JPS6151620B2 - - Google Patents
Info
- Publication number
- JPS6151620B2 JPS6151620B2 JP56001341A JP134181A JPS6151620B2 JP S6151620 B2 JPS6151620 B2 JP S6151620B2 JP 56001341 A JP56001341 A JP 56001341A JP 134181 A JP134181 A JP 134181A JP S6151620 B2 JPS6151620 B2 JP S6151620B2
- Authority
- JP
- Japan
- Prior art keywords
- wear resistance
- content
- alloys
- alloy
- present
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 10
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 239000010949 copper Substances 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 description 11
- 239000000956 alloy Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 11
- 229910000765 intermetallic Inorganic materials 0.000 description 5
- 229910052710 silicon Inorganic materials 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 229910052748 manganese Inorganic materials 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 3
- 229910001369 Brass Inorganic materials 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- 229910018643 Mn—Si Inorganic materials 0.000 description 2
- 239000010951 brass Substances 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 229910052718 tin Inorganic materials 0.000 description 2
- 229910052725 zinc Inorganic materials 0.000 description 2
- 229910000906 Bronze Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910017518 Cu Zn Inorganic materials 0.000 description 1
- 229910017752 Cu-Zn Inorganic materials 0.000 description 1
- 229910017943 Cu—Zn Inorganic materials 0.000 description 1
- 229910003310 Ni-Al Inorganic materials 0.000 description 1
- 229910018098 Ni-Si Inorganic materials 0.000 description 1
- 229910018529 Ni—Si Inorganic materials 0.000 description 1
- 240000007643 Phytolacca americana Species 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000010974 bronze Substances 0.000 description 1
- 239000003610 charcoal Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- KUNSUQLRTQLHQQ-UHFFFAOYSA-N copper tin Chemical compound [Cu].[Sn] KUNSUQLRTQLHQQ-UHFFFAOYSA-N 0.000 description 1
- TVZPLCNGKSPOJA-UHFFFAOYSA-N copper zinc Chemical compound [Cu].[Zn] TVZPLCNGKSPOJA-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 229910001651 emery Inorganic materials 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D2200/00—Materials; Production methods therefor
- F16D2200/0004—Materials; Production methods therefor metallic
- F16D2200/0026—Non-ferro
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D23/00—Details of mechanically-actuated clutches not specific for one distinct type
- F16D23/02—Arrangements for synchronisation, also for power-operated clutches
- F16D23/025—Synchro rings
Landscapes
- Mechanical Operated Clutches (AREA)
- Sliding-Contact Bearings (AREA)
Description
本発明は耐摩耗性に優れた高力銅合金に関し、
さらに詳しくは、高速度、高荷重の摺動条件で使
用される、例えば、自動車等に用いられているシ
ンクロナイザーリング（別名ポークリング）に用
いられる耐摩耗性に優れた高力銅合金に関するも
のである。
従来よりシンクロナイザー用合金としては、黄
銅中にMn−Siの金属間化合物を分散させ耐摩耗
性を良好にした合金やアルミニウム青銅が用いら
れている。
しかしながら、最近、より高速、高荷重という
苛酷な条件下にも耐えられる耐摩耗性銅合金が要
求されてきている。
本発明は上記したような高速、高荷重の摺動条
件下において、従来合金より優れた耐摩耗性を有
する高力銅合金を提供しようとするものである。
本発明に係る耐摩耗性に優れた高力銅合金の特
徴とするところは、Zn20〜40％、Al ２〜５％、
Mn0.75〜7.5％、Si0.25〜2.5％、Ni0.5〜５％、
Cr0.01〜0.2％、Sn0.1〜２％、残部銅及び不純物
からなるものである。
本発明に係る耐摩耗性に優れた高力銅合金につ
いて詳細に説明する。
先づ、本発明に係る耐摩耗性に優れた高力銅合
金の含有成分、成分割合について説明する。
ZnはCu−Zn系合金の耐摩耗性に重大な影響を
与えるものであり、母相がβ相の場合この特性が
良くなるが、β相単一の場合は脆くなり、耐摩耗
性の他に靭性をも要求される場合には母相はα＋
βが望まれ、この観点からZnの含有量は他の含
有元素のZn当量も鑑み、20〜40％の範囲とす
る。
Alは母相を強化すると共に耐食性を向上させ
る元素であるが、AlのZn当量が６と非常に高い
ためAl含有量が多くなるとγ相が現われ熱間加
工性を悪くする。含有量が２％未満ではAlの効
果が得られず、また、５％を越えると上記した悪
い影響がある。よつてAl含有量は２〜５％とす
る。
Mn、SiはMn5Si3の金属間化合物を形成し、耐
摩耗性を向上させるが、このMn5Si3の含有量が
１％未満ではこの効果は得られず、また、10％を
越えると靭性が劣つてくる。そして、MnとSiが
Mn5Si3の金属間化合物を形成するとき、MnとSi
の重量比は１：0.3であり、よつて、Mnは0.75〜
7.5％、Siは0.25〜2.5％とする。
NiはNi−Al、Ni−Siの金属間化合物を形成
し、母相を強化する効果があり、また、母相に晶
出（析出）するMn5Si3金属間化合物の成長を抑
制し、これを微細にする効果もある。含有量が
0.5％未満ではこの効果は得られ難く、５％を越
えて含有されると鋳造温度を上昇させなければな
らず鋳塊の健全性を損なうことによる。よつて、
Ni含有量は0.5〜５％とする。
Crは結晶粒を微細化する効果があり、含有量
が0.01％未満ではこの効果は望めず、0.2％を越
えて含有されると鋳造時の鋳流れ性を悪くする。
よつて、Cr含有量は0.01〜0.2％とする。
Snは含有元素のうちでも特徴的な元素であ
り、従来のMn−Si黄銅より優れた耐摩耗性を発
揮させる効果があり、また、耐食性を向上させ
る。含有量が0.1％未満ではこれらの効果は得ら
れず、２％を越えて含有させると鋳塊の逆偏析を
招き好ましくない。よつて、Sn含有量は0.1〜２
％とする。
本発明に係る耐摩耗性に優れた高力銅合金の実
施例を比較合金と共に説明
実施例
The present invention relates to a high-strength copper alloy with excellent wear resistance,
More specifically, it relates to high-strength copper alloys with excellent wear resistance used in synchronizer rings (also known as poke rings) used in automobiles, etc., which are used under high-speed, high-load sliding conditions. It is. Conventionally, alloys for synchronizers include alloys in which Mn-Si intermetallic compounds are dispersed in brass to improve wear resistance, and aluminum bronze. However, recently there has been a demand for wear-resistant copper alloys that can withstand even harsher conditions such as higher speeds and higher loads. The present invention aims to provide a high-strength copper alloy that has better wear resistance than conventional alloys under the above-mentioned high-speed, high-load sliding conditions. The features of the high-strength copper alloy with excellent wear resistance according to the present invention include 20 to 40% Zn, 2 to 5% Al,
Mn0.75~7.5%, Si0.25~2.5%, Ni0.5~5%,
It consists of 0.01-0.2% Cr, 0.1-2% Sn, and the balance copper and impurities. The high-strength copper alloy with excellent wear resistance according to the present invention will be explained in detail. First, the components and proportions of the high-strength copper alloy with excellent wear resistance according to the present invention will be explained. Zn has a significant effect on the wear resistance of Cu-Zn alloys, and when the parent phase is a β phase, this property improves, but when it is a single β phase, it becomes brittle and deteriorates wear resistance and other properties. If toughness is also required, the matrix should be α+
β is desired, and from this point of view, the Zn content is set in the range of 20 to 40%, taking into account the Zn equivalents of other contained elements. Al is an element that strengthens the matrix and improves corrosion resistance, but since the Zn equivalent of Al is very high at 6, when the Al content increases, a γ phase appears and impairs hot workability. If the content is less than 2%, the effects of Al cannot be obtained, and if the content exceeds 5%, there will be the above-mentioned negative effects. Therefore, the Al content is set to 2 to 5%. Mn and Si form an intermetallic compound of Mn 5 Si 3 and improve wear resistance, but this effect cannot be obtained if the Mn 5 Si 3 content is less than 1%, and if it exceeds 10%. and the toughness deteriorates. And Mn and Si
When forming an intermetallic compound of Mn 5 Si 3 , Mn and Si
The weight ratio of is 1:0.3, so Mn is 0.75~
7.5%, and Si is 0.25 to 2.5%. Ni forms intermetallic compounds of Ni-Al and Ni-Si and has the effect of strengthening the matrix, and also suppresses the growth of Mn 5 Si 3 intermetallic compounds that crystallize (precipitate) in the matrix, It also has the effect of making this finer. The content is
If the content is less than 0.5%, it is difficult to obtain this effect, and if the content exceeds 5%, the casting temperature must be increased, which impairs the integrity of the ingot. Then,
The Ni content is 0.5 to 5%. Cr has the effect of refining crystal grains, and if the content is less than 0.01%, this effect cannot be expected, and if the content exceeds 0.2%, it will deteriorate the flowability during casting.
Therefore, the Cr content is set to 0.01 to 0.2%. Sn is a characteristic element among the contained elements, and has the effect of exhibiting better wear resistance than conventional Mn-Si brass, and also improves corrosion resistance. If the content is less than 0.1%, these effects cannot be obtained, and if the content exceeds 2%, this is undesirable because it causes reverse segregation of the ingot. Therefore, the Sn content is between 0.1 and 2.
%. Examples of high-strength copper alloys with excellent wear resistance according to the present invention, along with comparative alloys
【表】
第１表の含有成分、及び、成分割合となるよう
に、クリプトル電気炉を用いて電解銅を黒鉛坩堝
で、木炭被覆下にて溶解して、更に、Ni、Cu−
15Cr中間合金、Mn、Si、Al、Sn、Znを添加し溶
け落ち後金型に鋳込んで、60mmｔ×60mmｗ×140
mmｌの鋳塊を得た。比較合金の鋳塊も上記と同様
にして得た。
この鋳塊を厚さ55mmまで面削し、圧延開始温度
750℃で厚さ８mmまで圧延した。さらに、650℃で
２時間保持後水中急冷することにより試料を調整
した。
次に、この板材から圧延方向に平行に引張試験
片（JIS13号Ｂ）、及び、圧延方向に直角な方向か
らシヤルピー衝撃試験片（JIS4号）をそれぞれ作
製した。
試験結果を第２表に示す。[Table] Electrolytic copper was melted under charcoal coating in a graphite crucible using a Kryptor electric furnace, and Ni, Cu-
Add 15Cr intermediate alloy, Mn, Si, Al, Sn, and Zn, and after melting down, cast into a mold, 60mmt x 60mmw x 140
An ingot of mml was obtained. Ingots of comparative alloys were also obtained in the same manner as above. This ingot was faceted to a thickness of 55 mm, and the rolling start temperature was
It was rolled to a thickness of 8 mm at 750°C. Furthermore, the sample was prepared by holding it at 650°C for 2 hours and then rapidly cooling it in water. Next, a tensile test specimen (JIS No. 13 B) was prepared from this plate material in parallel to the rolling direction, and a Charpy impact test specimen (JIS No. 4) was prepared in a direction perpendicular to the rolling direction. The test results are shown in Table 2.
【表】
この第２表からも明らかであるが、本発明に係
る合金（No.1）は比較合金（No.2）比べ耐力が
高く、高力であり、また、衝撃値は略同等である
ことがわかる。
さらに、同じ板材から８mmｔ×25mmｗ×50mmｌ
（＃1000エメリーペーパで研摩仕上げ）の摩耗試
験片を作成し、下記条件で試験を行ない比摩耗量
を算出した。
摩耗試験条件
摩耗試験機・大越式迅速摩耗試験機
相手材・JIS SUS−２
摩擦距離・100ｍ
最終荷重・2.1Kg
摩擦速度・0.1〜3.5m/sec
添付図面に試験結果を示す。図中・は本発明に
係る合金（No.1）、〇は比較合金（No.2）を示し
ている。
この添付図面より、No.1はNo.2より優れて安
定した耐摩耗量を示していることがわかる。
以上説明したように、本発明に係る耐摩耗性に
優れた高力銅合金は上記の構成を有しているもの
であるから、常温での耐力が高く、耐摩耗性も優
れているので、高速、高荷重の条件下で摺動する
部分の材料として有効であり、自動車等に用いら
れるシンクロナイザーリング（別名ボーリン
グ）、及びブツシング等に使用することができ
る。[Table] As is clear from Table 2, the alloy according to the present invention (No. 1) has higher yield strength and strength than the comparative alloy (No. 2), and its impact value is almost the same. I understand that there is something. Furthermore, from the same board material, 8mmt x 25mmw x 50mml
A wear test piece (polished with #1000 emery paper) was prepared and tested under the following conditions to calculate the specific wear amount. Wear test conditions Wear tester/Okoshi type rapid wear tester Compatible material: JIS SUS-2 Friction distance: 100m Final load: 2.1Kg Friction speed: 0.1 to 3.5m/sec The test results are shown in the attached drawing. In the figure, . indicates an alloy according to the present invention (No. 1), and ○ indicates a comparative alloy (No. 2). From this attached drawing, it can be seen that No. 1 exhibits a more stable wear resistance than No. 2. As explained above, since the high-strength copper alloy with excellent wear resistance according to the present invention has the above-mentioned structure, it has high yield strength at room temperature and excellent wear resistance. It is effective as a material for parts that slide under high speed and high load conditions, and can be used for synchronizer rings (also known as boring) used in automobiles, bushings, etc.
添付図面は摩耗速度と比摩耗量とを示すグラフ
である。
The attached drawing is a graph showing wear rate and specific wear amount.
Claims (1)
％、Si0.25〜2.5％、Ni0.5〜５％、Cr0.01〜0.2
％、Sn0.1〜２％、残部Cu及び不純物からなる耐
摩耗性に優れた高力銅合金。1 Zn20~40%, Al 2~5%, Mn0.75~7.5
%, Si0.25~2.5%, Ni0.5~5%, Cr0.01~0.2
%, Sn0.1~2%, balance Cu and impurities. High strength copper alloy with excellent wear resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56001341A JPS57114632A (en) | 1981-01-08 | 1981-01-08 | High-strength copper alloy with superior wear resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP56001341A JPS57114632A (en) | 1981-01-08 | 1981-01-08 | High-strength copper alloy with superior wear resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS57114632A JPS57114632A (en) | 1982-07-16 |
| JPS6151620B2 true JPS6151620B2 (en) | 1986-11-10 |
Family
ID=11498786
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP56001341A Granted JPS57114632A (en) | 1981-01-08 | 1981-01-08 | High-strength copper alloy with superior wear resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS57114632A (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3427740A1 (en) * | 1984-07-27 | 1986-02-06 | Diehl GmbH & Co, 8500 Nürnberg | BRASS ALLOY, MANUFACTURING METHOD AND USE |
| JPH0757899B2 (en) * | 1985-07-10 | 1995-06-21 | 株式会社日立製作所 | Wear resistant copper alloy |
| DE3735783C1 (en) * | 1987-10-22 | 1989-06-15 | Diehl Gmbh & Co | Use of a copper-zinc alloy |
| JP2605791B2 (en) * | 1988-03-31 | 1997-04-30 | 三菱マテリアル株式会社 | Transmission synchronous ring made of Cu-based sintered alloy |
| JPH01252744A (en) * | 1988-03-31 | 1989-10-09 | Mitsubishi Metal Corp | Synchronous ring for gearbox made of sintered cu alloy |
| CN107267789A (en) * | 2017-07-25 | 2017-10-20 | 苏州三冷暖工程有限公司 | A kind of preparation method of the effective brass alloys of air conditioner condensation |
| CN112695216B (en) * | 2020-12-08 | 2021-12-28 | 宁波正元铜合金有限公司 | Preparation method of manganese brass alloy with three strengthening phases |
-
1981
- 1981-01-08 JP JP56001341A patent/JPS57114632A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS57114632A (en) | 1982-07-16 |
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