JP3558350B2 - Fe-based soft magnetic alloy and manufacturing method - Google Patents
Fe-based soft magnetic alloy and manufacturing method Download PDFInfo
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- JP3558350B2 JP3558350B2 JP31711292A JP31711292A JP3558350B2 JP 3558350 B2 JP3558350 B2 JP 3558350B2 JP 31711292 A JP31711292 A JP 31711292A JP 31711292 A JP31711292 A JP 31711292A JP 3558350 B2 JP3558350 B2 JP 3558350B2
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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
Description
【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基軟磁性合金及びその製造方法に関する。
【０００２】
【従来の技術及び発明が解決しようとする課題】
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、一般的にコア損失が大きく、透磁率も低い。さらに飽和磁歪も大きいためまだ磁気特性の面では十分とは言えない。
【０００３】
本願発明は、このような従来のＦｅ系非晶質磁性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。
【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の結果、Ｆｅ−Ｂ系Ｆｅ基軟磁性合金にＡｌ及び特定の元素Ｍ、特にＮｂ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−Ｂ−Ａｌ−Ｍ系Ｆｅ基軟磁性合金にリン（Ｐ）及び炭素（Ｃ）を添加した場合、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。
【０００５】
即ち、本発明のＦｅ基軟磁性合金は、（Ｆｅ1-xＡx）100-a-b-c-d-e-fＡｌaＭbＭ’cＢdＰeＣf（式中、ＡはＣｏ及び／又はＮｉ、ＭはＮｂ、Ｍｏ、Ｔａ、Ｚｒ、Ｖから選ばれる１種又は２種以上の元素を表わし、Ｍ'はＳｉ元素を表わす。ｘは０≦ｘ≦０．２、またａ、ｂ、ｃ、ｄ、ｅ、ｆは原子％を表わし、それぞれ、２．５≦ａ≦１０、３≦ｂ≦２０、０≦ｃ≦６、１≦ｄ≦９、２＜ｅ≦９、０．１≦ｆ≦５を満たし、ＰとＣの組成比ｅ／ｆ（原子比）が、１≦ｅ／ｆ≦４０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、更に結晶粒は鉄を主体としたｂｃｃ固溶体から成るものである。
【０００６】
本発明の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。
【０００７】
本発明のＦｅ基軟磁性合金において、Ｆｅはｘが０から０．２の範囲でＡ（Ｃｏ及び／又はＮｉ）で置換することができる。Ａは熱処理時に生成するＦｅを主体としたｂｃｃ結晶に固溶し、特にＣｏは飽和磁化、Ｎｉは結晶磁気異方性定数の改善に寄与する。本発明において、Ａの含有量（ＦｅとＡの合計を１とした場合のＡの割合）ｘが０．２より多いとｂｃｃ構造以外の生成相がみられ軟磁気特性が劣化する。このため、Ａの含有量ｘは、０．２以下であることが好ましい。さらに好ましくは、０．１以下である。
【０００８】
Ａｌは本発明の合金の必須元素であり、Ａｌを特定量（２．５原子％以上１０原子％以下）添加することにより、結晶磁気異方性の小さい軟磁性を示す結晶（Ｆｅ基ｂｃｃ固溶体）の結晶化温度（Ｔx1）と軟磁性を阻害する結晶（例えばＦｅ−Ｂ系結晶）の結晶化温度（Ｔx2）との温度差（△Ｔ）を大きくすることができ、熱処理時のＦｅ−Ｂ系結晶等の生成を抑制すると共に、比較的低い温度の熱処理で軟磁気特性を導出することができる。ＡｌはＮｉ（Ｃｏ）と同様にＦｅとの相互パラメータが負であるため、Ａｌを添加することにより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。また、Ａｌは熱処理により生成した析出結晶粒を微細化するものと推定される。以上のことから、本合金系においてＡｌ添加によって結晶磁気異方性の小さい微細結晶粒が選択的に生成されるので、これによって優れた軟磁気特性が発現すると思われる。
【０００９】
本発明においてＡｌの含有量ａは、好ましくは２．５〜１０原子％、更に好ましくは３〜６原子％である。３〜６原子％の範囲において、特に鉄損の小さい合金を得ることができる。
【００１０】
本発明における元素ＭはＮｂ、Ｍｏ、Ｔａ、Ｚｒ、Ｖから選ばれる１種又は２種以上の元素で、軟磁性の発現を阻害する、Ｆｅ−Ｂ、Ｆｅ−Ｐ系結晶の析出を抑制あるいは析出開始温度を高い温度に移動させる効果があると推察される。さらに、元素Ｍの添加は結晶粒の微細化のみならず非晶質形成能を向上させる効果がある。また、ＭとしてはＮｂが好適である。
【００１１】
本発明における元素Ｍの含有量ｂは、３原子％から２０原子％、好ましくは３〜１５原子％、更に好ましくは５〜１０原子％である。
【００１２】
本発明における元素Ｍ’は、Ｓｉ元素で、Ｆｅと固溶体を形成し、６原子％以下添加することにより軟磁性を向上させる。
【００１３】
ホウ素（Ｂ）は本発明の合金の必須元素であり非晶質形成に寄与し、Ｂが９原子％を超えると磁気特性が良好な熱処理条件では磁歪が大きくなる。よって、好ましい範囲は１原子％〜９原子％、最も好ましい範囲は２原子％〜８原子％である。
【００１４】
本発明においてリン（Ｐ）と炭素（Ｃ）はそれぞれ必須元素であり、元素Ｐは非晶質形成範囲の拡大に寄与する。またＣは結晶粒を微細化し軟磁気特性を向上させる。但しＰが９原子％を超えると熱処理によりＦｅ−Ｐ系結晶が析出し軟磁性の発現を阻害するので、Ｐの含有量ｅは２原子％を超え９原子％以下、好ましくは２．５原子％〜９原子％、更に好ましくは３原子％〜７原子％である。
【００１５】
またＣが５原子％を超えると熱処理によりＦｅ−Ｃが生成しやすくなり軟磁性の発現を阻害するので、Ｃの含有量ｆは、０．１原子％〜５原子であり、好ましくは、０．５原子％〜３原子％、更に好ましくは０．５原子％〜２原子％である。
【００１６】
また本発明の合金において、元素Ｍ、Ｐ及びＣはともに耐食性を向上させる働きがある。このような効果を得るために、これら元素の含有量合計の好ましい範囲は、５．１原子％＜ｂ＋ｅ＋ｆ≦３４原子％であり、更に好ましくは１０原子％＜ｂ＋ｅ＋ｆ≦３４原子％である。
【００１７】
更に本発明の合金では、ＰとＣとを複合添加することにより、保磁力の低減および軟磁気特性（鉄損および透磁率）が改善される。ＰとＣの組成比率（原子比ｅ／ｆ）において、好ましい範囲は、１≦ｅ／ｆ≦４０、好ましくは２＜ｅ／ｆ＜２０であり、最も好ましい範囲は、２≦ｅ／ｆ≦７である。
【００１８】
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。
【００１９】
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。
【００２０】
また本発明の合金に含まれる微細結晶粒は主としてｂｃｃ構造を有しており、Ｆｅ及びＡｌを主体としてＭ、Ｍ'および微量のＢ、Ｐ、Ｃ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。
【００２１】
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、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ができる。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)。
【００２２】
更に本発明のＦｅ基軟磁性合金は、磁歪が小さく、磁束密度が大きく、好適には飽和磁歪λsが−５×１０-6≦λs≦＋１０×１０-6の範囲にあるものであり、飽和磁束密度Ｂsが好ましくは１．２以上のものである。
【００２３】
このような本発明のＦｅ基軟磁性合金は、一般にアモルファス合金を形成する液体急冷法、（例えば単ロール法）、キャビテーション法、薄膜作製法（例えばスパッタ法、メッキ法または蒸着法等）あるいは粉体作製法（例えばメカニカルアロイング法）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％以上を結晶化することにより得られる。なおこの急冷合金は非晶質でもよく、あるいは非晶質と結晶質が混在する合金でもよい。
【００２４】
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等の不活性ガス、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。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、更に好ましくは０．５〜３時間とする。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。本発明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または一部結晶質の混合した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。
【００２５】
本発明合金の用途は磁気ヘッド、高周波トランス、可飽和リアクトル、チョークコイル等の材料として広く使用することができる。
【００２６】
【実施例】
以下、実施例を挙げて更に説明する。
【００２７】
実施例１及び２、比較例
単ロール法を用いて、Ｆｅ、Ａｌ、Ｎｂ、Ｂ、Ｐ、Ｃを含有する溶湯からアルゴンガス１気圧雰囲気中で幅５mm程度、板厚約２０μｍの急冷薄帯を作成し試料とした。この試料を窒素ガスの存在下６００℃で約１時間無磁場で熱処理した。
【００２８】
得られたＦｅ基軟磁性合金の合金組成を表１に示した。また、表２に得られたＦｅ基軟磁性合金の飽和磁束密度Ｂｓ（Ｔ）、保磁力Ｈｃ（mOe）、周波数１ＫＨｚ及び最大励磁磁界５ｍＯｅでの実効透磁率μ（1KHz）、周波数１００ｋＨｚ及び最大磁束密度０．１Ｔでの鉄損値Ｐｃ（W/Kg)、飽和磁歪λs（×１０-6）を示した。なお組成はＣ以外の元素はＩＣＰ分析によって決定し、Ｃは二酸化炭素に変換し、赤外線検出器で検出し決定した。
【００２９】
なお、実施例１及び２において、α−Ｆｅ（１１０）の回折強度と非晶質の回折強度から求めた熱処理後の試料の結晶化度はいずれも８０％以上であった。またそれら結晶粒の平均粒径は実施例１の合金では１００オングストローム、実施例２の合金では１２０オングストロームであった。
【００３０】
また比較例としてＦｅ78Ｓｉ9Ｂ13（比較例１、市販品）の特性を併せて表２に示した。
【００３１】
【発明の効果】
以上の実施例からも明らかなように、本発明によればＦｅ−Ｂ系合金にＡｌ及び特定の元素を添加するとともに特定量のリン及び炭素を添加することにより、優れた軟磁性特性のＦｅ基軟磁性合金を提供できる。[0001]
[Industrial applications]
The present invention relates to an Fe-based soft magnetic alloy, and more particularly to an Fe-based soft magnetic alloy having good soft magnetic properties and a method for producing the same.
[0002]
Problems to be solved by the prior art and the invention
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 alloys, but generally have large core loss and low magnetic permeability. Furthermore, since the saturation magnetostriction is large, it cannot be said that the magnetic properties are still sufficient.
[0003]
An object of the present invention is to provide a novel Fe-based soft magnetic alloy which is a soft magnetic material that replaces such conventional Fe-based amorphous magnetism, has a low saturation magnetostriction and iron loss, and is low in cost. With the goal.
[0004]
[Means for Solving the Problems]
In order to achieve such an object, the present inventors have conducted intensive studies on Fe-based soft magnetic alloys. As a result, when adding Al and a specific element M, particularly Nb, to an Fe-B-based Fe-based soft magnetic alloy, excellent results were obtained. It exhibits soft magnetic properties, for example, low saturation magnetostriction, and excellent soft magnetic properties when phosphorus (P) and carbon (C) are added to such Fe-B-Al-M-based Fe-based soft magnetic alloy. Have been found, and the present invention has been achieved.
[0005]
That, Fe-based soft magnetic alloy of the present invention, (Fe 1-x A x ) 100-abcdef Al a M b M 'c B d P e C f ( wherein, A is Co and / or Ni, M is Represents one or more elements selected from Nb, Mo, Ta, Zr, and V , M ′ represents a Si element , x is 0 ≦ x ≦ 0.2, and a, b, c, d, e and f represent atomic%, and 2.5 ≦ a ≦ 10 , 3 ≦ b ≦ 20, 0 ≦ c ≦ 6, 1 ≦ d ≦ 9, 2 <e ≦ 9, and 0.1 ≦ f ≦ 5, respectively. Is satisfied, and the composition ratio e / f (atomic ratio) of P and C satisfies 1 ≦ e / f ≦ 40). In particular, at least 30% or more of the structure has fine crystals. Preferably, the grains are made of grains, and the grains are made of a bcc solid solution mainly composed of iron .
[0006]
The alloy structure of the Fe-based soft magnetic alloy of the present invention immediately after quenching is desirably in an amorphous state, but may be partially crystalline as long as soft magnetic properties can be obtained after heat treatment.
[0007]
In the Fe-based soft magnetic alloy of the present invention, Fe can be substituted with A (Co and / or Ni) when x is in the range of 0 to 0.2. A forms a solid solution in the bcc crystal mainly composed of Fe generated during the heat treatment, and particularly Co contributes to the saturation magnetization and Ni contributes to the improvement of the crystal magnetic anisotropy constant. In the present invention, if the content of A (the ratio of A when the total of Fe and A is 1) x is more than 0.2, a generated phase other than the bcc structure is observed, and the soft magnetic properties are deteriorated. Therefore, the content x of A is preferably 0.2 or less. More preferably, it is 0.1 or less.
[0008]
Al is an essential element of the alloy of the present invention, and a crystal (Fe-based bcc solid solution) having a small magnetic anisotropy and exhibiting soft magnetism can be obtained by adding a specific amount of Al ( 2.5 at% to 10 at% ). ) And the crystallization temperature (Tx2) of a crystal that inhibits soft magnetism (eg, Fe—B-based crystal) (ΔT) can be increased. The formation of the B-based crystal and the like can be suppressed, and the soft magnetic characteristics can be derived by heat treatment at a relatively low temperature. Since Al has a negative mutual parameter with Fe similarly to Ni (Co), Al is dissolved in a solid solution mainly composed of Fe by adding Al, that is, at a position of Fe atom in the α-Fe crystal structure. It is dissolved in the form of being substituted and stabilizes the bcc crystal. Also, it is presumed that Al refines the precipitated crystal grains generated by the heat treatment. From the above, it is considered that, in the present alloy system, fine crystal grains with small crystal magnetic anisotropy are selectively generated by the addition of Al, whereby excellent soft magnetic properties are exhibited.
[0009]
In the present invention, the Al content a is preferably 2.5 to 10 atomic% , and more preferably 3 to 6 atomic%. In the range of 3 to 6 atomic%, an alloy having particularly small iron loss can be obtained.
[0010]
The element M in the present invention is one or two or more elements selected from Nb, Mo, Ta, Zr, and V, which inhibits the development of soft magnetism, suppresses the precipitation of Fe-B, Fe-P-based crystals, or It is presumed that there is an effect of moving the precipitation start temperature to a higher temperature. Further, the addition of the element M has the effect of improving the ability to form an amorphous phase as well as making the crystal grains finer. Also, M is preferably Nb.
[0011]
The content b of the element M in the present invention is 3 to 20 atomic%, preferably 3 to 15 atomic%, more preferably 5 to 10 atomic%.
[0012]
The element M ′ in the present invention is a Si element , forms a solid solution with Fe, and improves soft magnetism by adding 6 atomic% or less.
[0013]
Boron (B) is an essential element of the alloy of the present invention and contributes to the formation of an amorphous phase. When B exceeds 9 atomic%, magnetostriction increases under heat treatment conditions with good magnetic properties. Therefore, a preferable range is 1 to 9 atomic%, and a most preferable range is 2 to 8 atomic%.
[0014]
In the present invention, phosphorus (P) and carbon (C) are essential elements, respectively, and the element P contributes to expansion of an amorphous formation range. C refines crystal grains and improves soft magnetic properties. However, if P exceeds 9 atomic%, the heat treatment precipitates Fe-P-based crystals and inhibits the development of soft magnetism. Therefore, the P content e is more than 2 atomic% and 9 atomic% or less, preferably 2.5 atomic%. % To 9 at%, more preferably 3 to 7 at%.
[0015]
Further, when C exceeds 5 atomic%, Fe-C is easily generated by heat treatment and the development of soft magnetism is inhibited. Therefore, the content f of C is 0.1 to 5 atomic%, and preferably 0 to 0 atomic%. It is from 0.5 at% to 3 at%, more preferably from 0.5 at% to 2 at%.
[0016]
Further, in the alloy of the present invention, the elements M, P and C all have a function of improving the corrosion resistance. In order to obtain such effects, a preferable range of the total content of these elements is 5.1 atomic% <b + e + f ≦ 34 atomic%, and more preferably 10 atomic% <b + e + f ≦ 34 atomic%.
[0017]
Further, in the alloy of the present invention, coercive force is reduced and soft magnetic properties (iron loss and magnetic permeability) are improved by adding P and C in combination. In the composition ratio of P and C (atomic ratio e / f), a preferable range is 1 ≦ e / f ≦ 40, preferably 2 <e / f <20, and a most preferable range is 2 ≦ e / f ≦. 7
[0018]
In the present invention, an alloy containing unavoidable impurities such as N, S, and O to such an extent that desired characteristics are not deteriorated is also included in the present invention.
[0019]
In the Fe-based soft magnetic alloy of the present invention, at least 30% or more of the entire structure is composed of fine crystal grains, and portions other than the fine crystal grains are mainly composed of amorphous and / or crystalline portions other than the above-mentioned fine crystal grains. In the present invention, when the proportion of the crystal grains is in the above range, excellent (soft) magnetic properties are exhibited. In the present invention, excellent (soft) magnetic properties are exhibited even when the ratio 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 it is most preferable that 70% or more is composed of fine crystal grains.
[0020]
Further, the fine crystal grains contained in the alloy of the present invention mainly have a bcc structure, and it is considered that M and M 'and trace amounts of B, P and C mainly form a solid solution mainly of Fe and Al. The fine grains have an average particle size of less than 1000 angstroms, preferably less than 500 angstroms, more preferably 50-300 angstroms. In the present invention, when the average particle size is 1000 Å or less, excellent magnetic properties can be obtained.
[0021]
In the present invention, the ratio of the crystal grains to the whole can be experimentally evaluated by an X-ray diffraction method or the like. That is, it can be evaluated from the ratio of the X-ray diffraction intensity of the X-ray diffraction line generated due to the crystallization to the X-ray diffraction intensity due to the halo peculiar to the amorphous which decreases with the crystallization. In the present invention, the average particle diameter is derived by the Scherrer's formula (t = 0.9λ / βcosθ) using the bcc peak reflection (110) of the X-ray diffraction pattern. (Element of X-ray Diffraction (Second Edition), BD Cullity), pp. 91-94).
[0022]
Further, the Fe-based soft magnetic alloy of the present invention has a low magnetostriction and a high magnetic flux density, and preferably has a saturation magnetostriction λs in the range of −5 × 10 −6 ≦ λs ≦ + 10 × 10 −6 , The magnetic flux density Bs is preferably 1.2 or more.
[0023]
Such an Fe-based soft magnetic alloy of the present invention is generally prepared by a liquid quenching method for forming an amorphous alloy (for example, a single roll method), a cavitation method, a thin film forming method (for example, a sputtering method, a plating method or a vapor deposition method) or a powder. After the quenched alloy having the above composition is formed into a ribbon, powder, fiber, fiber, or thin film by a body manufacturing method (for example, mechanical alloying method) or the like, the obtained quenched alloy is optionally subjected to a predetermined method. After being processed into a shape, it is obtained by heat treatment to crystallize at least a part, preferably 30% or more of the whole sample. The quenched alloy may be amorphous or an alloy in which amorphous and crystalline are mixed.
[0024]
Normally, a quenched ribbon is simply prepared by a roll method, and is formed into a predetermined shape such as a wound core and then heat-treated. The heat treatment is performed in a vacuum or in an atmosphere of an inert gas such as argon gas or nitrogen gas, a reducing gas such as H 2, or an oxidizing gas such as air. Preferably, it is performed in a vacuum or an inert gas atmosphere. The heat treatment temperature is about 200 to 800 ° C, preferably about 300 to 700 ° C, and more preferably about 400 to 700 ° C. The heat treatment time is within 24 hours, preferably 0.5 to 5 hours, and more preferably 0.5 to 3 hours. The heat treatment may be performed in the absence of a magnetic field or by applying a magnetic field. In the present invention, a soft magnetic alloy having excellent characteristics of the present invention can be obtained by heat-treating an amorphous or partially crystalline mixed alloy having the above composition within the above-mentioned temperature range and within the above-mentioned heat treatment time. .
[0025]
The alloy of the present invention can be widely used as a material for magnetic heads, high frequency transformers, saturable reactors, choke coils, and the like.
[0026]
【Example】
Hereinafter, the present invention is further described with reference to examples.
[0027]
Examples 1 and 2, Comparative Example Using a single roll method, a quenched ribbon having a width of about 5 mm and a plate thickness of about 20 μm from a molten metal containing Fe, Al, Nb, B, P, and C in an atmosphere of argon gas at 1 atm. Was prepared as a sample. This sample was heat-treated in the presence of nitrogen gas at 600 ° C. for about 1 hour without a magnetic field.
[0028]
Table 1 shows the alloy composition of the obtained Fe-based soft magnetic alloy. Further, the saturation magnetic flux density Bs (T), coercive force Hc (mOe), effective magnetic permeability μ (1 KHz) at a frequency of 1 KHz and a maximum exciting magnetic field of 5 mOe, a frequency of 100 kHz and a maximum of the Fe-based soft magnetic alloy obtained in Table 2 were obtained. The iron loss value Pc (W / Kg) and the saturation magnetostriction λs (× 10 −6 ) at a magnetic flux density of 0.1 T are shown. The composition was determined by ICP analysis for elements other than C, and C was converted to carbon dioxide and detected and determined by an infrared detector.
[0029]
In Examples 1 and 2, the crystallinity of the sample after the heat treatment obtained from the diffraction intensity of α-Fe (110) and the diffraction intensity of amorphous was 80% or more. The average grain size of the crystal grains was 100 Å for the alloy of Example 1 and 120 Å for the alloy of Example 2.
[0030]
Table 2 also shows the characteristics of Fe 78 Si 9 B 13 (Comparative Example 1, commercially available product) as a comparative example.
[0031]
【The invention's effect】
As is apparent from the above examples, according to the present invention, by adding Al and a specific element to a Fe-B-based alloy and adding a specific amount of phosphorus and carbon, Fe having excellent soft magnetic properties can be obtained. A base soft magnetic alloy can be provided.
Claims (8)
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| JP31711292A JP3558350B2 (en) | 1992-11-26 | 1992-11-26 | Fe-based soft magnetic alloy and manufacturing method |
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| JP31711292A JP3558350B2 (en) | 1992-11-26 | 1992-11-26 | Fe-based soft magnetic alloy and manufacturing method |
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| JP3442375B2 (en) * | 2000-11-29 | 2003-09-02 | アルプス電気株式会社 | Amorphous soft magnetic alloy |
| KR100690281B1 (en) * | 2004-11-22 | 2007-03-09 | 경북대학교 산학협력단 | Fe-based bulk amorphous alloy compositions containing more than 5 elements and composites containing the amorphous phase |
| KR101633611B1 (en) * | 2014-12-05 | 2016-06-27 | 주식회사 포스코 | High silicon electrical steel sheet with superior magnetic properties, and method for fabricating the high silicon electrical steel |
| JP6451877B1 (en) * | 2018-01-12 | 2019-01-16 | Tdk株式会社 | Soft magnetic alloys and magnetic parts |
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