JP3623970B2 - Fe-based soft magnetic alloy and manufacturing method - Google Patents
Fe-based soft magnetic alloy and manufacturing method Download PDFInfo
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- JP3623970B2 JP3623970B2 JP15833892A JP15833892A JP3623970B2 JP 3623970 B2 JP3623970 B2 JP 3623970B2 JP 15833892 A JP15833892 A JP 15833892A JP 15833892 A JP15833892 A JP 15833892A JP 3623970 B2 JP3623970 B2 JP 3623970B2
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- 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
- H01F1/032—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 hard-magnetic materials
- H01F1/04—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 hard-magnetic materials metals or alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C45/02—Amorphous alloys with iron as the major constituent
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- 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
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Description
【０００１】
【産業上の利用分野】
【０００２】
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基軟磁性合金及びその製造方法に関する。
【従来の技術及び発明が解決しようとする課題】
【０００３】
近年、磁気ヘッド、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系の非晶質磁性合金はＣｏ系よりも安価ではあるが、一般的に高周波領域においてコア損失が大きく、透磁率も低いという欠点があった。さらに飽和磁歪も大きいという欠点があった。
【０００４】
また、従来のＦｅ系の非晶質磁性合金としてＦｅ−Ｂ系のものが知られているが、一般にＢ（ホウ素）が高価であるため、Ｂを用いた軟磁性合金自体は高価になるという難点があった。
【０００５】
本願発明は、このような従来のＦｅ系非晶質磁性合金に代わる軟磁性材料であって、しかも飽和磁歪および鉄損が小さく、かつ、低コストである新規なＦｅ基軟磁性合金を提供することを目的とする。
【課題を解決するための手段】
【０００６】
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の結果、Ｆｅ−Ｐ系Ｆｅ基軟磁性合金に特定の元素Ｍ、特にＺｒを添加した場合、優れた軟磁気特性を示し、例えば飽和磁歪が低いこと、またこのようなＦｅ−Ｐ−Ｍ系Ｆｅ基軟磁性合金にＣｕを添加した場合に優れた軟磁気特性を示すことを見い出し、本発明に至ったものである。
【０００７】
即ち、本発明のＦｅ基軟磁性合金は、一般式Ｆｅ100-a-b-c-dＰaＭbＭ'cＣｕd（式中、ＭはＺｒ、Ｈｆ、Ｎｂ、Ｍｏ、Ｔｉ、Ｍ ' はＣｏ、Ｎｉから選ばれる１種類以上の元素を表わす。ａ、ｂ、ｃ、ｄは原子％を示し、それぞれ、０≦ａ≦２５、３＜ｂ＜１２、０≦ｃ≦２０、０≦ｄ≦５を満たすものとする）で表わされるものであり、特にその組織の少なくとも３０％以上が微細な結晶粒で生成されていることが好ましく、更に結晶粒は主として鉄を主体としたｂｃｃ固溶体から成るものである。
【０００８】
Ｐ（リン）は本発明の合金の必須元素であり、Ｂ（ホウ素）等の高価な元素を使用せずとも、Ｐを特定量（０原子％を超え２５原子％以下）添加することにより、急冷直後の非晶質形成範囲の拡大することができる。そのため全体として合金製造コストを低減することができる。
【０００９】
本発明におけるＰの含有量ａは、０原子％を超え２５原子％以下、好ましくは１〜１５原子％、更に好ましくは２〜１２原子％である。
【００１０】
一方、本発明のＦｅ基軟磁性合金に添加される元素Ｍは、軟磁性の発現を阻害する、Ｆｅ−Ｐ系結晶の析出を抑制あるいはＦｅ−Ｐ系結晶の析出開始温度を高い温度に移動させる効果があると現時点では推察されるものであり、ＭとしてＺｒ、Ｈｆ、Ｎｂ、Ｍｏ、Ｔｉが用いられる。これら元素のうち特にＺｒが好適である。このような元素Ｍの添加は、更に結晶粒の微細化およびＦｅ−Ｐ系合金における非晶質形成能を向上させる効果がある。
【００１１】
本発明における元素Ｍの含有量ｂは、０原子％を超え１５原子％以下、好ましくは２〜１５原子％、更に好ましくは３〜１２原子％である
本発明のＦｅ基軟磁性合金に更に添加される元素Ｍ'は、Ｃｏ、Ｎｉから選ばれる１種類以上の元素であり、これらの元素はＦｅとの相互パラメータが負であるため、Ｆｅを主体とした固溶体中に固溶され、即ちα−Ｆｅ結晶構造のＦｅ原子の位置に置換される形で固溶されｂｃｃ結晶を安定化するものと考えられる。これにより、ｂｃｃ結晶の真性的な結晶磁気異方性あるいは磁歪定数の小さい結晶粒が作成されため優れた軟磁気特性が発現されるものと思われる。
【００１２】
本発明における元素Ｍ'の含有量ｃは、０原子％を超え２０原子％以下、好ましくは１〜１５原子％である。
【００１３】
本発明のＦｅ基軟磁性合金においてＣｕは、非晶質を熱処理することにより得られる結晶粒の微細化に寄与する。また、結晶粒の微細化に伴い実効的な磁気異方性エネルギーが結晶粒の持つ真性的な結晶磁気異方性エネルギーよりも小さくなると考えられるので磁気特性も改善される。但し、Ｃｕの含有量を５原子％より多くすると急冷直後の合金は脆化してしまい合金製造の面から好ましくない。従って、本発明におけるＣｕの含有量ｄは０原子％以上５原子％以下、好ましくは０．５〜３原子％が好ましい。
【００１４】
なお、本発明においてはＮ、Ｓ、Ｏなどの不可避的不純物を、目的とするＦｅ基軟磁性合金の特性が劣化しない程度に含有している合金も本発明に含むものである。
【００１５】
本発明のＦｅ基軟磁性合金は組織全体の少なくとも３０％以上（３０％〜１００％）が微細な結晶粒から成り、微結晶粒以外の部分は主として非晶質およびまたは上記微結晶粒以外の結晶質部分よりなる。本発明では、結晶粒の割合が上記範囲にあるとき優れた（軟）磁気特性を示す。なお、本発明では微細結晶粒の割合が実質的に１００％であっても優れた（軟）磁気特性を示す。本発明のＦｅ基軟磁性合金においては磁気特性の面から、組織全体の少なくとも５０％以上が微細な結晶粒から成ることが特に好ましく、７０％以上が微細な結晶粒から成ることが最も好ましい。
【００１６】
また本発明の合金に含まれれる微細結晶粒は主としてｂｃｃ構造を有しており、Ｆｅを主体としてＭ、Ｍ'および微量のＰが固溶していると考えられる。この微細結晶粒は１０００オングストローム以下、好ましくは５００オングストローム以下、更に好ましくは５０〜３００オングストロームの平均粒径を有している。本発明では平均粒径が１０００オングストローム以下であることにより、優れた磁気特性が得られるものである。
【００１７】
本発明のＦｅ基軟磁性合金について、飽和磁歪（λs）は＋１０×１０-6〜−５×１０-6の範囲にある。
【００１８】
なお、本発明において結晶粒の全体に占める割合は、実験的にＸ線回折法等により評価することができる。即ち、完全に結晶化した状態（Ｘ線回折強度が飽和した状態）のＸ線回折強度を基準とし、これに対する測定すべき磁性合金材料のＸ線回折強度の割合をもって実験的に評価することができる。また、結晶化に伴い生じるＸ線回折線のＸ線回折強度と、結晶化に伴い減少する非晶質特有のハローによるＸ線回折強度との比から評価することもできる。また、本発明において平均粒径はＸ線回折図形のｂｃｃピーク反射（１１０）を用い、シェラーの式 （ｔ＝０．９λ／βｃｏｓθ）によって導出したものである（カリティ著、新版 Ｘ線回折要論（Element of X-ray Diffraction (Second Edition）、B.D. Cullity）、 ９１〜９４頁)。
【００１９】
このような微細結晶粒を有する本発明のＦｅ基軟磁性合金は、一般にアモルファス合金を形成する方法により所定形状の合金を作成した後熱処理することにより得られる。即ち、例えば単ロール法、双ロール法等の液体急冷法、キャビテーション法、スパッタ法、蒸着法等の薄膜作製法あるいはメカニカルアロイングのような粉体作製法等により上記組成の急冷合金をリボン状、粉末状、ファイバ状、繊維状又は薄膜状等に形成した後、得られた急冷合金を必要に応じて所定の形状に加工した後、熱処理し、少なくとも一部、好ましくは試料全体の３０％以上を結晶化する。Ｆｅ基軟磁性合金の急冷直後の合金構造は、非晶質状態が望ましいが、熱処理後に軟磁気特性が得られる範囲内であれば一部結晶質が混在していてもよい。
【００２０】
通常は、単にロール法により急冷薄帯を作成し、これを巻磁心等の所定の形状にした後熱処理する。熱処理は真空中あるいはアルゴンガスもしくは窒素ガスなど不活性ガス、Ｈ2等の還元性ガスもしくは空気等の酸化性ガス雰囲気中で行なうことができる。好ましくは真空中あるいは不活性ガス雰囲気中で行なう。熱処理温度は約２００〜８００℃程度、好ましくは３００〜７００℃程度、更に好ましくは４００〜７００℃程度とする。熱処理時間は２４時間以内、好ましくは０．５〜５時間程度とすることが好ましい。また、熱処理は無磁場中でも、また磁場を印加して行なってもよい。磁場を印加することにより磁気異方性を付与することができる。
【００２１】
本発明のＦｅ基軟磁性合金の製造方法では上記の温度範囲で且つ上記範囲の熱処理時間で上記組成の非晶質合金を熱処理することにより本発明の特性に優れた軟磁性合金を得ることができる。
【００２２】
以下、実施例を挙げて更に説明する。
【実施例】
【００２３】
実施例１〜３
単ロール法を用いて、Ｆｅ、Ｐ、Ｚｒ、（Ｃｕ）を含有する溶湯からアルゴンガス１気圧雰囲気中で幅１．５mm程度、板厚約１５〜２４μｍの急冷薄帯を作成し試料とした。この試料を表１に示す熱処理温度で窒素ガスの存在下約１時間無磁場で熱処理した。この試料について、周波数１００ｋＨｚ及び最大磁束密度０．１Ｔにおける鉄損値Ｐｃ（W/Kg）、周波数１ＫＨｚ及び最大励磁磁界５ｍＯｅにおける実効透磁率μ（1KHz）、飽和磁化Ｂｓ（emu/g）、飽和磁歪λs（×１０-6）をそれぞれ測定した。得られた合金試料の合金組成及び合金中の微細結晶粒の含有量及び平均粒径を表１に示した。表１から明らかなように本実施例の合金中の微細結晶粒の含有量は全て６０％以上であった。なお組成はＩＣＰ分析によって決定した。
【００２４】
【表１】
また、磁性特性の測定結果を表２に示した。
【００２６】
比較例としてＦｅ76Ｓｉ10Ｂ14（比較例１、市販品）及びＦｅ78Ｓｉ9Ｂ13（比較例２、市販品）を実施例と同様の条件で急冷合金とし、更に熱処理した後の鉄損、透磁率、飽和磁化、飽和磁歪を併せて表２に示した。
【００２７】
【表２】
表２からも明らかなように本発明のＦｅ基軟磁性合金は、Ｆｅ−Ｂ系非晶質軟磁性合金とほぼ同様の鉄損、透磁率を有し、Ｆｅ−Ｂ系非晶質軟磁性合金に代る磁性材料として十分実用できることが示された。
【００２９】
図１に単ロール法により作製したＦｅ88Ｐ2Ｚｒ9Ｃｕ1（実施例３）の急冷合金を６２０℃、１時間アルゴン雰囲気中で熱処理した場合のＸ線回折パターンを示した。
【００３０】
図より、熱処理により得られた合金構造は主にｂｃｃ構造であることがわかる。
【発明の効果】
【００３１】
以上の実施例からも明らかなように、本発明のＦｅ基軟磁性合金はＦｅ−Ｐ系を基本として特定の元素、特にＺｒを添加するとともにＣｕを添加することにより、低鉄損、高透磁率、低飽和磁歪等の優れた磁性特性を示し、Ｆｅ−Ｂ系軟磁性合金に代る磁性材料として磁気ヘッド、高周波トランス、可飽和リアクトル、チョークコイル等に広く実用することができる。また、本発明のＦｅ基軟磁性合金はホウ素Ｂの代りにリンＰを用いることにより、低コストのＦｅ基軟磁性合金を得ることができる。
【図面の簡単な説明】
【００３２】
【図１】本発明のＦｅ基軟磁性合金の熱処理後Ｘ線回折パターンを示す図。[0001]
[Industrial application fields]
[0002]
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 and a method for producing the same.
[Prior art and problems to be solved by the invention]
[0003]
In recent years, Fe-based amorphous magnetic alloys having a high saturation magnetic flux density are widely known as magnetic core materials for magnetic heads, high-frequency transformers, saturable reactors, choke coils, and the like. However, Fe-based amorphous magnetic alloys are less expensive than Co-based materials, but generally have the disadvantages of high core loss and low permeability in the high-frequency region. Furthermore, there was a drawback that the saturation magnetostriction was also large.
[0004]
In addition, Fe-B alloys are known as conventional Fe-based amorphous magnetic alloys. However, since B (boron) is generally expensive, a soft magnetic alloy using B itself is expensive. There were difficulties.
[0005]
The present invention provides a novel Fe-based soft magnetic alloy that is a soft magnetic material that can replace such a conventional Fe-based amorphous magnetic alloy and that has low saturation magnetostriction and iron loss and is low in cost. For the purpose.
[Means for Solving the Problems]
[0006]
In order to achieve such an object, the present inventors have conducted extensive research on Fe-based soft magnetic alloys. As a result, when a specific element M, particularly Zr, is added to an Fe-P-based Fe-based soft magnetic alloy, the present inventors have excellent soft magnetic properties. It has been found that, for example, the saturation magnetostriction is low, and excellent soft magnetic properties are exhibited when Cu is added to such an Fe-PM-based Fe-based soft magnetic alloy. It is.
[0007]
That is, the Fe-based soft magnetic alloy of the present invention has the general formula Fe100-abc-dPaMbM'cCud (wherein M is one or more selected from Zr, Hf, Nb, Mo, Ti, and M ' are Co and Ni ). A, b, c and d represent atomic%, and 0 ≦ a ≦ 25, 3 <b <12 , 0 ≦ c ≦ 20, and 0 ≦ d ≦ 5, respectively. In particular, it is preferable that at least 30% or more of the structure is formed of fine crystal grains, and the crystal grains are mainly composed of a bcc solid solution mainly composed of iron.
[0008]
P (phosphorus) is an essential element of the alloy of the present invention, and by adding a specific amount (greater than 0 atomic% and 25 atomic% or less) of P without using an expensive element such as B (boron), The amorphous formation range immediately after quenching can be expanded. Therefore, the alloy manufacturing cost can be reduced as a whole.
[0009]
The content a of P in the present invention is more than 0 atomic% and 25 atomic% or less, preferably 1 to 15 atomic%, more preferably 2 to 12 atomic%.
[0010]
On the other hand, the element M added to the Fe-based soft magnetic alloy of the present invention inhibits the appearance of soft magnetism, suppresses the precipitation of Fe—P crystals, or moves the precipitation start temperature of the Fe—P crystals to a higher temperature. At present, it is assumed that there is an effect of the above, and M is Zr, Hf, Nb, Mo, or Ti . Of these elements, Zr is particularly preferred. Such addition of the element M has an effect of further refinement of crystal grains and improvement of amorphous forming ability in the Fe-P alloy.
[0011]
The content b of the element M in the present invention is more than 0 atomic% and not more than 15 atomic%, preferably 2 to 15 atomic%, more preferably 3 to 12 atomic%, and further added to the Fe-based soft magnetic alloy of the present invention. The element M ′ is one or more elements selected from Co and Ni . Since these elements have negative mutual parameters with Fe, they are dissolved in a solid solution mainly composed of Fe, that is, α It is considered that the bcc crystal is stabilized by solid solution in the form of substitution at the position of Fe atom in the -Fe crystal structure. As a result, a crystal grain having a small intrinsic magnetocrystalline anisotropy or magnetostriction constant of the bcc crystal is produced, so that it is considered that excellent soft magnetic characteristics are exhibited.
[0012]
The content c of the element M ′ in the present invention is more than 0 atomic% and 20 atomic% or less, preferably 1 to 15 atomic%.
[0013]
In the Fe-based soft magnetic alloy of the present invention, Cu contributes to refinement of crystal grains obtained by heat-treating the amorphous. Further, since the effective magnetic anisotropy energy is considered to be smaller than the intrinsic crystal magnetic anisotropy energy of the crystal grains as the crystal grains are refined, the magnetic characteristics are also improved. However, if the Cu content is more than 5 atomic%, the alloy immediately after quenching becomes brittle, which is not preferable from the viewpoint of alloy production. Therefore, the Cu content d in the present invention is 0 atomic% or more and 5 atomic% or less, preferably 0.5 to 3 atomic%.
[0014]
In the present invention, alloys containing unavoidable impurities such as N, S and O to the extent that the characteristics of the target Fe-based soft magnetic alloy are not deteriorated are also included in the present invention.
[0015]
In the Fe-based soft magnetic alloy of the present invention, at least 30% or more (30% to 100%) of the entire structure is composed of fine crystal grains, and the portion other than the microcrystal grains is mainly amorphous and / or other than the microcrystal grains. It consists of a crystalline part. In the present invention, excellent (soft) magnetic properties are exhibited when the proportion of crystal grains is in the above range. In the present invention, excellent (soft) magnetic properties are exhibited even when the proportion of fine crystal grains is substantially 100%. In the Fe-based soft magnetic alloy of the present invention, from the viewpoint of magnetic properties, it is particularly preferable that at least 50% or more of the entire structure is composed of fine crystal grains, and most preferably 70% or more is composed of fine crystal grains.
[0016]
Further, the fine crystal grains contained in the alloy of the present invention mainly have a bcc structure, and it is considered that M, M ′ and a small amount of P are mainly dissolved in Fe. The fine crystal grains have an average grain size of 1000 angstroms or less, preferably 500 angstroms or less, more preferably 50 to 300 angstroms. In the present invention, excellent magnetic properties can be obtained when the average particle size is 1000 angstroms or less.
[0017]
For the Fe-based soft magnetic alloy of the present invention, the saturation magnetostriction (λs) is in the range of + 10 × 10 −6 to −5 × 10 −6 .
[0018]
In the present invention, the ratio of the crystal grains to the whole can be experimentally evaluated by the X-ray diffraction method or the like. That is, it is possible to experimentally evaluate the ratio of the X-ray diffraction intensity of the magnetic alloy material to be measured with respect to the X-ray diffraction intensity in a completely crystallized state (a state where the X-ray diffraction intensity is saturated). it can. It can also be evaluated from the ratio between the X-ray diffraction intensity of an X-ray diffraction line generated along with crystallization and the X-ray diffraction intensity due to an amorphous halo that decreases along with crystallization. In the present invention, the average particle diameter is derived from Scherrer's equation (t = 0.9λ / βcosθ) using the bcc peak reflection (110) of the X-ray diffraction pattern (Karrit, new edition X-ray diffraction required). (Element of X-ray Diffraction (Second Edition), BD Cullity), pages 91-94).
[0019]
The Fe-based soft magnetic alloy of the present invention having such fine crystal grains is generally obtained by preparing an alloy having a predetermined shape by a method of forming an amorphous alloy and then performing a heat treatment. That is, for example, a rapidly quenched alloy having the above composition is formed into a ribbon shape by a liquid quenching method such as a single roll method or a twin roll method, a thin film production method such as a cavitation method, a sputtering method or a vapor deposition method, or a powder production method such as mechanical alloying. After forming into a powder form, fiber form, fiber form or thin film form, etc., the obtained quenched alloy is processed into a predetermined shape as necessary, and then heat-treated, and at least a part, preferably 30% of the entire sample The above is crystallized. The alloy structure immediately after quenching of the Fe-based soft magnetic alloy is preferably in an amorphous state, but a part of the crystalline structure may be mixed as long as soft magnetic properties are obtained after heat treatment.
[0020]
Usually, a quenching ribbon is prepared simply by a roll method, and after making it into a predetermined shape such as a wound core, heat treatment is performed. The heat treatment can be performed in a vacuum or in an inert gas atmosphere such as an inert gas such as argon gas or nitrogen gas, a reducing gas such as H2, or air. Preferably, it is performed in a vacuum or in an inert gas atmosphere. The heat treatment temperature is about 200 to 800 ° C, preferably about 300 to 700 ° C, more preferably about 400 to 700 ° C. The heat treatment time is within 24 hours, preferably about 0.5 to 5 hours. Further, the heat treatment may be performed in the absence of a magnetic field or by applying a magnetic field. Magnetic anisotropy can be imparted by applying a magnetic field.
[0021]
In the method for producing an Fe-based soft magnetic alloy of the present invention, a soft magnetic alloy having excellent characteristics of the present invention can be obtained by heat-treating an amorphous alloy having the above composition within the above-mentioned temperature range and within the above-mentioned heat treatment time. it can.
[0022]
Hereinafter, an example is given and it demonstrates further.
【Example】
[0023]
Examples 1-3
Using a single roll method, a quenching ribbon having a width of about 1.5 mm and a plate thickness of about 15 to 24 μm was prepared from a molten metal containing Fe, P, Zr, and (Cu) in an atmosphere of argon gas at 1 atmosphere and used as a sample. . This sample was heat-treated in the absence of a magnetic field at the heat treatment temperature shown in Table 1 for about 1 hour in the presence of nitrogen gas. For this sample, iron loss value Pc (W / Kg) at a frequency of 100 kHz and maximum magnetic flux density of 0.1 T, effective permeability μ (1 KHz) at a frequency of 1 KHz and a maximum excitation magnetic field of 5 mOe, saturation magnetization Bs (emu / g), saturation Magnetostriction λs (× 10 −6 ) was measured. Table 1 shows the alloy composition of the obtained alloy sample, the content of fine crystal grains in the alloy, and the average grain size. As is apparent from Table 1, the content of fine crystal grains in the alloy of this example was 60% or more. The composition was determined by ICP analysis.
[0024]
[Table 1]
The measurement results of the magnetic properties are shown in Table 2.
[0026]
As a comparative example, Fe 76 Si 10 B 14 (Comparative Example 1, commercially available product) and Fe 78 Si 9 B 13 (Comparative Example 2, commercially available product) were made into rapidly quenched alloys under the same conditions as in the examples, and further heat-treated iron. The loss, magnetic permeability, saturation magnetization, and saturation magnetostriction are shown together in Table 2.
[0027]
[Table 2]
As apparent from Table 2, the Fe-based soft magnetic alloy of the present invention has substantially the same iron loss and magnetic permeability as the Fe-B amorphous soft magnetic alloy, and Fe-B amorphous soft magnetic. It has been shown that it can be used practically as a magnetic material instead of alloys.
[0029]
FIG. 1 shows an X-ray diffraction pattern in the case where a quenched alloy of Fe 88 P 2 Zr 9 Cu 1 (Example 3) produced by the single roll method is heat-treated in an argon atmosphere at 620 ° C. for 1 hour.
[0030]
From the figure, it can be seen that the alloy structure obtained by the heat treatment is mainly a bcc structure.
【The invention's effect】
[0031]
As is clear from the above examples, the Fe-based soft magnetic alloy of the present invention is based on the Fe-P system, and by adding a specific element, particularly Zr, and adding Cu, low iron loss and high permeability. It exhibits excellent magnetic properties such as magnetic susceptibility and low saturation magnetostriction, and can be widely used in magnetic heads, high-frequency transformers, saturable reactors, choke coils, and the like as magnetic materials in place of Fe-B soft magnetic alloys. Further, the Fe-based soft magnetic alloy of the present invention can obtain a low-cost Fe-based soft magnetic alloy by using phosphorus P in place of boron B.
[Brief description of the drawings]
[0032]
FIG. 1 is a view showing an X-ray diffraction pattern after heat treatment of an Fe-based soft magnetic alloy of the present invention.
Claims (7)
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15833892A JP3623970B2 (en) | 1992-06-17 | 1992-06-17 | Fe-based soft magnetic alloy and manufacturing method |
| CA002098532A CA2098532A1 (en) | 1992-06-17 | 1993-06-16 | Fe-base soft magnetic alloy and process for making same |
| DE69313938T DE69313938T2 (en) | 1992-06-17 | 1993-06-17 | Soft magnetic iron-based alloy and manufacturing process |
| EP93304762A EP0575190B1 (en) | 1992-06-17 | 1993-06-17 | Fe-base soft magnetic alloy and process for making same |
| KR1019930011091A KR0131376B1 (en) | 1992-06-17 | 1993-06-17 | Fe-bane soft magnetic alloy & process for making same |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15833892A JP3623970B2 (en) | 1992-06-17 | 1992-06-17 | Fe-based soft magnetic alloy and manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH062076A JPH062076A (en) | 1994-01-11 |
| JP3623970B2 true JP3623970B2 (en) | 2005-02-23 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15833892A Expired - Lifetime JP3623970B2 (en) | 1992-06-17 | 1992-06-17 | Fe-based soft magnetic alloy and manufacturing method |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP0575190B1 (en) |
| JP (1) | JP3623970B2 (en) |
| KR (1) | KR0131376B1 (en) |
| CA (1) | CA2098532A1 (en) |
| DE (1) | DE69313938T2 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4444482A1 (en) * | 1994-12-14 | 1996-06-27 | Bosch Gmbh Robert | Soft magnetic material |
| KR100916602B1 (en) * | 2002-11-11 | 2009-09-11 | 엘지디스플레이 주식회사 | Liquid crystal display device with soda-lime glass and method for fabricating of the same |
| CN102360670B (en) * | 2011-10-24 | 2014-01-08 | 南京信息工程大学 | Composite material with ferrite magnetic layer and amorphous soft magnetic core as well as preparation method thereof |
| CN104962821B (en) * | 2015-05-26 | 2017-03-22 | 北京科技大学 | Machining method of wire printer yoke iron seat part |
| JP7106919B2 (en) * | 2018-03-23 | 2022-07-27 | Tdk株式会社 | Soft magnetic thin films, thin film inductors and magnetic products |
| CN110998918B (en) | 2018-04-10 | 2022-12-06 | 株式会社Lg新能源 | Method for preparing iron phosphide, positive electrode for lithium secondary battery comprising iron phosphide, and lithium secondary battery comprising said positive electrode |
| KR102229460B1 (en) * | 2018-04-10 | 2021-03-18 | 주식회사 엘지화학 | Method for manufacturing iron phosphide |
| WO2019198949A1 (en) * | 2018-04-10 | 2019-10-17 | 주식회사 엘지화학 | Method of producing iron phosphide, positive electrode for lithium secondary battery comprising iron phosphide, and lithium secondary battery comprising same |
| DE102019105215A1 (en) * | 2019-03-01 | 2020-09-03 | Vacuumschmelze Gmbh & Co. Kg | Alloy and method of making a magnetic core |
| KR20220038899A (en) * | 2020-09-21 | 2022-03-29 | 엘지전자 주식회사 | Alloy powder and method of fabrication the same |
| CN112176222B (en) * | 2020-10-30 | 2021-12-17 | 东北大学 | Ce-containing Fe-Ni permalloy material and preparation method thereof |
| CN117026103A (en) * | 2023-08-08 | 2023-11-10 | 中南大学 | Multi-component soft magnetic alloy with high strength, high resistance and low resistance temperature coefficient, and preparation method and application thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2713711B2 (en) * | 1987-11-17 | 1998-02-16 | 日立金属株式会社 | Security sensor marker |
| JPH04272159A (en) * | 1991-01-08 | 1992-09-28 | Sumitomo Metal Ind Ltd | Ferrous magnetic alloy |
-
1992
- 1992-06-17 JP JP15833892A patent/JP3623970B2/en not_active Expired - Lifetime
-
1993
- 1993-06-16 CA CA002098532A patent/CA2098532A1/en not_active Abandoned
- 1993-06-17 EP EP93304762A patent/EP0575190B1/en not_active Expired - Lifetime
- 1993-06-17 KR KR1019930011091A patent/KR0131376B1/en not_active IP Right Cessation
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Also Published As
| Publication number | Publication date |
|---|---|
| DE69313938T2 (en) | 1998-03-05 |
| JPH062076A (en) | 1994-01-11 |
| DE69313938D1 (en) | 1997-10-23 |
| EP0575190B1 (en) | 1997-09-17 |
| EP0575190A3 (en) | 1994-01-26 |
| KR0131376B1 (en) | 1998-04-24 |
| EP0575190A2 (en) | 1993-12-22 |
| KR940006157A (en) | 1994-03-23 |
| CA2098532A1 (en) | 1993-12-18 |
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