JPH0643615B2 - Method for manufacturing ribbon having high saturation magnetization - Google Patents
Method for manufacturing ribbon having high saturation magnetizationInfo
- Publication number
- JPH0643615B2 JPH0643615B2 JP61149786A JP14978686A JPH0643615B2 JP H0643615 B2 JPH0643615 B2 JP H0643615B2 JP 61149786 A JP61149786 A JP 61149786A JP 14978686 A JP14978686 A JP 14978686A JP H0643615 B2 JPH0643615 B2 JP H0643615B2
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- Prior art keywords
- saturation magnetization
- ribbon
- less
- high saturation
- molten steel
- Prior art date
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties involving a particular fabrication or treatment of ingot or slab
- C21D8/1211—Rapid solidification; Thin strip casting
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Electromagnetism (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Soft Magnetic Materials (AREA)
- Continuous Casting (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Description
【発明の詳細な説明】 （産業上の利用分野） この発明は、高い飽和磁化を有する薄帯の製造方法に関
し、とくに｛100 ｝面内無方向性集合組織をそなえる電
磁材料用の急冷薄帯中にFe16N2の鉄窒化物の優先生成を
図ることにより、飽和磁化の有利な向上を達成しようと
するものである。Description: TECHNICAL FIELD The present invention relates to a method for producing a ribbon having a high saturation magnetization, and particularly to a quenched ribbon for an electromagnetic material having a {100} in-plane nondirectional texture. By preferentially forming iron nitride of Fe 16 N 2 therein, an attempt is made to achieve an advantageous improvement in saturation magnetization.
（従来の技術） 近年省エネルギーの視点に立脚して、溶鋼から直接電磁
材料用けい素鋼帯などの薄帯を製造するいわゆる直接製
板法が開発された（特開昭55-69223号、特開昭56-87627
号、特公昭58-53694号および特公昭58-58409号各公報参
照）。(Prior Art) In recent years, from the viewpoint of energy saving, a so-called direct plate-making method has been developed for directly manufacturing thin strips such as silicon steel strip for electromagnetic material from molten steel (Japanese Patent Laid-Open No. 55-69223, Kaisho 56-87627
No., Japanese Patent Publication No. 58-53694 and Japanese Patent Publication No. 58-58409).
この方法では、所定の成分組成に溶製した溶鋼を、円孔
状あるいはスリット状の噴射口を具えるノズルから高速
で回転するロールや連続ベルトあるいは回転するドラム
の内面などのような冷却面が高速で更新移動する冷却体
上に連続して供給することにより、直ちに20〜 500μｍ
厚の鋼薄帯を得ることができる。In this method, molten steel melted to a predetermined composition is cooled with a cooling surface such as a roll or a continuous belt or an inner surface of a rotating drum that rotates at high speed from a nozzle having a circular hole-shaped or slit-shaped injection port. 20 ~ 500μm immediately by continuously supplying on the cooling body which moves and renews at high speed
A thick steel ribbon can be obtained.
この方法によれば、溶鋼から一工程で製品あるいは半製
品を製造することができるので、製造コストを低下させ
ることができると同時に多大の省エネルギーを達成する
ことができる。とはいえこのようにして製造された薄帯
はそのままの状態では通常磁気特性が充分とはいい難い
ので、必要に応じて圧延、研磨、酸洗などの前処理を施
したのち、焼鈍が施されるのが一般的である。According to this method, since a product or a semi-finished product can be manufactured from molten steel in one step, the manufacturing cost can be reduced and at the same time a great energy saving can be achieved. However, since the magnetic properties of the thin ribbon produced in this way are usually not sufficient as they are, it is necessary to perform pretreatments such as rolling, polishing, and pickling, and then annealing. It is generally done.
この焼鈍においてとくに温度を1000℃以上に高めると、
特定の雰囲気中においては板面に平行な(100) 面を有す
る結晶粒のみが、選択的に成長して、いわゆる｛100 ｝
＜0k1＞ または｛100 ｝＜001＞ 方位の集積度が高い集
合組織が得られることが明らかにされている（T.Kan,Y.
Ito and H.Shimanaka:J.Magnetism Magnetic Material
s,26(1982),127 参照｝。In this annealing, especially if the temperature is raised to 1000 ° C or higher,
In a specific atmosphere, only the crystal grains with the (100) plane parallel to the plate surface grow selectively, so-called {100}
It has been clarified that a texture with a high degree of integration of <0k1> or {100} <001> orientation can be obtained (T.Kan, Y.
Ito and H. Shimanaka: J. Magnetism Magnetic Material
s, 26 (1982), 127}.
一方これとは別に近年の電子工業の飛躍的な発展は磁性
材料の開発研究に負うところが極めて大きいが、とくに
最近では鉄芯、磁気録音、電子機器の小型化および情報
の高密度化などのため飽和磁気モーメントが高い良好な
磁性材料が求められている。従来このような飽和磁気の
高い材料を得るためには、鉄を合金化することによって
その飽和磁化を増大させようとする試みが主になされて
きたが、かような添加元素はPtやPdなどの高価な元素ば
かりであるため工業的には利用されるまでに至っていな
い。On the other hand, apart from this, the dramatic development of the electronic industry in recent years is greatly owed to the research and development of magnetic materials, but recently, especially because of iron cores, magnetic recording, miniaturization of electronic devices and high density of information. A good magnetic material having a high saturation magnetic moment is required. Conventionally, in order to obtain such a material with high saturation magnetism, attempts have been made mainly to increase the saturation magnetization by alloying iron, but such additive elements include Pt and Pd. Since they are all expensive elements, they have not been industrially used yet.
（発明が解決しようとする問題点） このように従来は、飽和磁化が高くしかも安価な磁性材
料は存在せず、その開発が望まれていた。(Problems to be Solved by the Invention) As described above, conventionally, there has been no magnetic material having high saturation magnetization and being inexpensive, and the development thereof has been desired.
この発明は、上記の問題を有利に解決するもので、飽和
磁化に優れた磁性材料を安価に製造することができる新
規な方法を提案することを目的とする。The present invention advantageously solves the above problems, and an object of the present invention is to propose a novel method capable of inexpensively producing a magnetic material having excellent saturation magnetization.
（問題点を解決するための手段） ところで高橋らは、｛高橋実：固体物理，Vol.7(1972),
483 ｝，｛T.K.Kim and M.Takahashi:Appl.Phys.Lett.,
Vol.24(1972),492｝および（高橋実：学術月報，Vol.24
(1972),719 ｝において、２×10-4〜２×10-3Torrの窒
素雰囲気中で蒸着した鉄薄膜の飽和磁化の値は 26400〜
29000 Gauss であり、純鉄薄膜の飽和磁化の値21500 Ga
uss に比較してはるかに高いというきわめて興味深い実
験結果を示した。そしてこの高い飽和磁化は、鉄薄膜中
に優先形成されたFe16N2の鉄窒化物に由来することを電
子回折による結晶構造解析から明らかにした。その後光
岡らおよび近角は、｛光岡勝也，宮島英紀，近角聡信：
第２回日本応用磁気学会学術講演概要集，(1978)P.17
6｝および｛近角聡信：応用物理,53(1984)291｝におい
て、Fe16N2鉄窒化物の析出によって高い飽和磁化がもた
らされるのは、該窒化物の析出による格子の膨張または
ひずみのためであることを解明している。(Means for solving problems) By the way, Takahashi et al. {Mr. Takahashi: Solid State Physics, Vol.7 (1972),
483}, {TKKim and M. Takahashi: Appl.Phys.Lett.,
Vol.24 (1972), 492} and (Mr. Takahashi: Academic Monthly Report, Vol.24
(1972), 719}, the saturation magnetization of an iron thin film deposited in a nitrogen atmosphere of 2 × 10 -4 to 2 × 10 -3 Torr is 26400〜.
29000 Gauss and the saturation magnetization value of pure iron thin film 21500 Ga
It showed a very interesting experimental result that it was much higher than uss. And it was clarified from the crystal structure analysis by electron diffraction that this high saturation magnetization originates from the iron nitride of Fe 16 N 2 preferentially formed in the iron thin film. After that, Mitsuoka et al. And Chikaku {{Katsuya Mitsuoka, Hideki Miyajima, Satoshi Chikaku:
2nd Annual Meeting of Japan Society for Applied Magnetics, (1978) P.17
6} and {Satoshi Konakaku: Applied Physics, 53 (1984) 291}, the high saturation magnetization of Fe 16 N 2 iron nitride precipitation is caused by the expansion or strain of the lattice due to the precipitation of the nitride. It has been clarified that.
また上記の技術とは別に発明者らは、｛Y.Inokuti,N.Ni
shida and N.Ohashi:Met.Trans.6A(1975),773｝および
｛井口征夫：日本金属学会会報，15(1975)，101 ｝にお
いて、｛100 ｝面方位純鉄単結晶を、450 ℃から 500℃
の温度範囲においてアンモニアと水素ガスとの窒化雰囲
気中で処理すると、単結晶試料表面近傍に 0.5〜3 μｍ
程度のFe16N2が優先析出すること、またFe16N2と地鉄マ
トリックスとの整合関係は を満足することを示した。In addition to the above-mentioned technology, the inventors have also proposed {Y. Inokuti, N. Ni.
shida and N. Ohashi: Met. Trans.6A (1975), 773} and {Seio Iguchi: Bulletin of the Japan Institute of Metals, 15 (1975), 101}, {100} plane-oriented pure iron single crystal from 450 ℃ 500 ° C
When processed in a nitriding atmosphere of ammonia and hydrogen gas in the temperature range of 0.5 to 3 μm near the surface of the single crystal sample.
The degree of Fe 16 N 2 preferentially precipitates, and the matching relationship between Fe 16 N 2 and the matrix is It is shown that
上記した各公知事実に基き、発明者らは、飽和磁化の改
善にはFe16N2を主成分とする鉄窒化物を安定して析出さ
せることが重要との認識に立って：数多くの試行実験を
開始した。Based on the above-mentioned publicly known facts, the present inventors have recognized that it is important to stably deposit iron nitride containing Fe 16 N 2 as a main component for improving saturation magnetization: many trials The experiment started.
その結果、所期した目的の達成のためには、 (1) 素材中にTi,V,Cr,Mn,Ni,Co,Cu, Al,Zr,NbおよびMo
のうち少なくとも一種を含有させること、 (2) 薄帯あるいは薄膜であること、 (3) マトリックスが｛100 ｝面の集積度が高い集合組
織であること、 が不可欠であることを見出した。As a result, in order to achieve the intended purpose, (1) Ti, V, Cr, Mn, Ni, Co, Cu, Al, Zr, Nb and Mo in the material
It was found that the inclusion of at least one of these, (2) a ribbon or a thin film, and (3) a matrix having a texture with a high degree of integration of {100} planes were essential.
この発明は、上記の知見に立脚するものである。すなわ
ちこの発明は、C ：0.02wt% （以下単に％で示す）以
下、O ：0.01wt% 以下ならびにTi,V,Cr,Mn,Ni,Co,Cu,A
l,Zr,NbおよびMoのうちから選んだ少なくとも一種：10.
0% 以下を含み、残部は実質的にFeの組成になる溶鋼
を、その噴射ノズルから、冷却面が高速で更新移動する
冷却体上に連続して供給し、急冷凝固させて20〜 500μ
m 厚の薄帯としたのち、この薄帯をコイルに巻取ってか
ら、1000℃以上の温度で焼鈍を施して｛100 ｝＜0k1＞
または｛100 ｝＜001＞ 方位の集積度を高め、しかるの
ち窒素雰囲気中での窒化処理ついでFe16N2を主成分とす
る鉄窒化物の析出焼鈍処理を施すことからなる高い飽和
磁化を有する薄帯の製造方法である。The present invention is based on the above findings. That is, the present invention is C: 0.02 wt% (hereinafter simply referred to as%), O: 0.01 wt% or less, and Ti, V, Cr, Mn, Ni, Co, Cu, A
At least one selected from l, Zr, Nb and Mo: 10.
Molten steel containing 0% or less, the balance being substantially Fe composition, is continuously supplied from the injection nozzle onto a cooling body whose cooling surface renews and moves at high speed, and is rapidly solidified to 20 to 500 μm.
After making a m-thick ribbon, this ribbon was wound on a coil and then annealed at a temperature of 1000 ° C or more {100} <0k1>
Or it has a high saturation magnetization by increasing the degree of integration of {100} <001> orientation and then performing nitriding treatment in a nitrogen atmosphere and then precipitation annealing of iron nitride containing Fe 16 N 2 as a main component. It is a method of manufacturing a ribbon.
この発明において析出する鉄窒化物は主にFe16N2である
が、その立若干のFe4Nなどが含まれる。The iron nitride precipitated in the present invention is mainly Fe 16 N 2 , but a small amount of Fe 4 N 2 and the like are included.
（作 用） この発明においては、Ti,V,Cr,Mn,Ni,Co,Cu, Al,Zr,Nb
およびMoのうちから選んだ少なくとも一種を10.0％以下
（好ましくは 0.1％以上）の範囲で含有するものを対象
とするが、これはFe16N2の安定析出を図るためには、上
記の程度の添加量が不可欠だからである。(Operation) In this invention, Ti, V, Cr, Mn, Ni, Co, Cu, Al, Zr, Nb
And at least one selected from Mo are contained in the range of 10.0% or less (preferably 0.1% or more). However, this is in order to achieve stable precipitation of Fe 16 N 2. This is because the addition amount of is essential.
その他の元素としてC は、磁気特性に有害な元素である
ので、0.02％以下の範囲に限定した。As other elements, C is an element that is harmful to the magnetic properties, so it was limited to 0.02% or less.
またO は、鋼中で酸化物を形成し磁気特性の劣化を招く
のでその混入は極力低減することが望ましいが、0.01％
以下の範囲で許容できる。In addition, O forms an oxide in steel and causes deterioration of magnetic properties. Therefore, it is desirable to reduce the content of O as much as possible.
The following range is acceptable.
かかる組成になる溶鋼を、直接製板法によって20〜 500
μm 厚の薄帯とする。ここに薄帯の厚みを20〜 500μm
の範囲に限定したのは、20μm 以下の厚みの薄帯は安定
して製造することが難しく、一方、 500μm を超えると
冷却速度が遅くなって磁気特性の劣化を招くからであ
る。The molten steel having such a composition is used for 20 to 500 by the direct platemaking method.
Use a thin ribbon with a thickness of μm. The thickness of the ribbon here is 20-500 μm
The reason for limiting the range to is that it is difficult to stably produce a ribbon having a thickness of 20 μm or less, while if it exceeds 500 μm, the cooling rate becomes slow and the magnetic properties are deteriorated.
ついでかくして得られた急冷薄帯は、必要に応じて圧
延、研磨または酸洗などを施したのち、1000℃以上の温
度に加熱し、(100) 面を有する結晶粒を選択的に成長さ
せて、いわゆる(100) 面内無方向性集合組織を優先形成
させる。ここに焼鈍温度が1000℃に満たないと板面に平
行な(100) 面を有する結晶粒の成長が不十分であるの
で、焼鈍温度は1000℃以上とする必要がある。The quenched ribbon thus obtained is optionally rolled, polished or pickled, and then heated to a temperature of 1000 ° C or higher to selectively grow crystal grains having a (100) face. , Preferentially forming so-called (100) in-plane non-directional texture. If the annealing temperature is less than 1000 ° C, the growth of the crystal grains having the (100) plane parallel to the plate surface is insufficient, so the annealing temperature must be 1000 ° C or higher.
その後 300〜 700℃の温度範囲でNH3 とH2ガスなどの窒
化雰囲気中で窒化処理を施したのち冷却する。この冷却
は急冷であることが好ましい。After that, nitriding treatment is performed in a nitriding atmosphere such as NH 3 and H 2 gas in a temperature range of 300 to 700 ° C., and then cooling is performed. This cooling is preferably rapid cooling.
しかるのにFe16N2を主成分とする鉄窒化物の析出焼鈍処
理を施すわけであるが、この析出処理の処理条件は、 2
00〜 350℃、10〜600 min 程度とするのが望ましい。However, the precipitation annealing treatment of iron nitride containing Fe 16 N 2 as a main component is performed.
It is desirable that the temperature is 00 to 350 ° C and the temperature is 10 to 600 min.
（実施例） 実施例１ C ：0.005 〜0.011 ％、O ：0.0035〜0.0059％と、Crを
それぞれ２％、４％、６％および８％の範囲で含有し、
残部実質的にFeの組成になる溶鋼から、 100μm 厚の薄
帯を、双ロールを用いた直接製板法によって作成した。
ついでこの薄帯に、350 ℃で温間圧延を施して約50μm
厚に仕上げた。次に薄帯表面を脱脂したのちAl2O3(80%)
とMgO(15%)とTiO2(5%)の粉末をスラリーとして薄帯に塗
布して乾燥させ、直ちにコイルに巻き取った。次にこの
コイルにBox 炉中で1120℃、５時間の真空焼鈍を施した
のち、鋼板表面をエメリー研磨（#1200 まで）後、3%HF
とH2O2との混合液中で化学研磨した。その後 500℃のNH
3(5%) とH2(95%) ガスからなる窒化雰囲気中で窒化処理
後急冷した。しかるのち 250℃、３時間の焼鈍を施して Fe16N2を主成分とする鉄窒化物を析出させた。(Example) Example 1 C: 0.005 to 0.011%, O: 0.0035 to 0.0059% and Cr in the ranges of 2%, 4%, 6% and 8%, respectively,
A 100 μm-thick ribbon was prepared from the remaining molten steel having a substantially Fe composition by a direct plate-making method using twin rolls.
Then, this ribbon is warm-rolled at 350 ℃ to obtain about 50 μm.
Finished thick. Next, after degreasing the ribbon surface, Al 2 O 3 (80%)
Powders of MgO (15%) and TiO 2 (5%) were applied as a slurry on a ribbon, dried, and immediately wound into a coil. Next, this coil was vacuum-annealed at 1120 ° C for 5 hours in a Box furnace, and then the steel plate surface was emery-polished (up to # 1200) and then 3% HF
And chemical polishing in a mixed solution of H 2 O 2 and H 2 O 2 . Then NH at 500 ℃
After nitriding treatment in a nitriding atmosphere consisting of 3 (5%) and H 2 (95%) gas, it was cooled rapidly. After that, annealing was carried out at 250 ° C. for 3 hours to precipitate an iron nitride containing Fe 16 N 2 as a main component.
かくして得られた各薄帯の飽和磁化について調べた結果
を表１に示す。なお表１には比較のため、Fe16N2を析出
させない、単に真空焼鈍のみを施して得た薄帯の飽和磁
化について調べた結果も併せて示した。Table 1 shows the results of examining the saturation magnetization of each ribbon thus obtained. For comparison, Table 1 also shows the results of examining the saturation magnetization of a ribbon obtained by performing only vacuum annealing without precipitating Fe 16 N 2 .
表１に示した成績から明らかなように、この発明に従っ
て内部にFe16N2を微細に析出させた試料はいずれも、Fe
16N2の析出がないものに比べて、20〜30％程度も高い飽
和磁化を呈している。 As is clear from the results shown in Table 1, the samples in which Fe 16 N 2 was finely precipitated according to the present invention were all Fe samples.
It exhibits a saturation magnetization of 20 to 30% higher than that without 16 N 2 .
実施例２ C ：0.004 〜0.015 ％、O ：0.0025〜0.0088％を含み、
残部がそれぞれFe - 5.2％Ti、Fe -3.2 ％V 、Fe
- 9.5％Mn、Fe - 4.6％Ni、Fe - 3.9％Co、Fe -
6.2％Al、Fe - 3.9％Cu、Fe - 8.6％Zr、Fe -
3.9％Nb、Fe - 4.6％Mo、Fe - 2.6％Ti -3.6 Mn、
Fe - 5.3％Co -1.％Zr、Fe - 3.2％Al-1.5％Moの組
成になる溶鋼から、約80μm 厚の薄帯を双ロールを用い
た直接製板法によって作成した。ついでこの薄帯に、30
0 ℃で温間圧延を施して約40μm 厚に仕上げた。次に薄
帯表面を脱脂したのち、 Al2O3(60％)とMgO(35％)とTiO2(3％)とZrO2(2％)をスラ
リー塗布してから、1050℃で５時間の真空焼鈍を施し、
ついで鋼板表面を軽酸洗後電解研磨により中心線平均粗
さ0.1μm の鏡面状態に仕上げた。Example 2 C: 0.004 to 0.015%, O: 0.0025 to 0.0088%,
The balance is Fe-5.2% Ti, Fe -3.2% V, Fe
-9.5% Mn, Fe-4.6% Ni, Fe-3.9% Co, Fe-
6.2% Al, Fe-3.9% Cu, Fe-8.6% Zr, Fe-
3.9% Nb, Fe-4.6% Mo, Fe-2.6% Ti -3.6 Mn,
Thin strips of about 80 μm thickness were made from molten steel with the composition of Fe-5.3% Co -1.% Zr and Fe-3.2% Al-1.5% Mo by the direct plate making method using twin rolls. Then, in this ribbon, 30
It was warm-rolled at 0 ° C to a thickness of about 40 μm. Next, after degreasing the ribbon surface, apply slurry of Al 2 O 3 (60%), MgO (35%), TiO 2 (3%) and ZrO 2 (2%), and then at 1050 ℃ for 5 hours. Vacuum annealing of
Next, the surface of the steel sheet was lightly pickled and then electrolytically polished to a mirror finish with a center line average roughness of 0.1 μm.
その後500 ℃のNH3(10％)とH2（90％）ガスからなる窒
化雰囲気中で窒化処理後急冷した。しかるのち250 ℃で
５時間の焼鈍を施してFe16N2を主成分とする鉄窒化物を
析出させた。After that, nitriding was performed in a nitriding atmosphere composed of NH 3 (10%) and H 2 (90%) gas at 500 ° C., followed by rapid cooling. After that, annealing was carried out at 250 ° C. for 5 hours to precipitate an iron nitride containing Fe 16 N 2 as a main component.
かくして得られた各薄帯の飽和磁化および析出物のＸ線
回折結果を表２に同時に示す。Table 2 shows the saturation magnetization of each ribbon thus obtained and the X-ray diffraction results of the precipitates at the same time.
（発明の効果） かくしてこの発明によれば、従来、高い飽和磁化を得る
ためには不可欠とされた高価な合金元素を添加する必要
なしに、飽和磁化の格段の向上を実現することができ
る。 (Effect of the Invention) Thus, according to the present invention, it is possible to achieve a marked improvement in the saturation magnetization without the need to add an expensive alloying element, which was conventionally required to obtain a high saturation magnetization.
Claims (1)
んだ少なくとも一種：10.0wt%以下 を含み、残部は実質的にFeの組成になる溶鋼を、その噴
射ノズルから、冷却面が高速で更新移動する冷却体上に
連続して供給し、急冷凝固させて20〜 500μｍ厚の薄帯
としたのち、この薄帯をコイルに巻取ってから、1000℃
以上の温度で焼鈍を施して｛100 ｝＜0k1＞ または｛1
00 ｝＜001＞方位の集積度を高め、しかるのち窒素雰囲
気中での窒化処理ついでFe16N2を主成分とする鉄窒化物
の析出焼鈍処理を施すことを特徴とする、高い飽和磁化
を有する薄帯の製造方法。1. C: 0.02 wt% or less, O: 0.01 wt% or less, and at least one selected from Ti, V, Cr, Mn, Ni, Co, Cu, Al, Zr, Nb and Mo: 10.0 Molten steel containing less than wt% and the balance of which is substantially Fe is continuously supplied from its injection nozzle onto a cooling body whose cooling surface renews and moves at high speed, and is rapidly solidified to a thickness of 20 to 500 μm. After making this thin strip, wind this strip around the coil and
Annealed at the temperature above {100} <0k1> or {1
00} <001> orientation is increased, followed by nitriding treatment in a nitrogen atmosphere and then precipitation annealing treatment of iron nitride containing Fe 16 N 2 as a main component to obtain high saturation magnetization. A method for manufacturing the thin ribbon.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61149786A JPH0643615B2 (en) | 1986-06-27 | 1986-06-27 | Method for manufacturing ribbon having high saturation magnetization |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61149786A JPH0643615B2 (en) | 1986-06-27 | 1986-06-27 | Method for manufacturing ribbon having high saturation magnetization |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS637332A JPS637332A (en) | 1988-01-13 |
| JPH0643615B2 true JPH0643615B2 (en) | 1994-06-08 |
Family
ID=15482680
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61149786A Expired - Lifetime JPH0643615B2 (en) | 1986-06-27 | 1986-06-27 | Method for manufacturing ribbon having high saturation magnetization |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0643615B2 (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102018200373A1 (en) * | 2018-01-11 | 2019-07-11 | Robert Bosch Gmbh | Soft magnetic composite material and method for its production |
| EP4083239A4 (en) * | 2019-12-25 | 2024-01-17 | Hitachi Ltd | Soft magnetic steel sheet, method for manufacturing said soft magnetic steel sheet, and core and dynamo-electric machine in which said soft magnetic steel sheet is used |
| JP2022056923A (en) * | 2020-09-30 | 2022-04-11 | 株式会社日立製作所 | Soft magnetic material, method for manufacturing soft magnetic material and electric motor |
| JP2023100325A (en) * | 2022-01-06 | 2023-07-19 | 株式会社日立製作所 | Soft-magnetic iron alloy sheet, iron core using the same, and rotary electric machine |
| JP2023154178A (en) * | 2022-04-06 | 2023-10-19 | 株式会社日立製作所 | Soft magnetic iron alloy plate, production method for soft magnetic iron alloy plate, and iron core and rotary electrical machine each including soft magnetic iron alloy plate |
-
1986
- 1986-06-27 JP JP61149786A patent/JPH0643615B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS637332A (en) | 1988-01-13 |
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