has high saturation magnetic flux density and magnetic permeability and is less susceptible to deterioration due to resin molding is Fe-8.
Since it is a Co-8Si alloy, the effect of improving corrosion resistance was investigated based on this alloy below.
耐食性の改善は、ＣｒとＲｕを加えることで行った。そ
の結果を第２図に示す。Corrosion resistance was improved by adding Cr and Ru. The results are shown in FIG.
第２図に示す結果から本発明で限定した範囲が耐食性向
上の面で適切であったことが明らかである。From the results shown in FIG. 2, it is clear that the range limited by the present invention was appropriate in terms of improving corrosion resistance.
また、Ｃｒ、Ｒｕの添加量と飽和磁束密度の関係は、第
３図に示すようになった。Furthermore, the relationship between the amounts of Cr and Ru added and the saturation magnetic flux density is as shown in FIG.
発錆のない添加条件内での飽和磁束密度の最高値は１．
５％Ｃｒ−１％Ｒｕにおける１、４８Ｔであった。The maximum value of saturation magnetic flux density within the additive conditions without rusting is 1.
It was 1,48T in 5%Cr-1%Ru.
「発明の効果Ｊ
以上説明したように本発明は、Ｆｅを主成分とし、Ｃｏ
とＳｉとＡＩとＣｒ、 あるいは、ＣＯと８１とＡＩ
とＣｒとＲｕを特別な量含有するものであるために、磁
気特性に優れ、モールド後の磁気特性の劣化も少なく、
特に１３０００Ｇ以上の高い飽和磁束密度を示し、硬度
が高い上に、耐食性に６優れた合金である。“Effect of the Invention J As explained above, the present invention has Fe as a main component and Co
and Si, AI and Cr, or CO, 81 and AI
Because it contains special amounts of Cr and Ru, it has excellent magnetic properties and has little deterioration of magnetic properties after molding.
In particular, it is an alloy that exhibits a high saturation magnetic flux density of 13,000 G or more, has high hardness, and has excellent corrosion resistance.
従って本発明の合金で磁気へソドコアを構成することが
でき、その場合、モールド後の透磁率に優れ、モールド
後の保磁力か低く、センダスト以上の飽和磁束密度を示
すなどの磁気特性に優れ、硬度が高くて摩耗に強く、し
から耐食性に富む磁気ヘッドを得ることができる効果か
ある。即ち本発明の合金は、磁気記録媒体の高性能化が
進められている磁気カード用の磁気ヘッド材料などとし
て好適である。Therefore, it is possible to construct a magnetic hemisode core using the alloy of the present invention, and in that case, it has excellent magnetic properties such as excellent magnetic permeability after molding, low coercive force after molding, and a saturation magnetic flux density higher than that of Sendust. This has the effect of making it possible to obtain a magnetic head that has high hardness, is resistant to abrasion, and is highly corrosion resistant. That is, the alloy of the present invention is suitable as a magnetic head material for magnetic cards, where the performance of magnetic recording media is being improved.
第１図は本発明組成の各合金試料の腐食？ｌＩ定試験結
果を示す線図、第２図は本発明組成の合金試料と比較例
の合金試料の発錆試験結果を示す図、第３図はＲｕ、Ｃ
ｒの含ａ量と飽和磁束密度の関係を示す線図である。Figure 1 shows the corrosion of each alloy sample with the composition of the present invention. Figure 2 is a graph showing the results of the II constant test, Figure 2 is a diagram showing the results of the rusting test for the alloy sample with the composition of the present invention and the alloy sample of the comparative example, and Figure 3 is a diagram showing the results of the rusting test for the alloy sample of the present invention composition and the alloy sample of the comparative example.
FIG. 3 is a diagram showing the relationship between the a content of r and the saturation magnetic flux density.
Claims (1)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1094781A JPH0277560A (en) | 1988-06-03 | 1989-04-14 | Corrosion-resisting alloy with high saturation magnetic flux density |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP63-136791 | 1988-06-03 | ||
| JP13679188 | 1988-06-03 | ||
| JP1094781A JPH0277560A (en) | 1988-06-03 | 1989-04-14 | Corrosion-resisting alloy with high saturation magnetic flux density |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0277560A true JPH0277560A (en) | 1990-03-16 |
Family
ID=26436015
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1094781A Pending JPH0277560A (en) | 1988-06-03 | 1989-04-14 | Corrosion-resisting alloy with high saturation magnetic flux density |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0277560A (en) |
-
1989
- 1989-04-14 JP JP1094781A patent/JPH0277560A/en active Pending
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