[go: up one dir, main page]

WO2016117158A1 - Alliage de cuivre résistant à l'usure - Google Patents

Alliage de cuivre résistant à l'usure Download PDF

Info

Publication number
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
Authority
WO
WIPO (PCT)
Prior art keywords
phase
wear
mass
test
copper alloy
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.)
Ceased
Application number
PCT/JP2015/074702
Other languages
English (en)
Japanese (ja)
Inventor
山本　秀樹
健司 丸山
智樹 伊藤
祐行 森岡
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Joetsu Bronz1 Corp
Original Assignee
Joetsu Bronz1 Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Joetsu Bronz1 Corp filed Critical Joetsu Bronz1 Corp
Publication of WO2016117158A1 publication Critical patent/WO2016117158A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

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
    • 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
    • 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.

Landscapes

  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • General Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)

Abstract

La présente invention concerne un alliage de cuivre résistant à l'usure qui est solide, dur et résistant aux chocs et qui présente également un haut niveau de résistance à l'usure. Cet alliage de cuivre résistant à l'usure contient, en masse, entre 10 % et 40 % de zinc (Zn), entre 2 % et 9 % d'aluminium (Al), entre 0,4 % et 3,5 % de fer (Fe), entre 0,5 % et 4,0 % de nickel (Ni), entre 0,3 % et 2,0 % de cobalt (Co), entre 1,0 % et 5,0 % de manganèse (Mn) et entre 0,3 % et 3,5 % de silicium (Si), le reste comprenant du cuivre et des impuretés inévitables, et est caractérisé en ce qu'il présente une structure dans laquelle une phase α + β, une phase α + β + γ et/ou une phase β ont dispersé un composé intermétallique à base d'Al-Fe-Mn-Si-Ni-Co.
PCT/JP2015/074702 2015-01-20 2015-08-31 Alliage de cuivre résistant à l'usure Ceased WO2016117158A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2015-008574 2015-01-20
JP2015008574A JP6046177B2 (ja) 2015-01-20 2015-01-20 耐摩耗性銅合金

Publications (1)

Publication Number Publication Date
WO2016117158A1 true WO2016117158A1 (fr) 2016-07-28

Family

ID=56416721

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2015/074702 Ceased WO2016117158A1 (fr) 2015-01-20 2015-08-31 Alliage de cuivre résistant à l'usure

Country Status (3)

Country Link
JP (1) JP6046177B2 (fr)
TW (1) TWI662140B (fr)
WO (1) WO2016117158A1 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109881032B (zh) * 2019-03-11 2021-07-27 中南大学 一种高抗变色金色铜合金及制备方法
CN110863123A (zh) * 2019-11-29 2020-03-06 常熟市常氏瓶钳有限公司 一种制造瓶钳的铜合金配方
CN112522535B (zh) * 2020-12-08 2022-02-18 宁波正元铜合金有限公司 一种高强耐磨黄铜合金及其制备方法
CN114000008B (zh) * 2021-09-29 2022-06-24 宁波兴业盛泰集团有限公司 一种亚稳态难混溶铜铁合金及其制备方法

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63238258A (ja) * 1987-03-25 1988-10-04 Mitsubishi Metal Corp Ｃｕ系合金製変速機用同期リング
JPH09316570A (ja) * 1996-05-30 1997-12-09 Chuetsu Gokin Chuko Kk ワンウェイクラッチ用エンドベアリング及び その他の摺動部品

Family Cites Families (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103154284B (zh) * 2010-10-25 2014-11-12 三菱伸铜株式会社 耐压耐蚀性铜合金、钎焊结构体及钎焊结构体的制造方法
KR20160030113A (ko) * 2013-07-10 2016-03-16 미쓰비시 마테리알 가부시키가이샤 전자·전기 기기용 구리 합금, 전자·전기 기기용 구리 합금 박판, 전자·전기 기기용 도전 부품 및 단자

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS63238258A (ja) * 1987-03-25 1988-10-04 Mitsubishi Metal Corp Ｃｕ系合金製変速機用同期リング
JPH09316570A (ja) * 1996-05-30 1997-12-09 Chuetsu Gokin Chuko Kk ワンウェイクラッチ用エンドベアリング及び その他の摺動部品

Also Published As

Publication number Publication date
TW201627506A (zh) 2016-08-01
JP6046177B2 (ja) 2016-12-14
TWI662140B (zh) 2019-06-11
JP2016132803A (ja) 2016-07-25

Similar Documents

Publication Publication Date Title
JP5342882B2 (ja) 摺動部材用高力黄銅合金および摺動部材
JP5703881B2 (ja) 高強度マグネシウム合金およびその製造方法
JP5868510B2 (ja) 快削性無鉛銅合金及びその製造方法
EP3031569B1 (fr) Matériau allié de brasage à base de ni-cr-fe additionné de cu
KR20170088355A (ko) 구리를 포함하는 금속 합금
WO2016166779A1 (fr) Alliage d'aluminium pour coulée sous pression et alliage d'aluminium coulé sous pression l'utilisant
KR101756016B1 (ko) 다이캐스팅용 알루미늄 합금 및 이를 이용하여 제조한 알루미늄 합금의 열처리 방법
CN104018024B (zh) 青铜合金及其制造方法、使用青铜合金的滑动构件
JP5305323B2 (ja) ダイカスト用Ｚｎ合金およびダイカスト用Ｚｎ合金を用いたダイカスト部材の製造方法
JP2021511435A (ja) 鉛とビスマスが添加されていない快削性無鉛銅合金
JP6046177B2 (ja) 耐摩耗性銅合金
JP2016079498A (ja) シリンダライナ用ねずみ鋳鉄及びそれを用いたシリンダライナの製造方法
KR102546211B1 (ko) 알루미늄 합금
US20120258809A1 (en) Copper-tin multicomponent bronze containing hard phases, production process and use
US11091821B2 (en) Copper-based alloy
KR102489980B1 (ko) 알루미늄 합금
TW202444931A (zh) 快削性銅合金鑄件、及快削性銅合金鑄件的製造方法
KR20190054825A (ko) 내마모성 동합금 및 이의 제조방법
JP3920656B2 (ja) ホウ素含有高剛性Ａｌ合金
JP5449754B2 (ja) エンジンまたはコンプレッサーのピストンの鍛造方法
WO2020115932A1 (fr) Alliage cuivreux
JP6415096B2 (ja) 複合微細組織を有する耐摩耗性合金
KR101830841B1 (ko) 고내마모성을 갖는 싱크로나이저 링용 동합금 및 이의 제조방법
JP6415097B2 (ja) 複合微細組織を有する耐摩耗性合金
WO2013114582A1 (fr) Alliage d'aluminium présentant une résistance à l'usure, une aptitude à l'extrusion et une aptitude au façonnage par forgeage d'excellente qualité

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 15878847

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 15878847

Country of ref document: EP

Kind code of ref document: A1