JPH04341544A - Fe base soft magnetic alloy - Google Patents
Fe base soft magnetic alloyInfo
- Publication number
- JPH04341544A JPH04341544A JP3112800A JP11280091A JPH04341544A JP H04341544 A JPH04341544 A JP H04341544A JP 3112800 A JP3112800 A JP 3112800A JP 11280091 A JP11280091 A JP 11280091A JP H04341544 A JPH04341544 A JP H04341544A
- Authority
- JP
- Japan
- Prior art keywords
- soft magnetic
- magnetic alloy
- alloy
- amorphous
- present
- 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.)
- Withdrawn
Links
- 229910001004 magnetic alloy Inorganic materials 0.000 title claims abstract description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 41
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 239000006104 solid solution Substances 0.000 claims description 4
- 239000002178 crystalline material Substances 0.000 claims description 3
- 239000011162 core material Substances 0.000 abstract description 10
- 229910052802 copper Inorganic materials 0.000 abstract description 5
- -1 Si Al Inorganic materials 0.000 abstract description 2
- 239000007787 solid Substances 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 12
- 239000000956 alloy Substances 0.000 description 12
- 239000013078 crystal Substances 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000005470 impregnation Methods 0.000 description 4
- 238000002441 X-ray diffraction Methods 0.000 description 3
- 229910008423 Si—B Inorganic materials 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000002050 diffraction method Methods 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000000696 magnetic material Substances 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000001493 electron microscopy Methods 0.000 description 1
- 125000001475 halogen functional group Chemical group 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052763 palladium Inorganic materials 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000011347 resin Substances 0.000 description 1
- 229920005989 resin Polymers 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15308—Amorphous metallic alloys, e.g. glassy metals based on Fe/Ni
Landscapes
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
【０００１】0001
【産業上の利用分野】本発明は、Ｆｅ基軟磁性合金に係
わり、特に良好な軟磁気特性を有するＦｅ基軟磁性合金
に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an Fe-based soft magnetic alloy, and particularly to an Fe-based soft magnetic alloy having good soft magnetic properties.
【０００２】0002
【従来の技術及び発明が解決しようとする課題】近年、
高周波トランス、可飽和リアクトル、チョークコイル等
の磁心材料として、高い飽和磁束密度を有するＦｅ系の
非晶質磁性合金が広く知られている。しかし、Ｆｅ系非
晶質合金は一般に飽和磁歪定数が大きいため、コアを作
製した後、樹脂含浸、切断等応力が加わると、軟磁気特
性、特に鉄損が大幅に劣化する等の問題点があった。[Prior art and problems to be solved by the invention] In recent years,
Fe-based amorphous magnetic alloys having high saturation magnetic flux density are widely known as magnetic core materials for high frequency transformers, saturable reactors, choke coils, and the like. However, Fe-based amorphous alloys generally have a large saturation magnetostriction constant, so if stress is applied after the core is fabricated, such as by resin impregnation or cutting, there are problems such as significant deterioration of soft magnetic properties, especially iron loss. there were.
【０００３】本願発明は、このような従来のＦｅ系非晶
質合金に代わる軟磁性材料であり、軟磁気特性、特に鉄
損に優れた新規なＦｅ基軟磁性合金を提供することを目
的とする。更に、本発明は、従来の磁性材料製造装置を
利用して容易に製造することのできる比較的低融点のＦ
ｅ基軟磁性合金を提供することを目的とする。The present invention aims to provide a novel Fe-based soft magnetic alloy that is a soft magnetic material that can replace such conventional Fe-based amorphous alloys and has excellent soft magnetic properties, particularly iron loss. do. Furthermore, the present invention provides a relatively low melting point F that can be easily manufactured using conventional magnetic material manufacturing equipment.
The object of the present invention is to provide an e-based soft magnetic alloy.
【０００４】0004
【課題を解決するための手段】このような目的を達成す
るため本発明者は、Ｆｅ基軟磁性合金について鋭意研究
を進めた結果、Ｆｅ−Ｓｉ−Ｂ系合金にＡｌおよびＣｕ
を添加した合金が、小さな飽和磁歪定数を持つことを見
い出し、本発明に至ったものである。
即ち、本発明のＦｅ基軟磁性合金は、一般式（Ｆｅ１−
ＸＭＸ）１００−ａ−ｂ−ｃ−ｄＳｉａＡｌｂＢｃＣｕ
ｄ（式中、ＭはＣｏ及び／又はＮｉを示す。ｘは原子比
を、ａ、ｂ、ｃ、ｄは原子％を示し、それぞれ０≦ｘ≦
０．５、０≦ａ≦２４、１≦ｂ≦２０、４≦ｃ≦３０、
０．２≦ｄ≦３を満たすものとする）により表わされる
ものであり、特にその組織の少なくとも３０％以上が結
晶質で生成されていることが好ましく、この結晶質は鉄
を主体としたｂｃｃ固溶体から成るものである。[Means for Solving the Problems] In order to achieve the above object, the present inventor has carried out intensive research on Fe-based soft magnetic alloys, and as a result, has found that Al and Cu are added to Fe-Si-B alloys.
It was discovered that an alloy to which . That is, the Fe-based soft magnetic alloy of the present invention has the general formula (Fe1-
XMX) 100-a-b-c-dSiaAlbBcCu
d (in the formula, M represents Co and/or Ni; x represents the atomic ratio; a, b, c, and d represent atomic %; each 0≦x≦
0.5, 0≦a≦24, 1≦b≦20, 4≦c≦30,
0.2≦d≦3), and in particular, it is preferable that at least 30% of the structure is made of crystalline material, and this crystalline material is a BCC mainly composed of iron. It consists of a solid solution.
【０００５】本発明のＦｅ基軟磁性合金において、Ｆｅ
はその半分以下をＣｏ及び／又はＮｉで置換することが
できる。Ａｌは本発明合金の必須元素であり、Ａｌは本
発明合金を構成する結晶の結晶磁気異方性を小さくする
効果がある。Ａｌの含有量は、１原子％以上、２０原子
％以下、好ましくは４〜１２原子％である。この理由は
、Ａｌを１原子％以上とすることにより析出結晶の結晶
磁気異方性を小さくする効果が得られ、また、２０原子
％以下とすることにより非結晶合金の形成が阻害される
ことがない。In the Fe-based soft magnetic alloy of the present invention, Fe
less than half of it can be replaced with Co and/or Ni. Al is an essential element of the alloy of the present invention, and Al has the effect of reducing the magnetocrystalline anisotropy of the crystals constituting the alloy of the present invention. The content of Al is 1 atomic % or more and 20 atomic % or less, preferably 4 to 12 atomic %. The reason for this is that by setting the Al content to 1 atomic % or more, the effect of reducing the crystal magnetic anisotropy of the precipitated crystals can be obtained, and by setting the Al content to 20 atomic % or less, the formation of an amorphous alloy is inhibited. There is no.
【０００６】Ｃｕは、Ｆｅ基ｂｃｃ固溶体の生成温度を
低下させるとともに、結晶粒の粗大化を防ぐ効果がある
。その含有量は０．２〜３原子％である。この理由は、
Ｃｕを、このような範囲とすることにより磁気特性を劣
化させることなく、所期の効果を得ることができるから
である。本発明合金は非結晶状態から熱処理により結晶
化させることにより作製されるが、Ｂは本発明のＦｅ基
合金を急冷することにより非晶質化させる元素である。
Ｂの含有量は４〜３０原子％、好ましくは６〜１８原子
％である。Ｂを４原子％以上とすることにより本発明合
金を非晶質化させることができる。また、Ｂを３０原子
％以下とすることにより、熱処理によって非晶質状態か
ら結晶化する際、Ｂが多すぎるためＦｅ−Ｂ化合物が多
数析出し軟磁気特性が劣化するという傾向を押えること
ができる。Ｓｉの含有量は０〜２４原子％であり、飽和
磁歪を低くするためにＳｉは２４原子％以下が好ましい
。[0006] Cu has the effect of lowering the formation temperature of the Fe-based BCC solid solution and preventing coarsening of crystal grains. Its content is 0.2 to 3 at%. The reason for this is
This is because by setting Cu within such a range, the desired effect can be obtained without deteriorating the magnetic properties. The alloy of the present invention is produced by crystallizing it from an amorphous state through heat treatment, and B is an element that causes the Fe-based alloy of the present invention to become amorphous by rapidly cooling it. The content of B is 4 to 30 at%, preferably 6 to 18 at%. By setting B to 4 atomic % or more, the alloy of the present invention can be made amorphous. In addition, by controlling B to 30 atomic % or less, it is possible to suppress the tendency that when crystallizing from an amorphous state by heat treatment, a large number of Fe-B compounds precipitate due to too much B and the soft magnetic properties deteriorate. can. The content of Si is 0 to 24 atomic %, and preferably 24 atomic % or less to lower the saturation magnetostriction.
【０００７】本発明のＦｅ基軟磁性合金の基本的組成は
上述の、Ｆｅ（Ｍ）−Ｂ、Ｓｉ、Ａｌ、Ｃｕであるが、
更に耐食性等を向上させるために他の元素Ｍ’を加える
ことができる。Ｍ’としては、Ｐｄ、Ｒｕ、Ｇａ、Ｃｒ
、Ｙ、Ｗ、Ｎｂ、Ｔａ、Ｇｅ、Ｃ、Ｐから選ばれる１種
以上が挙げられる。これらの元素は、１０原子％以下、
好ましくは５原子％以下添加される。The basic composition of the Fe-based soft magnetic alloy of the present invention is the above-mentioned Fe(M)-B, Si, Al, and Cu.
Furthermore, other elements M' can be added to improve corrosion resistance and the like. M' is Pd, Ru, Ga, Cr
, Y, W, Nb, Ta, Ge, C, and P. These elements are contained in an amount of 10 atomic% or less,
Preferably, it is added in an amount of 5 atomic % or less.
【０００８】本発明のＦｅ基軟磁性合金は、ＡｌとＣｕ
を所定の割合で含有させることによって結晶磁気異方性
および飽和磁歪が極めて小さな結晶粒が微細に形成され
る。この結晶粒は１０００オングストローム以下、また
良好な軟磁気特性を得るためには５００オングストロー
ム以下が好ましい。また組織は主に結晶質と非晶質から
構成されるが、非晶質部分は結晶質部分よりも磁歪が大
きいため、少なくとも組織全体の３０％以上、好ましく
は６０％以上が結晶質で生成され、残部は非晶質である
ことが好ましい。なお、本発明では、結晶粒の大きさ、
結晶質の程度（結晶化度）は電子顕微鏡回折法およびＸ
線回折法で決定した。The Fe-based soft magnetic alloy of the present invention contains Al and Cu.
By containing in a predetermined proportion, fine crystal grains with extremely small magnetocrystalline anisotropy and saturation magnetostriction are formed. The grain size is preferably 1000 angstroms or less, and preferably 500 angstroms or less in order to obtain good soft magnetic properties. In addition, the structure is mainly composed of crystalline and amorphous materials, but since the amorphous portion has a larger magnetostriction than the crystalline portion, at least 30% or more of the entire structure, preferably 60% or more, is crystalline. and the remainder is preferably amorphous. In addition, in the present invention, the size of crystal grains,
The degree of crystallinity (crystallinity) was determined by electron microscopy diffraction method and
Determined by line diffraction method.
【０００９】本発明のＦｅ基軟磁性合金は、最初に非晶
質の薄帯、粉末、細線、薄膜等を作製した後、これら得
られた非晶質合金を熱処理することにより得られる。薄
帯の場合、単ロール法等により作製した試料を巻磁心等
の所定の形状にした後、約４００〜７００℃程度で熱処
理する。熱処理中に磁場を印加してもよい。また熱処理
は窒素ガス、アルゴンガス、真空中いずれの雰囲気中で
行なってもよい。The Fe-based soft magnetic alloy of the present invention can be obtained by first preparing an amorphous ribbon, powder, fine wire, thin film, etc., and then heat-treating the obtained amorphous alloy. In the case of a ribbon, a sample prepared by a single roll method or the like is formed into a predetermined shape such as a wound core, and then heat-treated at about 400 to 700°C. A magnetic field may be applied during the heat treatment. Further, the heat treatment may be performed in any atmosphere of nitrogen gas, argon gas, or vacuum.
【００１０】以下、実施例を挙げて更に説明する。[0010] Hereinafter, further explanation will be given with reference to examples.
【００１１】[0011]
【実施例】単ロール法を用いて、Ｆｅ、Ｓｉ、Ａｌ、Ｂ
、Ｃｕを含有する合金からアルゴンガス雰囲気中で幅３
ｍｍ、厚さ約１８μｍの急冷薄帯を作成した。この急冷
薄帯の組成及び結晶化温度を表１に示す。[Example] Using a single roll method, Fe, Si, Al, B
, width 3 in an argon gas atmosphere from a Cu-containing alloy.
A quenched ribbon having a thickness of about 18 μm and a thickness of about 18 μm was prepared. Table 1 shows the composition and crystallization temperature of this quenched ribbon.
【００１２】0012
【表１】[Table 1]
【００１３】表１より明らかなように、Ｃｕの添加は、
非晶質薄帯の結晶化温度を低下させる（結晶粒の析出を
早める）効果があることがわかる。次に、この薄帯のＸ
線回折パターンを図１に示した。図１からも明らかなよ
うに薄帯製造直後の薄帯は非晶質合金に特有のハローパ
ターンを示すことから、その構造は非晶質であることが
わかる。[0013] As is clear from Table 1, the addition of Cu
It can be seen that this has the effect of lowering the crystallization temperature of the amorphous ribbon (accelerating the precipitation of crystal grains). Next, the X of this thin strip
The line diffraction pattern is shown in Figure 1. As is clear from FIG. 1, the ribbon immediately after production exhibits a halo pattern characteristic of an amorphous alloy, which indicates that its structure is amorphous.
【００１４】次に得られた薄帯を内径１５ｍｍ、外径１
８ｍｍ程度の巻磁心とした後、窒素ガス気流中で５００
℃で約１時間保持した後、窒素気流中で冷却した。この
際、磁場は印加しなかった。この熱処理後のＸ線回折パ
ターンを図２に示した。熱処理後の薄帯ではＦｅ基ｂｃ
ｃ固溶体結晶の回折ピークが認められた。磁心の損失（
Ｗ／ｋｇ）は、周波数１００ｋＨｚ、最大磁束密度０．
１Ｔにてデジタルオシロスコープを用いて測定した交流
ヒステリシスループの囲む面積から決定した。飽和磁歪
定数λＳ（ｐｐｍ）は、ストレインゲージ法によって決
定した。結果を表２に示す。[0014] Next, the obtained ribbon has an inner diameter of 15 mm and an outer diameter of 1
After making a wound core of about 8 mm, it was heated for 500 min in a nitrogen gas stream.
After being maintained at °C for about 1 hour, it was cooled in a nitrogen stream. At this time, no magnetic field was applied. The X-ray diffraction pattern after this heat treatment is shown in FIG. In the ribbon after heat treatment, Fe-based bc
c Diffraction peaks of solid solution crystals were observed. Core loss (
W/kg) at a frequency of 100kHz and a maximum magnetic flux density of 0.
It was determined from the area surrounded by an AC hysteresis loop measured using a digital oscilloscope at 1T. The saturation magnetostriction constant λS (ppm) was determined by the strain gauge method. The results are shown in Table 2.
【００１５】[0015]
【表２】[Table 2]
【００１６】表２からも明らかなように実施例の磁心は
、従来のＦｅ基非晶質合金（比較例）に比べて、含浸に
よる磁心損失の増加は非常に小さい。この結果は、本発
明の磁性合金は飽和磁歪も従来のＦｅ基非晶質合金に比
べて１桁程度小さいことに対応している。以上より、本
発明合金は、含浸工程において磁性特性の劣化が非常に
小さいことが明らかとなった。As is clear from Table 2, the increase in core loss due to impregnation in the magnetic core of the example is much smaller than that of the conventional Fe-based amorphous alloy (comparative example). This result corresponds to the fact that the saturation magnetostriction of the magnetic alloy of the present invention is also about one order of magnitude smaller than that of the conventional Fe-based amorphous alloy. From the above, it has become clear that the alloy of the present invention exhibits very little deterioration in magnetic properties during the impregnation process.
【００１７】[0017]
【発明の効果】以上の実施例からも明らかなように、本
発明のＦｅ基軟磁性合金によれば、Ｆｅ−Ｓｉ−Ｂ系合
金にＡｌおよびＣｕを添加することにより、軟磁性特性
の優れた新規なＦｅ基軟磁性合金を得ることができる。
また本発明のＦｅ基軟磁性合金は低磁歪を示すため、含
浸後の鉄損の増加が小さく、磁心材料として好適である
。Effects of the Invention As is clear from the above examples, the Fe-based soft magnetic alloy of the present invention has excellent soft magnetic properties by adding Al and Cu to the Fe-Si-B alloy. A new Fe-based soft magnetic alloy can be obtained. Furthermore, since the Fe-based soft magnetic alloy of the present invention exhibits low magnetostriction, the increase in core loss after impregnation is small, making it suitable as a magnetic core material.
【図１】本発明のＦｅ基軟磁性合金薄帯の急冷直後にお
けるＸ線回折パターンを示す図。FIG. 1 is a diagram showing an X-ray diffraction pattern of the Fe-based soft magnetic alloy ribbon of the present invention immediately after quenching.
【図２】本発明のＦｅ基軟磁性合金薄帯の最適熱処理後
のＸ線回折パターンを示す図。FIG. 2 is a diagram showing the X-ray diffraction pattern of the Fe-based soft magnetic alloy ribbon of the present invention after optimum heat treatment.
Claims (3)
−ｃ−ｄＳｉａＡｌｂＢｃＣｕｄ（式中、ＭはＣｏ及び
／又はＮｉを表わす。ｘは原子比を、ａ、ｂ、ｃ、ｄは
原子％を表わし、それぞれ０≦ｘ≦０．５、０≦ａ≦２
４、１≦ｂ≦２０、４≦ｃ≦３０、０．２≦ｄ≦３を満
たすものとする）で表わされることを特徴とするＦｅ基
軟磁性合金。Claim 1: General formula (Fe1-XMX) 100-a-b
-c-dSiaAlbBcCud (In the formula, M represents Co and/or Ni. x represents the atomic ratio, and a, b, c, and d represent atomic %, respectively, 0≦x≦0.5, 0≦a≦ 2
4, 1≦b≦20, 4≦c≦30, 0.2≦d≦3).
成り、残部は非晶質であることを特徴とする第１項記載
のＦｅ基軟磁性合金。2. The Fe-based soft magnetic alloy according to claim 1, wherein at least 30% of the structure is crystalline and the remainder is amorphous.
であることを特徴とする第２項記載のＦｅ基軟磁性合金
。3. The Fe-based soft magnetic alloy according to claim 2, wherein the crystalline material is a BCC solid solution mainly composed of iron.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3112800A JPH04341544A (en) | 1991-05-17 | 1991-05-17 | Fe base soft magnetic alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3112800A JPH04341544A (en) | 1991-05-17 | 1991-05-17 | Fe base soft magnetic alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04341544A true JPH04341544A (en) | 1992-11-27 |
Family
ID=14595841
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3112800A Withdrawn JPH04341544A (en) | 1991-05-17 | 1991-05-17 | Fe base soft magnetic alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04341544A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000503169A (en) * | 1996-01-11 | 2000-03-14 | アライドシグナル・インコーポレーテッド | Distributed gap electric choke |
| CN102304680A (en) * | 2011-09-16 | 2012-01-04 | 中南大学 | Iron-based amorphous/nanocrystalline thin band with low cost and excellent soft magnetic properties and preparation method thereof |
| WO2020142810A1 (en) * | 2019-01-11 | 2020-07-16 | Monash University | Iron based alloy |
-
1991
- 1991-05-17 JP JP3112800A patent/JPH04341544A/en not_active Withdrawn
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000503169A (en) * | 1996-01-11 | 2000-03-14 | アライドシグナル・インコーポレーテッド | Distributed gap electric choke |
| CN102304680A (en) * | 2011-09-16 | 2012-01-04 | 中南大学 | Iron-based amorphous/nanocrystalline thin band with low cost and excellent soft magnetic properties and preparation method thereof |
| WO2020142810A1 (en) * | 2019-01-11 | 2020-07-16 | Monash University | Iron based alloy |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A300 | Application deemed to be withdrawn because no request for examination was validly filed |
Free format text: JAPANESE INTERMEDIATE CODE: A300 Effective date: 19980806 |