JPH0430452B2 - - Google Patents
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- Publication number
- JPH0430452B2 JPH0430452B2 JP28188585A JP28188585A JPH0430452B2 JP H0430452 B2 JPH0430452 B2 JP H0430452B2 JP 28188585 A JP28188585 A JP 28188585A JP 28188585 A JP28188585 A JP 28188585A JP H0430452 B2 JPH0430452 B2 JP H0430452B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy
- sintered
- density
- particle size
- 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.)
- Expired
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- 239000000843 powder Substances 0.000 claims description 31
- 229910045601 alloy Inorganic materials 0.000 claims description 23
- 239000000956 alloy Substances 0.000 claims description 23
- 229910017061 Fe Co Inorganic materials 0.000 claims description 18
- 238000000034 method Methods 0.000 claims description 18
- 239000002245 particle Substances 0.000 claims description 12
- 229910000531 Co alloy Inorganic materials 0.000 claims description 9
- 239000011812 mixed powder Substances 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 238000005245 sintering Methods 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 238000000889 atomisation Methods 0.000 claims 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 17
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 7
- 239000000696 magnetic material Substances 0.000 description 7
- 230000004907 flux Effects 0.000 description 5
- 239000000314 lubricant Substances 0.000 description 5
- 230000035699 permeability Effects 0.000 description 5
- QVYYOKWPCQYKEY-UHFFFAOYSA-N [Fe].[Co] Chemical compound [Fe].[Co] QVYYOKWPCQYKEY-UHFFFAOYSA-N 0.000 description 4
- 239000010941 cobalt Substances 0.000 description 4
- 229910017052 cobalt Inorganic materials 0.000 description 4
- 238000004663 powder metallurgy Methods 0.000 description 4
- 229910017082 Fe-Si Inorganic materials 0.000 description 3
- 229910017133 Fe—Si Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 229910052739 hydrogen Inorganic materials 0.000 description 3
- 239000001257 hydrogen Substances 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 238000000280 densification Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910000889 permalloy Inorganic materials 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 2
- 229910000976 Electrical steel Inorganic materials 0.000 description 1
- 229910002796 Si–Al Inorganic materials 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 230000005284 excitation Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000005307 ferromagnetism Effects 0.000 description 1
- 239000000289 melt material Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910000702 sendust Inorganic materials 0.000 description 1
- 239000007779 soft material Substances 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
- Soft Magnetic Materials (AREA)
Description
【発明の詳細な説明】
〔発明の概要〕
鉄−コバルト合金粉とコバルト粉との混合粉を
使用することによつて圧粉成形性、焼結性を向上
させた鉄−コバルト焼結合金を得る。[Detailed Description of the Invention] [Summary of the Invention] An iron-cobalt sintered alloy with improved compactability and sinterability by using a mixed powder of iron-cobalt alloy powder and cobalt powder is provided. obtain.
本発明はFe−Co焼結合金に係り、特にFe−Co
合金粉とCo粉を使用するFe−Co焼結合金軟質磁
性材料に関するものである。
The present invention relates to Fe-Co sintered alloys, and particularly to Fe-Co sintered alloys.
The present invention relates to a Fe-Co sintered alloy soft magnetic material using alloy powder and Co powder.
一般に磁気的に軟らかい材料である軟質磁性材
料は透磁率および磁束密度が高い。この軟質磁性
材料は鉄、けい素鋼（Fe−Si）、パーマロイ（Fe
−Ni）、センダスト（Fe−Si−Al）、パーメンジ
ユール（Fe−Co）等の材料がある。
Soft magnetic materials, which are generally magnetically soft materials, have high magnetic permeability and magnetic flux density. This soft magnetic material is made of iron, silicon steel (Fe-Si), permalloy (Fe-Si), and permalloy (Fe-Si).
-Ni), sendust (Fe-Si-Al), and permendile (Fe-Co).
本発明が対象とする鉄・コバルト（Fe−Co）
合金軟質磁性材料はコバルト50％、鉄50％の組成
（重量％）において最高の飽和磁束密度を有し且
つ最大透磁率を示すが冷間加工が困難である。 Iron/cobalt (Fe-Co) targeted by the present invention
Alloy soft magnetic materials have the highest saturation magnetic flux density and maximum magnetic permeability at a composition (wt%) of 50% cobalt and 50% iron, but are difficult to cold work.
そこでバナジウム（Ｖ）を２％添加し、冷間加
工性をわずかに改善した2V−パーメンジユール
（スーパーメンダー）が使用されているが未だ十
分な冷間加工性を有するに至つておらず、なお冷
間加工性改善の要望が高まつている。 Therefore, 2V-Permendeur (Super Mender), which has 2% vanadium (V) added to slightly improve cold workability, is used, but it still does not have sufficient cold workability. Demand for improved workability is increasing.
粉末冶金法は上記のような難加工性材料の製造
方法として有力なものの一つであるが、粉末冶金
で製造したパーメンジユールと、溶製によつて得
られたパーメンジユールを比較すると、従来、前
者のパーメンジユールの磁気的性質、例えば飽和
磁束密度、最大透磁率等が後者のそれと比較して
低いものであつた。 Powder metallurgy is one of the most effective methods for producing difficult-to-process materials such as those mentioned above, but when we compare permendial produced by powder metallurgy and permendial obtained by melting, we find that the former Permendial's magnetic properties, such as saturation magnetic flux density and maximum permeability, were lower than those of the latter.
このように粉末冶金法で製造したパーメンジユ
ールの方が溶製によつて得られた、パーメンジユ
ールより特性が低いのは鉄粉とコバルト粉と潤滑
剤とを混合し、成形し、焼結していたことに起因
するものと思われる。すなわち鉄のコバルト中へ
の拡散係数がコバルトの鉄中への拡散係数よりも
大きいために鉄にカーケンドールボイド
（Kirkendall void）が発生すること、および焼
結温度領域（1150〜1450℃）における鉄・コバル
ト合金の結晶構造（fcc相）に起因する拡散係数
の低さのために焼結工程において緻密化、および
合金としての均一化が不十分で良好な磁気的性質
が得られなかつた。 In this way, permendial manufactured by powder metallurgy has lower properties than permendil obtained by melting, because iron powder, cobalt powder, and lubricant are mixed, molded, and sintered. This seems to be due to this. In other words, Kirkendall voids occur in iron because the diffusion coefficient of iron into cobalt is larger than the diffusion coefficient of cobalt into iron. -Due to the low diffusion coefficient due to the crystal structure (fcc phase) of cobalt alloy, densification and uniformity of the alloy were insufficient during the sintering process, and good magnetic properties could not be obtained.
本発明の目的は粉末冶金法による鉄・コバルト
合金の磁気的性質を改善することであり、良好な
磁気的性質を有する鉄・コバルト系の焼結軟質磁
性材料を提供することにある。 An object of the present invention is to improve the magnetic properties of an iron-cobalt alloy produced by powder metallurgy, and to provide an iron-cobalt-based sintered soft magnetic material having good magnetic properties.
上記の目的は、本発明によれば、実質的にFe
およびCoから成るFe−Co合金粉末とCo粉末との
混合粉末を原料として焼結を行うFe−Co焼結合
金の製造方法であつて、前記Fe−Co合金粉末と
前記Co粉末の平均粒径の比が30：１〜10：３で
あることを特徴とするFe−Co焼結合金の製造方
法によつて達成される。
According to the present invention, the above object is achieved by substantially Fe
A method for producing an Fe-Co sintered alloy, which comprises sintering a mixed powder of Fe-Co alloy powder and Co powder consisting of This is achieved by a method for producing an Fe--Co sintered alloy characterized in that the ratio of
すなわち本発明は磁気的性質の低下を引き起す
原因となる第３元素の添加によらず出発材料とし
て、平均粒径の比が30：１〜10：３であるFe−
Co合金粉末とCo粉末との混合粉末を用いること
により圧粉成形性を向上させFe−Co合金粉とCo
粉の相互拡散係数を調節し焼結体の緻密化、均一
化を向上させたものである。
That is, the present invention does not involve the addition of a third element that causes a decrease in magnetic properties, but instead uses Fe-1 as a starting material, the average particle size ratio of which is 30:1 to 10:3.
By using a mixed powder of Co alloy powder and Co powder, the compactability is improved and Fe-Co alloy powder and Co
This improves the densification and uniformity of the sintered body by adjusting the interdiffusion coefficient of the powder.
本発明において、混合粉末を構成するFe−Co
合金粉末とCo粉末との平均粒径の比を30：１〜
10：３としたのは、焼結時のカーケンドールボイ
ドの発生を防止して高い焼結密度が得られるよう
にFeおよびCoの相互拡散係数を適切に調整する
ためである。この観点から、Fe−Co合金粉末の
平均粒径を10〜30μｍとし、Co粉末の平均粒径を
１〜3μｍとすることが望ましい。 In the present invention, Fe-Co constituting the mixed powder
The average particle size ratio of alloy powder and Co powder is 30:1 ~
The reason for setting the ratio to 10:3 is to appropriately adjust the interdiffusion coefficients of Fe and Co so as to prevent the occurrence of Kirkendall voids during sintering and obtain a high sintered density. From this point of view, it is desirable that the average particle size of the Fe-Co alloy powder be 10 to 30 μm, and the average particle size of the Co powder be 1 to 3 μm.
以下本発明の実施例を説明する。 Examples of the present invention will be described below.
原料粉としてアトマイズ法により得られた平均
粒径10〜30μｍのFe−ｘ重量％Co合金粉（ｘ＝
10，20，30，40）と還元法により得られた平均粒
径１〜3μｍのコバルト粉を用意し、Fe／Coの重
量比が１となるように調製し、さらに潤滑剤とし
て0.75重量％のステアリン酸亜鉛を加えて混合し
た。これらの混合粉を392MPa（4t／cm2）の成形
圧力で外径45mm、内径35mm、厚さ７mmのリング形
状に圧粉成形した。引き継いて400℃の温度で加
熱することにより前述の潤滑剤を圧粉体から蒸発
除去し、次に550〜850℃の温度、水素雰囲気中で
１時間仮焼結し、更に588MPa（6t／cm2）の圧力
で再圧縮成形を行つた。最後にこの仮焼結品をプ
ツシヤー型水素雰囲気炉で1300〜1400℃で１時間
焼結した。上記工程では出発材料をFe−Co合金
粉とCo粉との混合粉を使用した以外は通常の工
程である。得られたFe−Co焼結合金の組成はFe
が45〜55重量％であつた。またこの工程によつて
得られたFe−Co焼結合金の特性は以下に説明す
る比較例と共に説明する。 Fe-x wt% Co alloy powder (x =
10, 20, 30, 40) and cobalt powder with an average particle size of 1 to 3 μm obtained by a reduction method, prepared so that the weight ratio of Fe/Co was 1, and further added 0.75% by weight as a lubricant. of zinc stearate was added and mixed. These mixed powders were compacted into a ring shape having an outer diameter of 45 mm, an inner diameter of 35 mm, and a thickness of 7 mm at a molding pressure of 392 MPa (4 t/cm 2 ). The lubricant mentioned above is then removed by evaporation from the green compact by heating at a temperature of 400℃, followed by pre-sintering for 1 hour in a hydrogen atmosphere at a temperature of 550 to 850℃, and further heated to 588MPa (6t/cm). 2 ) Recompression molding was performed at the pressure. Finally, this pre-sintered product was sintered in a pusher type hydrogen atmosphere furnace at 1300-1400°C for 1 hour. The above process is a normal process except that a mixed powder of Fe--Co alloy powder and Co powder is used as the starting material. The composition of the obtained Fe-Co sintered alloy is Fe
was 45-55% by weight. Further, the characteristics of the Fe-Co sintered alloy obtained by this process will be explained together with comparative examples explained below.
実施例 ２
原料粉としてアトマイズ法により得られた平均
粒径10〜30μｍのFe−ｘ重量％Co合金粉（ｘ＝
10，20，30，40）と還元法により得られた平均粒
径１〜3μｍのコバルト粉を用意し、Fe／Coの重
量比が１となるように調製し、さらに潤滑剤とし
て0.75重量％のステアリン酸亜鉛を加えて混合し
た。これらの混合粉を392MPa（4t／cm2）の成形
圧力で外径45mm、内径35mm、厚さ７mmのリング形
状に圧粉成形した。引き継いて400℃の温度で加
熱することにより前述の潤滑剤を圧粉体から蒸発
除去し、プツシヤー型水素雰囲気炉で1300〜1400
℃で１時間焼結した。得られた材料の特性は実施
例１と同様である。上記工程では仮焼結工程、再
圧縮工程を省略している。このため、製品形状に
制限が少なくなる。さらに、２工程を省略できる
ので作業工程の大幅な短縮が可能となり、コスト
の低下につながる。Example 2 Fe-x wt% Co alloy powder (x =
10, 20, 30, 40) and cobalt powder with an average particle size of 1 to 3 μm obtained by a reduction method, prepared so that the weight ratio of Fe/Co was 1, and further added 0.75% by weight as a lubricant. of zinc stearate was added and mixed. These mixed powders were compacted into a ring shape having an outer diameter of 45 mm, an inner diameter of 35 mm, and a thickness of 7 mm at a molding pressure of 392 MPa (4 t/cm 2 ). The above-mentioned lubricant is then evaporated from the green compact by heating it at a temperature of 400℃, and the powder is heated at a temperature of 1300 to 1400℃ in a pusher-type hydrogen atmosphere furnace.
Sintered at ℃ for 1 hour. The properties of the obtained material are similar to those in Example 1. In the above process, the temporary sintering process and the recompression process are omitted. Therefore, there are fewer restrictions on the product shape. Furthermore, since two steps can be omitted, the work steps can be significantly shortened, leading to a reduction in costs.
上記実施例において平均粒径を20〜30μｍのコ
バルト粉を用いた以外は本比較例の諸条件は同一
である。
The conditions of this comparative example are the same as in the above example except that cobalt powder having an average particle size of 20 to 30 μm was used.
第１図は実施例と比較例（従来例）におけるグ
リーン（圧粉体）密度および焼結密度を示す。グ
リーン密度とは圧粉成形を行つた段階での密度を
意味しており、寸法および重量を測定し、計算に
より密度を求めた。また、焼結密度はJISZ2505
に規定されている「金属焼結体の密度測定方法」
によつて求めた。このようにして求めたそれぞれ
の密度を溶製材のFe−50％Co合金（パーメンジ
ユール
）の密度8.18ｇ／c.c.（R.M.Bozorth：
Ferromagnetism，D.Van Nostrand Co.，Inc.，
P.190（1964））で除して相対密度とした。図−１
から明らかなように粒径の小さなCo粉を使用す
ることにより、グリーン密度および焼結密度とも
大きく向上していることがわかる。次に得られた
焼結合金に励磁コイルおよびサーチコイルを共に
42ターン巻き、最大印加磁場4KA／ｍ（50Oe）に
て直流自記磁束計を用いて、BHヒステリシス曲
線を描き磁束密度、保磁力、および透磁率を測定
した。 FIG. 1 shows the green (green compact) density and sintered density in the example and comparative example (conventional example). Green density means the density at the stage of powder compaction, and the density was determined by measuring the dimensions and weight and calculating. In addition, the sintered density is JISZ2505
"Method for measuring the density of metal sintered bodies" specified in
It was determined by The density of the Fe-50% Co alloy (Permendial) obtained in this way is 8.18 g/cc (RMBozorth:
Ferromagnetism, D. Van Nostrand Co., Inc.
P.190 (1964)) to obtain the relative density. Figure-1
As is clear from the figure, both green density and sintered density are greatly improved by using Co powder with a small particle size. Next, an excitation coil and a search coil are attached to the obtained sintered alloy.
A BH hysteresis curve was drawn and the magnetic flux density, coercive force, and magnetic permeability were measured using a DC self-recording magnetometer with 42 turns of winding and a maximum applied magnetic field of 4 KA/m (50 Oe).
第２図は上記実施例と比較例における磁気的性
質を示す。第２図から明らかなように粒径の小さ
なCo粉を用いることにより、軟質磁性材料とし
て好ましい磁気的性質（高磁束密度、低保磁力、
高透磁率）が向上する。 FIG. 2 shows the magnetic properties of the above example and comparative example. As is clear from Figure 2, by using Co powder with a small particle size, it has favorable magnetic properties (high magnetic flux density, low coercive force, etc.) as a soft magnetic material.
High magnetic permeability) is improved.
以上説明したように本発明によれば、グリーン
密度および焼結密度を高め、その結果として良好
な磁気的性質を有するFe−Co焼結合金を得るこ
とができる。したがつて本発明による焼結軟質磁
性材料を電磁部品に応用すれば、切削加工が非常
に困難なパーメンジユール溶製材を用いるよりも
経済的に有利である。
As explained above, according to the present invention, the green density and the sintered density can be increased, and as a result, an Fe--Co sintered alloy having good magnetic properties can be obtained. Therefore, if the sintered soft magnetic material of the present invention is applied to electromagnetic parts, it is economically more advantageous than using permendial melt material, which is extremely difficult to cut.
第１図は実施例と比較例（従来例）におけるグ
リーン（圧粉体）密度および焼結密度を示し、第
２図は上記実施例と比較例における磁気的特性を
示す。
FIG. 1 shows the green (green compact) density and sintered density in the example and comparative example (conventional example), and FIG. 2 shows the magnetic properties in the above example and comparative example.
Claims (1)
末とCo粉末との混合粉末を原料として焼結を行
うFe−Co焼結合金の製造方法であつて、前記Fe
−Co合金粉末と前記Co粉末の平均粒径の比が
30：１〜10：３であることを特徴とするFe−Co
焼結合金の製造方法。 ２ 前記Fe−Co合金粉末の平均粒径が10〜30μｍ
であり、前記Co粉末の平均粒径が１〜3μｍであ
ることを特徴とする特許請求の範囲第１項に記載
の方法。 ３ 前記Fe−Co合金粉末としてアトマイズ法に
より制造されたFe−Co合金粉末を用い、前記Co
粉末として還元法により製造されたCo粉末を用
いることを特徴とする特許請求の範囲第１項また
は第２項に記載の方法。 ４ 前記混合粉末のFe含有量とCo含有量の重量
比がほぼ１：１であることを特徴とする特許請求
の範囲第１項に記載の方法。[Scope of Claims] 1. A method for producing an Fe-Co sintered alloy in which sintering is performed using a mixed powder of Fe-Co alloy powder and Co powder consisting essentially of Fe and Co, the method comprising:
−The ratio of the average particle size of the Co alloy powder and the Co powder is
Fe-Co characterized by a ratio of 30:1 to 10:3
Method for manufacturing sintered alloy. 2 The average particle size of the Fe-Co alloy powder is 10 to 30 μm
The method according to claim 1, wherein the Co powder has an average particle size of 1 to 3 μm. 3 Using Fe-Co alloy powder produced by an atomization method as the Fe-Co alloy powder,
The method according to claim 1 or 2, characterized in that Co powder produced by a reduction method is used as the powder. 4. The method according to claim 1, wherein the weight ratio of Fe content to Co content in the mixed powder is approximately 1:1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28188585A JPS62142750A (en) | 1985-12-17 | 1985-12-17 | Sintered fe-co alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP28188585A JPS62142750A (en) | 1985-12-17 | 1985-12-17 | Sintered fe-co alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62142750A JPS62142750A (en) | 1987-06-26 |
| JPH0430452B2 true JPH0430452B2 (en) | 1992-05-21 |
Family
ID=17645323
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP28188585A Granted JPS62142750A (en) | 1985-12-17 | 1985-12-17 | Sintered fe-co alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62142750A (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO1989012112A1 (en) * | 1988-05-30 | 1989-12-14 | Kawasaki Steel Corporation | SINTERED MAGNETIC Fe-Co MATERIAL AND PROCESS FOR ITS PRODUCTION |
| JP2022035559A (en) | 2020-08-21 | 2022-03-04 | 株式会社村田製作所 | Composite magnetic body |
-
1985
- 1985-12-17 JP JP28188585A patent/JPS62142750A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62142750A (en) | 1987-06-26 |
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