JPS5943882A - Corrosion and wear resistant amorphous alloy and its manufacture - Google Patents
Corrosion and wear resistant amorphous alloy and its manufactureInfo
- Publication number
- JPS5943882A JPS5943882A JP15383682A JP15383682A JPS5943882A JP S5943882 A JPS5943882 A JP S5943882A JP 15383682 A JP15383682 A JP 15383682A JP 15383682 A JP15383682 A JP 15383682A JP S5943882 A JPS5943882 A JP S5943882A
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- Prior art keywords
- amorphous alloy
- corrosion
- oxide film
- alloy
- amorphous
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Abstract
Description
【発明の詳細な説明】
〔発明の技術分野〕
本発明は、非晶質合金及びその製造法に関し、更に詳し
くは、耐食性及び耐摩耗性が改善された非晶質合金及び
その製造法に関する。DETAILED DESCRIPTION OF THE INVENTION [Technical Field of the Invention] The present invention relates to an amorphous alloy and a method for producing the same, and more particularly to an amorphous alloy with improved corrosion resistance and wear resistance and a method for producing the same.
最近、液体急冷法を用いて作製される非晶質合金は、優
れた磁気特性、機械的性′1!↓、tftft性的性質
い新しい金属材料として注目を集めている。特に、磁性
材料として、その大きな用途が期待されている。Recently, amorphous alloys produced using the liquid quenching method have excellent magnetic properties and mechanical properties! ↓, tftft It is attracting attention as a new metal material with sexual properties. In particular, its use as a magnetic material is expected to be significant.
磁性材料は様々な雰囲気下に置かれるので、その耐食性
、例えば、高温、多湿状態又は[(4もしくけ塩基性の
雰囲気下等における耐食性は重要な意義を有する。Since magnetic materials are exposed to various atmospheres, their corrosion resistance, such as corrosion resistance under high temperature, high humidity conditions, or basic atmospheres, is of important significance.
非晶質合金は、cr−pt−複合的に含有する場合には
、優れた耐食性を示すことが知られているが、その他の
非晶質合金は、一般には活性で耐食性はよくない。Pの
含有は結晶化温度を低下させ、また、高温条件下では偏
析が起り易く、熱的安定性も劣るのであまシ好ましくな
い。従って、良好な熱的安定性を伺るには、Cr P
を複合的に含有するものを用することかできず。It is known that amorphous alloys exhibit excellent corrosion resistance when they contain cr-pt composites, but other amorphous alloys are generally active and do not have good corrosion resistance. Containing P lowers the crystallization temperature, tends to cause segregation under high-temperature conditions, and has poor thermal stability, so it is not preferable. Therefore, for good thermal stability, CrP
It is not possible to use products that contain a combination of .
耐食性が低下することは避は升い。また、非晶質合金は
非常に硬いが、一般に耐摩耗性が劣ることも知られてい
る。例えば、磁気テープによる摩耗量は硬さが約V2の
フェライトに比べて非常に大きい。A decrease in corrosion resistance is inevitable. It is also known that although amorphous alloys are very hard, they generally have poor wear resistance. For example, the amount of wear caused by magnetic tape is much greater than that of ferrite, which has a hardness of approximately V2.
従来、磁性体として非晶質合金を用いる場合に、絶縁層
を形成させることを目的として、非晶質合金を100c
以下の温度で酸化浴に浸漬して、あるーは陽極酸化法を
用いて表向に酸化皮膜を形成させる方法(特15iI昭
54 46539号公報)が知られている。しかしなが
ら、この方法において形成される酸化皮膜は結晶+4酸
化物を含有するものではない。更に、本発明者らの研究
によれば、このような方法による酸化皮膜の形成法では
、酸化皮膜が薄く、かつ、アモルファス状態になってお
り、また酸化皮11Qと非晶質合金との結合度が弱いた
め充分なIAij食性及び耐摩耗性が得られ彦いという
欠点があった。Conventionally, when an amorphous alloy is used as a magnetic material, the amorphous alloy is used to form an insulating layer.
A method is known in which an oxide film is formed on the surface by immersing the material in an oxidizing bath at the following temperature or by using an anodic oxidation method (Japanese Patent Publication No. 15iI 1984-46539). However, the oxide film formed by this method does not contain crystalline +4 oxide. Furthermore, according to the research of the present inventors, in the method of forming an oxide film using such a method, the oxide film is thin and in an amorphous state, and the bond between the oxide film 11Q and the amorphous alloy is reduced. The disadvantage was that sufficient IAij corrosion resistance and abrasion resistance could not be obtained due to the low strength.
本発明は、前述した従来の非晶質合金及びその製造法の
欠点を解消したもので、優れた耐食性及び面]摩耗性を
有する非晶質合金及びその製造法を提供することを目的
とする。The present invention eliminates the drawbacks of the conventional amorphous alloy and its manufacturing method described above, and aims to provide an amorphous alloy having excellent corrosion resistance and surface wear resistance, and a manufacturing method thereof. .
本発明者らは、前記した点に鑑みで鋭えヱ研究を重ねた
結果、非晶質合金の酸化処理を1(′う温、かつ、高圧
下で行なうことにょシ、本発明の目的を達成できること
を見出し、本発明を完成するに至った。As a result of extensive research in view of the above points, the present inventors have discovered that the purpose of the present invention is to carry out the oxidation treatment of an amorphous alloy at We have discovered what can be achieved and have completed the present invention.
即ち1本発明の非晶質合金Fi、表面に結晶性酸化物を
含有する酸化皮膜を有する非晶質合金からなることを特
徴とするものである。Specifically, the amorphous alloy Fi of the present invention is characterized in that it is an amorphous alloy having an oxide film containing a crystalline oxide on its surface.
本発明の非晶質合金は、以下のようにして製造すること
ができる。The amorphous alloy of the present invention can be manufactured as follows.
非晶質合金としては、次の組成を有するものが用いられ
る。As the amorphous alloy, one having the following composition is used.
即ち、原子チ表示で示すと、
次式: (Col−x−yFexMy)zGtoo−Z
又は((:a 1−x−y FexMy ) uT
xoo−u(式中、MitTi 、V、Cr、Mn、N
i 、Cu+Zr+Nb、Mo、Ru、Rh、Pd、A
g+H,f、Ta+W+Retpt、Au、Y 及び
希土類元素からなる群から選ばれる少なくとも1種の元
素を表わし;GはB。That is, when expressed in atomic units, the following formula: (Col-x-yFexMy)zGtoo-Z
or ((:a 1-x-y FexMy ) uT
xoo-u (where MitTi, V, Cr, Mn, N
i, Cu+Zr+Nb, Mo, Ru, Rh, Pd, A
G represents at least one element selected from the group consisting of g+H, f, Ta+W+Retpt, Au, Y, and rare earth elements; G is B;
c+si+p及びQeからなる群から選ばれる少なくと
も1種の元素を表わし;Tは’I” i + Z r
+IIftV、Nb、TalWIMOIY及び希土類元
素からなる群から選ばれる少なくとも1種の元素を表わ
し; X r yT Z及びUはそれぞれ、0≦X≦1
.0≦y≦0.2.65≦2≦90及び85≦U≦95
の関係を満足する数を表わす。)
で示される非晶質合金が用いられる。Represents at least one element selected from the group consisting of c + si + p and Qe; T is 'I'' i + Z r
+IIftV, Nb, TalWIMOIY and at least one element selected from the group consisting of rare earth elements; X r yT Z and U each satisfy 0≦X≦1
.. 0≦y≦0.2.65≦2≦90 and 85≦U≦95
represents a number that satisfies the relationship. ) is used.
非晶質合金が優れた耐食性及び耐摩耗性を有するための
一要件として、非晶仰合金の表面に結晶性酸化物を含有
する酸化皮膜を有することが挙げられるが、このような
非晶質合金を製造するには、高温、かつ、高圧下におい
て酸化処理を行なうことが必要である。One of the requirements for an amorphous alloy to have excellent corrosion resistance and wear resistance is to have an oxide film containing a crystalline oxide on the surface of the amorphous alloy. In order to manufacture the alloy, it is necessary to perform an oxidation treatment at high temperature and under high pressure.
この時の温度はなるべく高い方が短時間で結晶性酸化物
が形成される六め望ましbが、あま多温度が高すぎると
非晶質合金が結晶化するという問題が発生するので結晶
化温度以下の温度が望ましく、具体的には150〜50
0 Cであることが好ましく、250〜400cである
ことが更に好ましい。高圧化の手段としては、ガス、液
体のどちらを用いてもよいが、得られる圧力が40〜2
00気圧であることが好ましく、60〜1o。It is desirable that the temperature at this time be as high as possible to form crystalline oxides in a short time, but if the temperature is too high, the problem of crystallization of the amorphous alloy will occur, so crystallization will not occur. It is desirable that the temperature is below the temperature, specifically 150 to 50
It is preferably 0 C, and more preferably 250 to 400 C. As a means of increasing the pressure, either gas or liquid may be used, but the pressure obtained is 40 to 2
00 atm, preferably 60 to 1o.
気圧であることが更に好ましい。処理時間は、処理温度
及び処理圧力により異なるが、一般には、0.5〜10
0時間であシ、特に5〜24時間であることが好ましい
。More preferably, it is atmospheric pressure. The processing time varies depending on the processing temperature and processing pressure, but is generally 0.5 to 10
It is preferably 0 hours, particularly 5 to 24 hours.
一般的な手段としてはオートクレーブ等の高温の水蒸気
中で処理するのが手軽な方法である。A common and easy method is to process in high-temperature steam, such as in an autoclave.
以上のように処理することにょシ、形成される酸化皮膜
及びそれに含有される結晶性酸化物は、非晶質合金の主
成分により異なるが、例えば、Feが主成分の非晶質合
金にあってはFe3O4Iγ−Fe2O3等が、COが
主成分である非晶質合金にあってはCooあるいはCo
30.が形成されることが多いが、これらは製造条件に
より異なる。The oxide film formed and the crystalline oxide contained therein vary depending on the main component of the amorphous alloy, but for example, in an amorphous alloy whose main component is Fe, For example, Fe3O4Iγ-Fe2O3 etc., and for amorphous alloys whose main component is CO, Coo or Co
30. are often formed, but these vary depending on the manufacturing conditions.
また、 CoとFeとをともに含有−する非晶質合金に
あってはb CoFe2O4等のCo−1i’e糸1圓
化物が形成される。In addition, in the case of an amorphous alloy containing both Co and Fe, a monoclonal product of Co-1i'e yarn such as CoFe2O4 is formed.
上記のいずれの結晶性酸化物が形成場れた場合であって
も、著しくm1]食性及び面]ノν・耗性が改善されて
いることがIl’!i食試験及び摩れ試1に大の結釆よ
り判明した。No matter where any of the above-mentioned crystalline oxides are formed, it is found that the eating and abrasion properties are significantly improved. This was confirmed from the results of the i-eating test and the rubbing test 1.
得られた非晶1」合金は、その酸化皮膜の厚さが、
0.05〜5μmであるものが女rtしく 、 0.1
〜1μmであるものが更に好ましい。この厚さが0.0
5 ttnt未満であると、結晶性酸化物の成長が少な
く。The obtained amorphous 1'' alloy has an oxide film thickness of
Those with a diameter of 0.05 to 5 μm are considered feminine and 0.1
More preferably, the thickness is 1 μm. This thickness is 0.0
When it is less than 5 ttnt, the growth of crystalline oxide is small.
耐食性及び耐摩耗性の向上があ筐り見らhず5μmを超
えると、非晶質合金層の割合が低下するのヤ実用上好ま
しくない。If the thickness exceeds 5 μm, the proportion of the amorphous alloy layer decreases, which is not preferred in practice, without improving corrosion resistance and wear resistance.
上記酸化皮膜に含有される結晶性酸化物の大きさは、0
.01〜5μmであることが好ましく 、0.1〜2μ
mであることが更に好ましい。この大きさが0.01μ
m未満であると、耐食性及び耐摩耗性がそれほど改善さ
れず、5μmを超えると、酸化皮膜層以下の内部非晶質
合金相の一部が結晶化して充分な機械的強度を得ること
ができない。The size of the crystalline oxide contained in the oxide film is 0
.. It is preferably 0.1 to 5 μm, and 0.1 to 2 μm.
More preferably, it is m. This size is 0.01μ
If it is less than m, corrosion resistance and wear resistance will not be improved much, and if it exceeds 5 μm, a part of the internal amorphous alloy phase below the oxide film layer will crystallize, making it impossible to obtain sufficient mechanical strength. .
本発明によシ得られた非晶質合金は、隋れた耐食性及び
耐摩耗性を有する。The amorphous alloy obtained according to the invention has excellent corrosion and wear resistance.
以下、実施例により本発明を更に詳細に説明する。 Hereinafter, the present invention will be explained in more detail with reference to Examples.
実施例1
単ロール法を用いて幅10節、厚さ20μmの(Fe0
.95 CrO,05)85 S 13B12非晶質合
金を作製した。これより長さ約1mを切取シ、オートク
レーブを用いて400C,105気圧の条件下に12時
間装いた。取出したサンプルは表面が黒色になっていた
。走査型電子顕微鏡(SEM)を用いて表面状態を観察
したところ、第1図に示すように非晶質合金相内に約1
μmの結晶性酸化物が微細に析出していた。X線を用い
てこの結晶性酸化物を同定したところFe3O4である
ことが判明した。Example 1 Using a single roll method, a (Fe0
.. A 95CrO,05)85S 13B12 amorphous alloy was prepared. A length of about 1 m was cut out from this, and it was placed in an autoclave at 400 C and 105 atm for 12 hours. The surface of the sample taken out was black. When the surface condition was observed using a scanning electron microscope (SEM), as shown in Figure 1, approximately 1
Fine crystalline oxides of μm size were precipitated. When this crystalline oxide was identified using X-rays, it was found to be Fe3O4.
上記表面を酸化処理した非晶質合金と、上記酸化処理を
しない同一組成の非晶質合金に対して、それぞれラッピ
ングテープを4.75cm/秒の速度で走行させて摩れ
1社を測定し、両者を比較した。A wrapping tape was run at a speed of 4.75 cm/sec to measure wear on the amorphous alloy whose surface had been oxidized and the amorphous alloy with the same composition that had not been oxidized. , compared the two.
100時間時間後の摩耗量はオートクレーブ処理をした
ものが2μm、オートクレーブ処理をしなかったものは
20μmであり、前者は著しく面1摩耗性が改善されて
いることが判明した。The amount of wear after 100 hours was 2 μm for the autoclaved sample and 20 μm for the non-autoclaved sample, indicating that the surface 1 abrasion properties of the former were significantly improved.
実施例2
単ロール法を用いて幅10嗣、厚さ20μmの(Coo
9oFeo、o6cro、o4)yysiIoB13
非晶質合金を作製した。これより長さ5mを切取りオ
ートクレーブを用いて300C,80気圧の条件下に2
4時間装いた。取出したサンプルは表面が黒色になって
いた。SEMを用いて表面状態を観察したところ、約0
.5μmの結晶性酸化物が微細に析出していた。X線を
用いてこの結晶性酸化物を同定したところCO3O4が
主体で、その他同だできない結晶性酸化物が混在してい
ることが判明した。Example 2 Using a single roll method, a (Coo
9oFeo, o6cro, o4)yysiIoB13
An amorphous alloy was produced. A length of 5m was cut from this and was placed in an autoclave at 300C and 80atm for 2 hours.
I dressed up for 4 hours. The surface of the sample taken out was black. When the surface condition was observed using SEM, it was found that approximately 0
.. A fine crystalline oxide of 5 μm was precipitated. When this crystalline oxide was identified using X-rays, it was found that CO3O4 was the main component, and other crystalline oxides that were not identical were also present.
上記表面を酸化処理した非晶質合金と、上記酸化処理を
しない同一組成の非晶質合金に対して、それぞれCO−
γFe 203塗布のVTRデープを7m1秒の速度で
走行させて摩耗111を測定し、両者を比較した。CO-
A VTR tape coated with γFe 203 was run at a speed of 7 ml/sec, wear 111 was measured, and the two were compared.
100時間時間後の摩耗量はオートクレーブ処理をした
ものが3μm、オートクレーブ処理をしなかったものは
45μmであシ、前者は著しく耐摩耗性が改善されてい
ることが判明した。The amount of wear after 100 hours was 3 μm for the autoclaved sample and 45 μm for the non-autoclaved sample, indicating that the former had significantly improved wear resistance.
実施例3
単ロール法を用いて幅10鵡、厚さ20μmの(C00
,91FeO,Off Mo、03 )75 S ’
10 B15非晶質合金(M:MO、Nb + Ta
)を作製した。これより長さ各5mを切取シオートクレ
ープを用いて300t:’ 、 80気圧の条件下に2
4時間装いた。取出したサンプルはいずれも表面が黒色
になっていた。SEMを用いて表面状態を観察したとこ
ろ、約0.5μmの結晶性酸化物が微細に析出していた
。Example 3 Using a single roll method, a (C00
,91FeO,Off Mo,03)75S'
10 B15 amorphous alloy (M: MO, Nb + Ta
) was created. Cut out 5 m long pieces from this and use a sciauto crepe to make 300 t:', 2 at 80 atm.
I dressed up for 4 hours. The surfaces of all the samples taken were black. When the surface condition was observed using SEM, it was found that crystalline oxides of about 0.5 μm were finely precipitated.
上記オートクレーブ処理した各サンプルを第2図に模式
的にボーノ°定tiL位−電h!t i、I、: fa
c+を用いて水中での分極抵IIj−全測5Q +/
@ オートクレーノ゛処理をしない・リンノルと比千’
< L 1t−0オー トクレーフ′処理に、 l/
’L ”ダンノルtj)分4M JiL抗tJ、 M
: Alo 、 Nb。FIG. 2 schematically shows each of the autoclaved samples described above. t i, I,: fa
Polarization resistance IIj in water using c+ - total measurement 5Q +/
@ No autocrane treatment・Rinnor and Sen'
< L 1t-0 autoclave treatment, l/
'L ``Dannol tj) min 4M JiL anti tJ, M
: Alo, Nb.
’fn ノ谷す’ 7ブA i7 ?I L、−rニー
4:trA:h、 25.C4、ZOQ。'fn no valley' 7buA i7? IL, -r knee 4:trA:h, 25. C4, ZOQ.
20Ωであつli二3.−リハオートクレーン゛処j!
l したサンダルの分4i< lit;抗kl−M :
Mo 、 Nb 、 Taのい一、J” it &n
r=J L ’T: 41 m (+ (+ (lΩ
’t#JJ−(llb P、L、イー4食性を示し/
イー。同様の実験を0. I N −lieノ及び(1
,I N −NaCJ の本釣液中で行なったが、A−
トクレープ処理劇の耐食性はA−)り1ノーノ゛未処J
’J! 4’Jに比べて約100倍高い耐食性を小した
。20Ω and 23. - Rehabilitation auto crane place!
l sandals min 4i <lit; anti-kl-M:
Mo, Nb, Ta no Iichi, J" it &n
r=J L'T: 41 m (+ (+ (lΩ
't#JJ-(llb P, L, E tetraphagous /
E. A similar experiment was conducted with 0. I N -lieノ and (1
, I N -NaCJ, but A-
Corrosion resistance after crepe treatment is unresolved.
'J! The corrosion resistance is about 100 times higher than that of 4'J.
以」・実施的て示しlζ如く、木兄間のu114♂、h
合金は著しい耐食性及び1illl摩れ、ゼ1をシ1、
し、実用性の高い非晶質合金である。・As shown in the practical example, U114♂ between Kien and h
The alloy has remarkable corrosion resistance and 1illll wear resistance,
However, it is a highly practical amorphous alloy.
lA1[A21は、不発IJ14に係る非晶質合金の表
向を4000倍に拡大して撮影しlc、写真である。
第2図rj、、+に4食性を評仙1する定’JIJ、位
電解+ン16゜の模式図である。
A・・・ボテ/ショスタット。
B・・・エレクトロメータ、
C・・・11glft!1発生器、 D・・・レコーダ
。
E・・・補助電極、 F・・・試料、l・・・電解
セル、 2・・・腐食静、3・・・照合11を極。
):1°511・、jl
第21・41A1 [A21 is a photograph taken by magnifying 4000 times of the surface of the amorphous alloy related to unexploded IJ14. Figure 2 is a schematic diagram of the positional electrolyte +n 16°, where rj,, + has a four-feeding habit. A...Bote/Schostat. B...Electrometer, C...11glft! 1 generator, D... recorder. E... Auxiliary electrode, F... Sample, l... Electrolytic cell, 2... Corrosion static, 3... Verification 11 as the pole. ): 1°511・,jl 21st・4
Claims (1)
とを特徴とする耐食性・面・j摩耗性非晶質合金。 2 結晶性酸化物の大きさが0.01〜5μmである特
許請求の範囲第1項記載の耐食性・耐摩耗性非晶質合金
。 3 酸化皮膜の厚さが0.05〜5ttmである特許請
求の範囲第1項又は第2項記載の耐食性・創摩耗性非晶
質合金。 4 非晶質合金を酸化処理して、該非晶質合金の表面に
酸化皮膜を形成させる非晶質合金の製造法において、非
晶質合金の酸化処理を高温、かつ、高圧下で行なうこと
を特徴とする耐食性・耐摩耗性非晶質合金の製造法。 5 酸化処理の条件が150〜500C,40〜200
気圧である特許請求の範囲第4項記載の製造法。[Scope of Claims] 1. A corrosion-resistant, surface-wearing, amorphous alloy characterized by having an oxide film containing a crystalline oxide on its surface. 2. The corrosion-resistant and wear-resistant amorphous alloy according to claim 1, wherein the crystalline oxide has a size of 0.01 to 5 μm. 3. The corrosion-resistant and abrasion-resistant amorphous alloy according to claim 1 or 2, wherein the oxide film has a thickness of 0.05 to 5 ttm. 4. In a method for producing an amorphous alloy in which an oxidation treatment is performed on an amorphous alloy to form an oxide film on the surface of the amorphous alloy, the oxidation treatment of the amorphous alloy is carried out at high temperature and under high pressure. A manufacturing method for amorphous alloys with characteristic corrosion and wear resistance. 5 Oxidation treatment conditions are 150-500C, 40-200C
The manufacturing method according to claim 4, wherein the pressure is atmospheric pressure.
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15383682A JPS5943882A (en) | 1982-09-06 | 1982-09-06 | Corrosion and wear resistant amorphous alloy and its manufacture |
CA000433383A CA1205725A (en) | 1982-09-06 | 1983-07-27 | Corrosion-resistant and wear-resistant amorphous alloy and a method for preparing the same |
US06/518,850 US4504327A (en) | 1982-09-06 | 1983-08-01 | Corrosion-resistant and wear-resistant magnetic amorphous alloy and a method for preparing the same |
DE8383107853T DE3368690D1 (en) | 1982-09-06 | 1983-08-09 | Corrosion-resistant and wear-resistant amorphous alloy and a method for preparing the same |
EP83107853A EP0105137B2 (en) | 1982-09-06 | 1983-08-09 | Corrosion-resistant and wear-resistant amorphous alloy and a method for preparing the same |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP15383682A JPS5943882A (en) | 1982-09-06 | 1982-09-06 | Corrosion and wear resistant amorphous alloy and its manufacture |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5943882A true JPS5943882A (en) | 1984-03-12 |
JPS6155590B2 JPS6155590B2 (en) | 1986-11-28 |
Family
ID=15571151
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP15383682A Granted JPS5943882A (en) | 1982-09-06 | 1982-09-06 | Corrosion and wear resistant amorphous alloy and its manufacture |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5943882A (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06346219A (en) * | 1993-06-15 | 1994-12-20 | Matsushita Electric Works Ltd | Magnetic material using amorphous magnetic alloy, method for producing the same and device therefor |
JPH1068060A (en) * | 1996-08-27 | 1998-03-10 | Agency Of Ind Science & Technol | Method for coloring titanium series alloy by oxidation under heating |
JP2001140047A (en) * | 1999-11-18 | 2001-05-22 | Ykk Corp | Surface hardened formed part made of amorphous alloy, and its manufacturing method |
JP2016197720A (en) * | 2015-04-02 | 2016-11-24 | 日立金属株式会社 | Magnetic core and manufacturing method therefor, and on-vehicle component |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS53108026A (en) * | 1977-02-26 | 1978-09-20 | Vacuumschmelze Gmbh | Method of reducing magnetic hysteris loss of thin belt material made of soft magnetic amorphous alloy |
JPS57169207A (en) * | 1981-04-10 | 1982-10-18 | Nippon Steel Corp | Amorphous alloy with excellent constant permeability and manufacture thereof |
JPS5934781A (en) * | 1982-08-20 | 1984-02-25 | Mitsubishi Electric Corp | Encoder between frames of vector quantizing system |
-
1982
- 1982-09-06 JP JP15383682A patent/JPS5943882A/en active Granted
Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS53108026A (en) * | 1977-02-26 | 1978-09-20 | Vacuumschmelze Gmbh | Method of reducing magnetic hysteris loss of thin belt material made of soft magnetic amorphous alloy |
JPS57169207A (en) * | 1981-04-10 | 1982-10-18 | Nippon Steel Corp | Amorphous alloy with excellent constant permeability and manufacture thereof |
JPS5934781A (en) * | 1982-08-20 | 1984-02-25 | Mitsubishi Electric Corp | Encoder between frames of vector quantizing system |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06346219A (en) * | 1993-06-15 | 1994-12-20 | Matsushita Electric Works Ltd | Magnetic material using amorphous magnetic alloy, method for producing the same and device therefor |
JPH1068060A (en) * | 1996-08-27 | 1998-03-10 | Agency Of Ind Science & Technol | Method for coloring titanium series alloy by oxidation under heating |
JP2001140047A (en) * | 1999-11-18 | 2001-05-22 | Ykk Corp | Surface hardened formed part made of amorphous alloy, and its manufacturing method |
JP2016197720A (en) * | 2015-04-02 | 2016-11-24 | 日立金属株式会社 | Magnetic core and manufacturing method therefor, and on-vehicle component |
Also Published As
Publication number | Publication date |
---|---|
JPS6155590B2 (en) | 1986-11-28 |
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