JPH02173224A - Manufacture of sintered aluminum bronze alloy - Google Patents
Manufacture of sintered aluminum bronze alloyInfo
- Publication number
- JPH02173224A JPH02173224A JP32719188A JP32719188A JPH02173224A JP H02173224 A JPH02173224 A JP H02173224A JP 32719188 A JP32719188 A JP 32719188A JP 32719188 A JP32719188 A JP 32719188A JP H02173224 A JPH02173224 A JP H02173224A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- alloy
- sintering
- alloy powder
- sintered
- 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
- 229910000906 Bronze Inorganic materials 0.000 title claims abstract description 12
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 10
- 239000000843 powder Substances 0.000 claims abstract description 65
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 52
- 239000000956 alloy Substances 0.000 claims abstract description 52
- 238000005245 sintering Methods 0.000 claims abstract description 29
- 229910052802 copper Inorganic materials 0.000 claims abstract description 7
- 229910017767 Cu—Al Inorganic materials 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 5
- 239000011812 mixed powder Substances 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910000967 As alloy Inorganic materials 0.000 claims abstract 2
- 239000000758 substrate Substances 0.000 claims description 4
- 229910000838 Al alloy Inorganic materials 0.000 claims description 3
- 238000000034 method Methods 0.000 abstract description 7
- 239000011159 matrix material Substances 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 230000000694 effects Effects 0.000 description 15
- 239000004570 mortar (masonry) Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 239000010949 copper Substances 0.000 description 6
- 230000001737 promoting effect Effects 0.000 description 6
- 238000005452 bending Methods 0.000 description 5
- 238000004663 powder metallurgy Methods 0.000 description 5
- 229910001096 P alloy Inorganic materials 0.000 description 4
- 238000005275 alloying Methods 0.000 description 4
- 239000010974 bronze Substances 0.000 description 4
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000000465 moulding Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 229910019142 PO4 Inorganic materials 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000004907 flux Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 2
- 239000010452 phosphate Substances 0.000 description 2
- 229910001369 Brass Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000010951 brass Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000010494 dissociation reaction Methods 0.000 description 1
- 230000005593 dissociations Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000001272 pressureless sintering Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明はアルミニウム青銅合金の製造方法に関するもの
であり、より詳しくは粉末冶金法による焼結アルミニウ
ム青銅合金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 an aluminum bronze alloy, and more particularly to a method for producing a sintered aluminum bronze alloy by a powder metallurgy method.
アルミニウム青銅は銅系合金の中でも特に強度。 Aluminum bronze is particularly strong among copper-based alloys.
耐食性２耐摩耗性等に優れ、産業上広く利用されている
。しかし、本合金を粉末冶金法で製造する場合、原料粉
の表面を覆っているＡｌ２Ｏ３皮膜によって粉末同志の
焼結が阻害され、通常の無加圧下における焼結操作では
十分な強度を有する焼結合金が得られない。このため、
フラックスを添加する方法や低融点のＣｕ−Ａｌ合金粉
やＡｌ粉を添加する方法が提案されている。しかしなが
ら、前者の場合、粉末同志の焼結はよく進行するものの
焼結中にフラックスが気化して焼結炉などを腐食し、焼
結炉の寿命を著しく縮め、また後者の場合でも、粉末の
焼結がなお十分でなく、しかも焼結中に発生した液相が
基質中に拡散した後に粗大な孔が残留するため、焼結合
金の強度は甚だ不十分なものである。It has excellent corrosion resistance 2 and wear resistance, and is widely used in industry. However, when this alloy is manufactured using the powder metallurgy method, the Al2O3 film covering the surface of the raw material powder inhibits the sintering of the powders, and the sintered bond has sufficient strength in normal sintering operations under no pressure. I can't get money. For this reason,
A method of adding flux and a method of adding low melting point Cu-Al alloy powder or Al powder have been proposed. However, in the former case, although sintering of the powders progresses well, the flux evaporates during sintering and corrodes the sintering furnace, significantly shortening the life of the sintering furnace. The strength of the sintered alloy is very insufficient, since sintering is still insufficient and coarse pores remain after the liquid phase generated during sintering has diffused into the matrix.
本発明者らは、粉末冶金法における通常の無加圧下での
焼結操作により、焼結アルミニウム青銅合金を製造する
ための方法について種々検討を重ねた結果、本発明を完
成させたものである。The present inventors have completed the present invention as a result of various studies on a method for producing a sintered aluminum-bronze alloy by a normal pressure-free sintering operation in powder metallurgy. .
本発明は、基質を構成する合金粉末がＣｕ−１舎金粉、
Ｃｕ扮、及び１扮より選ばれる１種の粉末もしくは２
種以上からなる混合粉末に、Ｐを０．５ｍａｓｓ％以上
含み、残部がＣｒ、Ｍｎ、Ｆｅ、Ｃｏ、Ｎｉ及びＣｕの
１種以上からなるＰを含む合金粉を１種以上添加し、成
形、焼結することを特徴とする焼結アルミニウム合金の
製造方法である。In the present invention, the alloy powder constituting the substrate is Cu-1 metal powder,
Cu powder, and 1 type of powder selected from 1 powder or 2 powders
Adding one or more types of alloy powder containing P containing 0.5 mass% or more of P and the balance consisting of one or more types of Cr, Mn, Fe, Co, Ni, and Cu to a mixed powder consisting of at least one type, forming, This is a method for producing a sintered aluminum alloy, which is characterized by sintering.
本発明に記載の１合金粉の添加により、アルミニウム青
銅組成の原料粉の焼結が著しく促進する理由については
明確ではないが、Ｐが原料粉の表面に存在するＡｈ（ｈ
皮膜とリン酸塩を形成してこれを破壊し、焼結が促進さ
れるものと推察される。Although it is not clear why the addition of the 1 alloy powder described in the present invention significantly accelerates the sintering of the raw material powder of aluminum bronze composition, it is clear that P is present on the surface of the raw material powder.
It is presumed that the sintering is promoted by forming a film and phosphate and destroying this.
ただし、Ｐは酸素との親和力が大きく、しかも蒸気圧も
高いため、これを単独で添加した場合には、焼結に先立
つ昇温過程において酸化あるいは昇華してしまう。この
ため、本発明では、その活動度を下げる目的で請求の範
囲に記載の金属との合金の形で添加したものである。こ
れらの金属は１）との親和力が比較的大きく、しかも、
アルミニウム青銅基質中にＡＩｚ０３とリン酸塩を形成
するに十分な量のＰを溶解させるだけの解離圧を有する
合金を形成する。However, since P has a large affinity for oxygen and a high vapor pressure, if P is added alone, it will oxidize or sublimate during the temperature raising process prior to sintering. Therefore, in the present invention, it is added in the form of an alloy with the metal described in the claims for the purpose of lowering its activity. These metals have a relatively large affinity with 1), and
An alloy is formed that has a dissociation pressure sufficient to dissolve enough P to form AIz03 and phosphate in the aluminum bronze matrix.
＋ＴＩ記Ｐ合金の組成については、焼結温度においてＰ
合金が液相であれば、萌記へ１□０３皮膜の破壊及び焼
結そのものを促進するため、この意味ではＰ合金の融点
はできるだけ低くなるような組成がよいとは思われるが
、これについてはそれほど厳密さを必要とするものでは
ない。しかし、Ｐ量が０．５ｍａｓｓχを下回るとＰの
・活動度が低下してその効果が発現せず、一方、遊離の
Ｐが生成するような組成域においては、前述のように遊
離のＰが昇温過程において酸化あるいは昇華して、焼結
の促進に対してほとんどその効果を発揮しない。これら
のことがらＰｉが０．５ｍａｓｓ！以下の１合金粉の添
加、または′Ｍ離のＰが生成する組成の１合金粉の添加
は好ましいものとは言えない。+ Regarding the composition of the P alloy in TI, P at the sintering temperature is
If the alloy is in a liquid phase, it will promote the destruction of the Moeki 1□03 film and sintering itself, so in this sense it would be better to have a composition that lowers the melting point of the P alloy as much as possible. does not require much rigor. However, when the amount of P is less than 0.5 massχ, the activity of P decreases and the effect is not expressed.On the other hand, in the composition range where free P is generated, as mentioned above, free P is It oxidizes or sublimates during the temperature rising process and has almost no effect on promoting sintering. These things make Pi 0.5mass! It cannot be said that the following addition of an alloy powder or the addition of an alloy powder having a composition that produces P of 'M separation is preferable.
また、Ｐとの合金元素としては、請求の範囲に記載の金
属元素のうちの１種類に限らず、２種以上を含んでもか
まわない。この場合、それぞれの元素を単独で合金した
場合よりも焼結促進に対する効果が増大する場合がある
。Moreover, the alloying element with P is not limited to one type of the metal elements described in the claims, but may include two or more types. In this case, the effect on promoting sintering may be greater than when each element is alloyed alone.
このような焼結促進効果に対する添加２合金粉の合金元
素の種類、組成の影響に関しては、本発明者らはＰと合
金元素との親和力及びｐｔａ成、即ら合金中のＰの活動
度に関係しているものと推察しているが、これらの関係
について一義的に決定するまでには至っていない。しか
しながら、本発明者らの実験では、焼結促進の効果はＭ
ｎ−１合金粉の場合が最も大きく、従って、添加１合金
粉中のＰの活動度がＭｎ−Ｐ合金中のＰの活動度と同程
度となるような場合に、最も焼結促進の効果が大きくな
るものと推察される。Regarding the influence of the type and composition of the alloying element of the added alloy powder 2 on the sintering promotion effect, the present inventors investigated the affinity between P and the alloying element and the PTA formation, that is, the activity level of P in the alloy. Although we speculate that they are related, we have not reached the point where we can unambiguously determine these relationships. However, in our experiments, the effect of promoting sintering was
The effect of promoting sintering is greatest in the case of n-1 alloy powder, and therefore, when the activity of P in addition 1 alloy powder is comparable to the activity of P in Mn-P alloy, the effect of promoting sintering is greatest. is expected to increase.
１合金粉の添加量については添加される総ＰＭとして焼
結アルミニウム合金全体の０．０１〜２ｍａｓｓ％の範
囲が適当であり、ｐＨがこれ以下では焼結促進の効果が
発現セす、一方、これ以上では焼結合金の脆化をまねく
。Regarding the amount of alloy powder added, it is appropriate that the total PM added is in the range of 0.01 to 2 mass% of the entire sintered aluminum alloy, and if the pH is below this, the effect of promoting sintering will be expressed. If it exceeds this, the sintered alloy will become brittle.
本発明において用いられるＣｕ−Ａ１合金粉、Ｃｕ粉、
Ａｌ扮及び１合金粉の粒度については、なるべ（細かい
方が好ましく、Ｃｕ−Ａｌ合金粉、Ｃｕ扮及びＡｌ粉に
ついては２００μｍ以下、また、１合金粉については１
５０μｍ以下の粉末を用いることが望ましい。Cu-A1 alloy powder used in the present invention, Cu powder,
Regarding the particle size of the Al layer and 1 alloy powder, the finer the finer, the finer the particle size, 200 μm or less for the Cu-Al alloy powder, the Cu layer and the Al powder, and 1
It is desirable to use powder with a diameter of 50 μm or less.
本発明における焼結合金の製造は粉末冶金における一般
的な還元炉を用いた通常の無加圧焼結によって行うこと
が可能であり、焼結雰囲気中の酸素分圧が低ければ低い
ほど、また、焼結温度は基質の融点を上限として高くな
るほど、得られる焼結合金の強度、延性は向上する。The production of the sintered alloy in the present invention can be carried out by ordinary pressureless sintering using a reduction furnace commonly used in powder metallurgy, and the lower the oxygen partial pressure in the sintering atmosphere, the more The higher the sintering temperature is, with the upper limit being the melting point of the substrate, the higher the strength and ductility of the obtained sintered alloy.
なお、本発明においては基本的にはＣｕ−へ１２元系に
対して適用することを想定しているが、アルミニウム青
銅における一般的な合金元素であるＮｉ。Although the present invention is basically intended to be applied to a 12-element system including Cu-, Ni is a common alloying element in aluminum bronze.
Ｆｅ、Ｍｎ等を、合金粉、単体粉あるいは１合金粉の形
で添加してもよく、さらには同様の方法でＺｎを添加す
ることにより、高力黄銅組成の焼結合金の製造にも適用
できる。Fe, Mn, etc. may be added in the form of alloy powder, single powder, or single alloy powder, and by adding Zn in the same way, it can also be applied to the production of sintered alloys with high strength brass composition. can.
次に、本発明の代表的な実施例に一ついて記述する。 Next, one typical embodiment of the present invention will be described.
実施例■
Ｃｕ−８＋ｎａｓｓχＡ１合金粉に２ｍａｓｓＸのＣｒ
−８ｍａｓｓχＰ合金粉を添加して乳鉢中で混合後、成
形圧力６ｔ／ｃＪで幅１０ｍｍ、厚さ３ 、５ｍｍの板
状に圧縮成形し、水素気流中で１０００°Ｃ１時間加熱
した。得られた焼結体は、相対密度９４．０％、引張り
強さ２９ｋｇｆ／＋＋ｕｎ２．硬さｌ１８７９で内側曲
率半径３ｍｍにおける７０°曲げに対して亀裂を発生せ
ず、十分な靭性が認められた。Example ■ 2massX of Cr in Cu-8+nassχA1 alloy powder
-8 mass χP alloy powder was added and mixed in a mortar, then compression molded into a plate shape with a width of 10 mm and a thickness of 3.5 mm at a molding pressure of 6 t/cJ, and heated at 1000° C. for 1 hour in a hydrogen stream. The obtained sintered body had a relative density of 94.0% and a tensile strength of 29 kgf/++un2. With a hardness of 1879, no cracks were generated when bent at 70° with an inner radius of curvature of 3 mm, and sufficient toughness was observed.
実施例■
Ｃｕ−８ｍａｓｓχＡ１合金粉に２ｍａｓｓ％のＭｎ−
５，５ｍａｓｓＸＰ合金粉を添加して乳鉢中で混合後、
実施例■と回し方法で成形、焼結した。得られた焼結体
、は相対密度９７．４χ、引張り強さ４３ｋｇｆ／ｍｍ
２．硬さＩＩ、＋９５で内側曲率半径３ｍｍにおける１
８０°曲げに対して亀裂を発生せず、十分な靭性が認め
られた。Example ■ 2 mass% Mn- in Cu-8 mass χA1 alloy powder
After adding 5,5 massXP alloy powder and mixing in a mortar,
It was molded and sintered in the same manner as in Example (2). The obtained sintered body had a relative density of 97.4χ and a tensile strength of 43 kgf/mm.
2. 1 at hardness II, +95 and inner radius of curvature 3 mm
No cracks occurred when bent at 80°, and sufficient toughness was observed.
実施例■
Ｃｕ−８ｍａｓｓ％ＡＩ合金粉に２ｍａｓｓ％のＦｅ−
１０Ｆｅ−１ＯＰ合金粉を添加して乳鉢中で混合後、実
施例■と同じ方法で成形、焼結した。得られた焼結体は
、相対密度９６χ、引張り強さ３２ｋｇｆ／ｎ＋ｍ”、
硬さ＋＋ａ８０で内側曲率半径３＋ｒ＋ｍにおける９０
°曲げに対して亀裂を発生せず、十分な靭性が認められ
た。Example ■ 2 mass% Fe- to Cu-8 mass% AI alloy powder
After adding 10Fe-1OP alloy powder and mixing in a mortar, it was molded and sintered in the same manner as in Example (2). The obtained sintered body had a relative density of 96χ, a tensile strength of 32 kgf/n+m'',
Hardness ++ a 80 and inner radius of curvature 3 + r + m 90
°No cracks occurred during bending, and sufficient toughness was observed.
実施例■
Ｃｕ−８ｍａｓｓＸＡ１合金粉に２ｍａｓｓ％のＣｏ４
２ｍａｓｓ％Ｐ合金粉を添加して乳鉢中で混合後、実施
例■と同じ方法で成形、焼結した。得られた焼結体は、
相対密度９６χ、引張り強さ３１ｋｇｆ／ｍｍ”、硬さ
ｔ＋ ｍ ８１で内側曲率半径３ｍｍにおける９０°曲
げに対して亀裂を発生せず、十分な靭性が認められた。Example ■ 2mass% Co4 in Cu-8massXA1 alloy powder
After adding 2 mass% P alloy powder and mixing in a mortar, it was molded and sintered in the same manner as in Example (2). The obtained sintered body is
It had a relative density of 96χ, a tensile strength of 31 kgf/mm'', a hardness of t+m of 81, and exhibited sufficient toughness with no cracking when bent at 90° at an inner radius of curvature of 3 mm.
実施例■
Ｃｕ−８ｍａｓｓχＡ１合金粉に２ｍａｓｓ％のＮｉ−
１Ｎｉ−１Ｏ’ｔＰ合金粉を添加して乳鉢中で混合後、
実施例■と同じ方法で成形、焼結した。得られた焼結体
は、相対密度９７χ、引張り強さ３５ｋｇｆ／ｍｍ２．
硬さ１１．８５で内側曲率半径３ｍｍにおける１４０°
曲げに対して亀裂を発生せず、十分な靭性が認められた
。Example ■ 2 mass% Ni- in Cu-8 mass χA1 alloy powder
After adding 1Ni-1O'tP alloy powder and mixing in a mortar,
It was molded and sintered in the same manner as in Example (2). The obtained sintered body had a relative density of 97χ and a tensile strength of 35 kgf/mm2.
140° at hardness 11.85 and inner radius of curvature 3mm
No cracks occurred during bending, and sufficient toughness was observed.
実施例■
Ｃｕ−８ｍａｓｓ！Ａ １合金粉に２ｍａｓｓ％のＣｕ
−１４ｍａｓｓχＰ合金粉を添加して乳鉢中で混合後、
実施例■と同し方法で成形、焼結した。得られた焼結体
は、相対密度９７．８χ、引張り強さ３５ｋｇｆ／ｍｍ
２．硬さＨ３８４で内側曲率半径３ｍｍにおける１４０
°曲げに対して亀裂を発生せず、十分な靭性が認められ
た。Example ■ Cu-8mass! A 2 mass% Cu in 1 alloy powder
- After adding 14massχP alloy powder and mixing in a mortar,
It was molded and sintered in the same manner as in Example (2). The obtained sintered body has a relative density of 97.8χ and a tensile strength of 35 kgf/mm.
2. 140 at hardness H384 and inner radius of curvature 3mm
°No cracks occurred during bending, and sufficient toughness was observed.
実施例■
Ｃｕ−８ｍａｓｓＸＡＩ合金粉に２ｍａｓｓ％のＮｉ−
１３ｍａｓｓχＣｒ−１Ｃｒ−１ＯχＰ合金粉を添加し
て乳鉢中で混合後、実施例■と同じ方法で成形、焼結し
た。得られた焼結体は、相対密度９８．４χ１引張り強
さ４４ｋｇｆ／ｎ＋ｎ＋２、硬さ１１８９５で内側曲率
半径３ｍｍにおける１８０°曲げに対して亀裂を発生せ
ず、著しい靭性が認められた。Example ■ 2 mass% Ni- in Cu-8 mass XAI alloy powder
13 mass χCr-1Cr-1OχP alloy powder was added and mixed in a mortar, followed by molding and sintering in the same manner as in Example (2). The obtained sintered body had a relative density of 98.4x1, a tensile strength of 44 kgf/n+n+2, and a hardness of 11895, and exhibited remarkable toughness without cracking when bent at 180° at an inner radius of curvature of 3 mm.
実施例■
Ｃｕ−１Ｃｕ−１ｌχＡ１合金扮とＣｏ扮の４：１混合
粉に対しＭｎ−８ｍａｓｓχＰ合金粉を２χ添加して乳
鉢中で混合後、実施例■と同じ方法で成形、焼結した。Example (2) To a 4:1 mixed powder of Cu-1Cu-11xA1 alloy and Co, 2x of Mn-8massxP alloy powder was added and mixed in a mortar, followed by molding and sintering in the same manner as in Example (2).
得られた焼結体は、相対密度９８．７χ、引張り強さ４
２ｋｇｆ／ｍｍ２゜硬さｌＩ＋９４で内側曲率半径３ｍ
ｍにおける１８０°曲げに対して亀裂を発生せず、著し
い靭性が認められた。The obtained sintered body had a relative density of 98.7χ and a tensile strength of 4.
2kgf/mm2゜hardness lI+94, inner radius of curvature 3m
No cracks occurred during 180° bending at m, and remarkable toughness was observed.
比較例■
Ｃｕ−８ｍａｓｓχＡ１合金を実施例■と同じ方法で成
形、焼結した。得られた焼結体の密度比は８７ｚで、引
張り強さ７ｋｇｆ／＋ｍ２．内側曲率半径３ｍｍにおけ
る曲げ角はほぼ０°で、実施例■〜■に比べて強度、靭
性ともに著しく劣っていた。Comparative Example ■ A Cu-8massχA1 alloy was molded and sintered in the same manner as in Example ■. The density ratio of the obtained sintered body was 87z, and the tensile strength was 7kgf/+m2. The bending angle at an inner radius of curvature of 3 mm was approximately 0°, and both the strength and toughness were significantly inferior to Examples ① to ②.
［発明の効果］
以上、本発明により、従来法では製造することができな
かった粉末冶金法による焼結アルミニウムが銅合金の製
造が可能となる。このような焼結アルミニウム青銅合金
は種々の低域部品、その他に利用できる。[Effects of the Invention] As described above, according to the present invention, it is possible to produce a copper alloy from sintered aluminum by powder metallurgy, which could not be produced by conventional methods. Such a sintered aluminum-bronze alloy can be used in various low-frequency parts and other applications.
Claims (2)
ｕ粉、及びＡｌ粉より選ばれる１種の粉末もしくは２種
以上からなる混合粉末に、Ｐを０．５ｍａｓｓ％以上含
み、残部がＣｒ、Ｍｎ、Ｆｅ、Ｃｏ、Ｎｉ及びＣｕの１
種以上からなる合金粉を１種以上添加し、成形、焼結す
ることを特徴とする焼結アルミニウム合金の製造方法。(1) The alloy powder constituting the substrate is Cu-Al alloy powder, C
One type of powder selected from U powder and Al powder, or a mixed powder of two or more types, containing 0.5 mass% or more of P, and the balance being Cr, Mn, Fe, Co, Ni, and Cu.
A method for producing a sintered aluminum alloy, which comprises adding one or more types of alloy powder, forming and sintering the alloy powder.
量が基質の合金粉末に対し、０．０１〜２ｍａｓｓ％の
範囲にあることを特徴とする請求の範囲（１）に記載の
焼結アルミニウム青銅合金の製造方法。(2) Total P of the powder added as alloy powder containing the above P
The method for producing a sintered aluminum bronze alloy according to claim 1, wherein the amount is in the range of 0.01 to 2 mass% based on the alloy powder of the substrate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32719188A JPH02173224A (en) | 1988-12-24 | 1988-12-24 | Manufacture of sintered aluminum bronze alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32719188A JPH02173224A (en) | 1988-12-24 | 1988-12-24 | Manufacture of sintered aluminum bronze alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02173224A true JPH02173224A (en) | 1990-07-04 |
Family
ID=18196329
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32719188A Pending JPH02173224A (en) | 1988-12-24 | 1988-12-24 | Manufacture of sintered aluminum bronze alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02173224A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009114486A (en) * | 2007-11-02 | 2009-05-28 | Fukuda Metal Foil & Powder Co Ltd | Sintering assistant, aluminum-containing copper-based alloy powder to be sintered, and sintered compact formed by sintering the aluminum-containing copper-based alloy powder |
| JP2011171274A (en) * | 2010-01-25 | 2011-09-01 | Hitachi Chem Co Ltd | Paste composition for electrode, and solar cell |
| WO2012008196A1 (en) * | 2010-07-14 | 2012-01-19 | 三井金属鉱業株式会社 | Copper powder for electrically conductive paste, and electrically conductive paste |
| WO2015029922A1 (en) * | 2013-08-27 | 2015-03-05 | Ntn株式会社 | Sintered bearing for fuel pump and method for manufacturing same |
| JP2017193781A (en) * | 2013-08-27 | 2017-10-26 | Ntn株式会社 | Sintered bearing for fuel pump and method of manufacturing the same |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS497106A (en) * | 1972-05-14 | 1974-01-22 | ||
| JPS56152902A (en) * | 1980-04-28 | 1981-11-26 | Fukuda Kinzoku Hakufun Kogyo Kk | Powder for sintered copper alloy containing aluminum |
-
1988
- 1988-12-24 JP JP32719188A patent/JPH02173224A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS497106A (en) * | 1972-05-14 | 1974-01-22 | ||
| JPS56152902A (en) * | 1980-04-28 | 1981-11-26 | Fukuda Kinzoku Hakufun Kogyo Kk | Powder for sintered copper alloy containing aluminum |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2009114486A (en) * | 2007-11-02 | 2009-05-28 | Fukuda Metal Foil & Powder Co Ltd | Sintering assistant, aluminum-containing copper-based alloy powder to be sintered, and sintered compact formed by sintering the aluminum-containing copper-based alloy powder |
| JP2011171274A (en) * | 2010-01-25 | 2011-09-01 | Hitachi Chem Co Ltd | Paste composition for electrode, and solar cell |
| WO2012008196A1 (en) * | 2010-07-14 | 2012-01-19 | 三井金属鉱業株式会社 | Copper powder for electrically conductive paste, and electrically conductive paste |
| JP2012021193A (en) * | 2010-07-14 | 2012-02-02 | Mitsui Mining & Smelting Co Ltd | Copper powder for electrically conductive paste, and electrically conductive paste |
| WO2015029922A1 (en) * | 2013-08-27 | 2015-03-05 | Ntn株式会社 | Sintered bearing for fuel pump and method for manufacturing same |
| JP2015227500A (en) * | 2013-08-27 | 2015-12-17 | Ntn株式会社 | Sintered bearing for fuel pump and production method thereof |
| CN105473258A (en) * | 2013-08-27 | 2016-04-06 | Ntn株式会社 | Sintered bearing for fuel pump and method for manufacturing same |
| US20160223018A1 (en) * | 2013-08-27 | 2016-08-04 | Yoshinori Ito | Sintered bearing for fuel pump and method of manufacturing same |
| JP2017193781A (en) * | 2013-08-27 | 2017-10-26 | Ntn株式会社 | Sintered bearing for fuel pump and method of manufacturing the same |
| JP2018053367A (en) * | 2013-08-27 | 2018-04-05 | Ntn株式会社 | Sintered bearing for fuel pump and method of manufacturing the same |
| CN108620590A (en) * | 2013-08-27 | 2018-10-09 | Ntn株式会社 | Petrolift sintered bearing and its manufacturing method |
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