JPH0310001A - Manufacture of super fine crystal alloy powder - Google Patents
Manufacture of super fine crystal alloy powderInfo
- Publication number
- JPH0310001A JPH0310001A JP1143756A JP14375689A JPH0310001A JP H0310001 A JPH0310001 A JP H0310001A JP 1143756 A JP1143756 A JP 1143756A JP 14375689 A JP14375689 A JP 14375689A JP H0310001 A JPH0310001 A JP H0310001A
- Authority
- JP
- Japan
- Prior art keywords
- alloy powder
- alloy
- producing
- powder
- fine crystal
- 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 56
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 45
- 239000000956 alloy Substances 0.000 title claims abstract description 45
- 239000013078 crystal Substances 0.000 title claims abstract description 23
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 17
- 238000005551 mechanical alloying Methods 0.000 claims abstract description 17
- 229910000808 amorphous metal alloy Inorganic materials 0.000 claims abstract description 10
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 238000000227 grinding Methods 0.000 claims abstract description 7
- 238000010438 heat treatment Methods 0.000 claims abstract description 7
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052715 tantalum Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 239000011261 inert gas Substances 0.000 claims abstract description 4
- 239000003960 organic solvent Substances 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 239000012298 atmosphere Substances 0.000 claims description 5
- 239000000463 material Substances 0.000 claims description 4
- 239000000203 mixture Substances 0.000 abstract description 9
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052751 metal Inorganic materials 0.000 abstract description 5
- 239000002184 metal Substances 0.000 abstract description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 abstract description 4
- 238000007254 oxidation reaction Methods 0.000 abstract description 3
- 150000002739 metals Chemical class 0.000 abstract description 2
- -1 etc. Substances 0.000 abstract 1
- 238000000034 method Methods 0.000 description 5
- 239000002245 particle Substances 0.000 description 5
- 238000002441 X-ray diffraction Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000001816 cooling Methods 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000009692 water atomization Methods 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000000113 differential scanning calorimetry Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 125000001475 halogen functional group Chemical group 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000010298 pulverizing process Methods 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 238000002003 electron diffraction Methods 0.000 description 1
- 238000000635 electron micrograph Methods 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910052732 germanium Inorganic materials 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 229910001004 magnetic alloy Inorganic materials 0.000 description 1
- 238000010299 mechanically pulverizing process Methods 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
- H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
- H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
- H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
- H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
- H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
- H01F1/147—Alloys characterised by their composition
- H01F1/153—Amorphous metallic alloys, e.g. glassy metals
- H01F1/15341—Preparation processes therefor
- H01F1/1535—Preparation processes therefor by powder metallurgy, e.g. spark erosion
Landscapes
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Chemical & Material Sciences (AREA)
- Dispersion Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Powder Metallurgy (AREA)
- Soft Magnetic Materials (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は圧粉磁心や磁気シールド材等の材料として用い
ることのできる軟磁気特性に優れたＦｅ基超微結晶合金
粉末の製造方法に関するものである。[Detailed Description of the Invention] [Industrial Application Field] The present invention relates to a method for producing Fe-based ultrafine crystal alloy powder that has excellent soft magnetic properties and can be used as a material for powder magnetic cores, magnetic shielding materials, etc. It is.
［従来の技術］
少なくとも組織の５０％が微細な結晶粒からなるＦｅ−
Ｃｕ （ＳＬ、Ｂ）−Ｍ系（ＭはＮｂ、Ｗ。[Prior art] At least 50% of the structure consists of fine crystal grains.
Cu (SL, B)-M system (M is Nb, W.
Ｔａ等の元素）Ｆｅ基基磁磁性合金ヨーロッパ公開特許
番号０２７１６５７号公報に開示されている。Elements such as Ta) Fe-based magnetic alloys are disclosed in European Patent Publication No. 0271657.
この合金はＦｅ基であるにもかかわらず低磁歪で、しか
も軟磁気特性に優れているものである。Although this alloy is Fe-based, it has low magnetostriction and excellent soft magnetic properties.
また、上記公報にはこのＦｅ基基磁磁性合金同組成の非
晶質合金リボンを得た後、加熱処理することにより、超
微細な結晶粒からなる組織を得ることによって作製され
ることも開示されている。The above publication also discloses that this Fe-based magnetomagnetic alloy can be produced by obtaining an amorphous alloy ribbon with the same composition and then heat-treating it to obtain a structure consisting of ultrafine crystal grains. has been done.
［本発明が解決しようとする課題］
前記した合金粉末の製造方法では、母合金作製のための
溶解工程および溶湯金属を超急冷する工程を含んでいる
０本発明に係る合金系において、Ｃｕが多量に含まれる
と溶湯のＦｅと分離してしまうため、超急冷においても
強制固溶が不可能となりＣｕが析出し、その結果軟磁気
特性の劣化をもたらす。したがって磁気特性を考慮した
場合には、組成が大幅に限定されてしまう問題点があっ
た。さらに蒸気圧の高い元素やその他のＦｅと固溶しに
くい元素を添加して軟磁性特性の向上図る場合も、組成
制御や均一な組織を有する合金を製造することが難しい
という問題もある。[Problems to be Solved by the Present Invention] The method for producing alloy powder described above includes a melting step for preparing a master alloy and a step of ultra-quenching molten metal.In the alloy system according to the present invention, Cu is If a large amount of Cu is contained, it will separate from Fe in the molten metal, making forced solid solution impossible even during ultra-rapid cooling, causing Cu to precipitate, resulting in deterioration of soft magnetic properties. Therefore, when magnetic properties are taken into consideration, there is a problem in that the composition is significantly limited. Furthermore, even when attempting to improve soft magnetic properties by adding elements with high vapor pressure or other elements that are difficult to form a solid solution with Fe, there are also problems in that it is difficult to control the composition and produce an alloy with a uniform structure.
本発明の目的は、広い組成範囲にわたって製造が容易な
Ｆｅ基超微結晶合金粉末の製造方法を提供することであ
る。An object of the present invention is to provide a method for producing Fe-based ultrafine crystalline alloy powder that can be easily produced over a wide composition range.
［課題を解決するための手段］
本発明はメカニカルアロイングによりＦｅ、 Ｃｕ、Ｍ
（但しＭはＮｂ、 Ｗ、 Ｔａ、 Ｚｒ、 Ｈｆ。[Means for solving the problem] The present invention provides Fe, Cu, M through mechanical alloying.
(However, M is Nb, W, Ta, Zr, Hf.
ＴｉおよびＭｏの群から選ばれた少なくとも１種以上の
元素）を必須元素として含む非晶質合金粉末を作製する
工程と、前記非晶質合金を加熱することにより、組織の
少なくとも５０％が微細な結晶粒からなる合金粉末を得
る工程からなることを特徴とするＦｅ基超超微結晶台金
粉末製造方法である。At least 50% of the structure is made fine by the process of producing an amorphous alloy powder containing as an essential element at least one element selected from the group of Ti and Mo, and by heating the amorphous alloy. This is a method for producing Fe-based ultra-ultrafine crystal base metal powder, which is characterized in that it consists of a step of obtaining an alloy powder consisting of crystal grains.
メカニカルアロイングとは振動ミル、転勤ミル、アトリ
ッシュミルの高エネルギーミルにより、各種金属単体粉
、又は一部分合金粉を調合し、機械的に混合粉砕とた合
金化する方法である。このメカニカルアロイングを上記
Ｆｅ−Ｃｕ−Ｍ系合金に使用し、混合粉砕の条件を代え
ることにより非晶質合金を得ることができる。さらに、
この非晶質合金を加熱することにより軟磁性特性に優れ
たＦｅ基超超微結晶合金粉得ることができる。Mechanical alloying is a method in which various single metal powders or partially alloyed powders are prepared using a high-energy mill such as a vibration mill, transfer mill, or Atlish mill, and are mechanically mixed, ground, and alloyed. An amorphous alloy can be obtained by applying this mechanical alloying to the Fe-Cu-M alloy and changing the mixing and pulverizing conditions. moreover,
By heating this amorphous alloy, it is possible to obtain Fe-based ultra-ultrafine crystalline alloy powder having excellent soft magnetic properties.
この時、非晶質合金化を促進するためにＳｉ。At this time, Si is added to promote amorphous alloying.
Ｂ、Ｐ、Ｃ，Ｇｅ、Ｇａ、Ｓｂ、 Ｉｎ等の元素を添
加する方が好ましい。It is preferable to add elements such as B, P, C, Ge, Ga, Sb, and In.
また、メカニカルアロイングの際に混合粉砕条件を代え
ることによって直接軟磁気特性に優れたＦｅ基超超微結
晶合金粉得ることができる。Further, by changing the mixing and pulverizing conditions during mechanical alloying, it is possible to directly obtain Fe-based ultra-ultrafine crystal alloy powder with excellent soft magnetic properties.
メカニカルアロイングは有機溶媒中例えばメタノール又
はアセトン中で行うことにより合金の酸化の防止とボー
ルミル等の壁面に合金粉等が付着するのを防止できる。Mechanical alloying can be carried out in an organic solvent such as methanol or acetone to prevent oxidation of the alloy and to prevent alloy powder etc. from adhering to the wall surface of a ball mill or the like.
また、メカニカルアロイングを不活性ガス雰囲気または
真空中で行うことにより、酸化による軟磁性特性の劣化
を防止することができる。Furthermore, by performing mechanical alloying in an inert gas atmosphere or vacuum, deterioration of soft magnetic properties due to oxidation can be prevented.
上記メカニカルアロイングに変えてメカニカルグライン
ディングを使用しても同様の効果が得られる。ここでメ
カニカルグラインディングとはあらかじめ高周波溶媒炉
真空溶解炉等により作製した目的組成の合金を機械的に
微粉砕して非晶質粉末あるいは微結晶合金粉末を得る方
法である。Similar effects can be obtained by using mechanical grinding instead of the mechanical alloying described above. Here, mechanical grinding is a method of obtaining an amorphous powder or a microcrystalline alloy powder by mechanically pulverizing an alloy having a desired composition, which has been prepared in advance in a high-frequency solvent furnace, vacuum melting furnace, or the like.
メカニカルグラインディングでは一旦合金化したものを
用いる。但し、全体が均一な組織を有する必要はない。Mechanical grinding uses alloyed materials. However, it is not necessary to have a uniform structure throughout.
メカニカルアロイングおよびメカニカルグラインディン
グにより作製した合金粉末は磁場を印加しながら、ホッ
トプレスなどで圧粉体を作製することで粉末には誘導磁
気異方性が付けることができる。その他、回転磁場中で
熱処理することにより誘導磁気異方性を低減し、軟磁気
特性を改善することが可能である。Alloy powder produced by mechanical alloying and mechanical grinding can be given induced magnetic anisotropy by producing a powder compact by hot pressing or the like while applying a magnetic field. In addition, heat treatment in a rotating magnetic field can reduce induced magnetic anisotropy and improve soft magnetic properties.
実旌肛
ＦｅｂａＱＣｕ、Ｎｂ、Ｓｉ、、、、Ｂ、の組成に純金
属のＦｅ、Ｃｕ、Ｎｂ、ＳＬ、Ｂ粉末を調合後、窒素ガ
ス雰囲気中でボールミルにより２０時間メカニカルアロ
イングした。得られた粉末は２〇−以ドの球状のものが
大部分であった。得られた粉中のＸｇ回折パターンを測
定したところアモルファス合金特有のハローパターを示
した。結晶化温度は示差走査熱量計（Ｄ Ｓ Ｃ）によ
り１０℃／ａ＋ｉｎの昇進速度で測定した場合５０５℃
であった。次いでこの粉末を５０５℃に保った炉に１時
間入れ、５０’Ｃ／ｎ＋ｉｎの冷却速度で室温まで冷却
した。Pure metals Fe, Cu, Nb, SL, and B powders were mixed into the composition of FebaQCu, Nb, Si, . Most of the obtained powder was spherical with a diameter of 20° or smaller. When the Xg diffraction pattern of the obtained powder was measured, it showed a halo pattern peculiar to an amorphous alloy. The crystallization temperature is 505°C when measured by differential scanning calorimetry (DSC) at a rate of increase of 10°C/a+in.
Met. The powder was then placed in a furnace maintained at 505°C for 1 hour and cooled to room temperature at a cooling rate of 50'C/n+in.
得られた粉末のＸ線回折パターンを測定したところ結晶
のピークが認められた１次にこの粉末の組織を透過電子
顕微鏡により観察した。得られた結果を第１図に示す。When the X-ray diffraction pattern of the obtained powder was measured, a crystal peak was observed.The structure of this powder was then observed using a transmission electron microscope. The results obtained are shown in FIG.
組織は大部分が４００〜５００人の粒径の微細な結晶粒
から成っており、Ｘ線回折および電子線回折の結果、こ
の結晶粒はＢ。The structure consists mostly of fine crystal grains with a grain size of 400 to 500 grains, and as a result of X-ray diffraction and electron diffraction, this crystal grain is B.
８１などを固溶したｂｃｃ構造のＦｅ、固溶体であるこ
とが確認された。次に、この粉末の磁気特性を振動型磁
力計（ＶＳＭ）により測定した。飽和磁束密度Ｂｓは１
０５ｋＧ、保磁力Ｈｅは０゜３０ｅであり優れた軟磁気
特性を示した。It was confirmed that this was a solid solution of Fe having a bcc structure in which 81 and the like were dissolved in solid solution. Next, the magnetic properties of this powder were measured using a vibrating magnetometer (VSM). The saturation magnetic flux density Bs is 1
05kG, coercive force He was 0°30e, and exhibited excellent soft magnetic properties.
来育鏝又
ＦｅｂａＱＣｕ、、ｓＮｂ＋、ｓＳｉ＋ｓ、ｓＢｓの組
成の合金を高周波溶解で製造後合金を粒径が１００〜２
００．になるまで粗粉砕し窒素ガス雰囲気中でボールミ
ルにより２５時間かけて、メカニカルブライディングし
た。得られた粉末の粒径は２５１以下の球状のものが大
部分であった。After manufacturing alloys with the compositions of FebaQCu, sNb+, sSi+s, and sBs using high-frequency melting, the alloys have a grain size of 100 to 2.
00. The powder was coarsely pulverized until it became 25 hours and then mechanically brined using a ball mill in a nitrogen gas atmosphere for 25 hours. Most of the obtained powder was spherical with a particle size of 251 particles or less.
得られた粉末のＸ線回折パターンを測定したところ実施
例１と同様のハローパターンであった。When the X-ray diffraction pattern of the obtained powder was measured, it was found to have a halo pattern similar to that of Example 1.
結晶化温度は示差走査熱量計（ＤＳＣ）により１０’Ｃ
／ｍｉｎの昇進速度で測定した場合５１２℃であった。The crystallization temperature was determined to be 10'C by differential scanning calorimetry (DSC).
The temperature was 512° C. when measured at a promotion rate of /min.
次いでこの粉末なＮ８ガス雰囲気中で５０５℃に保った
炉に１時間入れ、５０℃／ｍｉｎの冷却速度で室温まで
冷却した。Next, it was placed in a furnace maintained at 505°C in this powdery N8 gas atmosphere for 1 hour, and cooled to room temperature at a cooling rate of 50°C/min.
得られた粉末のＸ線回折パターンを測定したところ実施
例１に示すような結晶のピークが認められた。透過電子
顕微鏡による観察の結果組織の大部分が３００〜５００
人の粒径の微細な結晶粒からなることが確認された。When the X-ray diffraction pattern of the obtained powder was measured, crystal peaks as shown in Example 1 were observed. As a result of observation using a transmission electron microscope, most of the structure has a diameter of 300 to 500.
It was confirmed that it consists of fine crystal grains with the size of a human grain.
次にこの粉末の磁気特性を振動型磁力計（ＶＳＭ）によ
り測定した。飽和磁束密度Ｂｓは１３゜５ｋＧ、保磁力
Ｈｃは０，７５０ｅが得られた。Next, the magnetic properties of this powder were measured using a vibrating magnetometer (VSM). A saturation magnetic flux density Bs of 13°5 kG and a coercive force Hc of 0,750e were obtained.
宋惠氾
第１表に、水アトマイズ法および本発明に係る製造法で
あるメカニカルアロイング法により作製されて、粒径約
５０−以下の球状のアモルファス合金粉末を窒素雰囲気
中で熱処理して作製した。Song Huifu Table 1 shows that spherical amorphous alloy powders with a particle size of about 50 mm or less were prepared by the water atomization method and the mechanical alloying method, which is a manufacturing method according to the present invention, and were heat-treated in a nitrogen atmosphere.
粒径が約３００〜５００人の超微結晶合金粉末の保磁力
Ｈｃを各組成ごとに比較して示す。表から水アトマイズ
法で作製された合金粉末のＨｃはばらつきが大きいがメ
カニカルアロイングにより作製された合金粉末はＨｅの
ばらつきが小さく、その値も良好な軟磁気特性を示して
いる。これは、Ｃｕを多量に含有している場合、水アト
マイズ法で作製された合金粉末にはＣｕがわずかに析出
して軟磁気特性を劣化させているが、メカニカルアロイ
ングにより作製された合金粉末はＣｕを多量に含有して
いるにもかかわらず、粒度および内部組織が非常に均一
であるためと考えられる。The coercive force Hc of ultrafine crystalline alloy powder having a grain size of about 300 to 500 particles is shown in comparison for each composition. As can be seen from the table, the alloy powder produced by the water atomization method has a large variation in Hc, but the alloy powder produced by mechanical alloying has a small variation in He, and this value also shows good soft magnetic properties. This is because when alloy powders made by water atomization contain a large amount of Cu, a small amount of Cu precipitates and deteriorates the soft magnetic properties, whereas alloy powders made by mechanical alloying This is thought to be because the particle size and internal structure are very uniform despite containing a large amount of Cu.
以下余白
［発明の効果］
本発明によれば特性のばらつきが少ない、軟磁気特性の
優れた合金粉末が得られ、圧粉磁心、等の作製に有効で
ある。Margins below [Effects of the Invention] According to the present invention, an alloy powder with excellent soft magnetic properties with little variation in properties can be obtained, and is effective for producing powder magnetic cores and the like.
第１図は本発明により得られた合金粉末の電子顕微鏡写
真をトレースした図である。
手続乎旧正書（自発）FIG. 1 is a traced electron micrograph of an alloy powder obtained according to the present invention. Proceedings of the Old Orthodox Book (Spontaneous)
Claims (8)
しＭはＮｂ，Ｗ，Ｔａ，Ｚｒ，Ｈｆ，ＴｉおよびＭｏの
群から選ばれた少なくとも１種以上の元素）を必須元素
として含む非晶質合金粉末を作製する工程と、前記非晶
質合金を加熱することにより、組織の少なくとも５０％
が微細な結晶粒からなる合金粉末を得る工程からなるこ
とを特徴とするＦｅ基超微結晶合金粉末の製造方法。(1) Amorphous material containing Fe, Cu, and M (where M is at least one element selected from the group of Nb, W, Ta, Zr, Hf, Ti, and Mo) as essential elements by mechanical alloying By preparing an alloy powder and heating the amorphous alloy, at least 50% of the structure is
1. A method for producing an Fe-based ultrafine crystalline alloy powder, comprising the step of obtaining an alloy powder consisting of fine crystal grains.
しＭはＮｂ，Ｗ，Ｔａ，Ｚｒ，Ｈｆ，ＴｉおよびＭｏの
群から選ばれた少なくとも１種以上の元素）を必須元素
として含む組織の少なくとも５０％が微細な結晶粒から
なる合金粉末を得る工程からなることを特徴とするＦｅ
基超微結晶合金粉末の製造方法。(2) At least one of the structures containing Fe, Cu, and M (where M is at least one element selected from the group of Nb, W, Ta, Zr, Hf, Ti, and Mo) as essential elements by mechanical alloying. Fe characterized by comprising a step of obtaining an alloy powder of which 50% consists of fine crystal grains.
A method for producing a base ultrafine crystalline alloy powder.
特徴とする請求項１又は２に記載のＦｅ基超微結晶合金
粉末の製造方法。(3) The method for producing Fe-based ultrafine crystal alloy powder according to claim 1 or 2, characterized in that the mechanical alloying is performed in an organic solvent.
うことを特徴とする請求項１又は２に記載のＦｅ基超微
結晶合金粉末の製造方法。(4) The method for producing Fe-based ultrafine crystal alloy powder according to claim 1 or 2, wherein the mechanical alloying is performed in an inert gas atmosphere.
Ｍ（但しＭはＮｂ，Ｗ，Ｔａ，Ｚｒ，Ｈｆ，Ｔｉおよび
Ｍｏの群から選ばれた少なくとも１種以上の元素）を必
須元素として含む非晶質合金粉末を作製する工程と、前
記非晶質合金を加熱することにより、組織の少なくとも
５０％が微細な結晶粒からなる合金粉末を得る工程から
なることを特徴とするＦｅ基超微結晶合金粉末の製造方
法。(5) Fe, Cu,
A step of producing an amorphous alloy powder containing M (where M is at least one element selected from the group of Nb, W, Ta, Zr, Hf, Ti, and Mo) as an essential element; 1. A method for producing Fe-based ultrafine-crystalline alloy powder, comprising the step of heating a fine alloy to obtain an alloy powder in which at least 50% of the structure consists of fine crystal grains.
Ｍ（但しＭはＮｂ，Ｗ，Ｔａ，Ｚｒ，Ｈｆ，Ｔｉおよび
Ｍｏの群から選ばれた少なくとも１種以上の元素）を必
須元素として含む組織の少なくとも５０％が微細な結晶
粒からなる合金粉末を得る工程からなることを特徴とす
るＦｅ基超微結晶合金粉末の製造方法。(6) Fe, Cu,
An alloy powder containing M (where M is at least one element selected from the group of Nb, W, Ta, Zr, Hf, Ti, and Mo) as an essential element, in which at least 50% of the structure is composed of fine crystal grains. A method for producing Fe-based ultrafine crystal alloy powder, comprising the steps of obtaining:
ことを特徴とする請求項５又は６に記載のＦｅ基超微結
晶合金粉末の製造方法。(7) The method for producing Fe-based ultrafine crystal alloy powder according to claim 5 or 6, characterized in that the mechanical grinding is performed in an organic solvent.
中で行うことを特徴とする請求項５又は６に記載のＦｅ
基超微結晶合金粉末の製造方法。(8) The Fe according to claim 5 or 6, wherein the mechanical grinding is performed in an inert gas atmosphere.
A method for producing a base ultrafine crystalline alloy powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1143756A JPH0310001A (en) | 1989-06-06 | 1989-06-06 | Manufacture of super fine crystal alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1143756A JPH0310001A (en) | 1989-06-06 | 1989-06-06 | Manufacture of super fine crystal alloy powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0310001A true JPH0310001A (en) | 1991-01-17 |
Family
ID=15346288
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1143756A Pending JPH0310001A (en) | 1989-06-06 | 1989-06-06 | Manufacture of super fine crystal alloy powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0310001A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04329844A (en) * | 1991-04-26 | 1992-11-18 | Agency Of Ind Science & Technol | Manufacture of fine carbide dispersed alloy by using mechanical alloying method |
| JP2013231214A (en) * | 2012-04-27 | 2013-11-14 | Kyb Co Ltd | Method for producing sliding member |
-
1989
- 1989-06-06 JP JP1143756A patent/JPH0310001A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04329844A (en) * | 1991-04-26 | 1992-11-18 | Agency Of Ind Science & Technol | Manufacture of fine carbide dispersed alloy by using mechanical alloying method |
| JP2013231214A (en) * | 2012-04-27 | 2013-11-14 | Kyb Co Ltd | Method for producing sliding member |
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