JP2004018889A - Elliptic nanocrystal magnetic material - Google Patents
Elliptic nanocrystal magnetic material Download PDFInfo
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【０００１】
【産業上の利用分野】
本発明は、特に良好な軟磁気特性を有するＦｅ基軟磁性合金粉末およびその製造方法に関する。
【０００２】
【従来の技術】
従来から、軟磁気特性に優れた合金としては、非晶質合金、ナノ結晶磁性材料が知られており、形状加工が容易な粉末への適応が図られている。たとえば、特開平５−３３５１２９、特開平１１−２６９５０９にて、Ｆｅ基軟磁性合金リボンを粉砕した軟磁性合金粉末粉末の提案がなされいるが、磁性体の形状が扁平ではあるが、一定な形状でないため、必ずしも磁気特性が満足できなかった。
【０００３】
一方、Ｆｅ−Ｓｉ−Ａｌ合金粉末としては、特開平１１−３２９８２にて磁性粉の形状のアスペクト比を上げた圧粉磁心の提案があるが、アトマイズ法で得られた磁性粉を更に、ボールミルを使用して扁平化処理をするため、この方法も一定な形状を得ることが困難であり、磁気特性に問題があった。
【０００４】
一方、扁平形状の金属粉末の製造方法としては、特開平７−１６６２１２で金属溶湯をアトマイズし、微細な液滴にし、金属回転冷却体に衝突させる方法の提案がなされており、磁性材料への適応も提案されてはいるが、必ずしも十分な磁気特性が得られていないのが、現状であった。
【０００５】
【発明が解決しようとする課題】
本発明は軟磁性合金粉末の磁気特性向上、その中でも特に、ナノ結晶磁性粉末、非晶質磁性粉末の磁気特性向上することを課題とする。
【０００６】
【課題を解決するための手段】
本発明は、ナノ結晶磁性粉末および非晶質磁性粉末の磁性粉の形状に関して、鋭意検討した結果、磁性粉の楕円状の形状が磁気特性の向上の効果があることを見出し、本発明に到達した。
【０００７】
すなわち、本発明は、構造がナノ結晶磁性材料、非晶質磁性材料であって、形状が楕円状であり、最大厚みが５ミクロン以下、長径が２０〜５００ミクロン、短径が１０〜２００ミクロンであり、縦径／横径＝１．０〜４．０であることを特徴とし、保磁力、飽和磁化に代表される軟磁気特性が優れた磁性粉である。
【０００８】
本発明に用いられる磁性粉の形状は、丸みを帯びた楕円状であって、角張った形状では無い。その寸法は長径方向の寸法が２０〜５００ミクロン、短径方向の寸法が１０〜２００ミクロン、長径／短径＝１．０〜４．０であって、厚みが５ミクロン以下のものが良い。
【０００９】
本発明に用いられるナノ結晶磁性材料は組織が粒径１００ｎｍ以下のナノ結晶粒を主成分とする磁性材料であり、非晶質合金を結晶温度以下で熱処理し、ナノ結晶粒を析出させることで得られる。ナノ結晶磁性材料の組成としては、ナノ結晶磁性材料として代表的なＦｅ−Ｃｕ−Ｎｂ−Ｓｉ−Ｂでもよいが、最も望ましくは、一般式（Ｆｅ１−ｘＭｘ）１００−ａ−ｂ−ｃ−ｄＳｉａＡｌｂＢｃＭ’ｄ（式中、ＭはＣｏ及び／又はＮｉ、Ｍ’はＮｂ、Ｍｏ、Ｚｒ、Ｗ、Ｔａ、Ｈｆ、Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｙ、Ｐｄ、Ｒｕ、Ｇａ、Ｇｅ、Ｃ、Ｐから選ばれる１種類以上の元素を表わす。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≦ｄ≦１０を満たすものとする）で表わされる組成が望ましい。
【００１０】
一方、同じく本発明に用いられる非晶質磁性材料は、熱処理後も非晶質構造を維持しており、非晶質磁性材料の組成としては、一般式（Ｆｅ１−ｘＭｘ）１００−ａ−ｂ−ｃＳｉａＢｂＭ’ｃ（式中、ＭはＣｏ及び／又はＮｉ、Ｍ’はＮｂ、Ｍｏ、Ｚｒ、Ｗ、Ｔａ、Ｈｆ、Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｙ、Ｐｄ、Ｒｕ、Ｇａ、Ｇｅ、Ｃ、Ｐから選ばれる１種類以上の元素を表わす。ｘは原子比を、ａ、ｂ、ｃは原子％を示し、それぞれ０≦ｘ＜１、０≦ａ≦２４、４≦ｂ≦３０、０≦ｃ≦１０を満たすものとする）が望ましい。
【００１１】
【発明の実施の形態】
本発明に用いられる磁性粉の形状は、丸みを帯びた楕円状であって、角張った形状では無い。その寸法は長径方向の寸法が２０〜５００ミクロン、短径方向の寸法が１０〜２００ミクロン、長径／短径＝１．０〜４．０であって、厚みが５ミクロン以下のものが良い。更に望ましくは、寸法は長径方向の寸法が５０〜２００ミクロン、短径方向の寸法が１５〜６０ミクロン、長径／短径＝１．３〜３．５であって、厚みが３ミクロン以下のものが好ましい。
【００１２】
本発明の磁性粉の製造方法であるが、特開平７−１６６２１２に基づいた方法で作製された。すなわち、磁性粉組成の合金を高周波溶解炉で溶湯とし、溶解炉の底に取り付けたノズルを通して溶湯を流下させ、ノズル先に取り付けたガスアトマイズ部より高圧ガスで溶湯を微粒化し、更にこの微粒化させた溶湯を金属の回転冷却体に衝突させ、楕円状扁平磁性粉を作製する。この時、合金の組成により溶湯の粘度が変化し、粘度が高すぎると、粒径が大きくなりすぎて、前記形状の楕円状扁平磁性粉が得られ無い。また、粘度が低すぎると、粒径が小さくなりすぎて、前記形状の楕円状扁平磁性粉が得られ無い。前記形状の楕円状扁平磁性粉を得るのに最も適した組成は、（Ｆｅ１−ｘＭｘ）１００−ａ−ｂ−ｃ−ｄＳｉａＡｌｂＢｃＭ’ｄ（式中、ＭはＣｏ及び／又はＮｉ、Ｍ’はＮｂ、Ｍｏ、Ｚｒ、Ｗ、Ｔａ、Ｈｆ、Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｙ、Ｐｄ、Ｒｕ、Ｇａ、Ｇｅ、Ｃ、Ｐから選ばれる１種類以上の元素を表わす。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≦ｄ≦１０を満たすものとする）で表される組成、または、一般式（Ｆｅ１−ｘＭｘ）１００−ａ−ｂ−ｃＳｉａＢｂＭ’ｃ（式中、ＭはＣｏ及び／又はＮｉ、Ｍ’はＮｂ、Ｍｏ、Ｚｒ、Ｗ、Ｔａ、Ｈｆ、Ｔｉ、Ｖ、Ｃｒ、Ｍｎ、Ｙ、Ｐｄ、Ｒｕ、Ｇａ、Ｇｅ、Ｃ、Ｐから選ばれる１種類以上の元素を表わす。ｘは原子比を、ａ、ｂ、ｃは原子％を示し、それぞれ０≦ｘ＜１、０≦ａ≦２４、４≦ｂ≦３０、０≦ｃ≦１０を満たすものとする）で表される組成であった。
【００１３】
軟磁気特性向上のためには、磁性粉の１００％が楕円状偏平磁性粉であることが望ましいが、角張った燐片状の形状の磁性粉や球状の磁性粉など楕円状磁性粉異なる形状の磁性粉との混合物でも良い。
【００１４】
【実施例】（実施例１） Ｆｅ６６Ｎｉ４Ｓｉ１４Ｂ９Ａｌ４Ｎｂ３の合金を高周波溶解炉で１３００℃の溶湯とし、溶解炉の底に取り付けたノズルを通して溶湯を流下させ、ノズル先に取り付けたガスアトマイズ部より７５ｋｇ／ｃｍ２の高圧ガスで溶湯を微粒化し、更にこの微粒化させた溶湯をロール径１９０ｍｍ、円錐角度８０度、回転数７２００ｒｐｍの回転冷却体に衝突させ、Ｆｅ６６Ｎｉ４Ｓｉ１４Ｂ９Ａｌ４Ｎｂ３（ａｔ％）の組成を有する長径２００ミクロン、短径６０ミクロン、厚み２ミクロンの楕円状扁平磁性粉を作製した。作製した磁性粉を５５０℃で１時間、窒素ガス雰囲気中で熱処理した。図１、図２に作製した磁性粉の熱処理前後のＸ線回折の結果を示す。図１より熱処理前の磁性粉は典型的な非晶質のハローパターンを示し、完全な非晶質であることが明らかになった。また図２より熱処理後の磁性粉はナノ結晶化しており、ピーク幅よりほぼ２０ｎｍのナノ結晶が析出していることが明らかになった。図３に熱処理後の楕円状扁平ナノ結晶磁性粉の電子顕微鏡（ＳＥＭ）写真を示す。
【００１５】
得られたナノ結晶磁性粉の保磁力（Ｈｃ）、飽和磁化（Ｍｓ）の磁化測定を行なった。表１に測定結果を示す。なお、保磁力（Ｈｃ）、飽和磁化（Ｍｓ）の測定は振動試料型磁力計にて行なった。本発明の楕円状扁平磁性粉は優れた軟磁気特性を示していることがわかる。
（比較例１）実施例１と同一組成であり片ロール法で作製されたリボンを粉砕して得られた燐片状磁性粉の磁化測定結果を比較例１として表１に示す。実施例１と比べ、保磁力、飽和磁化特性に劣っていることがわかる。
【００１６】
（実施例２）実施例１と同様に合金を高周波溶解炉で１３００℃の溶湯とし、溶解炉の底に取り付けたノズルを通して溶湯を流下させ、ノズル先に取り付けたガスアトマイズ部より７５ｋｇ／ｃｍ２の高圧ガスで溶湯を微粒化し、更にこの微粒化させた溶湯をロール径１９０ｍｍ、円錐角度８０度、回転数７２００ｒｐｍの回転冷却体に衝突させ、Ｃｏ６６Ｆｅ４Ｎｉ１Ｂ１４Ｓｉ１５（ａｔ％）の組成を有する長径５０ミクロン、短径３０ミクロン、厚み３ミクロンの楕円状扁平磁性粉を作製した。作製した磁性粉を３８０℃で１時間、窒素ガス雰囲気中で熱処理した。図４、図５に作製した磁性粉の熱処理前後のＸ線回折の結果を示す。図４、図５より熱処理前の磁性粉は典型的な非晶質のハローパターンを示し、熱処理前後に拘わらず、完全な非晶質であることが明らかになった。
【００１７】
得られた非晶質磁性粉の保磁力（Ｈｃ）、飽和磁化（Ｍｓ）の磁化測定を行なった。表１に測定結果を併せて示す。本発明の非晶質楕円状扁平磁性粉は優れた軟磁気特性を示していることがわかる。
（比較例２）比較例１と同様、実施例２と同一組成のリボンを粉砕し、燐片型の磁性粉の測定結果を比較例２として表１に示す。実施例２と比べ、保磁力、飽和磁化特性に劣っていることがわかる。
（実施例３） 実施例１と同様に合金を高周波溶解炉で１３００℃の溶湯とし、溶解炉の底に取り付けたノズルを通して溶湯を流下させ、ノズル先に取り付けたガスアトマイズ部より７５ｋｇ／ｃｍ２の高圧ガスで溶湯を微粒化し、更にこの微粒化させた溶湯をロール径１９０ｍｍ、円錐角度８０度、回転数７２００ｒｐｍの回転冷却体に衝突させ、Ｆｅ７８Ｓｉ９Ｂ１２（ａｔ％）の組成を有する長径１５０ミクロン、短径６０ミクロン、厚み２ミクロンの楕円状扁平磁性粉を作製した。作製した磁性粉を４００℃で１時間、窒素ガス雰囲気中で熱処理した。作製した磁性粉の熱処理前後のＸ線回折を測定した結果、実施例２の場合と同様に、熱処理前の磁性粉は典型的な非晶質のハローパターンを示し、熱処理前後に拘わらず、完全な非晶質であることが明らかになった。
【００１８】
得られた非晶質磁性粉の保磁力（Ｈｃ）、飽和磁化（Ｍｓ）の磁化測定を行なった。表１に測定結果を併せて示す。本発明の楕円状扁平非晶質磁性粉は優れた軟磁気特性を示していることがわかる。
（比較例３） 比較例１と同様、実施例３と同一組成のリボンを粉砕し、燐片型の磁性粉の測定結果を比較例３として表１に示す。実施例３と比べ、保磁力、飽和磁化特性に劣っていることがわかる。
【００１９】
【表１】
【発明の効果】
本発明は軟磁性合金粉末を楕円状偏平ナノ結晶磁性粉とすることにより、優れた磁気特性を有するナノ結晶磁性粉末、非晶質磁性粉末を提供することができた。
【図面の簡単な説明】
【図１】本発明に係る熱処理前の楕円状扁平ナノ結晶磁性粉のＸ線回折図形である。
【図２】本発明に係る熱処理後の楕円状扁平ナノ結晶軟磁性合金のＸ線回折図形である。
【図３】本発明に係る熱処理後の楕円状扁平ナノ結晶軟磁性合金の電子顕微鏡（ＳＥＭ）写真である。
【図４】本発明に係る熱処理前の楕円状扁平非晶質磁性粉のＸ線回折図形である。
【図５】本発明に係る熱処理後の楕円状扁平非晶質軟磁性合金のＸ線回折図形である。[0001]
[Industrial applications]
The present invention relates to an Fe-based soft magnetic alloy powder having particularly good soft magnetic properties and a method for producing the same.
[0002]
[Prior art]
Conventionally, amorphous alloys and nanocrystalline magnetic materials have been known as alloys having excellent soft magnetic properties, and their application to powders that can be easily processed has been attempted. For example, in Japanese Patent Application Laid-Open Nos. Hei 5-335129 and Hei 11-269509, soft magnetic alloy powders obtained by pulverizing an Fe-based soft magnetic alloy ribbon are proposed. Therefore, the magnetic properties could not always be satisfied.
[0003]
On the other hand, as an Fe-Si-Al alloy powder, there is a proposal in JP-A-11-32982 of a dust core with an increased aspect ratio of the shape of the magnetic powder. However, the magnetic powder obtained by the atomizing method is further subjected to ball milling. In this method, it is difficult to obtain a uniform shape, and there is a problem in magnetic characteristics.
[0004]
On the other hand, as a method of manufacturing a flat metal powder, a method of atomizing a molten metal into fine droplets and colliding with a metal rotary cooling body has been proposed in JP-A-7-166212. Although adaptation has been proposed, at present, sufficient magnetic properties have not been obtained.
[0005]
[Problems to be solved by the invention]
An object of the present invention is to improve the magnetic properties of soft magnetic alloy powders, and particularly to improve the magnetic properties of nanocrystalline magnetic powders and amorphous magnetic powders.
[0006]
[Means for Solving the Problems]
The present invention has conducted intensive studies on the shapes of the magnetic powders of the nanocrystalline magnetic powder and the amorphous magnetic powder, and has found that the elliptical shape of the magnetic powder has the effect of improving the magnetic properties, and has reached the present invention. did.
[0007]
That is, the present invention relates to a nanocrystalline magnetic material and an amorphous magnetic material having an elliptical shape, a maximum thickness of 5 microns or less, a major axis of 20 to 500 microns, and a minor axis of 10 to 200 microns. Wherein the ratio of longitudinal diameter / horizontal diameter is 1.0 to 4.0, and is a magnetic powder excellent in soft magnetic properties represented by coercive force and saturation magnetization.
[0008]
The shape of the magnetic powder used in the present invention is a rounded ellipse, not an angular shape. The size is preferably 20 to 500 microns in the major axis direction, 10 to 200 microns in the minor axis direction, 1.0 to 4.0 in the major axis / minor axis, and 5 microns or less in thickness.
[0009]
The nanocrystalline magnetic material used in the present invention is a magnetic material mainly composed of nanocrystalline grains having a grain size of 100 nm or less, and is obtained by heat-treating an amorphous alloy at a crystalline temperature or less to precipitate nanocrystalline grains. can get. The composition of the nanocrystalline magnetic material may be Fe—Cu—Nb—Si—B, which is a typical nanocrystalline magnetic material, but is most preferably the general formula (Fe1-xMx) 100-abc-dSiaAlbBcM. 'd (where M is Co and / or Ni, M' is Nb, Mo, Zr, W, Ta, Hf, Ti, V, Cr, Mn, Y, Pd, Ru, Ga, Ge, C, P X represents an atomic ratio, a, b, c, and d represent atomic%, and 0 ≦ x ≦ 0.5, 0 ≦ a ≦ 24, and 1 ≦ b ≦ 20, respectively. 4 ≦ c ≦ 30 and 0 ≦ d ≦ 10).
[0010]
On the other hand, the amorphous magnetic material also used in the present invention maintains an amorphous structure after the heat treatment, and the composition of the amorphous magnetic material is represented by the general formula (Fe1-xMx) 100-ab -CSiaBbM'c (where M is Co and / or Ni, M 'is Nb, Mo, Zr, W, Ta, Hf, Ti, V, Cr, Mn, Y, Pd, Ru, Ga, Ge, C , P. At least x represents an atomic ratio, a, b, and c represent atomic%, and 0 ≦ x <1, 0 ≦ a ≦ 24, 4 ≦ b ≦ 30, 0 ≦ c ≦ 10).
[0011]
BEST MODE FOR CARRYING OUT THE INVENTION
The shape of the magnetic powder used in the present invention is a rounded ellipse, not an angular shape. The size is preferably 20 to 500 microns in the major axis direction, 10 to 200 microns in the minor axis direction, 1.0 to 4.0 in the major axis / minor axis, and 5 microns or less in thickness. More preferably, the dimension in the major axis direction is 50 to 200 microns, the dimension in the minor axis direction is 15 to 60 microns, and the major axis / minor axis is 1.3 to 3.5, and the thickness is 3 microns or less. Is preferred.
[0012]
The method for producing the magnetic powder of the present invention was produced by a method based on JP-A-7-166212. That is, an alloy having a magnetic powder composition is melted in a high-frequency melting furnace, the molten metal is allowed to flow down through a nozzle attached to the bottom of the melting furnace, and the molten metal is atomized with a high-pressure gas from a gas atomizing section attached to the nozzle tip, and further atomized. The molten metal is made to collide with a metal rotating cooling body to produce elliptical flat magnetic powder. At this time, the viscosity of the molten metal changes depending on the composition of the alloy. If the viscosity is too high, the particle size becomes too large, and the elliptical flat magnetic powder having the above-mentioned shape cannot be obtained. On the other hand, if the viscosity is too low, the particle size becomes too small, and an elliptical flat magnetic powder having the above-mentioned shape cannot be obtained. The composition most suitable for obtaining the elliptical flat magnetic powder having the above-mentioned shape is (Fe1-xMx) 100-abc-dSiaAlbBcM'd (where M is Co and / or Ni, and M 'is Nb , Mo, Zr, W, Ta, Hf, Ti, V, Cr, Mn, Y, Pd, Ru, Ga, Ge, C, P, where x represents the atomic ratio and a , B, c, and d represent atomic% and satisfy 0 ≦ x ≦ 0.5, 0 ≦ a ≦ 24, 1 ≦ b ≦ 20, 4 ≦ c ≦ 30, and 0 ≦ d ≦ 10, respectively. Or a general formula (Fe1-xMx) 100-ab-cSiaBbM'c (where M is Co and / or Ni, M 'is Nb, Mo, Zr, W, Ta, Hf , Ti, V, Cr, Mn, Y, Pd, Ru, Ga, Ge, C, P. x represents an atomic ratio, a, b, and c represent atomic%, and satisfy 0 ≦ x <1, 0 ≦ a ≦ 24, 4 ≦ b ≦ 30, and 0 ≦ c ≦ 10, respectively. Composition.
[0013]
In order to improve the soft magnetic properties, it is desirable that 100% of the magnetic powder is elliptical flat magnetic powder, but it is preferable that the elliptical magnetic powder having a different shape such as angular flaky magnetic powder or spherical magnetic powder. A mixture with magnetic powder may be used.
[0014]
EXAMPLES Example 1 An alloy of Fe 66 Ni 4 Si 14 B 9 Al 4 Nb 3 was melted at 1300 ° C. in a high-frequency melting furnace, and the molten metal was allowed to flow down through a nozzle attached to the bottom of the melting furnace. The molten metal is atomized with a high-pressure gas of 75 kg / cm 2 from a gas atomizing part attached to the furnace, and the atomized molten metal is caused to collide with a rotating cooling body having a roll diameter of 190 mm, a cone angle of 80 degrees, and a rotation speed of 7,200 rpm, to obtain Fe 66 Ni 4 An elliptic flat magnetic powder having a composition of Si 14 B 9 Al 4 Nb 3 (at%) having a major axis of 200 μm, a minor axis of 60 μm, and a thickness of 2 μm was prepared. The produced magnetic powder was heat-treated at 550 ° C. for 1 hour in a nitrogen gas atmosphere. FIGS. 1 and 2 show the results of X-ray diffraction before and after the heat treatment of the prepared magnetic powder. FIG. 1 shows that the magnetic powder before the heat treatment showed a typical amorphous halo pattern and was completely amorphous. FIG. 2 also revealed that the magnetic powder after the heat treatment was nanocrystallized, and nanocrystals having a peak width of about 20 nm were precipitated. FIG. 3 shows an electron microscope (SEM) photograph of the elliptical flat nanocrystalline magnetic powder after the heat treatment.
[0015]
The coercive force (Hc) and saturation magnetization (Ms) of the obtained nanocrystalline magnetic powder were measured. Table 1 shows the measurement results. The coercive force (Hc) and the saturation magnetization (Ms) were measured using a vibrating sample magnetometer. It can be seen that the elliptical flat magnetic powder of the present invention has excellent soft magnetic properties.
Comparative Example 1 Table 1 shows the results of magnetization measurement of flaky magnetic powder obtained by pulverizing a ribbon produced by the one-roll method and having the same composition as in Example 1. It can be seen that the coercive force and the saturation magnetization characteristics are inferior to Example 1.
[0016]
(Example 2) In the same manner as in Example 1, the alloy was melted at 1300 ° C in a high-frequency melting furnace, the molten metal was allowed to flow down through a nozzle attached to the bottom of the melting furnace, and a high pressure of 75 kg / cm2 was applied from a gas atomizing section attached to the nozzle tip. The melt is atomized by gas, and the atomized melt is impinged on a rotary cooling body having a roll diameter of 190 mm, a cone angle of 80 degrees, and a rotation speed of 7,200 rpm, to obtain Co 66 Fe 4 Ni 1 B 14 Si 15 (at%). An elliptical flat magnetic powder having a composition having a major axis of 50 microns, a minor axis of 30 microns and a thickness of 3 microns was prepared. The produced magnetic powder was heat-treated at 380 ° C. for 1 hour in a nitrogen gas atmosphere. 4 and 5 show the results of X-ray diffraction before and after the heat treatment of the prepared magnetic powder. 4 and 5, the magnetic powder before the heat treatment showed a typical amorphous halo pattern, and it became clear that the magnetic powder was completely amorphous before and after the heat treatment.
[0017]
The coercive force (Hc) and saturation magnetization (Ms) of the obtained amorphous magnetic powder were measured. Table 1 also shows the measurement results. It can be seen that the amorphous elliptical flat magnetic powder of the present invention has excellent soft magnetic properties.
(Comparative Example 2) As in Comparative Example 1, a ribbon having the same composition as in Example 2 was pulverized, and the measurement results of the scale-shaped magnetic powder are shown in Table 1 as Comparative Example 2. It can be seen that the coercive force and the saturation magnetization characteristics are inferior to Example 2.
(Example 3) An alloy was melted at 1300 ° C in a high-frequency melting furnace in the same manner as in Example 1, and the molten metal was allowed to flow down through a nozzle attached to the bottom of the melting furnace, and a high pressure of 75 kg / cm2 was applied from a gas atomizing section attached to the nozzle tip. The melt is atomized by gas, and the atomized melt is collided with a rotary cooling body having a roll diameter of 190 mm, a cone angle of 80 degrees, and a rotation speed of 7,200 rpm, and a long diameter having a composition of Fe 78 Si 9 B 12 (at%). An elliptical flat magnetic powder having a size of 150 microns, a short diameter of 60 microns and a thickness of 2 microns was prepared. The produced magnetic powder was heat-treated at 400 ° C. for 1 hour in a nitrogen gas atmosphere. As a result of measuring the X-ray diffraction of the prepared magnetic powder before and after the heat treatment, the magnetic powder before the heat treatment showed a typical amorphous halo pattern as in the case of Example 2, and the magnetic powder before and after the heat treatment was completely removed. It became clear that it was amorphous.
[0018]
The coercive force (Hc) and saturation magnetization (Ms) of the obtained amorphous magnetic powder were measured. Table 1 also shows the measurement results. It can be seen that the elliptical flat amorphous magnetic powder of the present invention has excellent soft magnetic properties.
Comparative Example 3 As in Comparative Example 1, a ribbon having the same composition as in Example 3 was pulverized, and the measurement results of the scale-shaped magnetic powder are shown in Table 1 as Comparative Example 3. It can be seen that the coercive force and the saturation magnetization characteristics are inferior to Example 3.
[0019]
[Table 1]
【The invention's effect】
The present invention can provide a nanocrystalline magnetic powder and an amorphous magnetic powder having excellent magnetic properties by using a soft magnetic alloy powder as an elliptical flat nanocrystalline magnetic powder.
[Brief description of the drawings]
FIG. 1 is an X-ray diffraction pattern of an elliptical flat nanocrystalline magnetic powder before heat treatment according to the present invention.
FIG. 2 is an X-ray diffraction pattern of an elliptical flat nanocrystalline soft magnetic alloy after heat treatment according to the present invention.
FIG. 3 is an electron microscope (SEM) photograph of an elliptical flat nanocrystalline soft magnetic alloy after heat treatment according to the present invention.
FIG. 4 is an X-ray diffraction pattern of the elliptical flat amorphous magnetic powder before heat treatment according to the present invention.
FIG. 5 is an X-ray diffraction pattern of an elliptical flat amorphous soft magnetic alloy after heat treatment according to the present invention.
Claims (4)
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| JP2002172093A JP2004018889A (en) | 2002-06-12 | 2002-06-12 | Elliptic nanocrystal magnetic material |
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| JP2002172093A JP2004018889A (en) | 2002-06-12 | 2002-06-12 | Elliptic nanocrystal magnetic material |
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| WO2008007346A2 (en) * | 2006-07-12 | 2008-01-17 | Vacuumschmelze Gmbh & Co. Kg | Method for the production of powder composite cores and powder composite core |
| KR100795878B1 (en) * | 2006-10-16 | 2008-01-21 | 김준기 | A mulberry vinegar containing calcium bamboo salt and the method thereof |
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| WO2008007346A2 (en) * | 2006-07-12 | 2008-01-17 | Vacuumschmelze Gmbh & Co. Kg | Method for the production of powder composite cores and powder composite core |
| WO2008007346A3 (en) * | 2006-07-12 | 2008-03-13 | Vacuumschmelze Gmbh & Co Kg | Method for the production of powder composite cores and powder composite core |
| GB2454823A (en) * | 2006-07-12 | 2009-05-20 | Vacuumschmelze Gmbh & Co Kg | Method for the production of powder composite cores and powder composite core |
| GB2454823B (en) * | 2006-07-12 | 2012-03-14 | Vacuumschmelze Gmbh & Co Kg | Method for the production of powder composite cores and powder composite core |
| US8216393B2 (en) | 2006-07-12 | 2012-07-10 | Vacuumschmelze Gmbh & Co. Kg | Method for the production of powder composite cores and powder composite core |
| KR100795878B1 (en) * | 2006-10-16 | 2008-01-21 | 김준기 | A mulberry vinegar containing calcium bamboo salt and the method thereof |
| KR100814586B1 (en) * | 2007-01-02 | 2008-03-17 | 이영희 | Method for preparing vinerar using banana and apple |
| CN102360667A (en) * | 2011-10-24 | 2012-02-22 | 南京信息工程大学 | Amorphous nanocrystalline soft magnetic magneto-sensitive composite material for sensing and preparation method thereof |
| CN102360667B (en) * | 2011-10-24 | 2013-11-13 | 南京信息工程大学 | Amorphous nanocrystalline soft magnetic magneto-sensitive composite material for sensing and preparation method thereof |
| WO2016121950A1 (en) * | 2015-01-30 | 2016-08-04 | 株式会社村田製作所 | Magnetic powder and production method thereof, magnetic core and production method thereof, coil component and motor |
| JPWO2016121950A1 (en) * | 2015-01-30 | 2017-12-21 | 株式会社村田製作所 | Magnetic powder and manufacturing method thereof, magnetic core and manufacturing method thereof, coil component, and motor |
| US10767249B2 (en) | 2015-01-30 | 2020-09-08 | Murata Manufacturing Co., Ltd. | Magnetic powder and production method thereof, magnetic core and production method thereof, coil component and motor |
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