JPS63166901A - Fe-si-a alloy powder - Google Patents
Fe-si-a alloy powderInfo
- Publication number
- JPS63166901A JPS63166901A JP61313983A JP31398386A JPS63166901A JP S63166901 A JPS63166901 A JP S63166901A JP 61313983 A JP61313983 A JP 61313983A JP 31398386 A JP31398386 A JP 31398386A JP S63166901 A JPS63166901 A JP S63166901A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy powder
- alloy
- blend
- alloyed
- 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.)
- Pending
Links
- 239000000843 powder Substances 0.000 title claims abstract description 107
- 239000000956 alloy Substances 0.000 title claims abstract description 51
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 50
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 11
- 229910002796 Si–Al Inorganic materials 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000011863 silicon-based powder Substances 0.000 claims abstract description 8
- 229910017082 Fe-Si Inorganic materials 0.000 claims abstract description 6
- 229910017133 Fe—Si Inorganic materials 0.000 claims abstract description 6
- 238000005275 alloying Methods 0.000 claims abstract description 4
- 239000010419 fine particle Substances 0.000 claims abstract 3
- 230000001590 oxidative effect Effects 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 abstract description 17
- 239000002184 metal Substances 0.000 abstract description 17
- 238000004519 manufacturing process Methods 0.000 abstract description 6
- 238000002156 mixing Methods 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 5
- 238000000227 grinding Methods 0.000 abstract description 3
- 238000004663 powder metallurgy Methods 0.000 abstract description 3
- 239000011261 inert gas Substances 0.000 abstract description 2
- 238000010907 mechanical stirring Methods 0.000 abstract description 2
- 239000003973 paint Substances 0.000 abstract description 2
- 239000007858 starting material Substances 0.000 abstract 1
- 238000000034 method Methods 0.000 description 15
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 10
- 229910000831 Steel Inorganic materials 0.000 description 9
- 239000010959 steel Substances 0.000 description 9
- 238000005551 mechanical alloying Methods 0.000 description 7
- 239000002245 particle Substances 0.000 description 7
- 229910052786 argon Inorganic materials 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 238000005245 sintering Methods 0.000 description 5
- 239000000498 cooling water Substances 0.000 description 4
- 238000011049 filling Methods 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 230000000630 rising effect Effects 0.000 description 4
- XOOUIPVCVHRTMJ-UHFFFAOYSA-L zinc stearate Chemical compound [Zn+2].CCCCCCCCCCCCCCCCCC([O-])=O.CCCCCCCCCCCCCCCCCC([O-])=O XOOUIPVCVHRTMJ-UHFFFAOYSA-L 0.000 description 4
- 238000000465 moulding Methods 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000010298 pulverizing process Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000009692 water atomization Methods 0.000 description 3
- 241000282326 Felis catus Species 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- 238000009694 cold isostatic pressing Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 229910052753 mercury Inorganic materials 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000007017 scission Effects 0.000 description 1
- 229910000702 sendust Inorganic materials 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000005303 weighing Methods 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〕
本発明は成形性の良好なるＦｅ−Ｓｉ−Ａｌ合金粉末に
関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a Fe-Si-Al alloy powder with good formability.
Ｆｅ−Ｓｉ−Ａｌ合金材料はセンダストの名でよく知ら
れており、高透磁率材料として代表的な材料の１つであ
る。Ｆｅ−Ｓｉ−Ａｌ合金粉末の用途で粉末冶金用、電
磁材用等が要求されている。The Fe-Si-Al alloy material is well known as Sendust, and is one of the typical high magnetic permeability materials. Fe-Si-Al alloy powder is required to be used in powder metallurgy, electromagnetic materials, etc.
従来、粉砕法で粉末を製造する場合、溶湯をインゴット
ケースに鋳込んでインゴットを作製する。Conventionally, when producing powder by a pulverization method, an ingot is produced by pouring molten metal into an ingot case.
インゴットの場合は熱処理を施して粗粉砕する。In the case of ingots, they are heat treated and coarsely ground.
粗粉砕したインゴットを再び粉砕機に入れて粉砕するこ
とによって金属粉末が得られる。しかしながら、前記工
程での金属粉末は硬くて脆い特徴を有しているので通常
のプレスでは成形体を製造するのは非常に難しい粉末で
ある。又、インゴットを作製する時に化学組成の偏析問
題がある。又、経済的に好ましい方法ではない。Metal powder is obtained by putting the coarsely crushed ingot back into the crusher and crushing it. However, since the metal powder used in the above process is hard and brittle, it is very difficult to produce a compact using a normal press. Furthermore, there is a problem of chemical composition segregation when producing ingots. Moreover, it is not an economically preferable method.
水アトマイズ法で製造する場合、金属溶滴を微細に粉砕
するのに噴霧圧力を高く、噴霧氷量を多くすることによ
って不規則状の金属粉末が得られる。しかしながら、水
を使用するために錆の発生の危険性が十分にあり、乾燥
において非常に難しい問題がある。又、前述と同様に成
形体を製造するのは難しい粉末である。When producing by the water atomization method, irregularly shaped metal powder can be obtained by increasing the spray pressure and the amount of sprayed ice to finely pulverize the metal droplets. However, since water is used, there is a significant risk of rust formation, and there are very difficult problems in drying. Further, as mentioned above, it is a powder that is difficult to manufacture into molded bodies.
粉砕法及びアトマイズ法によって得られた粉末を熱間静
水圧法又は、冷間静水圧法によって成形することが可能
であるが経済的に好ましい方法ではない。Although it is possible to mold the powder obtained by the pulverization method and the atomization method by the hot isostatic pressing method or the cold isostatic pressing method, this method is not economically preferable.
混合法で粉末を製造する場合、成形体を製造することが
可能であるが、各種金属粉末の比重が異なるので各種金
属粉末を混合した後、粉末移送の時、又、プレス作業の
振動により粉末の偏析を起こし、出来た成形体は不均一
な化学組成を有しており好ましい方法ではない。When producing powder by the mixing method, it is possible to produce a compact, but since the specific gravity of various metal powders is different, after mixing various metal powders, the powder may be mixed during powder transfer or due to vibrations during press operation. This is not a preferred method because it causes segregation and the resulting molded product has a non-uniform chemical composition.
従って、Ｆｅ−Ｓｉ−Ａｌ合金粉末を通常のプレスで安
定した成形体を製造する方法が望まれている。Therefore, there is a need for a method for producing stable compacts using ordinary pressing of Fe-Si-Al alloy powder.
本発明は前記従来の技術の問題点に留意してなされたも
のであり、Ｆｅ−５ｔ−Ａｌ合金の金属粉末を容易にか
つ節単に製造することを種々検討した結果、各粉末を機
械的に合金化して得られるＦｅ−Ｓｉ−４１合金粉末は
成形体を容易に製造でき、経済的なメリットも十分に得
られるとの知見にもとすき本発明を完成したものである
。The present invention has been made in consideration of the problems of the prior art, and as a result of various studies on how to easily and economically produce Fe-5t-Al alloy metal powder, it is possible to mechanically produce each powder. The present invention was completed based on the knowledge that the Fe-Si-41 alloy powder obtained by alloying can be easily manufactured into compacts and has sufficient economic benefits.
本発明は、Ｆｅ−Ｓｉ合金粉末、Ｆｅ−Ａｌ合金粉末、
Ｆｅ−Ｓｉ−４１合金粉末、Ｆｅ粉末、Ｓｉ粉末、Ａｌ
粉末を用いて１種又は２種以上選び組成が重量パーセン
トでＳｉ ７〜１１％、Ａｌ５〜７％、残部Ｆｅになる
ように配合して、非酸化性の雰囲気で機械的に合金化す
るとともに合金化した微細粒を多孔質状に造粒して得ら
れる、成形性の良好なＦｅ−３ｉ−Ａｌ合金粉末である
。The present invention provides Fe-Si alloy powder, Fe-Al alloy powder,
Fe-Si-41 alloy powder, Fe powder, Si powder, Al
Using powder, one or more types are selected and blended so that the composition is 7 to 11% Si, 5 to 7% Al, and the balance Fe in weight percent, and mechanically alloyed in a non-oxidizing atmosphere. Fe-3i-Al alloy powder with good formability is obtained by granulating alloyed fine grains into a porous shape.
本発明において、従来のＦｅ−３ｉ−４１合金粉末の製
造方法では通常のプレスを用いて成形体を製造すること
は非常に難しいもので、本発明においては、通常のプレ
スを用いて成形体を製造することを可能ならしめる合金
粉末を提供するものである。すなわち高エネルギー密度
を有する機械的攪拌式振動ミルのアトライター（商品名
）や電磁攪拌式振動ミルのリムマック（商品名）などを
使用して製造する方法である。従来からのボールミル、
ロットミルなどと区別している。In the present invention, it is very difficult to produce a compact using a normal press using the conventional method for producing Fe-3i-41 alloy powder. The present invention provides an alloy powder that can be manufactured. That is, this is a manufacturing method using a mechanical stirring type vibrating mill, Atliter (trade name), an electromagnetic stirring type vibrating mill, RIMMAC (trade name), etc., which have high energy density. Traditional ball mill,
It is distinguished from rot mills, etc.
本発明における合金とは、Ｃｕ−Ｐｂ合金、Ｆｅ−Ｐｂ
合金のような全（固溶しない合金は本発明においては合
金とは言わない。The alloy in the present invention refers to Cu-Pb alloy, Fe-Pb
An alloy that does not form a solid solution, such as an alloy, is not referred to as an alloy in the present invention.
本発明において、機械的合金化の前に原料として使用す
るＰｅ−８ｉ合金、Ｆｅ−Ａｌ合金、Ｆｅ粉末、Ｓｉ粉
末、Ａｌ粉末が極力酸化の少ない状態にすることが重要
である。In the present invention, it is important to bring the Pe-8i alloy, Fe-Al alloy, Fe powder, Si powder, and Al powder used as raw materials into a state with as little oxidation as possible before mechanical alloying.
各種金属粉末が酸化した原料を用いて機械的合金化法に
より出来たＦｅ−５ｔ−Ａｌ合金粉末は酸化物の影響が
生じて成形体強度を劣化させる。又、焼結工程における
焼結の進行を防げ良好な焼結体が得られない等の欠点が
ある。Fe-5t-Al alloy powder produced by a mechanical alloying method using raw materials in which various metal powders are oxidized is affected by oxides and deteriorates the strength of the compact. Further, there is a drawback that progress of sintering in the sintering process cannot be prevented and a good sintered body cannot be obtained.
各種金属粉末を原料として使用するにおいて、粗粉末、
例えばＩｎ＋ｍ以上の粉末を使用した場合、Ｆｅ−Ｓｉ
合金粉末、Ｆｅ−Ａｌ合金粉末、Ｓｉ粉末は短時間で細
粉化される。しかし、Ａｌ粉末、Ｆｅ粉末は材料の特性
として展延性を有しているので短時間での細粉化は難し
い。又、機械的合金化も難しい。When using various metal powders as raw materials, coarse powder,
For example, if powder of In+m or more is used, Fe-Si
Alloy powder, Fe-Al alloy powder, and Si powder are pulverized in a short time. However, since Al powder and Fe powder have malleability as a material characteristic, it is difficult to reduce them to fine powder in a short time. Also, mechanical alloying is difficult.
原料として使用する粉末は１４９μｍ以下の細粉を使用
することにより機械的合金化を促進させると同時に微粉
化を進行させて凝集力を増加する。付着凝集した合金粉
末は更に表面平滑化によって球状の多孔質状態に至る。By using fine powder of 149 μm or less as the raw material, mechanical alloying is promoted, and at the same time, pulverization is progressed to increase cohesive force. The surface of the adhered and agglomerated alloy powder is further smoothed, resulting in a spherical porous state.
又、偏析の少ない良好なＦｅ−３ｉ−４１合金粉末が得
られる。時間的にも短縮されるので粉末の酸化も防止で
きる。Moreover, a good Fe-3i-41 alloy powder with little segregation can be obtained. Since the time is shortened, oxidation of the powder can also be prevented.
機械的合金法による製造方法において粉砕機の容器内に
不活性ガス、例えば窒素ガス、アルゴンガスを導入する
ことにより、各種金属粉末が合金化の過程で極力酸化し
ないようにしてＦｅ−Ｓｉ−４１合金粉末の酸化を防止
することができる。In the manufacturing method using the mechanical alloying method, by introducing an inert gas such as nitrogen gas or argon gas into the container of the crusher, various metal powders are prevented from oxidizing as much as possible during the alloying process, and Fe-Si-41 Oxidation of alloy powder can be prevented.
容器内の温度を出来るだけ常温に近い状態で制御するこ
とにより金属粉末の発火、容器の強度の低下を防止する
ことができる。By controlling the temperature inside the container as close to room temperature as possible, it is possible to prevent the metal powder from igniting and reducing the strength of the container.
高エネルギー密度を有する粉砕機、アトライター装置の
容器に各種金属粉末と粉砕ボールを入れて粉砕、混合を
繰り返し行うことによって各種金属粉末は原子レベルに
近い複合化が進行すると同時に各元素は粒子内で均一な
状態で得られる。By putting various metal powders and grinding balls into the container of a grinder or attritor device that has high energy density, and repeating grinding and mixing, the various metal powders become composites close to the atomic level, and at the same time, each element is contained within the particles. obtained in a uniform state.
低エネルギー密度を有する粉砕機、振動式ボールミルに
よって各種金属粉末の粉砕は進行するが複合化までには
至らず各種金属粉末が混合された状態で粒子を形成して
いるので組成的には不均一な状態である。Although various metal powders are pulverized using a pulverizer with low energy density and a vibrating ball mill, they do not become composites, and the particles are formed by mixing various metal powders, so the composition is non-uniform. It is in a state of
本発明の機械的合金化法によるＦｅ−Ｓｉ−Ａｌ粉末の
平均粒径は３０μｍ以下で球状の多孔質状態に造粒され
た合金粉末が得られた。球状の多孔質状態に造粒された
合金粉末はプレスによる圧縮により、微細な粉末が多孔
質粉末の表面に食い込んで成形体を向上させていると考
えられる。The Fe-Si-Al powder obtained by the mechanical alloying method of the present invention had an average particle size of 30 μm or less and was granulated into a spherical porous state. It is thought that the alloy powder granulated into a spherical porous state is compressed by a press, and the fine powder bites into the surface of the porous powder, improving the quality of the compact.
なお、この粉末は機械的合金化処理によって高い冷間ひ
ずみを有しているので場合によっては、水素中又は、真
空中で８００〜１１００℃の範囲でひずみ取りを行う。In addition, since this powder has a high cold strain due to mechanical alloying treatment, the strain may be removed in hydrogen or vacuum at a temperature in the range of 800 to 1100°C.
前述の工程によって得られた球状の多孔質状態に造粒さ
れたＦｅ−Ｓｉ−Ａｌ合金粉末に潤滑剤を添加して通常
のプレスで５〜８ ｔ／ｃａｔで圧縮した結果、５ｔ／
ａｄの成形体はクラックが入り、ハンドリングが難しい
状態であった。６ ｔ／ｃａｌから８ ｔ／ｃｄの成形
体は良好な状態であった。As a result of adding a lubricant to the Fe-Si-Al alloy powder granulated into a spherical porous state obtained by the above process and compressing it with a normal press at 5 to 8 t/cat, 5 t/cat was obtained.
The ad molded product had cracks and was difficult to handle. The molded bodies of 6 t/cal to 8 t/cd were in good condition.
水アトマイズ法で製造した場合、粉末が不規則形状なの
でプレスで圧縮した場合、粉末にクラックが入りやすく
、又室温付近の塑性変形は（００１）面に沿ってへき開
破壊しやすいので、成形体を製造することは難しい。When manufactured by the water atomization method, the powder is irregularly shaped, so when it is compressed with a press, cracks tend to appear in the powder, and plastic deformation near room temperature tends to cause cleavage failure along the (001) plane, so the molded body is Difficult to manufacture.
本発明によって得られた合金粉末は非金属介在物、酸化
物等が殆ど含まれていない成形性の良好な合金粉末であ
る。The alloy powder obtained by the present invention is an alloy powder that contains almost no nonmetallic inclusions, oxides, etc. and has good formability.
以下、本発明の代表的な実施例を示す。 Hereinafter, typical examples of the present invention will be shown.
実施例（１）
７４μｍ以下のＦｅ（５８Ｘ）−３ｉ（４２％）合金粉
末と６３ｐｍ以下のＦｅ （５０χ） −Ａｌ （５０
Ｘ）粉末、６３ ｐ ｍ以下のＦｅ粉末を混合して、組
成が重量パーセントでＳｉ９％、Ａｌ６％、残部Ｆｅに
なるようにＦｅ−３ｉ合金粉末２１．４％、Ｆｅ−Ａｌ
合金粉末１２％、Ｆｅ粉末６６．０％を配合した。次に
アトライター（容量５りに上記のように配合された粉末
を２ｋｇ投入した。アジテータの回転数３００ｒｐｍ
、スチールボール径９ｍｍ 。Example (1) Fe(58X)-3i(42%) alloy powder of 74 μm or less and Fe(50χ)-Al(50
X) Fe-3i alloy powder 21.4%, Fe-Al
12% alloy powder and 66.0% Fe powder were blended. Next, 2 kg of the powder blended as above was added to the attritor (capacity 5).The rotation speed of the agitator was 300 rpm.
, steel ball diameter 9mm.
スチールボール充填型１１５ｋｇ 、アルゴンガス１１
／ｌｌ１ｉｎｉｌ！続導入、容器は冷却水を流して温度
上昇しないようにする。そして３０時間処理した。得ら
れた球状の多孔質合金粉末の平均粒径２２μｍであった
。次に１０００℃、２時間ｌＸｌ０−３ｍｍ ｌ１ｇ以
下の真空雰囲気中で熱処理を行ってひずみ取り焼鈍をし
た。熱処理した合金粉末にステアリン酸亜鉛１％添加し
て混合した。次に直径１２．３ｍｍの金型に合金粉末を
３ｇ投入して油圧式プレスで成形圧力６ｔ／ｃ＋ＩＩで
成形した。圧粉体密度が６．２ｇ／ａｉの成形体が得ら
れた。成形体をｌＸｌ０−’ｍ＋ｎ Ｈｇの真空雰囲気
中で１２５０℃、２時間焼結した結果、焼結体密度６．
０ｇ／ｃ＋ｄの焼結体が得られた。Steel ball filling mold 115kg, argon gas 11
/ll1inil! When introducing a continuous stream, the container should be flushed with cooling water to prevent the temperature from rising. It was then treated for 30 hours. The average particle size of the obtained spherical porous alloy powder was 22 μm. Next, strain relief annealing was performed by heat treatment at 1000° C. for 2 hours in a vacuum atmosphere of 1×10 −3 mm 1 g or less. 1% zinc stearate was added to the heat-treated alloy powder and mixed. Next, 3 g of alloy powder was put into a mold with a diameter of 12.3 mm, and molded using a hydraulic press at a molding pressure of 6 t/c+II. A molded body having a green compact density of 6.2 g/ai was obtained. The compact was sintered at 1250°C for 2 hours in a vacuum atmosphere of lXl0-'m+n Hg, and as a result, the sintered compact density was 6.
A sintered body of 0 g/c+d was obtained.
実施例（２）
７４μｍ以下のＦｅ （９７χ）−Ｓｉ（３χ）合金粉
末と７４μｍ以下のＦｅ （９８χ）−Ａｔ（２χ）合
金粉末、６３．ｃｒｍ以下のＰｅ粉末、６３μｍ以下の
Ｓｉ粉末、６３μｍ以下のＡｌ粉末を混合して、組成が
重量パーセントでＳｉ ９％、Ａｔ６％、残部Ｆｅにな
るようにＦｅ−Ｓｉ合金粉末６０％、Ｆｅ−Ａｌ合金粉
末２０％、Ｆｅ粉末７．２％、Ｓｉ粉末７．２％、■粉
末５．６％を配合した。次にリムマック（容ｆｆｉ ４
Ｚ）に上記のように配合した粉末を１ｋｇ投入した。ス
チールワイヤー径０．５ｍｍ 、長さ２０ｍｍ。Example (2) Fe (97χ)-Si(3χ) alloy powder of 74 μm or less and Fe (98χ)-At(2χ) alloy powder of 74 μm or less, 63. A Fe-Si alloy powder of 60%, Fe- 20% Al alloy powder, 7.2% Fe powder, 7.2% Si powder, and 5.6% ■ powder were blended. Next, Rimmac (Yongffi 4)
1 kg of the powder blended as above was added to Z). Steel wire diameter 0.5mm, length 20mm.
スチールワイヤ充填型ｉｔ ２ｋｇ、スチールワイヤ回
転数６Ｏｒｐｍ／ｓｅｃ 、アルゴンガスを容器内に充
填して密閉する。容器は冷却水を流して温度上昇しない
ようにする。そして３０時間処理した。得られた球状の
多孔質合金粉末の平均粒径２９μｍであった。A steel wire filling type IT weighs 2 kg, the steel wire rotation speed is 6 Orpm/sec, and the container is filled with argon gas and sealed. Run cooling water through the container to prevent the temperature from rising. It was then treated for 30 hours. The average particle size of the obtained spherical porous alloy powder was 29 μm.
次にステアリン酸亜鉛１％添加して混合した。次に直径
１２．３ｍｍの金型に合金粉末を３ｇ投入して油圧式プ
レスで成形圧力８ｔ／ｃＪで成形した。圧粉体密度が６
．１ｇ／ｃｄの成形体が得られた。成形体を水素雰囲気
中で１２５０℃、２時間焼結した結果、焼結体密度５．
９ｇ／ａｄの焼結体が得られた。Next, 1% zinc stearate was added and mixed. Next, 3 g of alloy powder was put into a mold with a diameter of 12.3 mm, and molded using a hydraulic press at a molding pressure of 8 t/cJ. Green density is 6
．． A molded article of 1 g/cd was obtained. As a result of sintering the compact at 1250°C for 2 hours in a hydrogen atmosphere, the sintered compact density was 5.
A sintered body weighing 9 g/ad was obtained.
実施例（３）
７４μｓ以下のＦｅ（７５Ｘ）−Ｓｉ（１０χ）−Ａｌ
（１５χ）合金粉末と６３μ量以下のＦｅ粉末、６３μ
ｍ以下のＳｉ粉末を混合して、組成が重量パーセントで
Ｓｉ ７％、八１６％、残部ＦｅになるようにＦｅ−Ｓ
ｉ−Ａｌ合金粉末４０％、Ｆｅ粉末５７％、Ｓｉ粉末３
％を配合した。次にアトライター（容量５１）に上記の
ように配合した粉末を２ｋｇ投入した。アジテータ−の
回転数３００ｒｐｍ、スチールボール径９ｍｍ、スチー
ルボール充填重量１５ｋｇ、アルゴンガスｌ １ ／ｍ
ｉｎ連続導入、容器は冷却水を流して温度上昇しないよ
うにして、３０時間処理した。得られた球状の多孔質合
金粉末の平均粒径は２５μｍであった。次にステアリン
酸亜鉛１％添加して混合した。次に直径１２．３ｍｍの
金型に合金粉末を３ｇ投入して油圧式プレスで成形圧カ
フｔ／ｃｌＩ！で成形した。圧粉体密度が６．３ｇ／ｃ
ａｌの成形体が得られた。成形体をＩ Ｘ １０−’ｍ
ｎ＋ Ｈｇの真空雰囲気中で１２５０℃、２時間焼結し
た結果、焼結体密度６．１ｇ／ｃｏ！の焼結体が得られ
た。Example (3) 74μs or less Fe(75X)-Si(10χ)-Al
(15χ) alloy powder and Fe powder with an amount of 63μ or less, 63μ
Fe-S is mixed with Si powder of less than
i-Al alloy powder 40%, Fe powder 57%, Si powder 3
% was added. Next, 2 kg of the powder blended as above was put into an attritor (capacity: 51). Agitator rotation speed 300 rpm, steel ball diameter 9 mm, steel ball filling weight 15 kg, argon gas l 1 /m
The treatment was continued for 30 hours, with cooling water flowing through the container to prevent the temperature from rising. The average particle size of the obtained spherical porous alloy powder was 25 μm. Next, 1% zinc stearate was added and mixed. Next, 3g of alloy powder was put into a mold with a diameter of 12.3mm and molded using a hydraulic press. It was molded with. Green density is 6.3g/c
A molded body of al was obtained. The molded body is I x 10-'m
As a result of sintering at 1250°C for 2 hours in an n+ Hg vacuum atmosphere, the sintered body density was 6.1 g/co! A sintered body was obtained.
実施例（４）
Ｆｅ（８５χ）−Ｓｉ（９％）−Ａｌ（６χ）合金粉末
を水アトマイズ法により、１５０μ−以下の合金粉末を
製造して、次にアトライター（容量５１）に合金粉末２
Ｋｇ投入し、アジテータ−の回転数３００ｒｐａｉ、ス
チールボール径９ｍｍ５スチールボール充填重量１５ｋ
ｇ、アルゴンガスｌ ｌ ／ｍｉｎ連続導入、容器は冷
却水を流して温度上昇しないようにして、３０時間処理
した。Example (4) An alloy powder of 150μ or less was produced from Fe(85χ)-Si(9%)-Al(6χ) alloy powder by a water atomization method, and then the alloy powder was placed in an attritor (capacity 51). 2
Kg input, agitator rotation speed 300 rpm, steel ball diameter 9mm, 5 steel balls filling weight 15k.
The treatment was carried out for 30 hours by continuously introducing argon gas at a rate of 1 l/min and by flowing cooling water into the container to prevent the temperature from rising.
得られた球状の多孔質合金粉末の平均粒径は２５μｍで
あった。次にステアリン酸亜鉛１％添加して混合した。The average particle size of the obtained spherical porous alloy powder was 25 μm. Next, 1% zinc stearate was added and mixed.
次に直径１２．３ｍｍｍの金型に合金粉末を３ｇ投入し
て、油圧式プレスで成形圧力８ｔ／ｃｄで成形した。圧
粉体密度が６．２ｇ／ａｎｔの成形体が得られた。成形
体をｌＸｌ０−’ｍｍ Ｉｌｇの真空雰囲気中で１２５
０℃、２時間焼結した結果、焼結体密度６．０ｇ／ｃｆ
ｆｌの焼結体が得られた。Next, 3 g of alloy powder was put into a mold with a diameter of 12.3 mm, and molded using a hydraulic press at a molding pressure of 8 t/cd. A molded body having a green compact density of 6.2 g/ant was obtained. The molded body was heated in a vacuum atmosphere of lXl0-'mm Ilg at 125
As a result of sintering at 0°C for 2 hours, the sintered body density was 6.0 g/cf.
A sintered body of fl was obtained.
以上、説明したように本発明によれば、成形性の良好な
Ｆｅ−Ｓｉ−Ｓ１合金粉末を容易に得ることができる。As described above, according to the present invention, Fe-Si-S1 alloy powder with good formability can be easily obtained.
本発明のＦｅ−５ｔ−Ａｌ合金粉末は粉末冶金用、電磁
材用、塗料用等に好適である。The Fe-5t-Al alloy powder of the present invention is suitable for powder metallurgy, electromagnetic materials, paints, etc.
Claims (1)
−Ｓｉ−Ａｌ合金粉末、Ｆｅ粉末、Ｓｉ粉末、Ａｌ粉末
を用いて、１種又は２種以上選び組成が重量パーセント
でＳｉ７〜１１％、Ａｌ５〜７％、残部Ｆｅになるよう
に配合して、非酸化性の雰囲気で機械的に合金化すると
ともに合金化した微細粒を多孔質状に造粒して得られる
、成形性の良好なＦｅ−Ｓｉ−Ａｌ合金粉末。(1) Fe-Si alloy powder, Fe-Al alloy powder, Fe
- Using Si-Al alloy powder, Fe powder, Si powder, and Al powder, one or more of them are selected and blended so that the composition is 7 to 11% Si, 5 to 7% Al, and the balance is Fe. , Fe-Si-Al alloy powder with good formability, which is obtained by mechanically alloying in a non-oxidizing atmosphere and granulating the alloyed fine particles into a porous shape.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61313983A JPS63166901A (en) | 1986-12-26 | 1986-12-26 | Fe-si-a alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61313983A JPS63166901A (en) | 1986-12-26 | 1986-12-26 | Fe-si-a alloy powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63166901A true JPS63166901A (en) | 1988-07-11 |
Family
ID=18047821
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61313983A Pending JPS63166901A (en) | 1986-12-26 | 1986-12-26 | Fe-si-a alloy powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63166901A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004043633A1 (en) * | 2002-11-13 | 2004-05-27 | Humanelecs Co., Ltd. | Fe-Si ALLOY POWDER CORES AND FABRICATION PROCESS THEREOF |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5271312A (en) * | 1975-12-11 | 1977-06-14 | Nippon Musical Instruments Mfg | Moulding method for pig dust alloy |
-
1986
- 1986-12-26 JP JP61313983A patent/JPS63166901A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5271312A (en) * | 1975-12-11 | 1977-06-14 | Nippon Musical Instruments Mfg | Moulding method for pig dust alloy |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004043633A1 (en) * | 2002-11-13 | 2004-05-27 | Humanelecs Co., Ltd. | Fe-Si ALLOY POWDER CORES AND FABRICATION PROCESS THEREOF |
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