WO2016117158A1 - Wear-resistant copper alloy - Google Patents
Wear-resistant copper alloy Download PDFInfo
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- WO2016117158A1 WO2016117158A1 PCT/JP2015/074702 JP2015074702W WO2016117158A1 WO 2016117158 A1 WO2016117158 A1 WO 2016117158A1 JP 2015074702 W JP2015074702 W JP 2015074702W WO 2016117158 A1 WO2016117158 A1 WO 2016117158A1
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- 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
- F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
- F16C33/00—Parts of bearings; Special methods for making bearings or parts thereof
- F16C33/02—Parts of sliding-contact bearings
- F16C33/04—Brasses; Bushes; Linings
- F16C33/06—Sliding surface mainly made of metal
- F16C33/12—Structural composition; Use of special materials or surface treatments, e.g. for rust-proofing
- F16C33/121—Use of special materials
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/04—Alloys based on copper with zinc as the next major constituent
Definitions
- the present invention relates to a wear-resistant copper alloy.
- brass alloys used for high-load applications include CAC301 to CAC304 described in JIS H5120, and manganese silicide-based intermetallic compound crystallized high-strength brass materials (hereinafter referred to as Mn-Si). Etc. Since these materials are used for bushes, construction machine parts, and the like, they are required to have high strength and high hardness, and excellent wear resistance and seizure resistance.
- CAC301 to CAC304 and Mn—Si system both have an ⁇ phase + ⁇ phase and ⁇ phase structure, and increase or decrease in the apparent zinc equivalent (hereinafter referred to as zinc equivalent) of the additive element. Changes the ratio of ⁇ phase, ⁇ phase, and ⁇ phase.
- the matrix phase structure is ⁇ single phase and the toughness is high, but the strength, hardness and wear resistance are low, causing deformation of the material and abrasive wear due to the load when used at high loads.
- zinc equivalent is high, precipitation of ⁇ phase results in ⁇ phase + ⁇ phase and hardness and wear resistance are improved, but strength, toughness and impact value are significantly reduced, so it cannot withstand the impact load acting on the sliding part. .
- the phase structure in the high strength brass system, it is possible to estimate the phase structure almost consistent with the Cu—Zn binary phase diagram by the zinc equivalent, and when the multi-component high strength brass material is replaced with the Cu—Zn binary phase diagram.
- the ⁇ phase precipitates in the ⁇ phase at the boundary of about 50% zinc equivalent. Since this ⁇ phase is hard and does not have ductility, the ⁇ phase + ⁇ phase structure has a significant adverse effect on strength, toughness, and impact resistance. Therefore, there is a limitation in adding Si having a zinc equivalent coefficient of 10 and high as long as it does not become ⁇ phase + ⁇ phase, and it has been difficult to improve wear resistance and secure strength, toughness, and impact resistance by adding Si.
- the present inventors have found that when the entire amount of Si added and other elements added are used for intermetallic compound formation, the intermetallic compound forming element does not dissolve in the matrix and the matrix structure Discovered that the impact on the As a result of further exploration, attention was paid to elements Co, Fe, and Mn having a zinc equivalent coefficient lower than 1 of Zn. These elements form an intermetallic compound at a constant ratio with Si, so that the solid solution of Si in the matrix is remarkably suppressed. However, Co, Fe, Mn, and Si elements are dissolved in the case of a certain ratio or more, but Co, Fe, and Mn are lower than the zinc equivalent coefficient of Si even if they are dissolved in the matrix.
- the present invention has been completed on the basis of the above-described knowledge, and it does not become a ⁇ phase + ⁇ phase structure with a zinc equivalent of 50% or more by addition of Si, and is in any of ⁇ phase + ⁇ phase, ⁇ phase + ⁇ phase + ⁇ phase, or ⁇ phase.
- An object of the present invention is to provide a wear-resistant copper alloy having a corresponding phase structure, maintaining strength, toughness and impact resistance and having a high level of wear resistance.
- the gist of the present invention will be described.
- the present invention relates to a wear-resistant copper alloy characterized by having a structure in which at least one Al—Fe—Mn—Si—Ni—Co intermetallic compound is dispersed.
- the mass ratio of Fe, Mn, Co and Si satisfies the following formula (1), and is related to the wear-resistant copper alloy according to claim 1.
- the left side A X is a value at the time of substituting Cu, Sn, Pb, Zn, the content of one of Al or Ni on the right side of the X, accompanied by substituting the elements of the content to the right of X
- the letters are represented as A Cu , A Sn , A Pb , A Zn , A Al or A Ni .
- the left side A X is a value at the time of substituting Cu, Sn, Pb, Zn, the content of one of Al or Ni on the right side of the X, accompanied by substituting the elements of the content to the right of X
- the letters are represented as A Cu , A Sn , A Pb , A Zn , A Al or A Ni .
- the addition of Si does not result in a ⁇ phase + ⁇ phase structure despite zinc equivalent of 50% or more, and corresponds to any of ⁇ phase + ⁇ phase, ⁇ phase + ⁇ phase + ⁇ phase, and ⁇ phase. It becomes a wear resistant copper alloy having a phase structure, maintaining strength, toughness and impact resistance and possessing a high level of wear resistance.
- the present invention does not cause ⁇ phase precipitation due to the addition of Si, but does not cause significant deterioration in strength, toughness, and impact resistance.
- This is a wear-resistant high-strength brass alloy whose wear resistance is improved by crystallizing and dispersing an Al—Fe—Mn—Si—Ni—Co intermetallic compound.
- Zn dissolves in the matrix and determines strength, hardness, wear resistance, and matrix structure.
- the matrix structure is determined as ⁇ phase, ⁇ phase + ⁇ phase + ⁇ phase, ⁇ phase + ⁇ phase, ⁇ phase, ⁇ phase + ⁇ phase, but Zn is less than 10% by mass Insufficient hardness tends to cause abrasive wear, leading to deterioration of wear resistance.
- Zn exceeds 40% by mass, strengthening of the parent phase by Zn is sufficient, but strengthening by Al solid solution in a range in which the ⁇ phase does not precipitate is insufficient, and zinc evaporation during casting is remarkable, so The amount added was 10 mass% to 40 mass%.
- Al contributes to the formation of intermetallic compounds and improves wear resistance, and also dissolves in the matrix and determines strength, hardness, wear resistance, and matrix structure.
- the matrix structure is determined as ⁇ phase, ⁇ phase + ⁇ phase + ⁇ phase, ⁇ phase + ⁇ phase, ⁇ phase, ⁇ phase + ⁇ phase, but when Al is less than 2% by mass Insufficient hardness tends to cause abrasive wear, which tends to deteriorate wear resistance. If the Al content exceeds 9% by mass, the ⁇ phase tends to exhibit eutectoid transformation, and the proportion of ⁇ phase + ⁇ phase + ⁇ phase in the ⁇ phase becomes large and deteriorates toughness. It was.
- Fe contributes to the formation of intermetallic compounds and improves wear resistance.
- the addition amount of Fe is set to 0.4 mass% to 3.5 mass%.
- Ni contributes to the formation of intermetallic compounds and improves wear resistance. Moreover, it dissolves in the matrix and improves the matrix strength. When Ni is less than 0.5% by mass, strengthening of the parent phase by Ni solid solution is insufficient, and when Ni exceeds 4.0% by mass, an effect commensurate with the cost cannot be obtained. It was set to 0.5 mass% to 4.0 mass%.
- Co contributes to the formation of intermetallic compounds and improves wear resistance. If it is less than 0.3% by mass, ductility is not improved by spheroidization of the intermetallic compound, and it is insufficient for forming a compound with Si. If C0 exceeds 2.0 mass%, an effect commensurate with the cost cannot be obtained, so the amount of Co added is set to 0.3 mass% to 2.0 mass%.
- Mn contributes to the formation of intermetallic compounds and improves wear resistance.
- Mn is less than 1.0% by mass, it is insufficient for forming an intermetallic compound, resulting in deterioration of wear resistance.
- Mn exceeds 5.0 mass%, ductility will deteriorate by the excessive production
- Si forms an intermetallic compound with the above-mentioned Al, Ni, Fe, Co, Mn and improves wear resistance. If Si is less than 0.3% by mass, it is insufficient for forming an intermetallic compound, resulting in deterioration of wear resistance. When Si exceeds 3.5% by mass, a large amount of Fe, Mn, and Co that suppress solid solution in the parent phase is required, and in addition, a large amount of intermetallic compounds are formed, resulting in reduced ductility. Was added in an amount of 0.3 mass% to 3.5 mass%.
- the present invention is intended to suppress solid solution of Si in the matrix and to prevent precipitation of ⁇ phase due to high zinc equivalent, and when Si is present in a certain ratio or more. Dissolves in the matrix and promotes ⁇ phase precipitation, leading to deterioration of strength, toughness and impact resistance. Therefore, the above formula (1) needs to be satisfied in order to suppress Si solid solution in the matrix phase.
- the above formula (1) indicates the mass% of Fe, Mn, and Co that binds to Si of about 1 mass%.
- the left side is equal to or greater than the right side, no solid solution occurs in the matrix of Si.
- the above formula (3) is satisfied, and the ⁇ phase is precipitated by maintaining a constant balance with other elements. It can be set as the structure which does not generate
- the value calculated by the right side of the said Formula (3) is called a mother phase zinc equivalent hereafter.
- FIGS. No. Nos. 1 to 8 are examples satisfying all the claims of the present application
- No. 1 to No. 8. 9 to 17 are comparative examples (the unit of each component is% by mass.
- Those satisfying the formulas (1) and (3) are marked with ⁇ , and those not satisfying are marked with x). These were melted using a high-frequency melting furnace and cast into two JIS ⁇ H 5120 B molds.
- JIS JIS Z2201-4 tensile test specimens were collected from No. B mold and subjected to a tensile test according to JIS ZZ2241. After the test, the tensile test piece chuck portion is cut at 20 mm, filled with resin, mirror-polished, and then observed with an optical microscope to observe the presence of ⁇ , ⁇ , and ⁇ phases.
- FIG. 1 JIS JIS Z2201-4 tensile test specimens were collected from No. B mold and subjected to a tensile test according to JIS ZZ2241. After the test, the tensile test piece chuck portion is cut at 20 mm, filled with resin, mirror-polished, and then observed with an optical microscope to observe the presence of ⁇ , ⁇ , and ⁇ phases.
- Zinc equivalent (%) (Y + ⁇ qt) / (X + Y + ⁇ qt) ⁇ 100 (mass%) (4)
- X is the actual Cu content (mass%) in the alloy
- Y is the actual Zn content (mass%) in the alloy
- q is the content of elements other than Cu and Zn (mass%).
- T are zinc equivalent coefficients of elements other than Cu and Zn.
- the zinc equivalent coefficient of Co is not yet clearly defined, it is calculated as 0.5 in this specification.
- No. 4 in FIGS. JIS Z 2202 V notch specimens (Fig. 8) were sampled from 18-27 component alloys and subjected to Charpy impact test at room temperature in accordance with JIS Z2242.
- Wear resistance was evaluated by a dry type Ogoshi type wear test.
- the surface with the large surface area becomes the test surface, and the test piece is fixed and the mating material is rotated at right angles.
- the load increases continuously and is 67N when the test distance reaches 200 m.
- the specific wear amount was calculated from the change in weight of the test piece before and after the test, and the larger the specific wear amount, the worse the wear resistance.
- the seizure resistance was evaluated by a Fabry test during oil immersion.
- the test material was sandwiched between the mating materials, and the load was continuously increased from the mating material side to rotate the pin. Evaluation was made by measuring the amount of work (kgf ⁇ s) given to the test material up to the stage where seizure occurred, and setting it as the Fabry value. The smaller the Fabry value, the worse the seizure resistance.
- FIGS. 1, 6, 7, 9, 10, and 11 The metal structure, tensile test, and Charpy test results are shown in FIGS. 1, 6, 7, 9, 10, and 11, and the Ogoshi type wear test and Fabry test results are shown in FIGS.
- the metal structure of this example has a structure in which an Al—Fe—Mn—Si—Ni—Co intermetallic compound is crystallized and dispersed in the matrix phase ( ⁇ phase + ⁇ phase + ⁇ phase or ⁇ phase). It was confirmed that Even when the parent phase is ⁇ phase + ⁇ phase, the excellent wear resistance characteristics similar to those of the present example are obtained when the Al—Fe—Mn—Si—Ni—Co intermetallic compound is crystallized and dispersed. It has been confirmed that
- FIG. 17 shows the Fabry test results, and it can be said that the examples (Nos. 18 to 22) also have superior seizure resistance compared to the comparative examples (Nos. 23 to 27).
- the examples suppress the solid solution of Si in the mother phase, and the parent phase is not composed of a ⁇ phase + ⁇ phase structure even though the zinc equivalent is 50% or more by balancing with other elements. It becomes a wear-resistant high-strength brass alloy having excellent wear-resistance characteristics while retaining a certain amount of strength, toughness and impact resistance. Therefore, it can be said that the alloy of the present invention composed of these materials is suitable for sliding members such as bushes and bearings.
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Abstract
The present invention provides a wear-resistant copper alloy that is strong, tough, and shock-resistant and that also has high-level wear resistance. This wear-resistant copper alloy contains, by mass, 10%-40% of Zn, 2%-9% of Al, 0.4%-3.5% of Fe, 0.5%-4.0% of Ni, 0.3%-2.0% of Co, 1.0%-5.0% of Mn, and 0.3%-3.5% of Si, the remainder comprising copper and unavoidable impurities, and is characterized by having a structure wherein an α+β phase, an α+β+γ phase, and/or a β phase has dispersed therein an Al-Fe-Mn-Si-Ni-Co-based intermetallic compound.
Description
本発明は、耐摩耗性銅合金に関するものである。
The present invention relates to a wear-resistant copper alloy.
従来、高荷重用途として使用される黄銅合金としては、JIS H 5120に記載されるCAC301～CAC304や、ケイ化マンガン系金属間化合物晶出型高力黄銅材（以下、Ｍｎ－Ｓｉ系という。）等が挙げられる。これらの材料は、ブッシュや建設機械用部品等に使用されることから、高強度・高硬度であり、耐摩耗性・耐焼付性に優れることが求められる。
Conventionally, brass alloys used for high-load applications include CAC301 to CAC304 described in JIS H5120, and manganese silicide-based intermetallic compound crystallized high-strength brass materials (hereinafter referred to as Mn-Si). Etc. Since these materials are used for bushes, construction machine parts, and the like, they are required to have high strength and high hardness, and excellent wear resistance and seizure resistance.
ところで、CAC301～CAC304、Ｍｎ－Ｓｉ系（例えば特許文献１等参照）は、ともにα相＋β相、β相組織であり、添加元素の見かけ上の亜鉛当量（以下、亜鉛当量という。）の増減によってα相、β相、γ相比率が変化する。
By the way, CAC301 to CAC304 and Mn—Si system (see, for example, Patent Document 1) both have an α phase + β phase and β phase structure, and increase or decrease in the apparent zinc equivalent (hereinafter referred to as zinc equivalent) of the additive element. Changes the ratio of α phase, β phase, and γ phase.
合金成分中、亜鉛当量が低い場合、母相組織はα単相となり靭性は高いが強度、硬度、耐摩耗性は低く、高荷重用途時、負荷荷重による材料の変形やアブレシブ摩耗を引き起こす。亜鉛当量が高い場合にはγ相の析出によってβ相＋γ相となり硬度、耐摩耗性は向上するが、強度、靭性、衝撃値が著しく低下するため摺動部に作用する衝撃荷重に耐えられない。
When the zinc equivalent in the alloy component is low, the matrix phase structure is α single phase and the toughness is high, but the strength, hardness and wear resistance are low, causing deformation of the material and abrasive wear due to the load when used at high loads. When zinc equivalent is high, precipitation of γ phase results in β phase + γ phase and hardness and wear resistance are improved, but strength, toughness and impact value are significantly reduced, so it cannot withstand the impact load acting on the sliding part. .
従って、高荷重摺動用途としてはα相＋β相、α相＋β相＋γ相、β相のように靭性、強度、硬度、耐摩耗性、耐衝撃性のバランスの取れた金属組織を呈する必要があるが、近年の産業機械部品の軽量化、長寿命化に伴い求められる摩耗特性は依然満たされていないのが現状である。
Therefore, for high-load sliding applications, it is necessary to exhibit a metal structure with a balance of toughness, strength, hardness, wear resistance, and impact resistance such as α phase + β phase, α phase + β phase + γ phase, and β phase. However, the present situation is that the wear characteristics required with the recent reduction in weight and life of industrial machine parts are still not satisfied.
即ち、高力黄銅系は、亜鉛当量によりＣｕ－Ｚｎ２元状態図とほぼ整合性の取れた相組織を推定することができ、多元系高力黄銅材をＣｕ－Ｚｎ２元状態図に置き換えた場合亜鉛当量５０％付近を境にβ相中にγ相が析出する。このγ相は硬質で延性を持たないためβ相＋γ相組織は強度、靭性、耐衝撃性に著しい悪影響を与える。よって、β相＋γ相とならない範囲で亜鉛当量係数１０と高いＳｉを添加することには制限があり、Ｓｉ添加による耐摩耗性向上及び強度、靭性、耐衝撃性の確保は困難であった。
That is, in the high strength brass system, it is possible to estimate the phase structure almost consistent with the Cu—Zn binary phase diagram by the zinc equivalent, and when the multi-component high strength brass material is replaced with the Cu—Zn binary phase diagram. The γ phase precipitates in the β phase at the boundary of about 50% zinc equivalent. Since this γ phase is hard and does not have ductility, the β phase + γ phase structure has a significant adverse effect on strength, toughness, and impact resistance. Therefore, there is a limitation in adding Si having a zinc equivalent coefficient of 10 and high as long as it does not become β phase + γ phase, and it has been difficult to improve wear resistance and secure strength, toughness, and impact resistance by adding Si.
本発明者らは鋭意研究した結果、Ｓｉ添加量分、その他元素添加量分とで金属間化合物形成に全量使用された場合、母相中へ金属間化合物形成元素が固溶せず母相組織への影響が薄いことを発見した。そして、さらに模索した結果、亜鉛当量係数がＺｎの１より低い元素Ｃｏ、Ｆｅ、Ｍｎに着目した。これらの元素は、Ｓｉと一定比率で金属間化合物を形成することでＳｉの母相への固溶が著しく抑制される。しかしながら、一定比率以上の場合にはＣｏ、Ｆｅ、Ｍｎ、Ｓｉ元素が固溶するが、Ｃｏ、Ｆｅ、Ｍｎは母相中へ固溶したとしてもＳｉの亜鉛当量係数１０に比較し低いことから母相組織への影響が軽微であるという結論に至った。これより、亜鉛当量係数が１０と高いＳｉをＦｅ、Ｍｎ、Ｃｏとの間に一定量添加することでＡｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｃｏ系金属間化合物を形成、晶出させ、Ｓｉ多量添加による高硬度化、高耐摩耗特性の保有が可能となる。したがって、母相中の固溶元素を抑制、制御することで最大限Ｓｉを添加させることができ、高亜鉛当量ながらもγ相が析出せず強度、靭性、耐衝撃性を維持することが可能であるとの知見を得た。
As a result of diligent research, the present inventors have found that when the entire amount of Si added and other elements added are used for intermetallic compound formation, the intermetallic compound forming element does not dissolve in the matrix and the matrix structure Discovered that the impact on the As a result of further exploration, attention was paid to elements Co, Fe, and Mn having a zinc equivalent coefficient lower than 1 of Zn. These elements form an intermetallic compound at a constant ratio with Si, so that the solid solution of Si in the matrix is remarkably suppressed. However, Co, Fe, Mn, and Si elements are dissolved in the case of a certain ratio or more, but Co, Fe, and Mn are lower than the zinc equivalent coefficient of Si even if they are dissolved in the matrix. The conclusion was reached that the impact on the parent phase organization was minor. From this, by adding a certain amount of Si with a high zinc equivalent coefficient of 10 between Fe, Mn, and Co, an Al-Fe-Mn-Si-Co intermetallic compound is formed and crystallized, and a large amount of Si is added. High hardness and high wear resistance can be achieved. Therefore, Si can be added to the maximum by suppressing and controlling the solid solution elements in the matrix phase, and it is possible to maintain strength, toughness and impact resistance without precipitation of γ phase despite high zinc equivalent. The knowledge that it is.
即ち、Ｓｉ、その他元素の母相中への固溶を制御することで亜鉛当量５０％以上ながらもγ相析出による強度、靭性、耐衝撃性の劣化が発生せず、Ｓｉ添加による耐摩耗性向上を図ることが可能であることを見出した。
That is, by controlling the solid solution of Si and other elements in the matrix, the strength, toughness, and impact resistance are not deteriorated due to the precipitation of γ phase while the zinc equivalent is 50% or more. It was found that improvement is possible.
本発明は上述の知見に基づき完成したもので、Ｓｉ添加により亜鉛当量５０％以上ながらもβ相＋γ相組織とならず、α相＋β相、α相＋β相＋γ相、β相のいずれかに該当した相組織を有し、強度、靭性、耐衝撃性を維持し高水準の耐摩耗性を保有した耐摩耗性銅合金を提供することを目的とする。
The present invention has been completed on the basis of the above-described knowledge, and it does not become a β phase + γ phase structure with a zinc equivalent of 50% or more by addition of Si, and is in any of α phase + β phase, α phase + β phase + γ phase, or β phase. An object of the present invention is to provide a wear-resistant copper alloy having a corresponding phase structure, maintaining strength, toughness and impact resistance and having a high level of wear resistance.
本発明の要旨を説明する。
The gist of the present invention will be described.
質量比で、Ｚｎ：１０～４０％、Ａｌ：２～９％、Ｆｅ：０．４～３．５％、Ｎｉ：０．５～４．０％、Ｃｏ：０．３～２．０％、Ｍｎ：１．０～５．０％、Ｓｉ：０．３～３．５％を含有し、残余がＣｕ及び不可避不純物から成り、α相＋β相、α相＋β相＋γ相若しくはβ相の少なくとも１つにＡｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｎｉ－Ｃｏ系金属間化合物が分散した組織を有することを特徴とする耐摩耗性銅合金に係るものである。
By mass ratio, Zn: 10-40%, Al: 2-9%, Fe: 0.4-3.5%, Ni: 0.5-4.0%, Co: 0.3-2.0% , Mn: 1.0 to 5.0%, Si: 0.3 to 3.5%, the balance is made of Cu and inevitable impurities, and α phase + β phase, α phase + β phase + γ phase or β phase The present invention relates to a wear-resistant copper alloy characterized by having a structure in which at least one Al—Fe—Mn—Si—Ni—Co intermetallic compound is dispersed.
また、Ｆｅ、Ｍｎ，Ｃｏ及びＳｉの質量比が下式（１）を満たすことを特徴とする請求項１記載の耐摩耗性銅合金に係るものである。
The mass ratio of Fe, Mn, Co and Si satisfies the following formula (1), and is related to the wear-resistant copper alloy according to claim 1.
また、各元素の質量比から下式（２）によって得られた値を下式（３）に代入した際、下式（３）を満たすことを特徴とする請求項１記載の耐摩耗性銅合金に係るものである。
The wear-resistant copper according to claim 1, wherein when the value obtained by the following formula (2) from the mass ratio of each element is substituted into the following formula (3), the following formula (3) is satisfied. It relates to alloys.
ここで、左辺ＡＸは、右辺のＸにＣｕ、Ｓｎ、Ｐｂ、Ｚｎ、Ａｌ若しくはＮｉのいずれかの含有量を代入した際の値であり、右辺のＸに含有量を代入した元素を添え字としてＡＣｕ、ＡＳｎ、ＡＰｂ、ＡＺｎ、ＡＡｌ若しくはＡＮｉと表す。
Here, the left side A X is a value at the time of substituting Cu, Sn, Pb, Zn, the content of one of Al or Ni on the right side of the X, accompanied by substituting the elements of the content to the right of X The letters are represented as A Cu , A Sn , A Pb , A Zn , A Al or A Ni .
また、各元素の質量比から下式（２）によって得られた値を下式（３）に代入した際、下式（３）を満たすことを特徴とする請求項２記載の耐摩耗性銅合金に係るものである。
The wear-resistant copper according to claim 2, wherein when the value obtained by the following formula (2) is substituted into the following formula (3) from the mass ratio of each element, the following formula (3) is satisfied: It relates to alloys.
ここで、左辺ＡＸは、右辺のＸにＣｕ、Ｓｎ、Ｐｂ、Ｚｎ、Ａｌ若しくはＮｉのいずれかの含有量を代入した際の値であり、右辺のＸに含有量を代入した元素を添え字としてＡＣｕ、ＡＳｎ、ＡＰｂ、ＡＺｎ、ＡＡｌ若しくはＡＮｉと表す。
Here, the left side A X is a value at the time of substituting Cu, Sn, Pb, Zn, the content of one of Al or Ni on the right side of the X, accompanied by substituting the elements of the content to the right of X The letters are represented as A Cu , A Sn , A Pb , A Zn , A Al or A Ni .
本発明は上述のように構成したから、Ｓｉ添加により亜鉛当量５０％以上ながらもβ相＋γ相組織とならず、α相＋β相、α相＋β相＋γ相、β相のいずれかに該当した相組織を有し、強度、靭性、耐衝撃性を維持し高水準の耐摩耗性を保有した耐摩耗性銅合金となる。
Since the present invention is configured as described above, the addition of Si does not result in a β phase + γ phase structure despite zinc equivalent of 50% or more, and corresponds to any of α phase + β phase, α phase + β phase + γ phase, and β phase. It becomes a wear resistant copper alloy having a phase structure, maintaining strength, toughness and impact resistance and possessing a high level of wear resistance.
好適と考える本発明の実施形態を本発明の作用を示して簡単に説明する。
Embodiments of the present invention that are considered to be suitable will be briefly described showing the operation of the present invention.
本発明は、Ｓｉ添加によって高亜鉛当量ながらもγ相析出がしないため強度、靭性、耐衝撃性の著しい劣化が発生せず、α相＋β相、α相＋β相＋γ相若しくはβ相組織中にＡｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｎｉ－Ｃｏ系金属間化合物を晶出分散させることで耐摩耗性向上を図った耐摩耗性高力黄銅合金である。
The present invention does not cause γ phase precipitation due to the addition of Si, but does not cause significant deterioration in strength, toughness, and impact resistance. This is a wear-resistant high-strength brass alloy whose wear resistance is improved by crystallizing and dispersing an Al—Fe—Mn—Si—Ni—Co intermetallic compound.
本発明において上記のように成分組成等を設定した理由について以下に説明する。
The reason for setting the component composition and the like as described above in the present invention will be described below.
Ｚｎは、母相中に固溶し、強度、硬度、耐摩耗性、母相組織を決定する。Ｚｎ量、その他添加元素量によって、母相組織がα相、α相＋β相＋γ相、α相＋β相、β相、β相＋γ相に決定されるが、Ｚｎが１０質量％未満であると硬さが不十分でアブレシブ摩耗が生じやすく耐摩耗性の悪化を招く。Ｚｎが４０質量％を超えるとＺｎによる母相強化は十分であるが、γ相が析出しない範囲でのＡｌ固溶による強化が不十分であり、また、鋳造時の亜鉛蒸発が著しいためＺｎの添加量を１０質量％～４０質量％とした。
Zn dissolves in the matrix and determines strength, hardness, wear resistance, and matrix structure. Depending on the amount of Zn and the amount of other added elements, the matrix structure is determined as α phase, α phase + β phase + γ phase, α phase + β phase, β phase, β phase + γ phase, but Zn is less than 10% by mass Insufficient hardness tends to cause abrasive wear, leading to deterioration of wear resistance. When Zn exceeds 40% by mass, strengthening of the parent phase by Zn is sufficient, but strengthening by Al solid solution in a range in which the γ phase does not precipitate is insufficient, and zinc evaporation during casting is remarkable, so The amount added was 10 mass% to 40 mass%.
Ａｌは、金属間化合物形成に寄与し耐摩耗性を向上させ、また、母相中に固溶し強度、硬度、耐摩耗性、母相組織を決定する。Ａｌ量、その他添加元素量によって、母相組織がα相、α相＋β相＋γ相、α相＋β相、β相、β相＋γ相に決定されるが、Ａｌが２質量％未満であると硬さが不十分でアブレシブ摩耗が生じ易く耐摩耗性の悪化を招きやすい。Ａｌが９質量％を超えるとβ相が共析変態を示し易くなり、α相＋β相＋γ相中のγ相割合が多量となり靭性を悪化させるためＡｌの添加量を２質量％～９質量％とした。
Al contributes to the formation of intermetallic compounds and improves wear resistance, and also dissolves in the matrix and determines strength, hardness, wear resistance, and matrix structure. Depending on the amount of Al and the amount of other added elements, the matrix structure is determined as α phase, α phase + β phase + γ phase, α phase + β phase, β phase, β phase + γ phase, but when Al is less than 2% by mass Insufficient hardness tends to cause abrasive wear, which tends to deteriorate wear resistance. If the Al content exceeds 9% by mass, the β phase tends to exhibit eutectoid transformation, and the proportion of α phase + β phase + γ phase in the γ phase becomes large and deteriorates toughness. It was.
Ｆｅは、金属間化合物形成に寄与し耐摩耗性を向上させる。Ｆｅが０．４質量％未満であるとＳｉとの化合物形成に不十分であり、Ｆｅが３．５質量％を超えると固溶限付近であることから溶解時溶け残りが生じハードスポットとなるためＦｅの添加量を０．４質量％～３．５質量％とした。
Fe contributes to the formation of intermetallic compounds and improves wear resistance. When Fe is less than 0.4% by mass, it is insufficient for forming a compound with Si. Therefore, the addition amount of Fe is set to 0.4 mass% to 3.5 mass%.
Ｎｉは、金属間化合物形成に寄与し耐摩耗性を向上させる。また、母相中に固溶し母相強度を向上させる。Ｎｉが０．５質量％未満であるとＮｉ固溶による母相強化が不十分であり、Ｎｉが４．０質量％を超えるとコストに見合った効果が得られないためＮｉの添加量を０．５質量％～４．０質量％とした。
Ni contributes to the formation of intermetallic compounds and improves wear resistance. Moreover, it dissolves in the matrix and improves the matrix strength. When Ni is less than 0.5% by mass, strengthening of the parent phase by Ni solid solution is insufficient, and when Ni exceeds 4.0% by mass, an effect commensurate with the cost cannot be obtained. It was set to 0.5 mass% to 4.0 mass%.
Ｃｏは、金属間化合物形成に寄与し耐摩耗性を向上させる。０．３質量％未満であると金属間化合物の球状化による延性向上を果たさず、また、Ｓｉとの化合物形成に不十分である。Ｃ０が２．０質量％を超えるとコストに見合った効果が得られないためＣｏの添加量を０．３質量％～２．０質量％とした。
Co contributes to the formation of intermetallic compounds and improves wear resistance. If it is less than 0.3% by mass, ductility is not improved by spheroidization of the intermetallic compound, and it is insufficient for forming a compound with Si. If C0 exceeds 2.0 mass%, an effect commensurate with the cost cannot be obtained, so the amount of Co added is set to 0.3 mass% to 2.0 mass%.
Ｍｎは、金属間化合物形成に寄与し耐摩耗性を向上させる。Ｍｎが１．０質量％未満であると金属間化合物形成に不十分であり耐摩耗性の悪化を招く。また、Ｍｎが５．０質量％を超えると針状金属間化合物生成過多により延性が悪化する。よって、Ｍｎの添加量を１．０質量％～５．０質量％とした。
Mn contributes to the formation of intermetallic compounds and improves wear resistance. When Mn is less than 1.0% by mass, it is insufficient for forming an intermetallic compound, resulting in deterioration of wear resistance. Moreover, when Mn exceeds 5.0 mass%, ductility will deteriorate by the excessive production | generation of an acicular intermetallic compound. Therefore, the amount of Mn added is set to 1.0 mass% to 5.0 mass%.
Ｓｉは、上述のＡｌ、Ｎｉ、Ｆｅ、Ｃｏ、Ｍｎと金属間化合物を形成し耐摩耗性を向上させる。Ｓｉが０．３質量％未満であると金属間化合物形成に不十分であり耐摩耗性の悪化を招く。Ｓｉが３．５質量％を超えると母相への固溶を抑制するＦｅ、Ｍｎ、Ｃｏが多量に必要となり、合わせて多量の金属間化合物が生成晶出することにより延性が低下するためＳｉの添加量を０．３質量％～３．５質量％とした。
Si forms an intermetallic compound with the above-mentioned Al, Ni, Fe, Co, Mn and improves wear resistance. If Si is less than 0.3% by mass, it is insufficient for forming an intermetallic compound, resulting in deterioration of wear resistance. When Si exceeds 3.5% by mass, a large amount of Fe, Mn, and Co that suppress solid solution in the parent phase is required, and in addition, a large amount of intermetallic compounds are formed, resulting in reduced ductility. Was added in an amount of 0.3 mass% to 3.5 mass%.
更に具体的には、本発明は、母相中へのＳｉ固溶を抑制し、高亜鉛当量で有るが故のγ相析出がないことを主旨としており、一定比率以上Ｓｉが存在した場合には母相中に固溶し、γ相析出を助長し強度、靭性、耐衝撃性の悪化を招く。そこで母相へのＳｉ固溶を抑えるため上記式（１）を満たす必要がある。
More specifically, the present invention is intended to suppress solid solution of Si in the matrix and to prevent precipitation of γ phase due to high zinc equivalent, and when Si is present in a certain ratio or more. Dissolves in the matrix and promotes γ phase precipitation, leading to deterioration of strength, toughness and impact resistance. Therefore, the above formula (1) needs to be satisfied in order to suppress Si solid solution in the matrix phase.
上記式（１）は、Ｆｅ、Ｍｎ、Ｃｏの１質量％辺りのＳｉと結合する質量％を示しており、左辺≧右辺で有る場合、Ｓｉの母相中の固溶は発生しない。しかしながら、他含有元素とのバランスによってγ相析出が発生するため、上記式（１）に加えて上記式（３）を満たし、他元素とのバランスを一定量に保つことでγ相の析出を発生させない構成とすることができる。また、上記式（３）の右辺で算出される値を以降は母相亜鉛当量と呼称する。
The above formula (1) indicates the mass% of Fe, Mn, and Co that binds to Si of about 1 mass%. When the left side is equal to or greater than the right side, no solid solution occurs in the matrix of Si. However, since γ phase precipitation occurs due to balance with other contained elements, in addition to the above formula (1), the above formula (3) is satisfied, and the γ phase is precipitated by maintaining a constant balance with other elements. It can be set as the structure which does not generate | occur | produce. Moreover, the value calculated by the right side of the said Formula (3) is called a mother phase zinc equivalent hereafter.
本発明の具体的な実施例について図面に基づいて説明する。
Specific embodiments of the present invention will be described with reference to the drawings.
本発明合金に係る供試材の化学成分組成を図２，３に示す。Ｎｏ．１～８は本願請求項全てを満たす実施例、Ｎｏ．９～１７は比較例である（各成分の単位は質量％。式（１）及び式（３）を満たすものには〇、満たさないものには×を付した。）。これらは高周波溶解炉を用いて溶解し、それぞれJIS H 5120 B号金型に２個ずつ鋳造した。
The chemical composition of the test material according to the alloy of the present invention is shown in FIGS. No. Nos. 1 to 8 are examples satisfying all the claims of the present application, No. 1 to No. 8. 9 to 17 are comparative examples (the unit of each component is% by mass. Those satisfying the formulas (1) and (3) are marked with 〇, and those not satisfying are marked with x). These were melted using a high-frequency melting furnace and cast into two JIS に H 5120 B molds.
B号金型からJIS Z 2201 4号引張試験片を採取し、JIS Z 2241に則り引張試験を行った。試験後、引張試験片チャック部を２０ｍｍで切断、樹脂埋め、鏡面研磨後、光学顕微鏡にて金属組織観察を行いα、β、γ相の有無について観察した金属組織を図１に示す。
JIS JIS Z2201-4 tensile test specimens were collected from No. B mold and subjected to a tensile test according to JIS ZZ2241. After the test, the tensile test piece chuck portion is cut at 20 mm, filled with resin, mirror-polished, and then observed with an optical microscope to observe the presence of α, β, and γ phases. FIG.
なお、亜鉛当量はGuilletの亜鉛当量係数によって下式（４）で求めた。
In addition, the zinc equivalent was calculated | required by the following Formula (4) with the zinc equivalent coefficient of Guillet.
亜鉛当量（％）＝(Ｙ+Σｑｔ)／(Ｘ＋Ｙ＋Σｑｔ)×１００（質量％）…（４）
式（４）において、Ｘは合金中の実際のＣｕ含有率（質量％）、Ｙは合金中の実際のＺｎ含有率（質量％）、ｑはＣｕ、Ｚｎ以外の元素含有率（質量％）、ｔはＣｕ、Ｚｎ以外の元素の亜鉛当量係数である。そして、各元素の亜鉛当量係数は、Ｚｎ＝１、Ｓｉ＝１０、Ａｌ＝６、Ｓｎ＝２、Ｐｂ＝１、Ｆｅ＝０．９、Ｍｎ＝０．５、Ｎｉ＝－１．３である。なお、Ｃｏの亜鉛当量係数は未だ明確に規定されていないが、本明細書にあたっては０．５として計算する。 Zinc equivalent (%) = (Y + Σqt) / (X + Y + Σqt) × 100 (mass%) (4)
In formula (4), X is the actual Cu content (mass%) in the alloy, Y is the actual Zn content (mass%) in the alloy, and q is the content of elements other than Cu and Zn (mass%). , T are zinc equivalent coefficients of elements other than Cu and Zn. The zinc equivalent coefficient of each element is Zn = 1, Si = 10, Al = 6, Sn = 2, Pb = 1, Fe = 0.9, Mn = 0.5, Ni = −1.3. . Although the zinc equivalent coefficient of Co is not yet clearly defined, it is calculated as 0.5 in this specification.
式（４）において、Ｘは合金中の実際のＣｕ含有率（質量％）、Ｙは合金中の実際のＺｎ含有率（質量％）、ｑはＣｕ、Ｚｎ以外の元素含有率（質量％）、ｔはＣｕ、Ｚｎ以外の元素の亜鉛当量係数である。そして、各元素の亜鉛当量係数は、Ｚｎ＝１、Ｓｉ＝１０、Ａｌ＝６、Ｓｎ＝２、Ｐｂ＝１、Ｆｅ＝０．９、Ｍｎ＝０．５、Ｎｉ＝－１．３である。なお、Ｃｏの亜鉛当量係数は未だ明確に規定されていないが、本明細書にあたっては０．５として計算する。 Zinc equivalent (%) = (Y + Σqt) / (X + Y + Σqt) × 100 (mass%) (4)
In formula (4), X is the actual Cu content (mass%) in the alloy, Y is the actual Zn content (mass%) in the alloy, and q is the content of elements other than Cu and Zn (mass%). , T are zinc equivalent coefficients of elements other than Cu and Zn. The zinc equivalent coefficient of each element is Zn = 1, Si = 10, Al = 6, Sn = 2, Pb = 1, Fe = 0.9, Mn = 0.5, Ni = −1.3. . Although the zinc equivalent coefficient of Co is not yet clearly defined, it is calculated as 0.5 in this specification.
また、耐衝撃特性を得るため、図４，５のＮｏ．１８～２７成分合金においてJIS Z 2202 Vノッチ試験片（図８）を採取し、JIS Z2242に則り室温にてシャルピー衝撃試験を行った。
Also, in order to obtain impact resistance characteristics, No. 4 in FIGS. JIS Z 2202 V notch specimens (Fig. 8) were sampled from 18-27 component alloys and subjected to Charpy impact test at room temperature in accordance with JIS Z2242.
図４，５に示すＮｏ．１８～２２の実施例、Ｎｏ．２３～２６の比較例としてのCAC301～CAC304、Ｎｏ．２７の比較例としてのＭｎ－Ｓｉ系（特許文献１）の供試材について、それぞれ高周波溶解炉を用いJIS H 5120 B号金型を用いて作製した。
No. shown in Figs. Nos. 18-22, no. CAC301 to CAC304 as comparative examples of Nos. Samples of Mn—Si (Patent Document 1) as 27 comparative examples were prepared using a high frequency melting furnace and a JIS H 5120 B die.
これら供試材より耐摩耗性、耐焼付性を評価した。
These samples were evaluated for wear resistance and seizure resistance.
耐摩耗性は乾式にて大越式摩耗試験より評価した。
Wear resistance was evaluated by a dry type Ogoshi type wear test.
・試験片形状 １０ｔ×２０ｗ×８０Ｌ
・相手材 SCM415 浸炭焼入 HRC56～59（図１２）
・試験速度 0.055、0.101、0.310、0.512 ｍ／ｓ 各３回
・荷重 初期荷重４．５Ｎ 最終荷重６７Ｎ
・試験距離 ２００ｍ ・ Specimen shape 10t × 20w × 80L
・ Countermaterial SCM415 Carburizing and quenching HRC56-59 (Fig. 12)
・ Test speed 0.055, 0.101, 0.310, 0.512 m /s 3 times each ・ Load Initial load 4.5N Final load 67N
・ Test distance 200m
・相手材 SCM415 浸炭焼入 HRC56～59（図１２）
・試験速度 0.055、0.101、0.310、0.512 ｍ／ｓ 各３回
・荷重 初期荷重４．５Ｎ 最終荷重６７Ｎ
・試験距離 ２００ｍ ・ Specimen shape 10t × 20w × 80L
・ Countermaterial SCM415 Carburizing and quenching HRC56-59 (Fig. 12)
・ Test speed 0.055, 0.101, 0.310, 0.512 m /
・ Test distance 200m
表面積の大きい面が試験面となり、試験片を固定し、相手材を直角に当て回転させる。荷重は連続的に増加し試験距離２００ｍ到達時６７Ｎである。評価は試験片の試験前、試験後の重量変化より比摩耗量を算出し、比摩耗量が大きいほど耐摩耗性が悪いと評価した。
The surface with the large surface area becomes the test surface, and the test piece is fixed and the mating material is rotated at right angles. The load increases continuously and is 67N when the test distance reaches 200 m. In the evaluation, the specific wear amount was calculated from the change in weight of the test piece before and after the test, and the larger the specific wear amount, the worse the wear resistance.
耐焼付性評価は油浸漬中にてファビリー試験より評価した。
The seizure resistance was evaluated by a Fabry test during oil immersion.
・試験片 図１３
・相手材 SCM415 浸炭焼入 HRC56～59（図１４）
・試験速度 ３００ｒｐｍ
・試験荷重 ３０ｋｇｆ／ｓ
・油種 シェル ターボオイル T32 ・ Test specimen Fig. 13
・ Countermaterial SCM415 Carburizing and quenching HRC56-59 (Fig. 14)
・ Test speed 300rpm
・ Test load 30kgf / s
・ Oil type Shell Turbo oil T32
・相手材 SCM415 浸炭焼入 HRC56～59（図１４）
・試験速度 ３００ｒｐｍ
・試験荷重 ３０ｋｇｆ／ｓ
・油種 シェル ターボオイル T32 ・ Test specimen Fig. 13
・ Countermaterial SCM415 Carburizing and quenching HRC56-59 (Fig. 14)
・ Test speed 300rpm
・ Test load 30kgf / s
・ Oil type Shell Turbo oil T32
試験材を相手材で挟み相手材側から連続的に荷重を増加しピンを回転させた。評価は焼付が生じた段階までに供試材に与えた仕事量（ｋｇｆ・ｓ）を測定しファビリー値とした。ファビリー値が小さいほど、耐焼付性が悪いと評価した。
The test material was sandwiched between the mating materials, and the load was continuously increased from the mating material side to rotate the pin. Evaluation was made by measuring the amount of work (kgf · s) given to the test material up to the stage where seizure occurred, and setting it as the Fabry value. The smaller the Fabry value, the worse the seizure resistance.
金属組織、引張試験、シャルピー試験結果を図1、６、７、９、１０、１１に示し、大越式摩耗試験、ファビリー試験結果を図１５、１６、１７に示す。
The metal structure, tensile test, and Charpy test results are shown in FIGS. 1, 6, 7, 9, 10, and 11, and the Ogoshi type wear test and Fabry test results are shown in FIGS.
図１より、本実施例の金属組織は母相（α相＋β相＋γ相若しくはβ相）にＡｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｎｉ－Ｃｏ系金属間化合物が晶出、分散した組織を呈していることが確認できた。なお、母相がα相＋β相である場合も、Ａｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｎｉ－Ｃｏ系金属間化合物が晶出、分散した組織であると本実施例と同様の優れた耐摩耗特性を具備するものとなることを確認している。
As shown in FIG. 1, the metal structure of this example has a structure in which an Al—Fe—Mn—Si—Ni—Co intermetallic compound is crystallized and dispersed in the matrix phase (α phase + β phase + γ phase or β phase). It was confirmed that Even when the parent phase is α phase + β phase, the excellent wear resistance characteristics similar to those of the present example are obtained when the Al—Fe—Mn—Si—Ni—Co intermetallic compound is crystallized and dispersed. It has been confirmed that
図２，３のＮｏ．９～１７においては図１のようにβ相＋γ相が確認される。これら比較例は式（１）または式（３）を満たさないため、母相がβ相＋γ相組織となった。式（１）を満たさない合金Ｎｏ．１６、１７においてはβ相＋γ相であるがため引張強さ、伸びがＮｏ．１～８より低い結果である。また、式（３）を満たさないが故にβ相＋γ相で構成される合金Ｎｏ．９～１５は図９、１０、１１に示すように各種特性の低下が見られ、特に図９の引張強さにおいては著しい低下が確認される。これらの結果より、機械的性質を一定量確保するには式（１）及び式（３）を満たす範囲内で合金を作製する必要がある。
No. in Figs. In 9 to 17, a β phase + γ phase is confirmed as shown in FIG. Since these comparative examples did not satisfy the formula (1) or the formula (3), the parent phase had a β phase + γ phase structure. Alloy No. 1 that does not satisfy Formula (1) Nos. 16 and 17 are β phase and γ phase, but the tensile strength and elongation are No. The result is lower than 1-8. In addition, since the formula (3) is not satisfied, the alloy no. As shown in FIGS. 9, 10, and 11, various characteristics are lowered in 9 to 15, and particularly in the tensile strength in FIG. 9, a significant decrease is confirmed. From these results, in order to secure a certain amount of mechanical properties, it is necessary to produce an alloy within a range satisfying the expressions (1) and (3).
上記結果より、母相がβ相＋γ相組織では機械的性質が悪化するため、式（１）及び（３）を満たすことが必須であり、これらを満たす範囲において作製された供試材の摩耗特性は図１５、１６、１７に記される結果であった。
From the above results, since the mechanical properties are deteriorated in the β phase + γ phase structure of the parent phase, it is essential to satisfy the formulas (1) and (3). The characteristics were the results shown in FIGS.
図１５、１６は大越式摩耗試験（摩耗速度0.055ｍ／ｓ、0.101ｍ／ｓ）の結果であるが、実施例（Ｎｏ．１８～２２）は比較例（Ｎｏ．２３～２７）に比べ摩耗量が少なく、優れた耐摩耗性を保有していると言える。
15 and 16 show the results of the Ogoshi type wear test (wear speeds 0.055 m / s, 0.101 m / s), but the examples (Nos. 18 to 22) are worn more than the comparative examples (Nos. 23 to 27). The amount is small and it can be said that it has excellent wear resistance.
図１７にはファビリー試験結果を示すが、こちらも実施例（Ｎｏ．１８～２２）は比較例（Ｎｏ．２３～２７）に比べ優れた耐焼付性を保有していると言える。
FIG. 17 shows the Fabry test results, and it can be said that the examples (Nos. 18 to 22) also have superior seizure resistance compared to the comparative examples (Nos. 23 to 27).
以上より、実施例はＳｉの母相への固溶を抑制し、かつ、他元素とのバランスをとることで亜鉛当量５０％以上ながらも母相がβ相＋γ相組織で構成されないが故、強度、靭性、耐衝撃性を一定量保有させた上で優れた耐摩耗特性を具備する耐摩耗性高力黄銅合金となる。よって、これらで構成される本発明合金はブッシュ、軸受等の摺動部材に適した材料といえる。
From the above, the examples suppress the solid solution of Si in the mother phase, and the parent phase is not composed of a β phase + γ phase structure even though the zinc equivalent is 50% or more by balancing with other elements. It becomes a wear-resistant high-strength brass alloy having excellent wear-resistance characteristics while retaining a certain amount of strength, toughness and impact resistance. Therefore, it can be said that the alloy of the present invention composed of these materials is suitable for sliding members such as bushes and bearings.
Claims (4)
- 質量比で、Ｚｎ：１０～４０％、Ａｌ：２～９％、Ｆｅ：０．４～３．５％、Ｎｉ：０．５～４．０％、Ｃｏ：０．３～２．０％、Ｍｎ：１．０～５．０％、Ｓｉ：０．３～３．５％を含有し、残余がＣｕ及び不可避不純物から成り、α相＋β相、α相＋β相＋γ相若しくはβ相の少なくとも１つにＡｌ－Ｆｅ－Ｍｎ－Ｓｉ－Ｎｉ－Ｃｏ系金属間化合物が分散した組織を有することを特徴とする耐摩耗性銅合金。 By mass ratio, Zn: 10-40%, Al: 2-9%, Fe: 0.4-3.5%, Ni: 0.5-4.0%, Co: 0.3-2.0% , Mn: 1.0 to 5.0%, Si: 0.3 to 3.5%, the balance is made of Cu and inevitable impurities, and α phase + β phase, α phase + β phase + γ phase or β phase A wear-resistant copper alloy having a structure in which at least one Al—Fe—Mn—Si—Ni—Co intermetallic compound is dispersed.
- Ｆｅ、Ｍｎ，Ｃｏ及びＳｉの質量比が下式（１）を満たすことを特徴とする請求項１記載の耐摩耗性銅合金。
- 各元素の質量比から下式（２）によって得られた値を下式（３）に代入した際、下式（３）を満たすことを特徴とする請求項１記載の耐摩耗性銅合金。
- 各元素の質量比から下式（２）によって得られた値を下式（３）に代入した際、下式（３）を満たすことを特徴とする請求項２記載の耐摩耗性銅合金。
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| JPS63238258A (en) * | 1987-03-25 | 1988-10-04 | Mitsubishi Metal Corp | Synchronous ring for change gear made of cu alloy |
| JPH09316570A (en) * | 1996-05-30 | 1997-12-09 | Chuetsu Gokin Chuko Kk | End bearing for one-way clutch and other sliding part |
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| CN105283567B (en) * | 2013-07-10 | 2017-06-09 | 三菱综合材料株式会社 | Electronic electric equipment copper alloy, electronic electric equipment copper alloy thin plate, electronic electric equipment conducting element and terminal |
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| JPS63238258A (en) * | 1987-03-25 | 1988-10-04 | Mitsubishi Metal Corp | Synchronous ring for change gear made of cu alloy |
| JPH09316570A (en) * | 1996-05-30 | 1997-12-09 | Chuetsu Gokin Chuko Kk | End bearing for one-way clutch and other sliding part |
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