JPH01246341A - Grain dispersion-type alloy and its manufacture - Google Patents
Grain dispersion-type alloy and its manufactureInfo
- Publication number
- JPH01246341A JPH01246341A JP7554888A JP7554888A JPH01246341A JP H01246341 A JPH01246341 A JP H01246341A JP 7554888 A JP7554888 A JP 7554888A JP 7554888 A JP7554888 A JP 7554888A JP H01246341 A JPH01246341 A JP H01246341A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- dispersed
- powder
- graphite
- steel
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 112
- 239000000956 alloy Substances 0.000 title claims abstract description 112
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 47
- 229910002804 graphite Inorganic materials 0.000 claims abstract description 43
- 239000010439 graphite Substances 0.000 claims abstract description 43
- 239000000843 powder Substances 0.000 claims abstract description 38
- 229910000997 High-speed steel Inorganic materials 0.000 claims abstract description 24
- 229910000943 NiAl Inorganic materials 0.000 claims abstract description 16
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000003756 stirring Methods 0.000 claims abstract description 15
- 229910017150 AlTi Inorganic materials 0.000 claims abstract description 10
- 238000004512 die casting Methods 0.000 claims abstract description 10
- 229910000765 intermetallic Inorganic materials 0.000 claims abstract description 10
- 229910000851 Alloy steel Inorganic materials 0.000 claims abstract description 9
- 229910017818 Cu—Mg Inorganic materials 0.000 claims abstract description 8
- 229910010380 TiNi Inorganic materials 0.000 claims abstract description 8
- 239000000919 ceramic Substances 0.000 claims abstract description 8
- 230000003014 reinforcing effect Effects 0.000 claims abstract description 8
- 239000006185 dispersion Substances 0.000 claims abstract description 4
- 229910016583 MnAl Inorganic materials 0.000 claims abstract description 3
- 239000002245 particle Substances 0.000 claims description 78
- 239000011159 matrix material Substances 0.000 claims description 31
- 229910001220 stainless steel Inorganic materials 0.000 claims description 18
- 229910017083 AlN Inorganic materials 0.000 claims 1
- 238000000034 method Methods 0.000 abstract description 13
- 229910001005 Ni3Al Inorganic materials 0.000 abstract description 8
- -1 Al3Ni Inorganic materials 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 5
- 229910052802 copper Inorganic materials 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract 3
- 229910052751 metal Inorganic materials 0.000 abstract 3
- 238000000465 moulding Methods 0.000 abstract 3
- 229910000669 Chrome steel Inorganic materials 0.000 abstract 1
- BSYNRYMUTXBXSQ-UHFFFAOYSA-N Aspirin Chemical compound CC(=O)OC1=CC=CC=C1C(O)=O BSYNRYMUTXBXSQ-UHFFFAOYSA-N 0.000 description 23
- 230000000052 comparative effect Effects 0.000 description 22
- 229910000861 Mg alloy Inorganic materials 0.000 description 10
- 239000002131 composite material Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000005245 sintering Methods 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 239000011651 chromium Substances 0.000 description 4
- 229910000838 Al alloy Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 229910000713 I alloy Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 229940125782 compound 2 Drugs 0.000 description 2
- 238000009770 conventional sintering Methods 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 229910001000 nickel titanium Inorganic materials 0.000 description 2
- 230000002265 prevention Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 101100156949 Arabidopsis thaliana XRN4 gene Proteins 0.000 description 1
- 229940126062 Compound A Drugs 0.000 description 1
- 229910001111 Fine metal Inorganic materials 0.000 description 1
- NLDMNSXOCDLTTB-UHFFFAOYSA-N Heterophylliin A Natural products O1C2COC(=O)C3=CC(O)=C(O)C(O)=C3C3=C(O)C(O)=C(O)C=C3C(=O)OC2C(OC(=O)C=2C=C(O)C(O)=C(O)C=2)C(O)C1OC(=O)C1=CC(O)=C(O)C(O)=C1 NLDMNSXOCDLTTB-UHFFFAOYSA-N 0.000 description 1
- 101100215777 Schizosaccharomyces pombe (strain 972 / ATCC 24843) ain1 gene Proteins 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 229940125904 compound 1 Drugs 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明は、黒鉛、セラミックス、金属間化合物２合金鋼
粒子分散型合金と、その製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to a graphite, ceramic, intermetallic compound 2 alloy steel particle dispersed alloy, and a method for producing the same.
［従来の技術］
アルミニウム合金は軽量で機械的性質に優れているが、
摩耗に弱いという欠点があり、その改善が要求されてい
る。[Prior art] Aluminum alloys are lightweight and have excellent mechanical properties, but
It has the disadvantage of being susceptible to wear, and there is a need to improve this.
アルミニウム合金の耐摩耗性を改善すめる手段として、
様々の方法があるが、その一つとして、素材そのものを
改善する方法がある。As a means to improve the wear resistance of aluminum alloys,
There are various methods, one of which is to improve the material itself.
素材を改善する一つの方法としては、強化粒子をアルミ
ニウム合金中に分散させる方法が知られている。One known method for improving the material is to disperse reinforcing particles into an aluminum alloy.
強化粒子として使用されているものとして、ＮｉＡｌ、
Ａｌ３Ｎｉ、Ｎｉ３Ａｌ、ＡｌＭｎ。Among those used as reinforcing particles are NiAl,
Al3Ni, Ni3Al, AlMn.
Ａ １３ Ｍｎ、 Ａ １４ Ｍｎ、 Ａ Ｔ６ Ｍｎ
。A 13 Mn, A 14 Mn, A T6 Mn
.
ＡｌＴｉ、 ＴｉＮｉ、ハイス１１ｉｌＩ（ＳＫＨｌ
０゜５１．５５，５７＞、高クロム鋼（ＳＫＤｌｌ。AlTi, TiNi, HSS 11ilI (SKHl
0゜51.55,57>, high chromium steel (SKDll.
５ＫＤ６１ＨＬ、Ｄ２ＳＶ）、粉末は高硬度でアリ、Ａ
Ｉ −８ｉ −Ｃｕ−ＭＣＪ系合金粉末のマトリック
ス材とは濡れ性がよく、しかも安定性に優れている。又
、ＡＩＮ粉末は高硬度で黒鉛粉末は潤滑性に冨んでいて
、耐摩耗性向上に有効でめる。5KD61HL, D2SV), powder has high hardness, A
The matrix material of the I-8i-Cu-MCJ alloy powder has good wettability and excellent stability. Furthermore, AIN powder has high hardness and graphite powder has rich lubricating properties, which are effective in improving wear resistance.
従来、複合化方法の一つに焼結法が有るが、これは、母
相の微細金属粉末にセラミックス。One of the conventional composite methods is the sintering method, which uses ceramics in the matrix of fine metal powder.
金属間化合物２合金鋼粉末を添加して機械的撹拌を行な
い、これをプレス成形し、加熱焼結して粒子分散型合金
を製造するもので、加熱焼結したものを押出機、圧延機
により目的とする製品を製造する方法である。Intermetallic Compound 2 Alloy steel powder is added, mechanically stirred, press-formed, and heated and sintered to produce a particle-dispersed alloy. It is a method of manufacturing the desired product.
し発明が解決しようとする課題］
従来の焼結法においては、セラミックス、金属間化合物
、合金鋼粉末と母相合金粉末とを機械的に撹拌混合する
際に、合金鋼粉末に均一に分散混合することは粒子間の
凝集、比重差等の為に困難であった。[Problems to be Solved by the Invention] In conventional sintering methods, when ceramics, intermetallic compounds, alloy steel powder, and matrix alloy powder are mechanically stirred and mixed, it is difficult to uniformly disperse and mix them into the alloy steel powder. It was difficult to do so due to aggregation between particles, differences in specific gravity, etc.
又、プレス成形、加熱焼結にざいして酸化を伴なう為に
、加熱焼結する過程で酸化防止方法、及び装置が必要で
あり、それ故に経費の点でコストアップし、更に加熱焼
結による時には寸法精度の高い製品が得られず、強度的
にも制約がある等の問題点を有している。In addition, since oxidation occurs during press forming and heat sintering, oxidation prevention methods and equipment are required during the heat sintering process, which increases costs and further increases the cost of heat sintering. When using this method, products with high dimensional accuracy cannot be obtained, and there are also problems in terms of strength.
この為、焼結法によらずに粒子が均一に分散した粒子分
散型合金を得ること及びその製造方法を開発することが
切望されている。Therefore, it is strongly desired to obtain a particle-dispersed alloy in which particles are uniformly dispersed without using a sintering method, and to develop a method for producing the same.
本発明は、従来の技術の有するこのような問題点に鑑み
てなされたものであり、その目的とするところは、強化
粒子が母合金マトリックスに均一に分散されていること
により耐摩耗性と機械的特性を有する粒子分散型合金と
、該粒子分散型合金を低コストに大量生産することがで
きる製造方法を提供しようとするものである。The present invention has been made in view of the above-mentioned problems of the conventional technology, and its purpose is to improve wear resistance and mechanical properties by uniformly dispersing reinforcing particles in the master alloy matrix. The purpose of the present invention is to provide a particle-dispersed alloy having excellent characteristics and a manufacturing method that can mass-produce the particle-dispersed alloy at low cost.
［課題を解決する為の手段］
上記目的を達成する為に、本発明の粒子分散型合金は、
ＡＩ −８＋−ｃｕ−ＭＱ系合金をマトリックスとして
、このマトリックスに黒鉛。[Means for Solving the Problems] In order to achieve the above object, the particle dispersed alloy of the present invention has the following features:
AI-8+-cu-MQ alloy is used as a matrix, and graphite is added to this matrix.
ＡＩＮ、ハイス鋼（ＳＫＩ−（５１，５５，５７゜５９
．１０）、高クロムＩ（ＳＫＤＩＩ。AIN, high speed steel (SKI-(51, 55, 57゜59
．． 10), high chromium I (SKDII).
５ＫＤ６１ＨＬ、Ｄ２ＳＶ）、Ｎ ｉＡｌ。5KD61HL, D2SV), N iAl.
Ａｌ３Ｎｉ、Ｎｉ３Ａｌ、ＭｎＡｌ。Al3Ni, Ni3Al, MnAl.
Ａ １３Ｍｎ、 Ａ １４Ｍｎ、 Ａ １６Ｍｎ。A 13Mn, A 14Mn, A 16Mn.
ＴｉＮｉ、ＡｌＴｉ粉末から選ばれる１種以上の強化粉
末を分散させたものである。One or more reinforcing powders selected from TiNi and AlTi powders are dispersed therein.
上記Ａ Ｉ −Ｓｉ −Ｃｕ−ｆＶＩＱ系合金が、Ａ１
−４〜２４ｗｔ％３ ｉ −０，８〜９ｗｔ％Ｃｕ−０
，１５〜５ｗｔ％ＭＣＩであることが効果的である。The above A I -Si -Cu-fVIQ alloy is A1
-4~24wt%3 i -0,8~9wt%Cu-0
, 15 to 5 wt% MCI is effective.
上記ＮｉＡｌ、Ａｌ３Ｎｉ、Ｎｉ３Ａｌ。The above NiAl, Al3Ni, Ni3Al.
ＭｎＡ Ｉ 、 Ａ Ｉ ３ Ｍｎ、 Ａ １４ Ｍｎ
。MnA I, A I 3 Mn, A 14 Mn
.
Ａｌ６Ｍｎ、ＴｉＮ ｉ、ＡｌＴｉ、 ハイス鋼及び高
クロム鋼のうちから選ばれる１種以上の強化粒子の添加
量が４〜ｓｏｗｔ％の範囲で必るとよい。The amount of one or more reinforcing particles selected from Al6Mn, TiNi, AlTi, high speed steel, and high chromium steel is preferably in the range of 4 to sowt%.
上記ＡＩＮ粉末又は黒鉛の添加量が２〜５０ｗｔ％の範
囲であるとよい。It is preferable that the amount of the AIN powder or graphite added is in the range of 2 to 50 wt%.
そして、前記粒子分散型合金の製造方法としては、Ａ
Ｉ −Ｓｉ −Ｃｕ−Ｍｇ系粉末に、セラミックス、黒
鉛、金属間化合物１合金鋼の粉末を直接添加し、撹拌混
合した後、ダイカスト成形することにより前記粉末を均
一にマトリックス中に分散させるようにしたのである。The method for producing the particle-dispersed alloy includes A
Ceramics, graphite, and intermetallic compound 1 alloy steel powder are directly added to the I-Si-Cu-Mg-based powder, stirred and mixed, and then die-cast to uniformly disperse the powder in the matrix. That's what I did.
［作 用］
本発明に用いられるＡ Ｉ −Ｓｉ −Ｃｕ−Ｍｇ系合
金はマトリックスとなるもので必って、代表的にはＡ
Ｉ −Ｓｉ −Ｃｕ−１’ｖＩＪ系合金テアッて、特に
Ａ１−４〜２４ｗｔ％５ｉ−０，８〜９ｗｔ％Ｃｕ −
０，１５〜５ｗｔ％ＭＱ合金が好ましく、他に添加元素
が入ってその機械的性質が改善されたものが好ましい。[Function] The AI-Si-Cu-Mg alloy used in the present invention is necessarily a matrix, and typically A
I-Si-Cu-1'vIJ alloy teat, especially A1-4~24wt%5i-0,8~9wt%Cu-
A 0.15 to 5 wt% MQ alloy is preferred, and one containing other additive elements to improve its mechanical properties is preferred.
この合金は、Ｆｅが０．５〜２．０ｗｔ％である口とが
好ましい。This alloy preferably contains 0.5 to 2.0 wt% Fe.
本発明において、マトリックスにＡｌ−Ｓｉ。In the present invention, the matrix is Al-Si.
−Ｃｕ−Ｍｇ系合金を用いる理由は、この合金が優れた
鋳造性、機械的性質を持つ為である。The reason for using the -Cu-Mg alloy is that this alloy has excellent castability and mechanical properties.
上記Ａ Ｉ −８ｉ −Ｃｕ−ＭＣＪ系合金におイテ、
Ｓｉの含有量が４ｗｔ％未満では機械的性質があまり良
くなく、２４ｗｔ％超でも機械的性質が低下する。It is applied to the above A I-8i-Cu-MCJ alloy,
If the Si content is less than 4 wt%, the mechanical properties are not very good, and if it exceeds 24 wt%, the mechanical properties are deteriorated.
本発明において、上記マトリックス中の分散粒子は、Ｎ
ｉＡｌ、Ａｌ３Ｎｉ、Ｎｉ３Ａｌ。In the present invention, the dispersed particles in the matrix are N
iAl, Al3Ni, Ni3Al.
Ａ ＩＭｎ、Ａ Ｉ３ Ｍｎ、Ａ Ｉ４ Ｍｎ。A IMn, A I3 Mn, A I4 Mn.
Ａｌ６Ｍｎ、ＮｉＴｉ、 ＡｌＴｉ、 ハイス８１Ｍ。Al6Mn, NiTi, AlTi, HSS 81M.
高クロム５ｔｉｌｌ、ＡＩＮ及び黒鉛のうちから選ばれ
る１種以上の粉末である。The powder is one or more selected from high chromium 5till, AIN, and graphite.
金属間化合物、合金鋼粉末を使用する理由は、これらの
粉末がマトリックスの合金に対して濡れ性が良く、しか
も安定性に優れている。The reason why intermetallic compounds and alloy steel powders are used is that these powders have good wettability to the matrix alloy and are excellent in stability.
又、ＡＩＮからなるセラミックス粒子は高硬度であり、
安定性に優れていて、更に黒鉛粒子は潤滑性に富み耐摩
耗性を向上させる。In addition, ceramic particles made of AIN have high hardness,
It has excellent stability, and the graphite particles also have rich lubricity and improve wear resistance.
ＮｉＡｌ、Ａｌ３Ｎｉ、Ｎｉ３Ａｌ。NiAl, Al3Ni, Ni3Al.
Ａ Ｉ Ｍｎ、 Ａ Ｉ ３ Ｍｎ、 Ａ ｌ ４ Ｍ
ｎ。A I Mn, A I 3 Mn, A I 4 M
n.
Ａｌ６Ｍｎ、ＮｉＴｉ、ＡｌＴｉ、高クロム鋼の粒子の
添加量は４〜５０ｗｔ％で必ることが好ましく、より好
ましくは５〜２０ｗｔ％である。The amount of particles of Al6Mn, NiTi, AlTi, and high chromium steel added is preferably 4 to 50 wt%, more preferably 5 to 20 wt%.
前記添加量が４ｗｔ％未満では耐摩耗性の向上効果がな
く、５０ｗｔ％超では撹拌段階で母合金が急激に凝固す
る為に、本発明の製造方法により製造することは困難で
ある。If the amount added is less than 4 wt%, there is no effect of improving wear resistance, and if it exceeds 50 wt%, the master alloy will rapidly solidify during the stirring stage, making it difficult to manufacture by the manufacturing method of the present invention.
一方、ＡＩＮ及び黒鉛粒子の場合、添加量は２〜５０ｗ
ｔ％であることが好ましく、より好ましくは３〜２０ｗ
ｔ％である。On the other hand, in the case of AIN and graphite particles, the amount added is 2 to 50w.
It is preferably t%, more preferably 3 to 20w
t%.
前記添加量が２ｗｔ％未満では耐摩耗性の向上効果がな
く、５０ｗｔ％超では複合化することが困難である。If the amount added is less than 2 wt%, there is no effect of improving wear resistance, and if it exceeds 50 wt%, it is difficult to form a composite.
又、黒鉛を除いた分散粒子の粒子径は
１００μｍ以下が好ましく、より好ましくは５０μｍ以
下である。Further, the particle diameter of the dispersed particles excluding graphite is preferably 100 μm or less, more preferably 50 μm or less.
黒鉛粒子１５０μｍ超の場合は、機械的性質を極めて低
下させる為である。This is because if the graphite particle size exceeds 150 μm, the mechanical properties will be extremely deteriorated.
前記マトリックスへ前記分散粒子が均一に分散されて、
耐摩耗性及びその他の機械的性質に。the dispersed particles are uniformly dispersed in the matrix,
For wear resistance and other mechanical properties.
優れた粒子分散合金が得られる。An alloy with excellent particle dispersion is obtained.
［実 施 例］ 以下に本発明の実施例につき説明する。[Example] Examples of the present invention will be described below.
実施例１
マトリックスであるＡ Ｉ −Ｓｉ −Ｃｕ−Ｍｇ系合
金溶湯中に粒子径が５０μｍ以下のＮｉＡｌ。Example 1 NiAl having a particle size of 50 μm or less is contained in a molten alloy of AI-Si-Cu-Mg as a matrix.
Ａ １３ Ｎ ＋、Ｎ １３ Ａ Ｉ、ＡｌＭｎ、金属
間化合物粉末、ハイス鋼、高クロム鋼、ＡＩＮ、黒鉛粉
末１種以上を添加したものを第１図に例示した撹拌装置
における撹拌槽１に入れ、撹拌羽根２をモーター３にて
回転させて撹拌混合し分散粒子混合合金溶湯３を得る。A mixture containing one or more of A 13 N +, N 13 A I, AlMn, intermetallic compound powder, high speed steel, high chromium steel, AIN, and graphite powder is placed in the stirring tank 1 of the stirring device illustrated in Fig. 1. , the stirring blade 2 is rotated by the motor 3 to stir and mix, thereby obtaining a molten alloy 3 mixed with dispersed particles.
これをダイカストマシンの金型に注渇し、粒子分散型合
金の試験片を鋳ゐした。This was poured into the mold of a die-casting machine, and a test piece of the particle-dispersed alloy was cast.
ハイス鋼、高クロム鋼、ＡＩＮ、ＮｉＡｌ十黒鉛、Ｎｉ
３Ａｌ＋黒鉛、Ａｌ３Ｎｉ＋黒鉛。High speed steel, high chromium steel, AIN, NiAl and graphite, Ni
3Al+graphite, Al3Ni+graphite.
ＡＩＮ＋黒鉛、ハイス鋼士黒鉛、高りロム鋼十黒鉛及び
ＡｌＭｎ粉末を添加して得られる試験片の拡大倍率５０
倍の顕微鏡写真を第２図（ａ）。Magnification magnification of 50 for test pieces obtained by adding AIN + graphite, high-speed steel graphite, high-temperature steel graphite, and AlMn powder
Figure 2(a) is a magnified micrograph.
（ｂ）、 （ｃ）、 （ｄ）、 （ｅ）、 （ｆ）、
（ｇ）、 （ｈｌ （ｉ）、 ＜ｊ）に夫々示す。(b), (c), (d), (e), (f),
(g), (hl (i), <j), respectively.
実施例２
マトリックスであるＡ Ｉ −Ｓｉ −Ｃｕ−Ｍｑ合金
溶湯中に粒子径が５０μｍ以下のＡｌＭｎ。Example 2 AlMn having a particle size of 50 μm or less in a molten A I -Si-Cu-Mq alloy that is a matrix.
ハイス鋼、高クロムＩ、ＡＩＮ粉末を投入添加して撹拌
混合後、ダイカストマシンの金型に溶湯して本発明の粒
子分散型合金で摩耗試験用試験片を鋳造した。High-speed steel, high chromium I powder, and AIN powder were added and stirred and mixed, and then the melt was placed in a mold of a die-casting machine, and a test piece for a wear test was cast using the particle-dispersed alloy of the present invention.
ここでは、母合金としてＡ ｌ−１９ｗｔ％Ｓｉ−７ｗ
ｔ％Ｃｕ−０，４ｗｔ％ＭＣＪ合金を用いた。Here, Al-19wt%Si-7w is used as the mother alloy.
A t%Cu-0.4wt% MCJ alloy was used.
分散粒子としては、ＡＩＭｒｌ、ハイス鋼、高クロム鋼
及びＡＩＮ粉末を用い、ハイス鋼、高クロム鋼は４．１
０ｗｔ％、ＡＩＮ粒子は２． ５ｗｔ％を使用した。As the dispersed particles, AIMrl, high speed steel, high chromium steel, and AIN powder are used, and high speed steel and high chromium steel are 4.1
0 wt%, AIN particles are 2. 5 wt% was used.
比較例としては、分散粒子を含有市内母合金のみのＡ
Ｉ −８ｗｔ％Ｓ ｉ −３ｗｔ％ＣＬＩ −０，２ｖ
ｔ％ＭＣＪ、 Ａ Ｉ −１９ｗｔ％３ ｒ −７ｗｔ
％ＣＬＩ−０．４ｗｔ％ＭＣＩ合金をダイカストマシン
にて摩耗試験片を鋳造した。As a comparative example, A of only the internal master alloy containing dispersed particles is used.
I -8wt%S i -3wt%CLI -0,2v
t%MCJ, A I -19wt%3 r -7wt
%CLI-0.4wt%MCI alloy was cast into wear test pieces using a die casting machine.
第３図（ａ）は、比較例として、Ａ Ｉ −ａｗｔ％３
ｒ −３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＱ合金とＡｌ−
１９ｗｔ％Ｓ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％ＭＱ
合金を用い、本発明例のマトリックスとして、Ａｌ−１
９ｗｔ％３ ｉ −７ｗｔ％ＣＬＩ−０．３ｗｔ％Ｍ（
］合金を用いた。FIG. 3(a) shows A I -awt%3 as a comparative example.
r -3wt%Cu-0,2wt%MQ alloy and Al-
19wt%S i -7wt%Cu-0,3wt%MQ
Al-1 is used as the matrix of the present invention example.
9wt%3i-7wt%CLI-0.3wt%M(
] alloy was used.
本発明例では、ハイス鋼粒子を分散粒子として分散し、
夫々分散粒子の添加量を４．１０ｗｔ％としたものにつ
いてプロットしたグラフである。In the example of the present invention, high-speed steel particles are dispersed as dispersed particles,
It is a graph plotted when the amount of added dispersed particles was 4.10 wt%.
尚、分散粒子の添加量が１０ｗｔ％以上としたものにつ
いてはほぼ１０ｗｔ％で飽和状態に達し、５０ｗｔ％で
同じ値を示したので図示を省略した。In addition, when the amount of dispersed particles added was 10 wt% or more, the saturation state was reached at approximately 10 wt%, and the same value was shown at 50 wt%, so illustration was omitted.
同図により４．Ｉｈｔ％ハイス鋼粒子分散合金は比較例
であるＡ Ｉ −１９ｗｔ％Ｓ １−７ｗｔ％Ｃｕ−０
，３ｗｔ％Ｍｇ合金よりも優れた耐摩耗性を示すことが
わかる。According to the same figure, 4. Iht% high speed steel particle dispersed alloy is a comparative example A I-19wt%S 1-7wt%Cu-0
, 3wt% Mg alloy.
又、ハイス鋼粒子を４ｗｔ％未満含有した場合は、その
粒子分散合金が母合金と同様の比摩耗量を示し、ハイス
鋼粒子を添加することによる耐摩耗性への影響はない。Furthermore, when the high speed steel particles are contained in an amount of less than 4 wt%, the particle-dispersed alloy exhibits the same specific wear amount as the mother alloy, and the addition of the high speed steel particles has no effect on wear resistance.
第３図（ｂ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＱ合金と、Ａ１−
１９ｗｔ％ ３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍ
ｇ合金を用い、本発明例のマトリックスとして、Ａ Ｉ
−１９ｗｔ％ ３ ｉ −７ｗｔ％Ｃｕ−ｏ、３ｗｔ
％Ｍｑ合金を用いた。FIG. 3(b) shows A I -8wt%3 as a comparative example.
i-3wt%Cu-0,2wt%MQ alloy and A1-
19wt% 3 i -7wt%Cu-0,3wt%M
g alloy as the matrix of the present invention example, A I
-19wt% 3 i -7wt%Cu-o, 3wt
%Mq alloy was used.
本発明例では、高クロム鋼粒子を分散粒子として分散し
、夫々分散粒子の添加量を４． ｉｏｗｔ％としたもの
についてプロットしたグラフである。In the example of the present invention, high chromium steel particles are dispersed as dispersed particles, and the amount of each dispersed particle added is 4. It is a graph plotted as iowt%.
尚、分散粒子の添加量がｉｏｗｔ％以上としたものにつ
いては、はぼ１０ｗｔ％で飽和状態に達し、５０ｗｔ％
で同じ値を示したので図示を省略した。In addition, for those in which the amount of dispersed particles added is iowt% or more, the saturated state is reached at about 10wt%, and 50wt%
The illustration was omitted because the values were the same.
同図により、４．１０ｗｔ％、高クロム鋼粒子分散合金
は比較例であるＡ Ｉ −１９ｗｔ％ｓ ｒ −７ｗｔ
％Ｃｕ−０，３ｗｔ％Ｍｇ合金より優れた耐摩耗性を示
すことがわかる。According to the same figure, the 4.10wt% high chromium steel particle dispersed alloy is a comparative example A I -19wt%s r -7wt
It can be seen that the alloy exhibits better wear resistance than the %Cu-0.3wt%Mg alloy.
第３図（Ｃ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％Ｍｇ合金と、Ａ１−
１９ｗｔ％Ｓ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ
合金を用いた。FIG. 3(C) shows A I -8wt%3 as a comparative example.
i-3wt%Cu-0,2wt%Mg alloy and A1-
19wt%Si-7wt%Cu-0,3wt%Mg
Alloy was used.
本発明例のマトリックスとしては、Ａ Ｉ −１９ｗｔ
％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ合金を用
いた。The matrix of the present invention example is A I-19wt
%3i-7wt%Cu-0,3wt%Mg alloy was used.
本発明例では、ＡＩＮ粒子を分散粒子として分散し、夫
々分散粒子の添加量を２． ５ｗｔ％としたものについ
てプロットしたグラフである。In the example of the present invention, AIN particles are dispersed as dispersed particles, and the amount of each dispersed particle added is 2. This is a graph plotted at 5 wt%.
尚、分散粒子の添加量が５ｗｔ％以上としたものについ
ては、はぼ５ｗｔ％で飽和状態に達し、５０ｗｔ％で同
じ値を示したので図示を省略した。In addition, for those in which the amount of dispersed particles added was 5 wt% or more, the saturated state was reached at approximately 5 wt%, and the same value was shown at 50 wt%, so illustration was omitted.
同図により、２． ５ｗｔ％ＡＩＮ粒子分散合金は、比
較例であるＡ Ｉ −１９ｗｔ％３１− ｚｗｔ％Ｃｕ
−０，３ｗｔ％ＭＱ合金より優れた耐摩耗性を示すこと
がわかる。According to the same figure, 2. The 5 wt% AIN particle dispersed alloy is a comparative example of A I-19 wt%31-zwt%Cu
It can be seen that -0.3 wt% MQ alloy exhibits superior wear resistance.
又、ＡＩＮ粒子を２ｗｔ％未満含有した場合は、その粒
子分散合金は母合金と同様の比摩耗量を示し、ＡＩＮ粒
子を添加することによる耐摩耗性への影響はない。Further, when the AIN particles are contained in an amount of less than 2 wt%, the particle-dispersed alloy exhibits the same specific wear amount as the mother alloy, and the addition of the AIN particles has no effect on the wear resistance.
第３図（ｄ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＣＩ合金と、Ａ１
−１９ｗｔ％Ｓ ｒ −３ｗｔ％Ｃｕ−０，３ｗｔ％Ｍ
ｇ合金を用いた。FIG. 3(d) shows A I -8wt%3 as a comparative example.
i-3wt%Cu-0,2wt%MCI alloy and A1
-19wt%S r -3wt%Cu -0,3wt%M
g alloy was used.
本発明例のマトリックスとしては、Ａ Ｉ −１５ｗｔ
％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％ＭＱ合金を用
いた。本発明例では、ＡｌＭｎ粒子を分散粒子として分
散し、夫々分散粒子の添加量をｉｏｗｔ％としたものに
ついてプロットしたグラフである。The matrix of the present invention example is A I-15wt
%3i-5wt%Cu-0,3wt%MQ alloy was used. In the example of the present invention, the graph is a graph in which AlMn particles are dispersed as dispersed particles, and the amount of each dispersed particle added is iowt%.
尚、分散粒子の添加量が４ｗｔ％以上については、はぼ
１０ｗｔ％の値と同様の値を示し、５０ｗｔ％まで同じ
値を示したので図示を省略した。Note that when the amount of added dispersed particles is 4 wt% or more, the values are almost the same as the values at 10 wt%, and the same values are shown up to 50 wt%, so illustration is omitted.
同図により、１０ｗｔ％ＡｌＭｎ粒子分散合金は比較例
であるＡ Ｉ −１９ｗｔ％Ｓ ｉ −７ｗｔ％ＣＵ−
０．３ｗｔ％ＭＣＩ合金より優れた耐摩耗性を示すこと
がわかる。According to the same figure, the 10wt% AlMn particle dispersed alloy is the comparative example A I -19wt%S i -7wt%CU-
It can be seen that it exhibits better wear resistance than the 0.3 wt% MCI alloy.
又、ＡｌＭｎ粒子を４ｗｔ％未満含有した場合は、その
粒子分散合金は母合金と同様の比摩耗量を示し、粒子を
添加することによる耐摩耗性への影響はない。Furthermore, when AlMn particles are contained in an amount of less than 4 wt%, the particle-dispersed alloy exhibits a specific wear amount similar to that of the mother alloy, and the addition of the particles has no effect on wear resistance.
更に、ＡｌＭｎ以外のＡｌ−Ｍｎ系の金属間化合物Ａ
Ｉ３ Ｍｎ、Ａ １４ Ｍｎ、Ａ １６ Ｍｎを添加し
た場合、はぼＡｌＭｎと同様の値を示したので図示を省
略した。Furthermore, Al-Mn-based intermetallic compound A other than AlMn
When I3Mn, A14Mn, and A16Mn were added, the values were similar to those of AlMn, so their illustration was omitted.
実施例３
マトリックスであるＡ Ｉ −Ｓｉ −Ｃｕ−ＭＣＪ系
合金溶湯中に粒子径が１２０μｍ以下の黒鉛粒子を添加
して撹拌混合後、複合化して更にこの黒鉛粒子分散合金
にＮｉＡｌ、Ａｌ３Ｎｉ。Example 3 Graphite particles with a particle size of 120 μm or less were added to a molten alloy of A I -Si -Cu-MCJ as a matrix, mixed with stirring, and then composited, and further NiAl and Al3Ni were added to this graphite particle dispersed alloy.
Ｎ １３Ａ１．ＡＩＮ、ハイス鋼、高クロム鋼粉末を添
加して撹拌混合後、ダイカストマシンに給湯して本発明
の粒子分散型合金の摩耗試験用試験片を鋳造した。N 13A1. After adding AIN, high-speed steel, and high-chromium steel powder and stirring and mixing, hot water was supplied to a die-casting machine to cast a wear test specimen of the particle-dispersed alloy of the present invention.
ここで、この実施例においては、母合金としてＡ Ｉ
−１５ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％Ｍ
ｑ合金を用いた。Here, in this example, A I is used as the master alloy.
-15wt%3i -5wt%Cu-0,3wt%M
q alloy was used.
分散粒子としては黒鉛を最初に添加、複合貸し、この黒
鉛粒子分散合金にＮｉＡｌ、Ａｌ３Ｎｉ、ＮｉＡｌ、ハ
イス鋼、高クロム鋼。Graphite is first added as the dispersed particles, and the graphite particle dispersed alloy is mixed with NiAl, Al3Ni, NiAl, high speed steel, and high chromium steel.
ＡＩＮ粉末を用いてハイス鋼、高クロム鋼。High speed steel and high chromium steel using AIN powder.
ＮｉＡｌ、Ａｌ３Ｎｉ、Ｎｉ３Ａｌは１０ｗｔ％。NiAl, Al3Ni, and Ni3Al are 10 wt%.
ＡＩＮ、黒鉛は５ｗｔ％を使用した。AIN and graphite were used at 5 wt%.
比較例としては、分散粒子を含有しない母合金のみのＡ
Ｉ −８ｗｔ％３ ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ
％ＭＣＩ合金と、Ａ Ｉ −１９ｗｔ％３ ｉ −７ｗ
ｔ％Ｃｕ−０，３ｗｔ％Ｍｇ合金を用いダイカストマシ
ンをより摩耗試験片を鋳造した。As a comparative example, A with only a master alloy containing no dispersed particles
I-8wt%3 i-3wt%Cu-0,2wt
%MCI alloy and A I -19wt%3i -7w
A wear test piece was cast using a die-casting machine using a t%Cu-0.3wt%Mg alloy.
第４図（ａ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｑｕ−０，２ｗｔ％Ｍｇ合金と、Ａ１−
１９ｗｔ％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ
合金を用い、本発明例のマトリックスには、Ａｌ−１５
ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣＩ合
金を用いた。FIG. 4(a) shows A I -8wt%3 as a comparative example.
i-3wt%Qu-0,2wt%Mg alloy and A1-
19wt%3i-7wt%Cu-0,3wt%Mg
The matrix of the present invention example includes Al-15 alloy.
A wt%3i-5wt%Cu-0,3wt%MCI alloy was used.
本発明例では、黒鉛粒子を分散粒子として分散させ、更
に、これにＮｉＡｌを添加し複合合金を製造し、この合
金の摩耗量を測定し、これを滑り速度に対してプロット
したグラフである。In an example of the present invention, graphite particles are dispersed as dispersed particles, NiAl is further added thereto to produce a composite alloy, the amount of wear of this alloy is measured, and this is a graph plotted against the sliding speed.
夫々の分散粒子の添加量は黒鉛５ｗｔ％でほぼ飽和状態
に達示し、黒鉛を２ｗｔ％添加した場合も５ｗｔ％に近
い値を示したので図示を省略した。The amount of each dispersed particle added reached a nearly saturated state at 5 wt % of graphite, and even when 2 wt % of graphite was added, the value was close to 5 wt %, so illustration was omitted.
更に、これに１０ｗｔ％ＮｉＡｌ粉末を添加した。Furthermore, 10 wt% NiAl powder was added to this.
同図により、５ｗ１％Ｃ＋１０ｗｔ％ＮｉＡ１粒子分散
合金は比較例であるＡ Ｉ −ａｗｔ％３１−３ｗｔ％
Ｃｕ−０，２ｗｔ％ＭＣＩ合金、Ａ Ｉ −１９ｗｔ％
３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％ＭＱ合金よりも
優れた耐摩耗性を示すことがわかる。According to the same figure, the 5w1%C+10wt%NiA1 particle dispersion alloy is a comparative example, A I -awt%31-3wt%.
Cu-0,2wt%MCI alloy, AI-19wt%
It can be seen that the alloy exhibits better wear resistance than the 3i-7wt%Cu-0,3wt%MQ alloy.
ＮｉＡ１粒子を４ｗｔ％未満含有した場合は、はぼ母合
金と同様の比摩耗量を示し、ＮｉＡ１粒子を添加するこ
とによる耐摩耗性への影響はない。又５ｗｔ％以上もほ
ぼ１０ｗｔ％に近い値を示し、飽和域に達する。When less than 4 wt% of NiA1 particles are contained, the specific wear amount is similar to that of the parent alloy, and the addition of NiA1 particles has no effect on wear resistance. Moreover, when it is 5 wt% or more, it shows a value close to 10 wt% and reaches the saturation range.
第４図（ｂ）は比較例として、Ａ Ｉ −ａｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％Ｍｇ合金と、Ａ１−
１９ｗｔ％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣ
Ｉ合金を用い、本発明例のマトリックスには、Ａｌ−１
５ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣＩ
合金を用いた。本発明例では、黒鉛粒子を分散させ、更
に、Ａ Ｉ ３ ｘ １粒子を添加し、撹拌混合し、複
合合金を製造し、この合金の摩耗量を測定し、これを滑
り速度に対してプロットしたグラフである。FIG. 4(b) shows A I -awt%3 as a comparative example.
i-3wt%Cu-0,2wt%Mg alloy and A1-
19wt%3i-7wt%Cu-0,3wt%MC
I alloy is used, and the matrix of the present invention example includes Al-1
5wt%3i-5wt%Cu-0,3wt%MCI
Alloy was used. In the example of the present invention, graphite particles are dispersed, and A I 3 x 1 particles are further added, stirred and mixed to produce a composite alloy, the wear amount of this alloy is measured, and this is plotted against the sliding speed. This is a graph.
同図により、５ｗｔ％Ｃ＋１０ｗｔ％Ａ ｌ ３ Ｎ
！粒子分散合金は、５ｗ１％Ｃ＋１０ｗｔ％ＮｉＡ１粒
子分散合金と同様の値を示し、比較例の合金よりも優れ
た耐摩耗性を示すことがわかる。According to the same figure, 5wt%C + 10wt%A l 3 N
! It can be seen that the particle-dispersed alloy exhibits similar values to the 5w1%C+10wt%NiA1 particle-dispersed alloy, and exhibits better wear resistance than the alloy of the comparative example.
第４図（Ｃ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＱ合金と、Ａ１−
１９ｗｔ％３ ｒ −７ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣ
Ｉ合金を用い、本発明例のマトリックスには、Ａｈ１５
ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％ＭＱ合金
を用いた。FIG. 4(C) shows A I -8wt%3 as a comparative example.
i-3wt%Cu-0,2wt%MQ alloy and A1-
19wt%3r-7wt%Cu-0,3wt%MC
I alloy is used, and the matrix of the present invention example includes Ah15
A wt%3i-5wt%Cu-0,3wt%MQ alloy was used.
本発明例では、黒鉛粒子を分散させ、更にＮ ！ ３
Ａ Ｉ粒子を添加し、撹拌混合し、複合合金を製造し、
この合金の摩耗量を測定し、これを滑り速度に対してプ
ロットしたグラフである。In the example of the present invention, graphite particles are dispersed and further N! 3
Add A I particles, stir and mix to produce a composite alloy,
This is a graph obtained by measuring the wear amount of this alloy and plotting it against the sliding speed.
同図により、５ｗｔ％Ｃ＋ １０ｖｔ％Ｎ ｉ３Ａ １
粒子分散合金は、比較例の合金よりも優れた耐摩耗性を
示すことがわかる。According to the same figure, 5wt%C+ 10vt%N i3A 1
It can be seen that the particle dispersed alloy exhibits better wear resistance than the comparative example alloy.
第４図（ｄ）は比較例として、Ａ Ｉ −８ｗｔ％３１
−３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＣＩ合金と、Ａｌ−１
９ｗｔ％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ合
金を用い、本発明例のマトリックスには、Ａｌ−１５Ｗ
１％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣ！合金
を用いた。FIG. 4(d) shows A I -8wt%31 as a comparative example.
-3wt%Cu-0,2wt%MCI alloy and Al-1
9wt%3i-7wt%Cu-0,3wt%Mg alloy was used, and the matrix of the present invention example was Al-15W.
1%3i-5wt%Cu-0,3wt%MC! Alloy was used.
本発明例では、黒鉛粒子を分散させ、更にハイス鋼粒子
を添加し、撹拌混合し、複合合金を製造し、この合金の
摩耗量を測定し、これを滑り速度に対してプロットした
グラフである。In an example of the present invention, graphite particles are dispersed, high-speed steel particles are further added, stirred and mixed to produce a composite alloy, the amount of wear of this alloy is measured, and this is a graph plotted against the sliding speed. .
同図により、５ｗｔ％（：＋１０ｗｔ％ハイス鋼粒子分
散合金は、比較例の合金よりも優れた耐摩耗性を示すこ
とがわかる。The figure shows that the 5wt% (:+10wt%) high-speed steel particle dispersed alloy exhibits better wear resistance than the alloy of the comparative example.
第４図（ｅ）は比較例として、Ａ ＋ −８ｗｔ％３１
−３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＣＩ合金と、Ａｌ−１
９ｗｔ％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％ＭＣＩ
合金を用い、本発明例のマトリックスには、Ａｌ−１５
ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ合金
を用いた。FIG. 4(e) shows A + -8wt%31 as a comparative example.
-3wt%Cu-0,2wt%MCI alloy and Al-1
9wt%3i-7wt%Cu-0,3wt%MCI
The matrix of the present invention example includes Al-15 alloy.
A wt%3i-5wt%Cu-0,3wt%Mg alloy was used.
本発明例では、黒鉛粒子を分散させ、更に高クロム鋼粒
子を添加し、撹拌混合して複合合金を製造し、この合金
の摩耗量を測定し、これを滑り速度に対してプロットし
たグラフである。In the example of the present invention, graphite particles are dispersed, high chromium steel particles are further added, and a composite alloy is produced by stirring and mixing.The amount of wear of this alloy is measured, and this is plotted against the sliding speed in a graph. be.
同図により、黒鉛及び黒鉛＋高クロム鋼粒子を添加する
ことにより比較例の合金よりも優れた耐摩耗性を示す。The figure shows that the addition of graphite and graphite + high chromium steel particles provides better wear resistance than the alloy of the comparative example.
第４図（ｆ）は比較例として、Ａ Ｉ −８ｗｔ％３
ｉ −３ｗｔ％Ｃｕ−０，２ｗｔ％ＭＣＩ合金と、Ａ１
−１９ｗｔ％３ ｉ −７ｗｔ％Ｃｕ−０，３ｗｔ％Ｍ
ｇ合金を用い、本発明例のマトリックスには、Ａｌ−１
５ｗｔ％３ ｉ −５ｗｔ％Ｃｕ−０，３ｗｔ％Ｍｇ合
金を用いた。FIG. 4(f) shows A I -8wt%3 as a comparative example.
i-3wt%Cu-0,2wt%MCI alloy and A1
-19wt%3i -7wt%Cu-0,3wt%M
g alloy is used, and the matrix of the present invention example includes Al-1
A 5wt%3i-5wt%Cu-0,3wt%Mg alloy was used.
本発明例では、黒鉛粒子を分散させ、更にＡＩＮ粒子を
添加し、撹拌混合して複合合金を製造し、この合金の摩
耗量を測定し、これを滑り速度に対してプロットしたグ
ラフである。In an example of the present invention, a composite alloy is manufactured by dispersing graphite particles, further adding AIN particles, stirring and mixing, and the amount of wear of this alloy is measured, and this is a graph plotted against the sliding speed.
同図により、黒鉛及び黒鉛＋ＡＩＮ粒子を添加すること
により比較例の合金よりも優れた耐摩耗性を示す。The figure shows that the addition of graphite and graphite+AIN particles provides better wear resistance than the alloy of the comparative example.
［発明の効果］
以上説明したように、本発明に係る粒子分散型合金にお
いては、ＮｉＡｌ、Ｎ！３ＡＩ。[Effects of the Invention] As explained above, in the particle-dispersed alloy according to the present invention, NiAl, N! 3AI.
Ａ １３ Ｎ、ＭｎＡ Ｉ、Ａｌ３Ｍｎ、Ａ １４ Ｍ
ｎ。A 13 N, MnA I, Al3Mn, A 14 M
n.
Ａｌ６Ｍｎ、ＡｌＴｉ、ＴｉＮｉ、 ハイス鋼。Al6Mn, AlTi, TiNi, high speed steel.
高クロムｉｌｌ、ＡＩＮ及び黒鉛粉末のうちから選。Select from high chromium ill, AIN and graphite powder.
ばれる１種以上の粉末が母合金マトリックスに均一に分
散されていることにより、耐摩耗性を向上させることが
できる効果がある。By uniformly dispersing one or more kinds of powders in the mother alloy matrix, wear resistance can be improved.
そして、本発明の粒子分散型合金の製造方法によれば、
Ｎ Ｉ Ａ ｌ 、 Ｎ ｉ ３ Ａ Ｉ 、 Ａ Ｉ
３ Ｎ ｉ 。According to the method for producing a particle-dispersed alloy of the present invention,
N I A l, N i 3 A I, A I
3 Ni.
Ａ ＩＭｎ、 Ａ Ｉ３ Ｍｎ、 Ａ １４Ｍｎ。A IMn, A I3 Mn, A 14 Mn.
１６Ｍｎ、ＡｌＴｉ、ＴｉＮｉ、 ハイス鋼。16Mn, AlTi, TiNi, high speed steel.
高クロム鋼、ＡＩＮ、黒鉛粉末のうちから選ばれる１種
以上の粉末を添加し、撹拌混合後、ダイカストマシンに
よって凝集することなしに、均一にマトリックスに分散
されている優れた耐摩耗性を有する粒子分散型合金が得
られると共に、ダイカスト鋳造法を利用するので、従来
の焼結、粉末冶金法のように高いコストの表面処理方法
や酸化防止方法及び装置を必要としないので、従来方法
と比較して加工費を低減でき、又、複雑な形状の製品を
容易に製造でき、多くの工程を省略できるので低コスト
に粒子分散型合金を大量生産することができる。One or more powders selected from high chromium steel, AIN, and graphite powder are added, and after stirring and mixing, they are uniformly dispersed in the matrix without agglomeration using a die-casting machine, resulting in excellent wear resistance. In addition to obtaining a particle-dispersed alloy, since die-casting is used, there is no need for high-cost surface treatment methods, oxidation prevention methods, and equipment as in conventional sintering and powder metallurgy methods, which makes it easier to compare with conventional methods. Processing costs can be reduced, products with complex shapes can be easily produced, and many steps can be omitted, making it possible to mass-produce particle-dispersed alloys at low cost.
第１図は本発明に係る粒子分散型合金の製造方法に用い
られる撹拌混合装置の一例を一部断面して示す正面図、
第２図（ａ）、 （ｂ）、 （ｃ）、 （ｄ）。
（ｅ）、 （ｆ）、 （（］）、 （ｈ）、 （ｉ）、
（ｊ）はマトリックスであるＡ Ｉ −８ｉ −Ｃｕ
−ｆＶ１ｇ系合金溶湯中に、ハイス鋼、高クロム鋼、Ａ
ＩＮ、ＮｉＡｌ＋黒鉛。
Ｎｉ３Ａｌ＋黒鉛、Ａｌ３Ｎｉ＋黒鉛、ＡＩＮ十黒鉛、
ハイス鋼士黒鉛、高りロム鋼＋黒鉛及びＡｌＭｎ粉末を
添加して得られた夫々の試験片の倍率５０倍の各顕微鏡
写真、第３図（ａ）、 （ｂ）。
（ｃｌ （ｄ）及び第４図（ａ）、 （ｂ）、 （Ｃ）
、 （ｄ）’、 （ｅ）、げ）は夫々前記試験片の相手
材に対する滑り速度と比摩耗分との関係を夫々示す各グ
ラフである。FIG. 1 is a partially cross-sectional front view of an example of a stirring and mixing device used in the method for producing a particle-dispersed alloy according to the present invention;
Figure 2 (a), (b), (c), (d). (e), (f), ((]), (h), (i),
(j) is the matrix A I -8i -Cu
- High speed steel, high chromium steel, A
IN, NiAl+graphite. Ni3Al+graphite, Al3Ni+graphite, AIN1 graphite,
FIGS. 3(a) and 3(b) are micrographs at a magnification of 50 times of test pieces obtained by adding high-speed steel graphite, high-temperature steel + graphite, and AlMn powder. (cl (d) and Figure 4 (a), (b), (C)
, (d)', (e), and (e) are graphs showing the relationship between the sliding speed of the test piece with respect to the mating material and the specific wear amount, respectively.
Claims (5)
して、このマトリックスに黒鉛、ＡｌＮ、ハイス鋼（Ｓ
ＫＨ５１、５５、５７、５９、１０）、高クロム鋼（Ｓ
ＫＤ１１、Ｄ２ＳＶ、ＳＫＤ６１ＨＬ）、ＮｉＡｌ、Ａ
ｌ＿３Ｎｉ、Ｎｉ＿３Ａｌ、ＭｎＡｌ、Ａｌ＿３Ｍｎ、 Ａｌ＿４Ｍｎ、Ａｌ＿６Ｍｎ、ＴｉＮｉ、ＡｌＴｉ粉末
から選ばれる１種以上の強化粉末を分散させたことを特
徴とする粒子分散型合金。(1) Al-Si-Cu-Mg alloy is used as a matrix, and this matrix contains graphite, AlN, and high-speed steel (S).
KH51, 55, 57, 59, 10), high chromium steel (S
KD11, D2SV, SKD61HL), NiAl, A
A particle-dispersed alloy characterized in that one or more reinforcing powders selected from l_3Ni, Ni_3Al, MnAl, Al_3Mn, Al_4Mn, Al_6Mn, TiNi, and AlTi powders are dispersed therein.
ｗｔ％Ｓｉ−０．８〜９ｗｔ％Ｃｕ−０．１５〜５ｗｔ
％Ｍｇである請求項１記載の粒子分散型合金。(2) Al-Si-Cu-Mg alloy is Ai-4~24
wt%Si-0.8~9wt%Cu-0.15~5wt
% Mg.
ｌ、Ａｌ＿３Ｍｎ、Ａｌ＿４Ｍｎ、 Ａｌ＿６Ｍｎ、ＴｉＮｉ、ＡｌＴｉ、ハイス鋼及び高ク
ロム鋼のうちから選ばれる１種以上の強化粒子の添加量
が４〜５０ｗｔ％の範囲である請求項１、２記載の粒子
分散型合金。(3) NiAl, Al_3Ni, Ni_3Al, MnA
3. The particle dispersion according to claim 1, wherein the amount of reinforcing particles selected from the group consisting of L, Al_3Mn, Al_4Mn, Al_6Mn, TiNi, AlTi, high speed steel, and high chromium steel is in the range of 4 to 50 wt%. mold alloy.
％の範囲である請求項１、２記載の粒子分散型合金。(4) Addition amount of AlN powder or graphite is 2 to 50wt
%.
黒鉛、金属間化合物および合金鋼の粉末を直接添加し、
撹拌混合した後、ダイカスト成形することにより前記粉
末を均一にマトリックス中に分散させることを特徴とす
る粒子分散型合金の製造方法。(5) Ceramics in Al-Si-Cu-Mg powder,
Direct addition of graphite, intermetallic compounds and alloy steel powders,
A method for producing a particle-dispersed alloy, characterized in that the powder is uniformly dispersed in a matrix by stirring and mixing and then die-casting.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7554888A JPH01246341A (en) | 1988-03-28 | 1988-03-28 | Grain dispersion-type alloy and its manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP7554888A JPH01246341A (en) | 1988-03-28 | 1988-03-28 | Grain dispersion-type alloy and its manufacture |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01246341A true JPH01246341A (en) | 1989-10-02 |
Family
ID=13579359
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP7554888A Pending JPH01246341A (en) | 1988-03-28 | 1988-03-28 | Grain dispersion-type alloy and its manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01246341A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5186234A (en) * | 1990-08-16 | 1993-02-16 | Alcan International Ltd. | Cast compsoite material with high silicon aluminum matrix alloy and its applications |
| JP2002155330A (en) * | 2000-11-16 | 2002-05-31 | Oiles Ind Co Ltd | Aluminum alloy for sliding members |
| JP2002155329A (en) * | 2000-11-16 | 2002-05-31 | Oiles Ind Co Ltd | Aluminum alloy for sliding members |
| CN113667862A (en) * | 2021-08-05 | 2021-11-19 | 贵州贵材创新科技股份有限公司 | TiAl intermetallic compound reinforced aluminum-silicon composite material and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56127759A (en) * | 1980-03-07 | 1981-10-06 | Mitsubishi Alum Co Ltd | Preparation of aluminum alloy foil for cathode of aluminum electrolytic condenser |
| JPS5881948A (en) * | 1981-11-11 | 1983-05-17 | Nissan Motor Co Ltd | Aluminum composite material excellent in wear resistance and vibration attenuating capacity |
| JPS61163249A (en) * | 1985-01-12 | 1986-07-23 | Sumitomo Electric Ind Ltd | Wear resisting aluminium composite material and its production |
| JPS6210236A (en) * | 1985-07-09 | 1987-01-19 | Teikoku Piston Ring Co Ltd | Aluminum alloy cylinder |
| JPS6233730A (en) * | 1985-08-02 | 1987-02-13 | Nissan Motor Co Ltd | Wear resistant composite material |
-
1988
- 1988-03-28 JP JP7554888A patent/JPH01246341A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56127759A (en) * | 1980-03-07 | 1981-10-06 | Mitsubishi Alum Co Ltd | Preparation of aluminum alloy foil for cathode of aluminum electrolytic condenser |
| JPS5881948A (en) * | 1981-11-11 | 1983-05-17 | Nissan Motor Co Ltd | Aluminum composite material excellent in wear resistance and vibration attenuating capacity |
| JPS61163249A (en) * | 1985-01-12 | 1986-07-23 | Sumitomo Electric Ind Ltd | Wear resisting aluminium composite material and its production |
| JPS6210236A (en) * | 1985-07-09 | 1987-01-19 | Teikoku Piston Ring Co Ltd | Aluminum alloy cylinder |
| JPS6233730A (en) * | 1985-08-02 | 1987-02-13 | Nissan Motor Co Ltd | Wear resistant composite material |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5186234A (en) * | 1990-08-16 | 1993-02-16 | Alcan International Ltd. | Cast compsoite material with high silicon aluminum matrix alloy and its applications |
| US5394928A (en) * | 1990-08-16 | 1995-03-07 | Alcan International Ltd. | Cast composite material with high-silicon aluminum matrix alloy and its applications |
| JP2002155330A (en) * | 2000-11-16 | 2002-05-31 | Oiles Ind Co Ltd | Aluminum alloy for sliding members |
| JP2002155329A (en) * | 2000-11-16 | 2002-05-31 | Oiles Ind Co Ltd | Aluminum alloy for sliding members |
| CN113667862A (en) * | 2021-08-05 | 2021-11-19 | 贵州贵材创新科技股份有限公司 | TiAl intermetallic compound reinforced aluminum-silicon composite material and preparation method thereof |
| CN113667862B (en) * | 2021-08-05 | 2022-04-19 | 贵州贵材创新科技股份有限公司 | TiAl intermetallic compound reinforced aluminum-silicon composite material and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109072349A (en) | Aluminum alloys containing iron, silicon, vanadium and copper and having a relatively bulky ceramic phase therein | |
| CA2738936A1 (en) | Aluminum alloy powder metal bulk chemistry formulation | |
| EP0171798B1 (en) | High strength material produced by consolidation of rapidly solidified aluminum alloy particulates | |
| JP2018529025A (en) | Composite materials with improved mechanical properties at high temperatures | |
| JP2010043297A (en) | Method for producing ceramic-particle-reinforced aluminum composite material | |
| Puspitasari et al. | Mechanical and physical properties of aluminium-silicon (Al-Si) casting alloys reinforced by Zinc Oxide (ZnO) | |
| JPS63312901A (en) | Heat resistant high tensile al alloy powder and composite ceramics reinforced heat resistant al alloy material using said powder | |
| US4906531A (en) | Alloys strengthened by dispersion of particles of a metal and an intermetallic compound and a process for producing such alloys | |
| JPS61163249A (en) | Wear resisting aluminium composite material and its production | |
| JP4008597B2 (en) | Aluminum-based composite material and manufacturing method thereof | |
| JP2554066B2 (en) | Intermetallic compound particle dispersion-reinforced die-cast composite material and method for producing the same | |
| JPH01246340A (en) | Grain dispersion-type alloy and its manufacture | |
| JP2646212B2 (en) | Intermetallic compound particle dispersion strengthened alloy and method for producing the same | |
| JPH0261023A (en) | Heat-resistant and wear-resistant aluminum alloy material and its manufacture | |
| JPH01247545A (en) | Grain dispersion type alloy and its manufacture | |
| JPS60125345A (en) | Aluminum alloy having high heat resistance and wear resistance and manufacture thereof | |
| JP2609107B2 (en) | Intermetallic compound particle dispersion strengthened alloy and method for producing the same | |
| ZLITINAH et al. | Some new directions in aluminum-based PM materials for automotive applications | |
| JPH1143729A (en) | Method for producing aluminum composite material excellent in high-temperature strength | |
| CN109136723B (en) | Self-propagating synthesis and application of iron-based composite powder | |
| JPH02115341A (en) | Oxide dispersion reinforced alloy | |
| JPS6312133B2 (en) | ||
| CN117921004B (en) | A raw material for thixotropic injection molding of metal materials and its preparation method and application | |
| JPH03264639A (en) | Al alloy product having high strength at high temperature | |
| JPH0320453B2 (en) |