JPH0499247A - Production of soft magnetic sintered parts by utilizing mechanical alloying - Google Patents
Production of soft magnetic sintered parts by utilizing mechanical alloyingInfo
- Publication number
- JPH0499247A JPH0499247A JP2210212A JP21021290A JPH0499247A JP H0499247 A JPH0499247 A JP H0499247A JP 2210212 A JP2210212 A JP 2210212A JP 21021290 A JP21021290 A JP 21021290A JP H0499247 A JPH0499247 A JP H0499247A
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- JP
- Japan
- Prior art keywords
- powder
- less
- soft magnetic
- weight
- pure
- 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.)
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- 238000005551 mechanical alloying Methods 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 239000000843 powder Substances 0.000 claims abstract description 35
- 239000013078 crystal Substances 0.000 claims abstract description 10
- 229910017082 Fe-Si Inorganic materials 0.000 claims abstract description 8
- 229910017133 Fe—Si Inorganic materials 0.000 claims abstract description 8
- 238000001125 extrusion Methods 0.000 claims abstract description 6
- 238000002425 crystallisation Methods 0.000 claims abstract description 4
- 230000008025 crystallization Effects 0.000 claims abstract description 4
- 238000000227 grinding Methods 0.000 claims abstract description 3
- 238000005245 sintering Methods 0.000 claims abstract 2
- 229910045601 alloy Inorganic materials 0.000 claims description 31
- 239000000956 alloy Substances 0.000 claims description 31
- 238000000034 method Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 9
- 239000000126 substance Substances 0.000 claims description 6
- 238000005275 alloying Methods 0.000 claims description 3
- 229910017086 Fe-M Inorganic materials 0.000 claims description 2
- 238000000465 moulding Methods 0.000 claims description 2
- 230000004907 flux Effects 0.000 abstract description 10
- 229910000808 amorphous metal alloy Inorganic materials 0.000 abstract description 3
- 229910000831 Steel Inorganic materials 0.000 abstract description 2
- 239000010959 steel Substances 0.000 abstract description 2
- 229910002796 Si–Al Inorganic materials 0.000 abstract 2
- 239000011863 silicon-based powder Substances 0.000 abstract 1
- 230000035699 permeability Effects 0.000 description 6
- 229910000976 Electrical steel Inorganic materials 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000005280 amorphization Methods 0.000 description 3
- 238000007712 rapid solidification Methods 0.000 description 3
- 239000000696 magnetic material Substances 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 125000002915 carbonyl group Chemical group [*:2]C([*:1])=O 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000001192 hot extrusion Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910000889 permalloy Inorganic materials 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はメカニカルアロイングを利用した新規な軟磁性
焼結部品の製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a novel method for manufacturing soft magnetic sintered parts using mechanical alloying.
軟磁性焼結部品は磁気ヘッド、柱上トランスモータ用鉄
心等に用いられるものであり、従来この分野ではフェラ
イト系、パーマロイ、ケイ素鋼あるいはアモルファス合
金などが使用されていた。Soft magnetic sintered parts are used in magnetic heads, cores for pole-mounted transformers, etc., and conventionally in this field, ferrite, permalloy, silicon steel, or amorphous alloys have been used.
アモルファス合金とは、単ロールや双ロール法のような
急冷凝固法で作成されるリボン状の合金であり、Ｆｅ系
とＣｏ系のものがある。軟磁性材料としては飽和磁束密
度、比透磁率が高く、磁心損失や磁歪定数の小さなもの
が望ましい。Amorphous alloys are ribbon-shaped alloys created by a rapid solidification method such as a single-roll or twin-roll method, and include Fe-based and Co-based alloys. The soft magnetic material preferably has high saturation magnetic flux density, high relative magnetic permeability, and low core loss and magnetostriction constant.
Ｃ発明が解決しようとする課題〕
上記の従来材料はいずれも一長一短であり、必ずしも全
てに優れた材料というものはなかった。Problems to be Solved by the Invention C] All of the above-mentioned conventional materials have advantages and disadvantages, and no material is necessarily superior in all respects.
すなわち、ケイ素鋼は飽和磁束密度が２，０と高いが磁
心損失が極めて大きく、比透磁率が２０００と小さい。That is, silicon steel has a high saturation magnetic flux density of 2.0, but has an extremely large magnetic core loss and a low relative magnetic permeability of 2000.
■一方、アモルファス合金は比透磁率が高く磁心損失が
小さいが、飽和磁束密度がＦｅ系で１．４１゜Ｃｏ系で
０，５５と小さい欠点がある。アモルファス合金が急冷
凝固法で作成されるｋめに、Ｂ（ホウ素）やＣ（炭素）
のような微量の元素をその化学組成として含有するため
、飽和磁束密度が低くなるのである。(2) On the other hand, amorphous alloys have high relative magnetic permeability and low core loss, but have the disadvantage that the saturation magnetic flux density is as low as 1.41° for Fe-based materials and 0.55° for Co-based materials. B (boron) and C (carbon) are used to create amorphous alloys by rapid solidification.
The saturation magnetic flux density is low because it contains trace amounts of elements such as in its chemical composition.
したがって、飽和磁束密度、軟磁気特性の優れたアモル
ファス合金が要求されており、本発明は急冷凝固法によ
らないアモルファス合金の新規な製造方法の掃供を課題
としてなされたものである。Therefore, there is a need for an amorphous alloy with excellent saturation magnetic flux density and soft magnetic properties, and the present invention has been made to provide a new method for producing an amorphous alloy that does not involve rapid solidification.
本発明者らは、Ｆｅ−Ｓｉ系合金のアモルファス材を急
冷法以外の手段で作成できれば、軟磁気特性の優れた合
金を得られると考え、鋭意研究の結果、メカニカルアロ
イングを利用してこの目的を達成できることを見出し本
発明に到った。The present inventors believe that if an amorphous Fe-Si alloy can be made by a method other than the rapid cooling method, an alloy with excellent soft magnetic properties can be obtained, and as a result of extensive research, they have developed an alloy using mechanical alloying. The inventors have discovered that the object can be achieved and have developed the present invention.
すなわち、本発明はＳｉ３〜７重量％残部Ｆｅ、 Ｍ７
重量％以下残部Ｆｅ、またはＳｉ０重量％以下１Ｍ６重
量％以下残部Ｆｅ、の化学組成を有する合金の粉末をＮ
雰囲気中にて１時間以上メカニカルグラインディングす
ることにより平均結晶が１１００ｎ以下の組織および／
またはアモルファス構造を有する処理粉末を作成し、該
処理粉末を合金の結晶化温度をＴｘ（’Ｃ）とするとき
（ＴＸ＋２０）℃以下の温度において押し出し法により
固化成形することを特徴とするメカニカルアロイングを
利用した軟磁性焼結部品の製造方法である。That is, in the present invention, Si3 to 7% by weight, balance Fe, M7
An alloy powder having a chemical composition of 0 wt% or less of Fe, or 0 wt% or less of Si, 1M or less of 6 wt% or less of Fe,
Mechanical grinding for over 1 hour in an atmosphere creates a structure with an average crystal size of 1100n or less and/or
Alternatively, a mechanical alloy is produced by preparing a treated powder having an amorphous structure, and solidifying and molding the treated powder by extrusion at a temperature of (TX+20)°C or lower, where the crystallization temperature of the alloy is Tx ('C). This is a method for manufacturing soft magnetic sintered parts using ing.
本発明において、純Ｆｅ、純Ｓｉ、純Ａｊ’、 Ｆｅ
Ｓｉ合金またはＦｅ−Ａｌ’合金の粉末を、ＳＬ３〜
７重量％残部Ｆｅ、／ｌｊ！７重量％以下残部Ｆｅ、ま
たはＳｉ１０重量％以下、／Ｖ６重量％以下残部Ｆｅの
化学組成に配合した後、Ａｒ雰囲気中にて５０時間以上
メカニカルアロイングすることにより平均結晶が１１０
０ｎ以下の組織および／またはアモルファス構造を有す
る処理粉末を作成することを、特に好丈しい実施態様と
して挙げることができる。In the present invention, pure Fe, pure Si, pure Aj', Fe
Si alloy or Fe-Al' alloy powder is SL3~
7% by weight balance Fe, /lj! After blending into a chemical composition with a balance of 7% by weight or less of Fe, or a Si of 10% by weight or less and a /V of 6% by weight or less and a balance of Fe, mechanical alloying is performed in an Ar atmosphere for 50 hours or more to obtain an average crystal of 110
Particularly advantageous embodiments include producing treated powders with a sub-On texture and/or an amorphous structure.
また、本発明においては、合金粉末が５重量％以下のＮ
ｂまたは／およびＣｕを合金元素として配合されている
ものは、Ｎｂはこの系のアモルファス化を容易にし、Ｃ
ｏは磁心損失を低下させ比透磁率を高める作用を有する
点で、特に好ましい実施態様である。Further, in the present invention, the alloy powder contains 5% by weight or less of N.
When B or/and Cu are blended as alloying elements, Nb facilitates the amorphization of the system, and C
o is a particularly preferred embodiment in that it has the effect of reducing core loss and increasing relative magnetic permeability.
本発明の方法を具体的に説明すると、原料粉末としては
Ｓｉ３〜７重量％残部ＦｅＳＭＴ重量％以下残部Ｆｅ、
または５１１０重量％以下１Ｍ６重量％以下残部Ｆｅを
化学組成として有する合金粉を用いることができる。ま
たは、純Ｆｅ、純Ｓｉ、純Ｍ、さらにはＦｅ−Ｓｉ母合
金、Ｆｅ−Ｍ母合金等の素粉末を用いることもできる。To specifically explain the method of the present invention, the raw material powder includes 3 to 7% by weight of Si, balance of FeSMT, balance of Fe,
Alternatively, an alloy powder having a chemical composition of 5110% by weight or less, 1M, 6% by weight or less, and the remainder Fe can be used. Alternatively, base powders such as pure Fe, pure Si, pure M, Fe-Si master alloy, Fe-M master alloy, etc. can also be used.
所望の化学組成となるように用意した原料粉をメカニカ
ルブライディング又はメカニカルアロイング（以下ＭＡ
とも略記する）することにより、アモルファス粉末また
はｌｏｏｎｍ以下の結晶粒を有するＭＡ粉末とする。Mechanical briding or mechanical alloying (hereinafter referred to as MA
(also abbreviated as "MA powder"), it is made into an amorphous powder or an MA powder having crystal grains of less than 10m.
なお、メカニカルブライディングもメカニカルアロイン
グも、共に粉末に歪を与えるという点、即ち、粉末に歪
エネルギーを蓄積させる方法である点では同じである。Note that both mechanical briding and mechanical alloying are the same in that they both apply strain to powder, that is, they are methods of accumulating strain energy in powder.
しかし、メカニカルブライディングが単に粉末を歪を与
える方法であるのに対して、メカニカルアロイングは、
２種又は３種以上の粉末を合金化させるプロセスでもを
る点で前者と相違している。However, while mechanical briding is simply a method of distorting powder, mechanical alloying is
It differs from the former in that it can also be used in a process of alloying two or more types of powder.
具体的にはアトライター装置を用いて、例えばＡｒガス
雰囲気中においてアジテータ−回転数２００ｒｐｍで５
０分間処理といった条件で行なうことで上記の粉末を得
ることができる。雰囲気は上記のＮが一般的であるが、
その他Ｎ、ガス雰囲気、Ｈ□を少量含有したＮガス雰囲
気、大気等でも行われる。Specifically, using an attritor device, for example, in an Ar gas atmosphere, an agitator is rotated at a rotation speed of 200 rpm.
The above powder can be obtained by performing the treatment for 0 minutes. The atmosphere is generally N as described above,
In addition, N gas atmosphere, N gas atmosphere containing a small amount of H□, air, etc. may also be used.
メカニカルブライディング又はメカニカルアロイングの
いずれも、必要以上の長時間行うと、雰囲気からのコン
タミネイションが増えるばかりである。したがってこれ
らの処理を行なう時間は、合金粉の性状、大きさ、硬度
等によるものの、メカニカルブライディングでは少なく
とも１時間以上、長くとも２０時間程度、メカニカルア
ロイングでは少なくとも１６〜５０５０時間行えば充分
に目的を達成できる。If either mechanical briding or mechanical alloying is performed for a longer time than necessary, contamination from the atmosphere will only increase. Therefore, although the time for performing these treatments depends on the properties, size, hardness, etc. of the alloy powder, for mechanical briding, it is sufficient to perform at least 1 hour or at most 20 hours, and for mechanical alloying, at least 16 to 5050 hours is sufficient. You can achieve your goals.
また、ボールミルを用いる振動ミル法によってもよい。Alternatively, a vibration milling method using a ball mill may be used.
この段階ではアモルファスと微細晶が混在していても構
わない。At this stage, there may be a mixture of amorphous and fine crystals.
以上で得られたＭＡ粉末を熱間押出法により固化成形す
るが、この時の温度はアモルファスの結晶化温度をＴｘ
（Ｃ）とするとき、（Ｔｘ＋２０）°Ｃ以下で押出しを
行なう。（Ｔｘ＋２０）’Ｃを越えると、合金の結晶化
及びその粗大化が顕著に起こるので不都合である。また
、下限値はないが、例えばアモルファスの転移温度をＴ
ｇ（’Ｃ）とするとき、（Ｔｇ−１５０）℃以下の温度
では押出し変形圧力が高くなり、押出しを行おうとする
と押詰まりが起こり、押出材を作成できなくなる。The MA powder obtained above is solidified and molded by hot extrusion, and the temperature at this time is Tx
When (C) is used, extrusion is performed at (Tx+20)°C or lower. Exceeding (Tx+20)'C is disadvantageous because crystallization and coarsening of the alloy occur significantly. Although there is no lower limit, for example, the transition temperature of amorphous is T
g('C), the extrusion deformation pressure becomes high at temperatures below (Tg-150)°C, and when extrusion is attempted, clogging occurs, making it impossible to create an extruded material.
本発明に従って作成された合金は微細な結晶粒を有する
ケイ素鋼である、結晶粒は２００〜３００Å以下の大き
さを有している。このため磁気的異方性が小さい。また
、ケイ素鋼であるため飽和磁束密度が高い上に、磁心損
失が小さく、磁歪定数も小さい。さらに、合金がアモル
ファス状態を経過していること、結晶粒が小さいこ吉か
ら、比透磁率も通常のケイ素鋼に較べ比較的小さな値を
示す。The alloy made according to the invention is a silicon steel with fine grains, the grains having a size of less than 200-300 Å. Therefore, the magnetic anisotropy is small. In addition, since it is made of silicon steel, it has a high saturation magnetic flux density, a small magnetic core loss, and a small magnetostriction constant. Furthermore, because the alloy is in an amorphous state and the crystal grains are small, the relative magnetic permeability also shows a relatively small value compared to ordinary silicon steel.
本発明のＦｅ−Ｓｉ鋼には微量の他元素、例えばＣｕや
Ｎｂを含んでいてもよい。Ｃｕは磁心損失を低下させ、
比透磁率を高めるが、これはＣｕが結晶粒径の微細化に
多少の効果を有することと関係があると考えられる。Ｃ
ｕの存在量は５重量に以下であることが好ましい。The Fe-Si steel of the present invention may contain trace amounts of other elements such as Cu and Nb. Cu lowers magnetic core loss,
Although the relative magnetic permeability is increased, this is thought to be related to the fact that Cu has some effect on making the crystal grain size finer. C
Preferably, the amount of u present is less than or equal to 5 parts by weight.
Ｎｂはこの系の合金のアモルファス化を容易にする働き
を有する。Ｎｂの存在量は５重量％であることが好まし
い。Nb has the function of facilitating the amorphization of this type of alloy. The amount of Nb present is preferably 5% by weight.
Ｃｕ、 Ｎｂの他にも、合金のアモルファス化を促進す
るような元素、結晶の微細化に効果かある元素等の存在
は差し支えない。In addition to Cu and Nb, there is no problem in the presence of elements that promote the amorphization of the alloy, elements that are effective in making the crystals finer, etc.
以下、実施例を挙げて本発明を具体的に説明するが、本
発明はこの範囲に限定されるものではない。Hereinafter, the present invention will be specifically explained with reference to Examples, but the present invention is not limited to this scope.
実施例１
ｆａｌＦｅ９６％−３ｉ４％、（ｂ）Ｆｅ９３％−３ｉ
４％−Ｎ３％、（ＣＩＦ２９３％−Ｍ７％、のアトマイ
ズ粉をそれぞれメカニカルブライディングした。また、
これとは別に純Ｆｅ（カーボニルＦｅ）粉、Ｆｅ−Ｓｉ
粉及びＦｅ−３０ＡＩ！粉（いずれも１００メツシユ以
下）をｌａｌ〜ｆｃｌの組成に配合し、これをメカニカ
ルアロイングした。Example 1 falFe96%-3i4%, (b) Fe93%-3i
Atomized powders of 4%-N3% and (CIF293%-M7%) were mechanically bridded.
Apart from this, pure Fe (carbonyl Fe) powder, Fe-Si
Powder and Fe-30AI! Powder (all 100 mesh or less) was blended into a composition of lal to fcl, and this was mechanically alloyed.
また、Ｆｅ−Ｎｂ −Ｃｕ粉を用いて、Ｆｅ９０％−３
ｉ６％−Ｎｂ２％−Ｃｕ２％の組成に配合した粉末につ
いても、メカニカルアロイングした。In addition, using Fe-Nb-Cu powder, Fe90%-3
Mechanical alloying was also performed on the powder blended with the composition of i6%-Nb2%-Cu2%.
以上のメカニカルブライディング、メカニカルアロイン
グは乾式アトライターを用いて、Ｎガス雰囲気中で７５
時間行った。アジテータ−回転数は１７５ｒｐｍとした
。The above mechanical briding and mechanical alloying are performed using a dry attritor in an N gas atmosphere.
Time went. The agitator rotation speed was 175 rpm.
得られたＭＡ粉末を軟鋼容器に充填し、７５０℃で押出
し加工し、粉末の固化を行った。The obtained MA powder was filled into a mild steel container and extruded at 750°C to solidify the powder.
得られた各合金の特性値を測定したところ、表１に示す
結果であった。この測定結果から、本発明品が飽和磁束
密度（Ｂｓ）、残留磁束密度（Ｂｒ）、保磁力（ＨＣ）
、最大磁化率（μｍａｗ）、において優れていることが
わかる。When the characteristic values of each obtained alloy were measured, the results were shown in Table 1. From this measurement result, it was found that the product of the present invention has a saturation magnetic flux density (Bs), a residual magnetic flux density (Br), and a coercive force (HC).
, maximum magnetic susceptibility (μmaw).
以」二のように、本発明による合金は軟磁性焼結部品は
高い飽和磁束密度と優れた軟磁気特性を有する合金であ
り、磁気ヘッドや柱上トランス、モータ内鉄心等の軟磁
性材料として有利な特性を有するものであり、産業上非
常に有効である。As described above, the alloy according to the present invention is an alloy that has high saturation magnetic flux density and excellent soft magnetic properties for soft magnetic sintered parts, and can be used as a soft magnetic material for magnetic heads, columnar transformers, cores in motors, etc. It has advantageous properties and is very effective industrially.
Claims (3)
部Ｆｅ、またはＳｉ１０重量％以下、Ａｌ重量％以下残
部Ｆｅ、の化学組成を有する合金の粉末をＡｒ雰囲気中
にて１時間以上メカニカルグラインディングすることに
より平均結晶が１００ｎｍ以下の組織および／またはア
モルファス構造を有する処理粉末を作成し、該処理粉末
を合金の結晶化温度をＴｘ（℃）とするとき（Ｔｘ＋２
０）℃以下の温度において押し出し法により固化成形す
ることを特徴とするメカニカルアロイングを利用した軟
磁性焼結部品の製造方法。(1) Mechanical grinding of an alloy powder having a chemical composition of 3 to 7% by weight of Si, balance of Fe, 7% by weight of Al or less, balance of Fe, or 10% or less of Si, balance of Fe of 10% or less by weight of Al, in an Ar atmosphere for more than 1 hour. When the crystallization temperature of the alloy is Tx (℃) (Tx+2
0) A method for manufacturing soft magnetic sintered parts using mechanical alloying, characterized by solidifying and molding by extrusion at a temperature of 0°C or lower.
Ｆｅ−Ｍ合金の粉末を、Ｓｉ３〜７重量％残部Ｆｅ、Ａ
ｌ７重量％以下残部Ｆｅ、またはＳｉ１０重量％以下、
Ａｌ６重量％以下残部Ｆｅの化学組成に配合した後、Ａ
ｒ雰囲気中にて５０時間以上メカニカルアロイングする
ことにより平均結晶が１００ｎｍ以下の組織および／ま
たはアモルファス構造を有する処理粉末を作成すること
を特徴とする請求項（１）記載のメカニカルアロイング
を利用した軟磁性焼結部品の製造方法。(2) Pure Fe, pure Si, pure Al, Fe-Si alloy or Fe-M alloy powder is mixed with 3 to 7% by weight Si, balance Fe, A
17% by weight or less, balance Fe, or Si 10% by weight or less,
After adding Al to the chemical composition of 6% by weight or less with the balance being Fe,
Utilizing the mechanical alloying according to claim (1), wherein a treated powder having an average crystal size of 100 nm or less and/or an amorphous structure is created by mechanical alloying for 50 hours or more in an r atmosphere. A method for manufacturing soft magnetic sintered parts.
合金元素として配合されていることを特徴とする請求項
（１）または（２）に記載のメカニカルアロイングを利
用した軟磁性焼結部品の製造方法。(3) Soft magnetic sintering using mechanical alloying according to claim (1) or (2), wherein the alloy powder contains 5% or less of Nb and/or Cu as an alloying element. How the parts are manufactured.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2210212A JPH0499247A (en) | 1990-08-10 | 1990-08-10 | Production of soft magnetic sintered parts by utilizing mechanical alloying |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2210212A JPH0499247A (en) | 1990-08-10 | 1990-08-10 | Production of soft magnetic sintered parts by utilizing mechanical alloying |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0499247A true JPH0499247A (en) | 1992-03-31 |
Family
ID=16585646
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2210212A Pending JPH0499247A (en) | 1990-08-10 | 1990-08-10 | Production of soft magnetic sintered parts by utilizing mechanical alloying |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0499247A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5443787A (en) * | 1993-07-13 | 1995-08-22 | Tdk Corporation | Method for preparing iron system soft magnetic sintered body |
| KR100960699B1 (en) * | 2008-01-16 | 2010-05-31 | 한양대학교 산학협력단 | Fabrication Method of Fe-Si type soft magnet powder and soft magnet core using the same |
| CN111020410A (en) * | 2019-11-13 | 2020-04-17 | 中国科学院宁波材料技术与工程研究所 | Iron-based nanocrystalline magnetically soft alloy and preparation method thereof |
-
1990
- 1990-08-10 JP JP2210212A patent/JPH0499247A/en active Pending
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5443787A (en) * | 1993-07-13 | 1995-08-22 | Tdk Corporation | Method for preparing iron system soft magnetic sintered body |
| KR100960699B1 (en) * | 2008-01-16 | 2010-05-31 | 한양대학교 산학협력단 | Fabrication Method of Fe-Si type soft magnet powder and soft magnet core using the same |
| CN111020410A (en) * | 2019-11-13 | 2020-04-17 | 中国科学院宁波材料技术与工程研究所 | Iron-based nanocrystalline magnetically soft alloy and preparation method thereof |
| CN111020410B (en) * | 2019-11-13 | 2020-11-03 | 中国科学院宁波材料技术与工程研究所 | Iron-based nanocrystalline magnetically soft alloy and preparation method thereof |
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