JPH01156452A - Fe-based magnetic alloy - Google Patents
Fe-based magnetic alloyInfo
- Publication number
- JPH01156452A JPH01156452A JP62313645A JP31364587A JPH01156452A JP H01156452 A JPH01156452 A JP H01156452A JP 62313645 A JP62313645 A JP 62313645A JP 31364587 A JP31364587 A JP 31364587A JP H01156452 A JPH01156452 A JP H01156452A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- magnetic alloy
- based magnetic
- magnetic
- amorphous
- 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.)
- Granted
Links
- 229910001004 magnetic alloy Inorganic materials 0.000 title claims abstract description 21
- 239000013078 crystal Substances 0.000 claims abstract description 17
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 239000006104 solid solution Substances 0.000 claims abstract description 5
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 4
- 229910052787 antimony Inorganic materials 0.000 claims abstract description 3
- 229910052796 boron Inorganic materials 0.000 claims abstract description 3
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 3
- 229910052733 gallium Inorganic materials 0.000 claims abstract description 3
- 229910052732 germanium Inorganic materials 0.000 claims abstract description 3
- 229910052738 indium Inorganic materials 0.000 claims abstract description 3
- 229910052727 yttrium Inorganic materials 0.000 claims abstract description 3
- 229910052782 aluminium Inorganic materials 0.000 claims abstract 2
- 229910052785 arsenic Inorganic materials 0.000 claims abstract 2
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract 2
- 229910052791 calcium Inorganic materials 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052735 hafnium Inorganic materials 0.000 claims description 2
- 229910052745 lead Inorganic materials 0.000 claims description 2
- 229910052749 magnesium Inorganic materials 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 2
- 229910052706 scandium Inorganic materials 0.000 claims description 2
- 229910052711 selenium Inorganic materials 0.000 claims description 2
- 229910052712 strontium Inorganic materials 0.000 claims description 2
- 229910052714 tellurium Inorganic materials 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 229910052737 gold Inorganic materials 0.000 claims 1
- 229910052744 lithium Inorganic materials 0.000 claims 1
- 229910052760 oxygen Inorganic materials 0.000 claims 1
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 claims 1
- 229910052702 rhenium Inorganic materials 0.000 claims 1
- 229910052717 sulfur Inorganic materials 0.000 claims 1
- 229910052720 vanadium Inorganic materials 0.000 claims 1
- 229910052725 zinc Inorganic materials 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 abstract description 59
- 239000000956 alloy Substances 0.000 abstract description 59
- 238000010438 heat treatment Methods 0.000 abstract description 23
- 239000000203 mixture Substances 0.000 abstract description 10
- 238000001816 cooling Methods 0.000 abstract description 5
- 229910052790 beryllium Inorganic materials 0.000 abstract description 2
- 229910017709 Ni Co Inorganic materials 0.000 abstract 1
- 229910003267 Ni-Co Inorganic materials 0.000 abstract 1
- 229910003262 Ni‐Co Inorganic materials 0.000 abstract 1
- 229910052710 silicon Inorganic materials 0.000 abstract 1
- 239000011162 core material Substances 0.000 description 31
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 21
- 125000004429 atom Chemical group 0.000 description 14
- 229910000808 amorphous metal alloy Inorganic materials 0.000 description 10
- 230000035699 permeability Effects 0.000 description 10
- 238000000034 method Methods 0.000 description 9
- 239000002245 particle Substances 0.000 description 7
- 238000002441 X-ray diffraction Methods 0.000 description 6
- 238000002425 crystallisation Methods 0.000 description 6
- 230000008025 crystallization Effects 0.000 description 6
- 230000004907 flux Effects 0.000 description 6
- 230000005389 magnetism Effects 0.000 description 6
- 230000005540 biological transmission Effects 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 125000005843 halogen group Chemical group 0.000 description 2
- 238000005470 impregnation Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000005300 metallic glass Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000009987 spinning Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000967 As alloy Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 229910001361 White metal Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000005280 amorphization Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 229910052788 barium Inorganic materials 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 229910052793 cadmium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000696 magnetic material Substances 0.000 description 1
- 238000001755 magnetron sputter deposition Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000004627 transmission electron microscopy Methods 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 239000010969 white metal Substances 0.000 description 1
Landscapes
- Soft Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
〔並業上の利用分野〕
本発明は、優れた磁気特性を有し、磁歪が小さいＦｅ基
磁性合金、特に組織の大半が微細な結晶粒からなるＦｅ
基磁性合金に関する０
従来、高周波トランス、磁気ヘッド、可飽和リアクトル
、チ璽−クコイル等の磁心材料として、うず電流損が少
ない等の利点を有するフェライトが主に用いられていた
。しかしフェライトは飽和磁束密度が低く、温度特性も
悪いため、高周波トランスやテ鵞−クコイルに用いる場
合磁心を小形化することが困難であるという欠点があっ
た。Detailed Description of the Invention [Field of Application in the Ordinary Industry] The present invention is directed to Fe-based magnetic alloys having excellent magnetic properties and low magnetostriction, particularly Fe-based magnetic alloys having a structure mostly composed of fine crystal grains.
0 Regarding Base Magnetic Alloys Conventionally, ferrite, which has advantages such as low eddy current loss, has been mainly used as a magnetic core material for high frequency transformers, magnetic heads, saturable reactors, check coils, etc. However, since ferrite has a low saturation magnetic flux density and poor temperature characteristics, it has the disadvantage that it is difficult to miniaturize the magnetic core when used in high frequency transformers and gear coils.
近年、従来の磁心材料に対抗するものとして高い飽和磁
束密度を有する非晶質磁性合金が有望視されておシ、種
々の組成のものが開発されている０非晶質合金は主とし
てＦｅ糸とＣｏ系に大別され、Ｆｅ系の非晶質合金は材
料コストがＣｏ系に比べ安くつくという利点がある反面
−船釣に高周波においてＣｏ系非晶質合金よシコア損失
が大きく、透磁率も低いという問題がある。これに対し
Ｃｏ糸の非晶質合金は高周波のコア損失が小さく、透磁
率も高いがコア損失や透磁率の経時変化が大きい。さら
に高価なＣｏを主原料とするため価格的な不利は免れな
い。In recent years, amorphous magnetic alloys with high saturation magnetic flux densities have been viewed as promising to compete with conventional magnetic core materials, and amorphous alloys with various compositions have been developed mainly using Fe yarns. Fe-based amorphous alloys have the advantage of being cheaper in material cost than Co-based alloys, but on the other hand, they have a higher core loss than Co-based amorphous alloys at high frequencies for boat fishing, and have lower magnetic permeability. The problem is that it is low. On the other hand, the amorphous alloy of Co thread has small core loss at high frequencies and high magnetic permeability, but the core loss and magnetic permeability change over time are large. Furthermore, since expensive Co is used as the main raw material, a cost disadvantage cannot be avoided.
このような状況下でＦｅ基非晶質磁性合金について種々
の提案がなされた。Under these circumstances, various proposals have been made regarding Fe-based amorphous magnetic alloys.
特公昭６０−１７０１９号は、７４〜８４原子チのＦｅ
と、８〜２４原料チのＢと、１６原子チ以下のＳｌ及び
６原子チ以下のＣの内の少なくとも１つ、とからなる組
成を有し、その構造の少なくとも８５チが非晶質金属素
地の形を有し、かつ非晶質金属素地の全体にわたって不
連続に分布された合金成分の結晶質粒子群の析出物を有
しておシ、結晶質粒子群は０，０５〜１μｍの平均粒度
及び１〜１０μｍの平均粒子間距離を有しておυ、粒子
群は全体の０．０１〜０．３の平均容積分率を占めてい
ることを特徴とする鉄基含硼素磁性非晶質合金を開示し
ている。この合金の結晶質粒子群は磁壁のピンニング点
として作用する不連続な分布のα−（Ｆｅ、Ｓｔ）粒子
群であるとされている。Special Publication No. 17019/1986 discloses Fe with 74 to 84 atoms.
, B of 8 to 24 raw materials, at least one of Sl of 16 atoms or less and C of 6 atoms or less, and at least 85 atoms of the structure are an amorphous metal. It has the shape of a matrix and has precipitates of crystalline particles of alloying components distributed discontinuously throughout the amorphous metal matrix, and the crystalline particles have a size of 0.05 to 1 μm. An iron-based boron-containing magnetic non-magnetic non-magnetic material having an average particle size and an average interparticle distance of 1 to 10 μm, and characterized in that the particle group occupies an average volume fraction of 0.01 to 0.3 of the whole. A crystalline alloy is disclosed. The crystalline grains of this alloy are said to be a discontinuously distributed α-(Fe, St) grains that act as pinning points of the domain wall.
また特開昭６０−５２５５７号はＦｅＢ ＣｕｂＢｅ
５ｔ（１（ただし７５≦ａ≦８５，０≦ｂ≦１．５．１
０≦Ｃ≦２０゜ｄ≦１０かつｃ＋ｄ≦６０）からなる低
損失非晶質磁性合金を開示している。この非晶質磁性合
金は結晶化温度以下でかつキュリー温度以上で熱処理さ
れる。Also, JP-A-60-52557 is FeB CubBe
5t(1 (however, 75≦a≦85, 0≦b≦1.5.1
Disclosed is a low-loss amorphous magnetic alloy having the following relationship: 0≦C≦20°d≦10 and c+d≦60). This amorphous magnetic alloy is heat treated at a temperature below the crystallization temperature and above the Curie temperature.
特公昭６０−１７０１９号のＦｅ基基磁磁性合金不連続
な結晶粒子群の存在によりコア損失が減少しているが、
経時変化が大きく高周波トランスやチ璽−りの磁心用材
料としては満足でない。Although the core loss is reduced due to the presence of discontinuous crystal grain groups in the Fe-based magnetomagnetic alloy of Japanese Patent Publication No. 60-17019,
It is unsatisfactory as a material for magnetic cores in high-frequency transformers and chisels because of its large change over time.
一方、特開昭６０−５２５５７号のＦｅ基非晶質合金は
Ｃｕを含有しているためにコア損失が著しく低下してい
るが、上記結晶質粒子含有Ｆｅ基非晶質合金と同様に満
足ではない。さらにコア損失の経時変化、透磁率等に関
しても十分ではないという問題がある。また、磁歪が大
きく磁気特性のばらつきも大きく、キュリー温度がＦｅ
−８ｔ−Ａ１合金やＦｅ−５ｔ合金よシ低く磁気特性の
安定性も劣る。On the other hand, the Fe-based amorphous alloy of JP-A No. 60-52557 contains Cu, so the core loss is significantly reduced, but it is not as satisfactory as the Fe-based amorphous alloy containing crystalline particles mentioned above. isn't it. Further, there are problems in that changes in core loss over time, magnetic permeability, etc. are not sufficient. In addition, the magnetostriction is large, the variation in magnetic properties is large, and the Curie temperature is
It is lower than -8t-A1 alloy and Fe-5t alloy, and its magnetic properties are also inferior in stability.
従って、本発明の目的は磁歪が小さくコア損失、コア損
失の経時変化、透磁率その他の磁気特性の安定性に優れ
た新規なＦｅ基基磁磁性合金提供することである。Therefore, an object of the present invention is to provide a novel Fe-based magnetomagnetic alloy that has low magnetostriction and excellent stability in core loss, change in core loss over time, magnetic permeability, and other magnetic properties.
上記目的に鑑み鋭意研究の結果、本発明者等は一般式
％式％
（原子チ）
（ただし、ＭはＮｂ、Ｗ、Ｔａ、Ｚｒ、Ｈｆ、Ｔｉ、Ｍ
ｏ＋Ｖ。As a result of intensive research in view of the above objectives, the present inventors have determined that the general formula % (atomic ti) (where M is Nb, W, Ta, Zr, Hf, Ti, M
o+V.
Ｃｒ 、 Ｍｎ ｐ白金属元素Ｓｃ、Ｙ、希土類元素＋
Ａｕ ａ Ｚｎ 。Cr, Mn p White metal element Sc, Y, rare earth element +
Au a Zn.
Ｓｎ ＊ Ｒｅからなる群から選ばれた少なくとも１種
の元素、ＸはＣｒ Ｇｅ ＊ Ｇａ ＊ ＡＬ 、Ｂｅ
からなる群から選ばれた少なくとも１種の元素、Ｙはｐ
＋ ｓｂ ＋ Ｉｎ ｒＡｓ ＋Ｌｉ ＋Ｍｇ、Ｃａ
＋Ｓｒ、Ｂａ＋Ｃｄ、Ｐｂ、Ｂｉ ｌＮｔ Ｏ＋Ｓ 、
Ｓｅ及びＴｅからなる群から選ばれた少なくとも１穐
の元素であシ、
０≦ａ＜０−２．０≦ｂ＜０．５．０≦ａ＋ｂ＜０．５
ｔ４≦ｙ≦６０，２≦２≦９，０≦α≦２０゜０≦γ≦
２０，０≦δ≦２，１０≦ｙ＋ｚ＋ｒ≦３５を満たす。At least one element selected from the group consisting of Sn*Re, X is CrGe*Ga*AL, Be
At least one element selected from the group consisting of, Y is p
+ sb + In rAs + Li + Mg, Ca
+Sr, Ba+Cd, Pb, Bi lNt O+S,
At least one element selected from the group consisting of Se and Te, 0≦a<0-2.0≦b<0.5.0≦a+b<0.5
t4≦y≦60, 2≦2≦9, 0≦α≦20゜0≦γ≦
20, 0≦δ≦2, 10≦y+z+r≦35.
）
によシ表わされる組成の合金において組織の少なくとも
５０％が微細な結晶粒からなり、前記結晶粒の最大寸法
で測定した粒径の平均が１０００Ａ以下の平均粒径を有
する場合、優れた軟磁性が得られることを見い出し本発
明に想到した。) If at least 50% of the structure of an alloy with the composition represented by They discovered that magnetism can be obtained and came up with the present invention.
本発明においてＳｔ、Ｂは必須の元素であシ、合金の結
晶粒微細化および磁歪調整軟磁気特性の改善に有用な元
素である。In the present invention, St and B are essential elements, and are elements useful for refining the crystal grains of the alloy and improving the magnetostriction adjustment soft magnetic properties.
本発明の合金は、好ましくは、−旦８１．Ｂ添加により
非晶質合金とした後で、熱処理によシ微細結晶粒を形成
することによシ得られる。The alloy of the present invention preferably comprises -dan81. It is obtained by forming an amorphous alloy by adding B and then forming fine crystal grains by heat treatment.
Ｓｔ含有ｊｋｙの限定理由は、ｙが３０原子チを超える
と軟磁気特性の良好な条件では磁歪が大きくなってしま
い好ましくなく、４原子−未満では軟磁気特性が著しく
劣化するため好ましくないためである。Ｂの含有量２の
限定理由は、２が２原子チ未満では均一な結晶粒組織が
得にくく軟磁気特性が劣化し好ましくなく、２が９ｙＡ
子チを超えると軟磁気特性の良好な熱処理条件では磁歪
が大きくなってしまい好ましくないためである。The reason for limiting the St-containing jky is that if y exceeds 30 atoms, the magnetostriction will become large under conditions with good soft magnetic properties, which is undesirable, and if y is less than 4 atoms, the soft magnetic properties will deteriorate significantly, which is undesirable. be. The reason for limiting the B content to 2 is that if 2 is less than 2 atoms, it is difficult to obtain a uniform crystal grain structure and the soft magnetic properties deteriorate, which is undesirable.
This is because if the magnetic field exceeds the maximum magnetostriction, the magnetostriction becomes large under heat treatment conditions that provide good soft magnetic properties, which is undesirable.
ＸはＣ、Ｇｅ 、 Ｇａ ＊ Ａｔ＋ Ｂｅからなる群
から選ばれた少なくとも１種の元素であシ、これらの元
素は非晶質化や磁歪、キエリー温度調整等に効果がある
Ｏ
Ｘの含有量γの限定理由は２０原子チを超えると、著し
く軟磁気特性が劣化し、飽和磁束密度も低下するためで
ある。X is at least one element selected from the group consisting of C, Ge, Ga*At+Be, and these elements are effective for amorphization, magnetostriction, Chier temperature adjustment, etc. The reason for limiting γ is that if it exceeds 20 atoms, the soft magnetic properties will deteriorate significantly and the saturation magnetic flux density will also decrease.
Ｓｔ、Ｂ、Ｘの総和量ｙ＋ｚ＋γの値に関しては、ｙ＋
ｚ＋γが１０原子チ未満では非晶質化が困難になシ磁気
特性が劣化し好ましくなく、一方、ｙ−Ｉ−ｚ＋ｒが３
５原子チを超えると、飽和磁束密度の著しい低下および
軟磁気特性の劣化がある。より好ましいＳｔ、Ｂ含有量
の範囲は、１０≦ｙ≦２５゜４≦２≦７である。Regarding the value of the total amount y+z+γ of St, B, and X, y+
If z+γ is less than 10 atoms, it is difficult to make it amorphous and the magnetic properties deteriorate, which is undesirable. On the other hand, if y-I-z+r is 3
If it exceeds 5 atoms, there will be a significant decrease in saturation magnetic flux density and deterioration of soft magnetic properties. A more preferable range of St and B content is 10≦y≦25°4≦2≦7.
この範囲で特に優れた軟磁性が得られ、磁歪も小さいも
のが得やすい。Within this range, particularly excellent soft magnetism can be obtained, and magnetostriction can also be easily obtained.
本発明に係る合金においてＭは、結晶粒を微細化したり
、耐食性を改善したりする効果を有しており、２０原子
チ以下含むことができる。この理由は、Ｍの含Ｍｉｉα
が２０原子チを越えた場合は飽和磁束密度の著しい低下
を示すためである。特に好ましいαの範囲は１≦α≦１
０であり、この範囲で優れた軟磁性を得ることができる
。特にＭとしてはＮｂ、Ｗ、Ｔａ及びＭｏが軟磁気特性
の面で好ましい。In the alloy according to the present invention, M has the effect of making crystal grains finer and improving corrosion resistance, and can be contained in an amount of 20 atoms or less. The reason for this is that M contains Miiα
This is because when the amount exceeds 20 atoms, the saturation magnetic flux density decreases significantly. A particularly preferable range of α is 1≦α≦1
0, and excellent soft magnetism can be obtained within this range. In particular, Nb, W, Ta, and Mo are preferable as M in terms of soft magnetic properties.
添加元素ＹはＰ ＊ Ｓｂ 、Ｉｎ ＊ Ａｓ ｒ Ｌ
ｉ＊ Ｎｉａ ｔ Ｃａ 、Ｓｒ ｒＢａ 、 Ｃｄ
、 Ｐｈ 、 Ｂｊ、 、 Ｎ ｒ Ｏｒ Ｓ ｒ Ｓ
ｅ及びＴｅからなる群から選ばれた少なくとも１種の元
素であり、２原子チ以下含んでも良い。The additive element Y is P*Sb, In*As r L
i* Niat Ca , Sr rBa , Cd
, Ph , Bj, , N r Or S r S
It is at least one element selected from the group consisting of e and Te, and may contain up to two atoms.
残部は不純物を除いて実質的にＦｅが主体であるが、Ｆ
ｅの１部はＮｉ及び／又はＣｏにより置換されていても
良い。Ｎｉの含有ＪｉｌａはＯＳａ＜０．２であるが、
これは０．２を超えると軟磁性が著しく劣化するためで
あり、ｔＶｆＫ好ましい範囲１１０≦ａ ；Ｓ ０．１
である。この範囲で特に良好な軟磁性が得られる。The remainder is essentially Fe, excluding impurities, but F
A part of e may be replaced by Ni and/or Co. Ni content Jila is OSa<0.2, but
This is because soft magnetism deteriorates significantly when it exceeds 0.2, and tVfK is preferably in the range 110≦a; S 0.1
It is. Particularly good soft magnetism can be obtained within this range.
Ｃｏの含有量すは０≦ｂ＜ｏ、ｓであり、Ｎｉの含有量
との総和ａ＋ｂは０≦ａ＋ｂ＜０．５である。特に好ま
しいＣｏの含有量およびＣｏとＮｉの含有量の総和は０
≦ｂ≦０．１．０≦ａ＋ｂ≦０．１である。The Co content satisfies 0≦b<o, s, and the total sum a+b with the Ni content satisfies 0≦a+b<0.5. Particularly preferable Co content and the sum of Co and Ni contents are 0
≦b≦0.1.0≦a+b≦0.1.
本発明合金は微細なりｃｃＦｅ固溶体を主体とする合金
で組織の少なくとも５０％が微細な結晶粒からなシ、前
記結晶粒の最大寸法で測定した粒径の平均が１０００Ａ
以下の平均粒径を有する合金である０
通常は単ロール法、双ロール法等の液体急冷法やスパッ
ター法、蒸着法等による気相急冷法等により非晶質合金
を作製後これを加熱し結晶化させることＫより作製され
る。The alloy of the present invention is an alloy mainly composed of a fine ccFe solid solution, in which at least 50% of the structure is composed of fine crystal grains, and the average grain size measured at the maximum dimension of the crystal grains is 1000A.
The alloy has an average grain size of It is made from crystallized K.
特に最大寸法で測定し九粒径の平均が５００Ａ以下の平
均粒径を有する場合、特に優れた軟磁気特性を得ること
ができる。Particularly excellent soft magnetic properties can be obtained when the average particle size of the nine particle sizes measured in the maximum dimension is 500A or less.
前記結晶粒の残部は主に非晶質であるが、本発明合金は
実質的に１００％結晶質であっても十分優れた軟磁気特
性を得ることができる。Although the remainder of the crystal grains are mainly amorphous, the alloy of the present invention can obtain sufficiently excellent soft magnetic properties even if it is substantially 100% crystalline.
また本発明合金はｂｃｃＦｅ固溶体を主体とする合金テ
あり、飽和磁歪λｓが一５ｘ１０〜＋５Ｘ１０−’の範
囲にあるものが得られ、Ｆｅ基アモルファス合金よシ著
しく磁歪が小さい。また、磁歪がほぼ零の合金も得るこ
とができる。Furthermore, the alloy of the present invention is an alloy mainly composed of bccFe solid solution, and the saturation magnetostriction λs is in the range of -5x10 to +5x10-', and the magnetostriction is significantly lower than that of the Fe-based amorphous alloy. Furthermore, alloys with almost zero magnetostriction can also be obtained.
本発明のＦｅ基磁性合金は、前述のように単ロール法、
双ロール法、遠心急冷法等によシ非晶質薄帯を作製後熱
処理を行ない微細な結晶粒を形成する方法、蒸着法、ス
パッター法やイオンブレーティング等によシ非晶質膜を
作製後熱処理し結晶化させる方法、アトマイズ法やキャ
ビテーシ冒ン法により非晶質粉を得た後熱処理し結晶化
させる方法や回転液中紡糸法やガラス被覆紡糸法により
、非晶質線を得た後熱処理し結晶化させる方法等いろい
ろな方法で作製することができる。したがって、本発明
合金は粉末、線、薄帯、膜などいろいろな形状のものが
でき、圧接等を行なえばバルク体も得ることができる。The Fe-based magnetic alloy of the present invention can be produced by the single roll method as described above.
Amorphous thin strips are prepared by the twin roll method, centrifugal quenching method, etc., and then heat treated to form fine crystal grains. Amorphous films are prepared by vapor deposition, sputtering, ion blating, etc. An amorphous wire was obtained by a method of post-heat treatment and crystallization, a method of obtaining amorphous powder by an atomization method or a cavitation blowing method, and then a method of heat-treating and crystallizing it, a spinning method in a rotating liquid, or a glass-covered spinning method. It can be produced by various methods such as a method of post-heat treatment and crystallization. Therefore, the alloy of the present invention can be made into various shapes such as powder, wire, ribbon, and film, and can also be made into a bulk body by pressure welding.
本合金を得る除行われる熱処理は内部歪を小さくするこ
とと、微細結晶粒組織とし軟磁気特性を向上させるとと
もに磁歪を小さくする目的で行われる。The heat treatment performed before obtaining this alloy is performed for the purpose of reducing internal strain, creating a fine grain structure, improving soft magnetic properties, and reducing magnetostriction.
熱処理は通常真空中または水紫ガス、窒素ガス。Heat treatment is usually done in vacuum or with water purple gas or nitrogen gas.
アルゴンガス等の不活性ガス雰囲気中において行なわれ
る。しかし場合によっては大気中で行っても良い。This is carried out in an inert gas atmosphere such as argon gas. However, depending on the case, it may be performed in the atmosphere.
熱処理温度及び時間は非晶質合金リボンからなる磁心の
形状、サイズ、組成により異なるが一般的に４５０℃〜
７００℃で５分から２４時間程度が望ましい。The heat treatment temperature and time vary depending on the shape, size, and composition of the magnetic core made of amorphous alloy ribbon, but generally 450℃~
Preferably, the temperature is 700°C for about 5 minutes to 24 hours.
熱処理の際の昇温や冷却の条件は状況に応じて任意に変
えることができる。また同一温度または異なる温度で複
数回にわけ熱処理を行ったシ、多段の熱処理パターンで
熱処理を行なうこともできる。更には、本合金は熱処理
を直流あるいは交流の磁場中で行なうこともできる。磁
場中熱処理によｐ本合金に磁気異方性を生じさせること
ができる。本合金からなる磁心の磁路方向に磁場を印加
し熱処理した場合は、Ｂ−Ｈカーブの角形性が良いもの
が得られ、可飽和リアクトル、磁気スイッチ、パルス圧
縮用コア、スパイク電圧防止用リアクトル等に好適な特
性が得られ、一方磁路と直角方向に磁場を印加し熱処理
した場合は、Ｂ−Ｈカーブが傾斜し、低角形比で恒速磁
率性に優れた特性が得られ、トランスやノイズフィルタ
ー、チ璽−クコイル等に好適となる。Conditions for heating and cooling during heat treatment can be arbitrarily changed depending on the situation. The heat treatment can also be performed in a multi-stage heat treatment pattern, in which the heat treatment is performed multiple times at the same temperature or at different temperatures. Furthermore, the present alloy can also be heat treated in a direct current or alternating current magnetic field. Magnetic anisotropy can be produced in the p-based alloy by heat treatment in a magnetic field. When heat-treated by applying a magnetic field in the magnetic path direction of a magnetic core made of this alloy, a product with good B-H curve squareness can be obtained, which can be used for saturable reactors, magnetic switches, cores for pulse compression, and reactors for preventing spike voltages. On the other hand, when heat treatment is performed by applying a magnetic field in the direction perpendicular to the magnetic path, the B-H curve becomes sloped, and excellent characteristics with low squareness ratio and constant velocity magnetic properties are obtained, and the transformer It is suitable for use as noise filters, check coils, etc.
磁場は熱処理の間中かける必要はなく、合金のキエリー
温度Ｔｃよシ低い温度でかければ十分効果がある。本発
明合金のキエリー温度は非晶質の場合よシ主相のキエリ
ー温度が上昇しており、非晶質合金のキエリー温度より
高い温度でも磁場中熱処理が適用できる。また回転磁場
中熱処理を行ない軟磁気特性を更に改善することもでき
る。また、熱処理の際合金に電流を流したシ、高周波磁
界を印加し合金を発熱させることにより合金を熱処理す
ることもできる。It is not necessary to apply a magnetic field throughout the heat treatment, and it is sufficiently effective if it is applied at a temperature lower than the Chierly temperature Tc of the alloy. The Chielly temperature of the main phase of the alloy of the present invention is higher than that of the amorphous alloy, and heat treatment in a magnetic field can be applied even at a temperature higher than the Chielly temperature of the amorphous alloy. Further, the soft magnetic properties can be further improved by heat treatment in a rotating magnetic field. Alternatively, the alloy can be heat-treated by passing a current through the alloy and applying a high-frequency magnetic field to generate heat in the alloy.
また応力下で熱処理し磁気特性を調整することもできる
。特に本発明の合金は低磁歪の特徴を有するため、合金
表面に絶縁層を形成したシ、含浸やコーティングを行ワ
ても磁気特性の劣化が小さい特徴があシ、優れた特性の
モールドコアやカットコア、コーティングコア、磁気ヘ
ッド等を作製できる。The magnetic properties can also be adjusted by heat treatment under stress. In particular, since the alloy of the present invention has the characteristic of low magnetostriction, it has the characteristic that the magnetic properties do not deteriorate even after forming an insulating layer on the alloy surface, impregnation or coating, and mold cores with excellent characteristics. Cut cores, coated cores, magnetic heads, etc. can be produced.
〔実施例〕
本発明を以下の実施例によシさらに詳細に説明するが、
本発明はこれらに限定されるものではないＯ
実施例１
原子チでＳｉ １７．５ａｔ％、Ｂ５ａｔ％、Ｎｂ５ａ
ｔ％及び残部実質的にＦｅからなる組成の溶湯から、単
ロール法により合金薄帯を作製した。板厚は１８μｍ幅
は３１１Ｉ＋であった。[Example] The present invention will be explained in more detail with reference to the following example.
The present invention is not limited to these examples. Example 1 Si 17.5 at%, B5 at%, Nb5a
An alloy ribbon was produced by a single roll method from a molten metal having a composition of t% and the balance substantially consisting of Fe. The plate thickness was 18 μm and the width was 311I+.
この合金のＸ線回折を行ったところ非晶質合金特有のハ
ローパターンが得られた。透過電子顕微鏡による組織観
察の結果でも結晶相は認められなかった。この合金の結
晶化温度は５４１℃であった０
次にこの合金を外径１９Ｍ、内径１５５ｍのトロイダル
状に巻き巻磁心を作製した。次にこの巻磁心を５６０℃
に保持したＡｒ雰囲気の炉に装入し、１時間保持後、５
いの冷却速度で室温まで冷却した。When this alloy was subjected to X-ray diffraction, a halo pattern unique to amorphous alloys was obtained. No crystalline phase was observed in the results of structure observation using a transmission electron microscope. The crystallization temperature of this alloy was 541° C. Next, this alloy was wound into a toroidal shape having an outer diameter of 19 m and an inner diameter of 155 m to prepare a wound magnetic core. Next, this wound magnetic core was heated to 560°C.
It was charged into a furnace with an Ar atmosphere maintained at
The mixture was cooled to room temperature at a cooling rate of 1.
第１図（ａ）にＸ線回折パターン、第１図（ｂ）に透過
電子顕微鏡で観、察したミクロ組織の模式図を示す。FIG. 1(a) shows an X-ray diffraction pattern, and FIG. 1(b) shows a schematic diagram of the microstructure observed and observed with a transmission electron microscope.
Ｘ線回折および透過電子顕微鏡による組織観察の結果よ
り本発明合金は組織の大部分が５０〜５００Ａの粒径の
微細なりｃｃＦｅ固溶体固溶体表ることが確認された。From the results of structure observation using X-ray diffraction and transmission electron microscopy, it was confirmed that the majority of the structure of the alloy of the present invention is a fine grain size of 50 to 500A and represents a ccFe solid solution.
磁気特性は、飽和磁束密度Ｂｓが１２．４ＫＧ、ＩＫＨ
ｚにおける実効透磁率が１４３００．２ＫＧ１００ＫＨ
ｚにおけるコア損失Ｗ２／１（ＩＩＫが６３０ ｍＷ／
ｃｃであり優れた軟磁性を示すことが確認された。また
飽和磁歪λ、は＋２．５Ｘ１０でありＦｅ基アモルファ
ス合金に比べ著しく小さいことが確認された。As for magnetic properties, saturation magnetic flux density Bs is 12.4KG, IKH
Effective magnetic permeability at z is 14300.2KG100KH
Core loss W2/1 at z (IIK is 630 mW/
cc and was confirmed to exhibit excellent soft magnetism. It was also confirmed that the saturation magnetostriction λ was +2.5×10, which was significantly smaller than that of the Fe-based amorphous alloy.
実流例２
原子チで５ｉ１７．８ａｔ％、Ｂ５．Ｏａｔ％、Ｎｂ３
．１ａｔチ及び残部実質的にＦｅからなる組成の溶湯か
ら、板厚１８μｍ帽５ｍの合金薄帯を単ロール法によシ
作製した。この合金はＸ線回折の結果非晶質合金特有の
ハローパターンを示し、透過電子顕微鏡による組織観察
の結果でも結晶相は認められず、非晶質単相であること
が′８ｇされた。Actual flow example 2 5i17.8at% in atoms, B5. Oat%, Nb3
．． An alloy thin strip having a thickness of 18 μm and 5 m was produced by a single roll method from a molten metal having a composition of 1 atm and the remainder substantially consisting of Fe. This alloy exhibited a halo pattern characteristic of amorphous alloys as a result of X-ray diffraction, and no crystalline phase was observed in the results of structural observation using a transmission electron microscope, indicating that it was an amorphous single phase.
次にこの合金薄帯を外径１９削内径１５ｍのトロイダル
状に巻回しトロイダル磁心とし窒素ガス雰囲気中で熱処
理を行った。保持時間は１時間とした。熱処理中試料に
は５００００ｅの磁場を印加し試料を回転させた。冷却
は５′ｃ／Ｈの冷却速度で行りた。Next, this alloy ribbon was wound into a toroidal shape having an outer diameter of 19 and an inner diameter of 15 m, and was heat-treated in a nitrogen gas atmosphere to form a toroidal magnetic core. The holding time was 1 hour. During the heat treatment, a magnetic field of 50,000 e was applied to the sample and the sample was rotated. Cooling was carried out at a cooling rate of 5'c/H.
熱処理温度と磁気特性の関係および結晶相の割合を第１
表に示す。The relationship between heat treatment temperature and magnetic properties and the ratio of crystalline phase are determined first.
Shown in the table.
第 １ 表
結晶相の比率が５０％を越えると飽和磁歪定数λＢが著
しく小さくなシ、かつ軟磁気特性も良好な特性を示すこ
とがわかる。結晶相の比率が０％の非晶質状態の合金よ
、り １ ＫＨｚの実効透磁率がやや低い場合もあるが
、実用的に問題ない値であり、λ８が著しく小さい特徴
があるため含浸等による歪による磁気特性の劣化が小さ
くモールドコア等に用いる場合有利となる。Table 1 It can be seen that when the ratio of crystalline phase exceeds 50%, the saturation magnetostriction constant λB becomes extremely small, and the soft magnetic properties also show good properties. Although the effective magnetic permeability at 1 KHz may be slightly lower than that of an amorphous alloy with a crystalline phase ratio of 0%, it is a value that poses no practical problem, and is characterized by a significantly small λ8, making it suitable for impregnation, etc. Since the deterioration of magnetic properties due to distortion is small, it is advantageous when used for mold cores, etc.
実施例６
第２表に示す組成の淳さ１５μｍ１幅５鱈の合金薄帯を
単ロール法により作製した。Example 6 An alloy ribbon having the composition shown in Table 2 and having a thickness of 15 μm and a width of 5 mm was produced by a single roll method.
次に、この合金薄帯を外径１９ｆｉ、内径１５鴫に巻回
しトロイダル磁心を作製し、Ｎ２ガス雰囲気中で結晶化
温度以上で熱処理後１００ＫＨｚ 、 ０．２７におけ
るコア損失、飽和磁歪λ８１２０℃に１０００時間保持
した後のコア損失の増加率を測定した。Next, this alloy ribbon was wound to have an outer diameter of 19 fi and an inner diameter of 15 mm to make a toroidal magnetic core, and after heat treatment in an N2 gas atmosphere at a temperature higher than the crystallization temperature, the core loss at 100 KHz, 0.27, and the saturation magnetostriction λ were 8120°C. The rate of increase in core loss after holding for 1000 hours was measured.
Ｗｏ：初期のコア損失 Ｗｔｏｏｏ ： １０００時間
後のコア損失筒 ２ 表
なお、透過電子顕微鏡による組織観察の結果ミクロ組織
は実施例１とほぼ同様であることが確認された。Wo: Initial core loss Wtooo: Core loss cylinder after 1000 hours Table 2 Note that as a result of structure observation using a transmission electron microscope, it was confirmed that the microstructure was almost the same as in Example 1.
表かられかるように本発明合金は従来のＦｅ基７モル７
アス合金よジ飽和磁歪λ８が著しく小さく、コア損失も
小さい。またＦｅ基およびＣｏ基アモルファス合金に比
べ著しくコア損失の経時変化率が小さく安定である。こ
のため高信頼性の磁心を作製することができる。As can be seen from the table, the alloy of the present invention has a Fe base of 7 mol 7
As alloy, the saturation magnetostriction λ8 is extremely small and the core loss is also small. Furthermore, compared to Fe-based and Co-based amorphous alloys, the rate of change in core loss over time is significantly smaller and more stable. Therefore, a highly reliable magnetic core can be manufactured.
実施例４
第３表に示す組成の厚さ６μｍの合金膜を７オトセラム
基板上にマグネトロンスパッタ法により作製し九。Ｘ線
回折の結果得られた合金膜はほぼ非晶質単相であること
が確認された。Example 4 An alloy film having the composition shown in Table 3 and having a thickness of 6 μm was prepared on an Otoceram substrate by magnetron sputtering. As a result of X-ray diffraction, it was confirmed that the alloy film obtained was almost an amorphous single phase.
次にこの合金をＮガス雰囲気中で結晶化温度以上に加熱
し熱処理した。得られた合金膜の組繊は実施例１とほぼ
同様でありた。次に、この合金膜のＩＭＨｚの実効透磁
率μｅＩＭを測定し、次に１２０℃１ｏｏｏ時間保持後
のＩＭＨｚの実効透磁率μ”ＩＭを測定した。ＩＭＨｚ
の実効透磁率の変化率Δμ０Ｍ第０Ｍ
衣かられかるように本発明合金膜は従来のア七ルファス
合金膜に比べ経時変化が著しく小さく優れている。Next, this alloy was heat treated in an N gas atmosphere to a temperature higher than the crystallization temperature. The fiber composition of the obtained alloy film was almost the same as in Example 1. Next, the IMHz effective magnetic permeability μeIM of this alloy film was measured, and then the IMHz effective magnetic permeability μ”IM after holding at 120°C for 100 hours was measured.IMHz
The rate of change in effective magnetic permeability Δμ0Mth0M As can be seen from the above, the alloy film of the present invention is superior in that the change over time is significantly smaller than that of the conventional alpha alpha alloy film.
本発明によれは優れた軟磁気特性を有し、磁歪が小さく
熱安定性にも優れたＦｅ基磁性合金を得ることができる
ため、その効果は著しいものがある。According to the present invention, it is possible to obtain an Fe-based magnetic alloy having excellent soft magnetic properties, low magnetostriction, and excellent thermal stability, so the effects are remarkable.
第１図（ａ）は本発明合金のＸ線回折パターンの一例を
示した図、第１図（ｂ）は本発明合金の透過電子顕微鏡
により観察した組織の模式図を示した図である。FIG. 1(a) is a diagram showing an example of the X-ray diffraction pattern of the alloy of the present invention, and FIG. 1(b) is a diagram showing a schematic diagram of the structure of the alloy of the present invention observed by a transmission electron microscope.
Claims (1)
０＿０＿−＿ｙ＿−＿ｚ＿−＿α＿−＿β＿−＿γ＿−
＿δＳｉ＿ｙＢ＿ｚＭ′＿αＸ＿γＹ＿δ（原子％） （ただし、Ｍ′はＮｂ、Ｗ、Ｔａ、Ｚｒ、Ｈｆ、Ｔｉ、
Ｍｏ、Ｖ、Ｃｒ、Ｍｎ、白金属元素、Ｓｃ、Ｙ、希土類
元素、Ａｕ、Ｚｎ、Ｓｎ、Ｒｅからなる群から選ばれた
少なくとも１種の元素、ＸはＣ、Ｇｅ、Ｇａ、Ａｌ、Ｂ
ｅからなる群から選ばれた少なくとも１種の元素、Ｙは
Ｐ、Ｓｂ、Ｉｎ、Ａｓ、Ｌｉ、Ｍｇ、Ｃａ、Ｓｒ、Ｂａ
、Ｃｄ、Ｐｂ、Ｂｉ、Ｎ、Ｏ、Ｓ、Ｓｅ及びＴｅからな
る群から選ばれた少なくとも１種の元素であり、 ０≦ａ＜０．２、０≦ｂ≦０．５、０≦ａ＋ｂ＜０．５
、４≦ｙ≦３０、２≦ｚ≦９、０≦α≦２０、０≦γ≦
２０、０≦δ≦２、１０≦ｙ＋ｚ＋γ≦３５を満たす。 ）により表わされる組成を有し、組織の少なくとも５０
％が微細な結晶粒からなり、前記結晶粒の最大寸法で測
定した粒径の平均が１０００Å以下の平均粒径を有する
ことを特徴とするＦｅ基磁性合金。 （２）特許請求の範囲第１項に記載のＦｅ基磁性合金に
おいて、ａ、ｂ、ｙ、ｚ、α、γが ０≦ａ≦０．１、０≦ｂ≦０．１、０≦ａ＋ｂ≦０．１
、１０≦ｙ≦２５、４≦ｚ≦７、１≦α≦１０、０≦γ
≦１０の関係を満足することを特徴とするＦｅ基磁性合
金。 （３）特許請求の範囲第１項乃至第２項に記載のＦｅ基
磁性合金において、前記組織の残部が非晶質であること
を特徴とするＦｅ基磁性合金。 （４）特許請求の範囲第１項乃至第２項に記載のＦｅ基
磁性合金において、前記組織が実質的に微細な結晶粒か
らなることを特徴とするＦｅ基磁性合金。 （５）前記結晶粒がｂｃｃ構造のＦｅ固溶体を主体とし
たものからなることを特徴とする特許請求の範囲第１項
乃至第４項に記載のＦｅ基磁性合金。 （６）前記結晶粒の最大寸法で測定した粒径の平均が５
００Å以下の平均粒径を有することを特徴とする特許請
求の範囲第１項乃至第５項記載のＦｅ基磁性合金。 （７）Ｍ′がＮｂ、Ｗ、Ｔａ及びＭｏからなる群から選
ばれる少なくとも１種の元素であることを特徴とする特
許請求の範囲第１項乃至第６項に記載のＦｅ基磁性合金
。 （８）飽和磁歪λ＿ｓが−５×１０＾−＾６〜＋５×１
０＾−＾６の範囲にあることを特徴とする特許請求の範
囲第１項乃至第７項に記載のＦｅ基磁性合金。[Claims] 1. General formula (Fe_1_-_a_-_bNi_aCo_b)_1_
0_0_-_y_-_z_-_α_-_β_-_γ_-
_δSi_yB_zM'_αX_γY_δ (atomic %) (However, M' is Nb, W, Ta, Zr, Hf, Ti,
At least one element selected from the group consisting of Mo, V, Cr, Mn, platinum metal element, Sc, Y, rare earth element, Au, Zn, Sn, Re, X is C, Ge, Ga, Al, B
At least one element selected from the group consisting of e, Y is P, Sb, In, As, Li, Mg, Ca, Sr, Ba
, Cd, Pb, Bi, N, O, S, Se, and Te, and 0≦a<0.2, 0≦b≦0.5, 0≦a+b <0.5
, 4≦y≦30, 2≦z≦9, 0≦α≦20, 0≦γ≦
20, 0≦δ≦2, 10≦y+z+γ≦35. ) and at least 50% of the tissue
% of the crystal grains, and the average grain size measured at the maximum dimension of the crystal grains is 1000 Å or less. (2) In the Fe-based magnetic alloy according to claim 1, a, b, y, z, α, and γ are 0≦a≦0.1, 0≦b≦0.1, 0≦a+b ≦0.1
, 10≦y≦25, 4≦z≦7, 1≦α≦10, 0≦γ
An Fe-based magnetic alloy characterized by satisfying the relationship of ≦10. (3) The Fe-based magnetic alloy according to claims 1 and 2, wherein the remainder of the structure is amorphous. (4) The Fe-based magnetic alloy according to claims 1 and 2, characterized in that the structure consists of substantially fine crystal grains. (5) The Fe-based magnetic alloy according to any one of claims 1 to 4, wherein the crystal grains are mainly composed of Fe solid solution having a bcc structure. (6) The average grain size measured at the maximum dimension of the crystal grains is 5
6. The Fe-based magnetic alloy according to claim 1, wherein the Fe-based magnetic alloy has an average grain size of 00 Å or less. (7) The Fe-based magnetic alloy according to any one of claims 1 to 6, wherein M' is at least one element selected from the group consisting of Nb, W, Ta, and Mo. (8) Saturation magnetostriction λ_s is -5×10^-^6 to +5×1
The Fe-based magnetic alloy according to any one of claims 1 to 7, characterized in that the Fe-based magnetic alloy is in the range of 0^-^6.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62313645A JP2713714B2 (en) | 1987-12-11 | 1987-12-11 | Fe-based magnetic alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62313645A JP2713714B2 (en) | 1987-12-11 | 1987-12-11 | Fe-based magnetic alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH01156452A true JPH01156452A (en) | 1989-06-20 |
| JP2713714B2 JP2713714B2 (en) | 1998-02-16 |
Family
ID=18043801
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62313645A Expired - Fee Related JP2713714B2 (en) | 1987-12-11 | 1987-12-11 | Fe-based magnetic alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2713714B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1198605A2 (en) * | 1999-05-25 | 2002-04-24 | Bechtel BWXT Idaho, LLC | Methods of forming steel |
| JP2002226956A (en) * | 2000-11-29 | 2002-08-14 | Alps Electric Co Ltd | Amorphous soft magnetic alloy |
| CN103668006A (en) * | 2013-12-19 | 2014-03-26 | 南京信息工程大学 | Nickel-free alloy and preparation method thereof |
| CN108251753A (en) * | 2018-02-08 | 2018-07-06 | 东北大学 | A kind of high-magnetostriction coefficient Fe-Ga base strips and preparation method thereof |
-
1987
- 1987-12-11 JP JP62313645A patent/JP2713714B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP1198605A2 (en) * | 1999-05-25 | 2002-04-24 | Bechtel BWXT Idaho, LLC | Methods of forming steel |
| EP1198605A4 (en) * | 1999-05-25 | 2002-11-06 | Bechtel Bwxt Idaho Llc | Methods of forming steel |
| EP1452617A1 (en) * | 1999-05-25 | 2004-09-01 | Bechtel BWXT Idaho, LLC | Methods of forming steel |
| JP2002226956A (en) * | 2000-11-29 | 2002-08-14 | Alps Electric Co Ltd | Amorphous soft magnetic alloy |
| CN103668006A (en) * | 2013-12-19 | 2014-03-26 | 南京信息工程大学 | Nickel-free alloy and preparation method thereof |
| CN108251753A (en) * | 2018-02-08 | 2018-07-06 | 东北大学 | A kind of high-magnetostriction coefficient Fe-Ga base strips and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2713714B2 (en) | 1998-02-16 |
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