JPH0559409A - Production of soft magnetic powder - Google Patents
Production of soft magnetic powderInfo
- Publication number
- JPH0559409A JPH0559409A JP3248367A JP24836791A JPH0559409A JP H0559409 A JPH0559409 A JP H0559409A JP 3248367 A JP3248367 A JP 3248367A JP 24836791 A JP24836791 A JP 24836791A JP H0559409 A JPH0559409 A JP H0559409A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- phase
- soft magnetic
- mixed
- metastable
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Withdrawn
Links
- 239000006247 magnetic powder Substances 0.000 title claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 239000000843 powder Substances 0.000 claims abstract description 56
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910017086 Fe-M Inorganic materials 0.000 claims abstract description 7
- 239000011812 mixed powder Substances 0.000 claims abstract description 5
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 3
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 3
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 3
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 3
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 3
- 238000005121 nitriding Methods 0.000 claims description 10
- 238000002156 mixing Methods 0.000 claims description 6
- 238000010298 pulverizing process Methods 0.000 claims description 3
- 239000000956 alloy Substances 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 claims 1
- 238000013329 compounding Methods 0.000 claims 1
- 238000006902 nitrogenation reaction Methods 0.000 claims 1
- 229910052715 tantalum Inorganic materials 0.000 abstract description 2
- 238000010336 energy treatment Methods 0.000 description 5
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000012733 comparative method Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910021529 ammonia Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 229920005989 resin Polymers 0.000 description 2
- 239000011347 resin Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910017076 Fe Zr Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000012298 atmosphere Substances 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000002003 electron diffraction Methods 0.000 description 1
- 238000005265 energy consumption Methods 0.000 description 1
- 239000003822 epoxy resin Substances 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 229920000647 polyepoxide Polymers 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 238000007740 vapor deposition Methods 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、飽和磁束密度（以
下、Ｂｓと記す）が高く、保磁力（以下、Ｈｃと記す）
の小さな軟磁性粉末に関するものである。This invention has a high saturation magnetic flux density (hereinafter referred to as Bs) and a coercive force (hereinafter referred to as Hc).
Of small soft magnetic powder.
【０００２】[0002]
【従来の技術】従来、モーターやトランスなどの磁心、
さらに磁気シールドなどの樹脂結合軟磁性複合部材が、
純Ｆｅ粉末などの軟磁性粉末に、所定割合のエポキシ樹
脂などの樹脂結合剤を配合し、混合した後、所定形状の
圧粉体に加圧成形し、この圧粉体に樹脂硬化処理を施す
ことにより製造されることは良く知られるところであ
る。2. Description of the Related Art Conventionally, magnetic cores of motors and transformers,
Furthermore, resin-bonded soft magnetic composite members such as magnetic shields,
A soft magnetic powder such as pure Fe powder is mixed with a resin binder such as an epoxy resin in a predetermined ratio, mixed, and then pressure-molded into a green compact having a predetermined shape, and the green compact is subjected to a resin curing treatment. It is well known that it is manufactured by
【０００３】上記純Ｆｅ粉末は、Ｂｓが十分に大きくな
いために、近年、上記純Ｆｅ粉末よりも高いＢｓを有す
る準安定Ｆｅ16Ｎ2 相を主体組織とした軟磁性粉末が注
目されてきた。Since the pure Fe powder does not have a sufficiently large Bs, a soft magnetic powder mainly composed of a metastable Fe 16 N 2 phase having a Bs higher than that of the pure Fe powder has recently been attracting attention. ..
【０００４】[0004]
【発明が解決しようとする課題】しかしながら、上記準
安定Ｆｅ16Ｎ2 相を主体組織とした軟磁性粉末は、Ｎ2
ガス中の蒸着やスパッタリングで形成される薄膜を剥離
し、粉砕して製造されるために量産することができず、
またこのようにして製造された準安定Ｆｅ16Ｎ2相を主
体組織とす軟磁性粉末は、高いＢｓを有するけれどもＨ
ｃが高く、そのためこの軟磁性粉末を用いて作製された
圧粉磁芯もＨｃが大きくなり、これが組込まれた各種電
気電子機器の高効率化および省エネルギー化を満足させ
ることはできなかった。However, the soft magnetic powder containing the metastable Fe 16 N 2 phase as the main structure is N 2
The thin film formed by vapor deposition or sputtering in gas is peeled off and cannot be mass-produced because it is manufactured by crushing,
In addition, the soft magnetic powder produced in this way and mainly composed of the metastable Fe 16 N 2 phase has a high Bs, though it has a high Bs.
Since c is high, the powder magnetic core produced using this soft magnetic powder also has a large Hc, and it has not been possible to satisfy the high efficiency and energy saving of various electric and electronic devices incorporating the same.
【０００５】[0005]
【課題を解決するための手段】そこで、本発明者等は、
かかる課題を解決すべく研究を行った結果、ＭをＴｉ，
Ｚｒ，Ｈｆ，Ｖ，ＮｂおよびＴａのうちの１種または２
種以上とすると、Ｍ粉末および／またはＦｅ−Ｍ粉末
に、α−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜３）を主体
組織とする窒化処理Ｆｅ粉末を配合し、得られた配合粉
末をアトライターミルや遊星ボールミルを用いて高エネ
ルギーを与えながら混合粉砕すると（以下、高エネルギ
ーを与えながら混合粉砕することを高エネルギー処理と
いう）、Ｍを固溶した準安定Ｆｅ16Ｎ2 相（以下、準安
定（Ｆｅ，Ｍ）16Ｎ2 相という）含む軟磁性粉末が得ら
れ、この軟磁性粉末はＢｓをほとんど低下させることな
くＨｃを大幅に低下させることができるという知見を得
たのである。Therefore, the present inventors have
As a result of conducting research to solve such problems, M is replaced by Ti,
One or two of Zr, Hf, V, Nb and Ta
If the number of seeds is not less than, a nitriding Fe powder mainly composed of α-Fe phase and ε-Fe X N phase (X = 2 to 3) was mixed with M powder and / or Fe-M powder, and obtained. When the compounded powder is mixed and pulverized by using an attritor mill or a planetary ball mill while giving high energy (hereinafter, mixing and pulverizing while giving high energy is referred to as high energy treatment), metastable Fe 16 N 2 in which M is dissolved is formed. A soft magnetic powder containing a phase (hereinafter referred to as a metastable (Fe, M) 16 N 2 phase) was obtained, and it was found that this soft magnetic powder can significantly reduce Hc without substantially reducing Bs. It was.
【０００６】この発明は、かかる知見にもとづいてなさ
れたものであって、Ｍ粉末および／またはＦｅ−Ｍ粉末
に、α−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜３）を主体
組織とする窒化処理Ｆｅ粉末を、全体組成が（Ｆ
ｅ1-Y，ＭY ）1-Z ＮZ （但し、ＹおよびＺはそれぞれ
モル比でＹ＝０．０２〜０．１５，Ｚ＝０．０５〜０．
１５）となるように配合し、得られた配合粉末を高エネ
ルギー処理する、準安定（Ｆｅ，Ｍ）16Ｎ2 相を有する
軟磁性粉末の製造法に特徴を有するものである。The present invention has been made on the basis of such findings, and is mainly composed of an M-powder and / or an Fe-M powder containing an α-Fe phase and an ε-Fe X N phase (X = 2 to 3). The entire composition of the nitriding Fe powder having the structure is (F
e 1-Y , M Y ) 1-Z N Z (wherein Y and Z are in a molar ratio of Y = 0.02 to 0.15, Z = 0.05 to 0.
It is characterized by a method for producing a soft magnetic powder having a metastable (Fe, M) 16 N 2 phase, in which the compounded powder is blended in the above 15) and the resulting blended powder is treated with high energy.
【０００７】上記Ｍ粉末および／またはＦｅ−Ｍ粉末
に、さらに、α−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜
３）を主体組織とする窒化処理Ｆｅ粉末を配合し、これ
に高エネルギー処理を施すと、上記配合粉末は混合粉末
となり、さらに粉砕・薄片化および薄片の冷間圧接ある
いは薄片のたたみ込みが同時に進行し、粉砕による組織
の微細化とともにＭ成分の合金化による組織の微細化が
促進され、準安定（Ｆｅ，Ｍ）16Ｎ2 相が生成して高Ｂ
ｓで低Ｈｃを有する軟磁性粉末が得られるものと考えら
れる。In addition to the above M powder and / or Fe-M powder, α-Fe phase and ε-Fe X N phase (X = 2 to
When a nitriding Fe powder mainly composed of 3) is mixed and subjected to high energy treatment, the above-mentioned mixed powder becomes a mixed powder, and further crushing and thinning and cold welding of the thin piece or convolution of the thin piece at the same time. As it progresses, the refinement of the structure by pulverization is promoted and the refinement of the structure by the alloying of the M component is promoted, and a metastable (Fe, M) 16 N 2 phase is generated, which results in a high B content.
It is believed that a soft magnetic powder having a low Hc at s can be obtained.
【０００８】この発明の製造法で原料粉末として用いる
α−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜３）を主体組織
とする窒化処理Ｆｅ粉末は、純Ｆｅ粉末をアンモニア雰
囲気において短時間窒化処理すると、純Ｆｅ粉末の内部
は窒化処理されずにα−Ｆｅ相のまま残り、表層部が窒
化されてε−ＦｅX Ｎ相（Ｘ＝２〜３）が生成されるこ
とにより製造される。The nitriding Fe powder mainly composed of the α-Fe phase and the ε-Fe X N phase (X = 2 to 3) used as the raw material powder in the production method of the present invention is a pure Fe powder which is short in a ammonia atmosphere. When the time nitriding treatment is performed, the inside of the pure Fe powder is not subjected to the nitriding treatment and remains in the α-Fe phase, and the surface layer portion is nitrided to produce the ε-Fe X N phase (X = 2 to 3). To be done.
【０００９】上記配合粉末の全体組成がモル比で（Ｆｅ
1-Y ，ＭY ）1-Z ＮZ （但し、Ｙ＝０．０２〜０．１
５，Ｚ＝０．０５〜０．１５）となるように限定した理
由は、Ｙが０．０２未満ではＭによるＦｅ16Ｎ2 相の結
晶粒を微細化させることができないためにＨｃを低下さ
せることができず、一方、Ｙが０．１５を越えるとＦｅ
16Ｎ2 相のＢｓが減少して好ましくないことによるもの
であり、さらにＺが０．０５未満でもまた０．１５を越
えても準安定（Ｆｅ，Ｍ）16Ｎ2 相の形成が困難となる
ために好ましくないことによるものである。The overall composition of the above-mentioned compounded powder is (Fe
1-Y , M Y ) 1-Z N Z (However, Y = 0.02 to 0.1
5, Z = 0.05 to 0.15), the reason for limiting it is that if Y is less than 0.02, the crystal grains of the Fe 16 N 2 phase due to M cannot be refined, so that Hc is lowered. On the other hand, if Y exceeds 0.15, Fe
This is because the Bs of the 16 N 2 phase is decreased, which is not preferable, and it is difficult to form a metastable (Fe, M) 16 N 2 phase even when Z is less than 0.05 or more than 0.15. This is because it is not preferable because
【００１０】さらに、この発明で採用する高エネルギー
処理は、アトライターミルや遊星ボールミルなどの混合
粉砕機を用い、通常の混合粉砕よりもボール数や回転数
を多くすることにより高エネルギーを付与し、混合粉砕
するものである。Further, the high energy treatment adopted in the present invention uses a mixing and crushing machine such as an attritor mill or a planetary ball mill, and imparts high energy by increasing the number of balls and the number of revolutions as compared with ordinary mixing and crushing. , Is mixed and crushed.
【００１１】[0011]
【実施例】原料粉末として、いずれも粒度：−１００メ
ッシュのＴｉ粉末、Ｚｒ末粉、Ｈｆ粉末、Ｖ粉末、Ｎｂ
粉末、Ｔａ粉末、表４〜表６に示される成分組成のＦｅ
−Ｔｉ粉末、Ｆｅ−Ｚｒ粉末、Ｆｅ−Ｈｆ粉末、Ｆｅ−
Ｖ粉末、Ｆｅ−Ｎｂ粉末、およびＦｅ−Ｔａ粉末を用意
した。[Examples] As raw material powders, Ti powder, Zr powder, Hf powder, V powder, Nb, each having a particle size of -100 mesh,
Powder, Ta powder, Fe having the component composition shown in Tables 4 to 6
-Ti powder, Fe-Zr powder, Fe-Hf powder, Fe-
V powder, Fe-Nb powder, and Fe-Ta powder were prepared.
【００１２】さらに粒度：−１００メッシュのアトマイ
ズ純Ｆｅ粉末をアンモニア気流中、温度：５７０℃で種
々の時間保持することにより窒化処理し、主要構成相が
いずれもα−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜３）か
らなり種々の窒素含有量を有する窒化処理Ｆｅ粉末を製
造し、原料粉末として用意した。Further, atomized pure Fe powder having a particle size of -100 mesh is subjected to a nitriding treatment by being kept in an ammonia stream at a temperature of 570 ° C. for various times, and the main constituent phases are α-Fe phase and ε-Fe X. Nitride-treated Fe powder consisting of N phase (X = 2 to 3) and having various nitrogen contents was manufactured and prepared as a raw material powder.
【００１３】これら原料粉末を全体組成が（Ｆｅ1-Y ，
ＭY ）1-Z ＮｚにおけるＹおよびＺのモル比が表１〜表
８に示される値となるように配合し、得られた配合粉末
を直径：１１mmのステンレス製ボール１１個とともに容
積：８０cm3 のステンレス製容器を備えた遊星ボールミ
ルの上記容器に装入し、容器内をＮ2 雰囲気として、容
器公転速度：３００r.p.m.で２０時間回転の高エネルギ
ー処理を施すことにより本発明法１〜４８、比較法１〜
１４を実施した。The total composition of these raw material powders is (Fe 1 -Y ,
M Y) 1-Z molar ratio of Y and Z in the Nz is blended so that the value shown in Table 1 to Table 8, formulated powder obtained diameter: 11 mm stainless steel ball 11 with volume: 80 cm The method of the present invention 1 to 3 by charging the above-mentioned container of a planetary ball mill equipped with a stainless steel container of 3 and applying a high energy treatment of 20 hours rotation at a container revolution speed of 300 rpm with an N 2 atmosphere in the container. 48, Comparative method 1
14 was carried out.
【００１４】なお、上記比較法１〜１４は、ＹまたはＺ
の値がこの発明の条件から外れており、この外れた値に
＊印を付して示してある。Incidentally, the above-mentioned comparative methods 1 to 14 are Y or Z.
Is out of the condition of the present invention, and this outlying value is marked with *.
【００１５】[0015]
【表１】 [Table 1]
【００１６】[0016]
【表２】 [Table 2]
【００１７】[0017]
【表３】 [Table 3]
【００１８】[0018]
【表４】 [Table 4]
【００１９】[0019]
【表５】 [Table 5]
【００２０】[0020]
【表６】 [Table 6]
【００２１】[0021]
【表７】 [Table 7]
【００２２】[0022]
【表８】 [Table 8]
【００２３】上記本発明法１〜４８および比較法１〜１
４を実施することにより得られた軟磁性粉末について、
準安定（Ｆｅ，Ｍ）16Ｎ2 相の生成率（容量％）を２０
０KV透過電子顕微鏡を用いて制限視野電子線回析を行
い、この結果の回折パターンの中の準安定（Ｆｅ，Ｍ）
16Ｎ2 相の反射を用いて暗視野像を結像して写真撮影
し、この写真から準安定（Ｆｅ，Ｍ）16Ｎ2 相の体積分
率を算出することにより求め、ＢｓおよびＨｃについて
も振動試料型磁力計を用い、それぞれ１０ｋＯｅ，１０
０Ｏｅの磁場を印加して測定し、これらの測定結果を表
９〜表１３に示した。The above-mentioned methods 1 to 48 of the present invention and comparative methods 1 to 1
Regarding the soft magnetic powder obtained by carrying out 4,
The generation rate (volume%) of the metastable (Fe, M) 16 N 2 phase was 20%.
Selective field electron diffraction was performed using a 0KV transmission electron microscope, and the metastable (Fe, M) in the diffraction pattern of this result was obtained.
A dark field image was formed using reflection of the 16 N 2 phase, photographed, and the volume fraction of the metastable (Fe, M) 16 N 2 phase was calculated from this photograph to obtain Bs and Hc. Also using a vibrating sample magnetometer, 10 kOe, 10
The measurement was performed by applying a magnetic field of 0 Oe, and the measurement results are shown in Tables 9 to 13.
【００２４】[0024]
【表９】 [Table 9]
【００２５】[0025]
【表１０】 [Table 10]
【００２６】[0026]
【表１１】 [Table 11]
【００２７】[0027]
【表１２】 [Table 12]
【００２８】[0028]
【表１３】 [Table 13]
【００２９】[0029]
【発明の効果】表１〜表１３に示される結果から、α−
Ｆｅ相とε−Ｆｅx Ｎ相（Ｘ＝２〜３）を主体組織とす
る窒化処理Ｆｅ粉末に、Ｍ粉末および／またはＦｅ−Ｍ
粉末を、全体組成が（Ｆｅ1-Y ，ＭY ）1-Z ＮZ （但
し、Ｙ＝０．０２〜０．１５，Ｚ＝０．０５〜０．１
５）となるように配合し、得られた配合粉末に高エネル
ギー処理を施すことにより、Ｂｓをほとんど低下するこ
となくＨｃを大幅に下げることができることがわかる。From the results shown in Tables 1 to 13, α-
A nitriding Fe powder mainly composed of Fe phase and ε-Fex N phase (X = 2 to 3) is added to M powder and / or Fe-M
The powder has a total composition of (Fe 1-Y , M Y ) 1-Z N Z (where Y = 0.02 to 0.15 and Z = 0.05 to 0.1).
It can be seen that Hc can be significantly reduced with almost no decrease in Bs by performing high energy treatment on the obtained mixed powder by blending so as to be 5).
【００３０】したがって、この発明により準安定（Ｆ
ｅ，Ｍ）16Ｎ2 相を含むＨｃの低い軟磁性粉末を量産す
ることができ、この軟磁性粉末を用いて高効率でエネル
ギー消費量の少ない樹脂結合圧粉電磁気部品を低コスト
で生産でき、産業の発展に大いに貢献することができ
る。Therefore, according to the present invention, the metastable (F
e, M) It is possible to mass-produce soft magnetic powder with low Hc containing 16 N 2 phase, and use this soft magnetic powder to produce highly efficient and low energy consumption resin-bonded powder electromagnetic components at low cost. , Can greatly contribute to the development of industry.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.5 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 33/04 Ｄ 8414−4Ｋ ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 5 Identification code Office reference number FI technical display location C22C 33/04 D 8414-4K
Claims (4)
Ｔａのうちの１種または２種以上とすると、Ｍ粉末に、
α−Ｆｅ相とε−ＦｅX Ｎ相（Ｘ＝２〜３）を主体組織
とする窒化処理Ｆｅ粉末を配合し、得られた配合粉末に
高エネルギーを与えながら混合粉砕処理することを特徴
とする、Ｍを固溶した準安定Ｆｅ16Ｎ2 相（以下、準安
定（Ｆｅ，Ｍ）16Ｎ2 相と記す）を有する軟磁性粉末の
製造法。1. When M is one or more of Ti, Zr, Hf, V, Nb and Ta, M powder is
It is characterized in that nitriding Fe powder having an α-Fe phase and an ε-Fe X N phase (X = 2 to 3) as a main structure is blended, and the resulting blended powder is mixed and pulverized while applying high energy. A method for producing a soft magnetic powder having a metastable Fe 16 N 2 phase (hereinafter referred to as a metastable (Fe, M) 16 N 2 phase) in which M is solid-solved.
ＦｅX Ｎ相（Ｘ＝２〜３）を主体組織とする窒化処理Ｆ
ｅ粉末を配合し、得られた配合粉末に高エネルギーを与
えながら混合粉砕処理することを特徴とする、準安定
（Ｆｅ，Ｍ）16Ｎ2 相を有する軟磁性粉末の製造法。2. An Fe-M alloy powder containing α-Fe phase and ε-
Nitrogenation treatment F mainly composed of Fe x N phase (X = 2 to 3)
A method for producing a soft magnetic powder having a metastable (Fe, M) 16 N 2 phase, which comprises blending e powder and subjecting the obtained blended powder to a mixing and pulverizing treatment while applying high energy.
相とε−ＦｅX Ｎ相（Ｘ＝２〜３）を主体組織とする窒
化処理Ｆｅ粉末を配合し、得られた配合粉末に高エネル
ギーを与えながら混合粉砕処理することを特徴とする、
準安定（Ｆｅ，Ｍ）16Ｎ2 相を有する軟磁性粉末の製造
法。3. The M powder and the Fe-M powder are mixed with α-Fe.
Phase and ε-Fe X N phase (X = 2 to 3) as a main structure are mixed, and nitriding Fe powder is mixed, and the resulting mixed powder is mixed and pulverized while giving high energy,
Method for producing soft magnetic powder having metastable (Fe, M) 16 N 2 phase.
ｅ1-Y ，ＭY）1-Z ＮZ （但し、ＹおよびＺはそれぞれ
モル比でＹ＝０．０２〜０．１５，Ｚ＝０．０５〜０．
１５）となるように配合して得られた配合粉末であるこ
とを特徴とする請求項１，２又は３記載の準安定（Ｆ
ｅ，Ｍ）16Ｎ2 相を有する軟磁性粉末の製造法。4. The above-mentioned compounded powder has a total composition of (F
e 1-Y , M Y ) 1-Z N Z (wherein Y and Z are in a molar ratio of Y = 0.02 to 0.15, Z = 0.05 to 0.
15) The metastable (F) according to claim 1, characterized in that it is a compounded powder obtained by compounding such that
e, M) A method for producing a soft magnetic powder having a 16 N 2 phase.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3248367A JPH0559409A (en) | 1991-09-02 | 1991-09-02 | Production of soft magnetic powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3248367A JPH0559409A (en) | 1991-09-02 | 1991-09-02 | Production of soft magnetic powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0559409A true JPH0559409A (en) | 1993-03-09 |
Family
ID=17177050
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3248367A Withdrawn JPH0559409A (en) | 1991-09-02 | 1991-09-02 | Production of soft magnetic powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0559409A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114890380A (en) * | 2022-05-12 | 2022-08-12 | 刘威 | Metastable hydrogen storage alloy and preparation method thereof |
-
1991
- 1991-09-02 JP JP3248367A patent/JPH0559409A/en not_active Withdrawn
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114890380A (en) * | 2022-05-12 | 2022-08-12 | 刘威 | Metastable hydrogen storage alloy and preparation method thereof |
| CN114890380B (en) * | 2022-05-12 | 2023-12-19 | 刘威 | Metastable state hydrogen storage alloy and preparation method thereof |
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