EP2135964A2 - Gleitmaterial auf Kupferbasis - Google Patents

Gleitmaterial auf Kupferbasis Download PDF

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Publication number
EP2135964A2
EP2135964A2 EP09008100A EP09008100A EP2135964A2 EP 2135964 A2 EP2135964 A2 EP 2135964A2 EP 09008100 A EP09008100 A EP 09008100A EP 09008100 A EP09008100 A EP 09008100A EP 2135964 A2 EP2135964 A2 EP 2135964A2
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EP
European Patent Office
Prior art keywords
phase
copper
mass
alloy
sliding material
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.)
Granted
Application number
EP09008100A
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English (en)
French (fr)
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EP2135964B1 (de
EP2135964A3 (de
Inventor
Shinji Ochi
Kazuaki Toda
Wataru Yago
Jun Yasukawa
Kouji Fujiyama
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Daido Metal Co Ltd
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Daido Metal Co Ltd
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Publication of EP2135964A3 publication Critical patent/EP2135964A3/de
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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 sliding material used under severe conditions.
  • the present invention relates to a copper-based sliding material suitable for e.g. a floating bush for turbochargers in motor vehicles or the like, and having high productivity.
  • the turbocharger has a structure to rotate a turbine at a high speed with high-temperature exhaust gas from an engine to drive a compressor, the operating conditions are extremely severe. Especially, when the engine is rotated at a high speed and then stopped immediately, oil supply to a floating bush is stopped, so that the temperature of the floating bush is elevated to higher than 300°C by heat conduction from a turbine casing. If the engine is restarted in this state, the turbine immediately approaches the highest rotation as high as 100,000 rpm. Since the supply of lubricant delays, however, lubrication effect falls in the stopped (dry-up) state. Specifically, the floating bush is required to have favorable resistance to seizing and abrasion even under the dry-up state at such a high temperature.
  • JP-A-03-215642 discloses, as a sliding material satisfying such requirements, high-strength brass composed of, by mass percent, 1 to 3.5% of Mn, 0.3 to 1.5% of Si, 10 to 25% of Zn, 5 to 18% of Pb, and the balance being Cu and unavoidable impurities.
  • Pb is uniformly dispersed in the whole structure and the matrix consists of a single ⁇ -phase.
  • JP-A-9-316570 discloses a manganese silicide high-strength brass which has a metal structure including ⁇ -phase controlled to be not more than 30% so that it can be subjected to cold plastic working.
  • the manganese silicide high-strength brass is composed of, by mass percent, 0.3 to 5% of Mn, 0.3 to 3% of Si, 15 to 37% of Zn, 0.3 to 4% of Bi, and the balance being Cu and unavoidable impurities.
  • the former sliding material has favorable performances in resistance to seizing and abrasion. Since it contains Pb, however, it has a problem in view of recent environmental concerns.
  • the latter sliding material includes a hard ⁇ -phase in the matrix, and thus the resistance to abrasion is improved. When it is used under severe conditions, such as a floating bush for a turbocharger, problems is still left in resistance to seizing.
  • JP-A-2004-137512 proposes a copper-based sliding material consisting of, by mass percent, 15 to 25% of Zn, 4.2 to 10% of Bi, 2 to 7% of Mn, 1 to 3% of Si, and the balance being Cu.
  • the matrix is composed of a single ⁇ -phase, and the eutectic structure composed of the ⁇ -phase and a Mn-Si compound, and Bi particles are dispersed in the matrix (see paragraphs [0009] to [0010]).
  • a Bi-particle phase is dispersed in the matrix of single ⁇ -phase by adding a large quantity of Bi.
  • the copper-based alloy is manufactured by a continuous casting method or the like suited to mass production, cracks possibly generate due to the stress during the drawing from the mold.
  • the stress during the drawing is applied to the copper-based alloy, it is considered that shear generates at the interface between the ⁇ -phase and the Bi-particle phase since the quantity of deformation differs between the ⁇ -phase having a high ductility and the Bi-particle phase having little ductility. The shear becomes the starting point of the cracking.
  • the alloy cracking can be reduced by lowering the drawing rate, the productivity lowers, and therefore there is no advantage to adopt the continuous casting method for mass production. Furthermore, if the Zn content is increased to make the matrix of the copper-based alloy be composed of the ⁇ -phase and ⁇ -phase structure, the strength of the matrix is increased and the ductility thereof is lowered. Thus, the cracking of the copper-based alloy unlikely occurs.
  • the sliding material for supporting a shaft rotating at a high speed in a high-temperature atmosphere such as for a turbocharger
  • the strength of the copper-based alloy becomes excessively high, and resistance to seizing and conformability (which is such property that the alloy deforms by itself, while it contacts the counter shaft, to reduce stress generated by the contact) are lowered.
  • the alloy cracking can be reduced by reducing the Bi content in the copper-based alloy disclosed in JP-A-2004-137512 , the content of Bi, which is a lubricating component, becomes excessively low, and the sliding property required in the sliding material for supporting a high-speed rotating shaft in a high-temperature atmosphere, such as for turbochargers, cannot be satisfied.
  • the invention is made in taking the above-described situations in consideration. It is an object of the invention to provide a copper-based sliding material that has improved resistance to seizing, abrasion and friction and conformability as well as improved productivity, even if it is used under severe conditions under which it is rotated at a high speed in a high-temperature atmosphere, such as a floating bush for a turbocharger for motor vehicles or the like.
  • the invention provides a copper-based sliding material consisting of 15.0 to 25.0 mass % of Zn, 4.2 to 10.0 mass % of Bi, 2.0 to 7.0 mass % of Mn, 1.0 to 3.0 mass % of Si, 0.1 to 2.0 mass % Sn, and the balance being Cu and unavoidable impurities.
  • the copper-based sliding material includes a single ⁇ -phase matrix in which a Mn-Si compound and a Bi-particle phase are dispersed, and the mass ratio of Sn to Bi is 0.024 to 0.200.
  • the mass ratio of Sn to Bi is 0.050 to 0.140.
  • a laminar "Sn-containing ⁇ -phase” is formed so as to surround the periphery of each crystal grain having the ⁇ -phase and the Bi-particle phase in the copper-based alloy structure.
  • the ductility of each phase in the copper-based alloy structure is in the order of: ⁇ -phase > "Sn-containing ⁇ -phase” > Bi-particle phase. Therefore, when a stress is applied, the "Sn-containing ⁇ -phase" plays a role to relax the deformation difference between the Bi-particle phase and the ⁇ -phase. This will function to relax the shear stress due to the difference in deformation between the ⁇ -phase and the Bi-particle phase generated during drawing in the continuous casting process, and thereby, it is considered that the problem of alloy cracking can be prevented.
  • the reason why the contents of Sn and Bi are determined to be, respectively, 0.1 to 2.0 mass % and 4.2 to 10 mass % and the mass ratio of Sn to Bi is determined to be 0.024 to 0.200 (more preferably 0.050 to 0.140) is as follows. If the mass ratio of Sn to Bi is smaller than 0.024, the amount of "Sn-containing ⁇ -phase" formed in the periphery of the Bi-particle phase is small and cannot completely surround the periphery of the Bi-particle phase, and the effect of preventing the cracking in the copper-based alloy is reduced. On the other hand, if the mass ratio of Sn to Bi exceeds 0.200, the effect of preventing cracking in the copper-based alloy is also reduced.
  • the Bi-Sn hypoeutectic alloy contains less Sn than the Bi-Sn eutectic composition (Bi-43 mass % Sn having a melting point at about 140°C). In this composition range, the melting point lowers according to increase in the Sn content.
  • the copper-based alloy is drawn after cooling it to lower than a temperature at which the Bi-particle phase, of which melting point is lowest in the copper-based alloy structure (the melting point is about 270°C), is fully solidified.
  • a Mn-Si compound used in a high-temperature region such as a floating bush for a turbocharger, is required to have high-temperature strength as well as ductility.
  • the strength of the copper-based alloy is lowered with the elevation of temperature, the high-temperature strength of the copper-based alloy can be increased by dispersing a Mn-Si compound whose strength is not lowered even at the high temperature.
  • Bi is added as a lubricating component for improving the resistance to seizing of the copper-based sliding material. Little Bi dissolves in the copper-alloy matrix, but is dispersed in the matrix as fine particles. If the quantity of the added Bi is less than 4.2 mass %, the effect to increase the resistance to seizing is insufficient for the copper-based sliding material to support the shaft rotating at a high speed in a high-temperature atmosphere. If the quantity is more than 10 mass %, the strength of the copper-based sliding material is lowered.
  • Mn improves the strength of the matrix. It forms hard compounds having excellent sliding properties, such as Mn-Si compounds (mainly Mn 5 Si 3 ), and contributes to improve the resistance to abrasion and seizing, friction properties, and strength at a high temperature. If the quantity of the added Mn is less than 2.0 mass %, the effect cannot be obtained. If the quantity is more than 7.0 mass %, the addition of Zn described below becomes hardly useful.
  • Si forms Mn-Si compounds with Mn as described above, and similar to Mn, it serves to improve the resistance to abrasion and seizing, friction properties, and strength at a high temperature.
  • the quantity of the added Si is determined by the composition of the Mn-Si compound. The compound is formed when the mass ratio of Mn to Si is 1:0.3. Therefore, the content of Si may be at least 0.6 mass %. However, since all Si does not form a compound with Mn, the minimum quantity of added Si in the present invention is determined to be 1.0 mass %. If the quantity exceeds 3.0 mass %, the quantity of free Si becomes excessive and causes the copper-based sliding material brittle.
  • Zn improves the strength of the matrix, resistance to abrasion, and corrosion resistance to lubricants.
  • the quantity of the added Zn will be mentioned. According to the Cu-Zn binary phase diagram, if the quantity of Zn is not more than 38.0 mass %, the matrix becomes a single ⁇ -phase, and if the quantity of Zn exceeds 38.0 mass %, a ⁇ - phase appears. However, when a third element dissolved in the ⁇ -phase or the ⁇ -phase, such as Mn and Si in the present invention, is added, Mn and Si change the structure of the matrix as if the quantity of the added Zn were increased. Therefore, the quantity of the added Zn is determined to be at most 25.0 mass % in consideration of the contents of Mn and Si. Thus, the matrix can be made to be a single ⁇ -phase. However, if the content of Zn is less than 15.0 mass %, the effect of the resistance to abrasion and corrosion to lubricants is degraded.
  • Fig. 1 shows a schematic diagram of a structure of the alloy of the present invention.
  • a Mn-Si compound 3 and a fine Bi-particle phase 4 are uniformly dispersed in a matrix of the single ⁇ -phase 1, 2 in the copper-based alloy.
  • the single ⁇ -phase is composed of a primary crystal ⁇ -phase 1 that contains little Sn, and a laminar "Sn-containing ⁇ -phase" 2 surrounding the periphery of the primary crystal ⁇ -phase 1.
  • the Bi-particle phase 4 is also surrounded by the laminar "Sn-containing ⁇ -phase" 2.
  • the Mn-Si compound 3 is distributed in the laminar "Sn-containing ⁇ -phase" 2.
  • the "Sn-containing ⁇ -phase" 2 is formed between the ⁇ -phase having a high ductility and the Bi-particle phase 4 having little ductility. It is considered that the "Sn-containing ⁇ -phase” 2 plays a role to relax the shear stress due to difference in the quantity of deformation between the Bi-particle phase 4 and the ⁇ -phase 1 when an external force is applied, and this functions to prevent alloy cracking generating between the ⁇ -phase 1 and the Bi-particle phase 4 during drawing in the continuous casting process.
  • the copper-based sliding material shown in Fig. 1 contains 20.0 mass % of Zn, 3.5 mass % of Mn, 1.5 mass % of Si, 6.5 mass % of Bi, and 0.47 mass % of Sn.
  • Examples 1 to 11 are within the scope of the present invention, among which Examples 1 to 9 contains substantially mean values of the contents range of Zn, Mn and Si.
  • Examples 10 and 11 contain Zn, respectively, at the upper and lower limits, and other components at mean value of the content range.
  • Examples 1 to 11 Examples 1 to 11 are examples wherein the invention according to claim 1 is embodied.
  • Examples 1 and 2 Examples 3 and 4, and Examples 5, 10 and 11 adopted "the mass ratio of Sn to Bi" is the upper limit, the lower limit, and the median value, respectively.
  • Examples 6 to 9 are examples wherein the invention according to claim 2 is embodied.
  • Examples 6 and 7, and Examples 8 and 9 adopted "the mass ratio of Sn to Bi" at the desirable upper limit and lower limit, respectively.
  • Comparative Examples 21 to 25 are out of the scope of the present invention.
  • Comparative Examples 21 and 22 and Comparative Examples 23 and 24 adopted "the mass ratio of Sn to Bi" to be lower than lower limit and higher than upper limit, respectively.
  • Comparative Example 25 does not contain Sn, which is the feature of the present invention.
  • the copper-based alloy of any of Examples 1 to 11 according to the present application has a structure, in which the Mn-Si compound and the fine Bi-particle phase are uniformly distributed in the matrix composed of the single ⁇ -phase as shown in Fig. 1 .
  • the matrix is composed of the single ⁇ -phase and the periphery of the ⁇ -phase primary crystal grain containing little Sn is completely surrounded by a laminar "Sn-containing ⁇ -phase".
  • the Bi-particle phase is also surrounded by the laminar "Sn-containing ⁇ -phase".
  • the Mn-Si compound is distributed in the laminar "Sn-containing ⁇ -phase".
  • the "Sn-containing ⁇ -phase" having intermediate ductility is present between the ⁇ -phase having a high ductility and the Bi-particle phase having little ductility. Therefore, it is considered that the "Sn-containing ⁇ -phase” plays the role to relax shear stress due to the difference in the quantity of deformation between the Bi-particle phase and the ⁇ -phase when an external force is applied, and this functions to prevent alloy cracking between the ⁇ -phase and the Bi-particle phase when the alloy is drawn in the continuous casting process. On the other hand, since the mass ratio of Sn to Bi was low in Comparative Examples 21 and 22, alloy cracking generated.
  • alloy cracking occurred in the Comparative Examples 23 and 24, since the mass ratio of Sn to Bi is high. This is considered because the Bi-particle phase reacts with the "Sn-containing ⁇ -phase" in the cooling process to form a Bi-Sn hypoeutectic alloy at the interface, and a part of the Bi-Sn hypoeutectic alloy is not yet solidified even when the copper alloy is drawn. Since the stress of drawing is applied to the copper alloy in the state, alloy cracking occurred. When the mass ratio of Sn to Bi is not more than 0.200, it is considered that little or no Bi-Sn hypoeutectic alloy is formed and the copper alloy cracking was prevented.
  • the copper-based sliding material according to the present invention is not only used in floating bushes for the turbochargers of motor vehicles and the like, but also widely applied to bearings in general which require, for example, resistance to seizing and abrasion, friction properties and conformability under severe conditions.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)
  • Supercharger (AREA)
  • Conductive Materials (AREA)
  • Contacts (AREA)
EP20090008100 2008-06-20 2009-06-19 Gleitmaterial auf Kupferbasis Active EP2135964B1 (de)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2008161635A JP5111253B2 (ja) 2008-06-20 2008-06-20 銅系摺動材料

Publications (3)

Publication Number Publication Date
EP2135964A2 true EP2135964A2 (de) 2009-12-23
EP2135964A3 EP2135964A3 (de) 2013-01-23
EP2135964B1 EP2135964B1 (de) 2014-03-12

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2489609A (en) * 2011-03-31 2012-10-03 Daido Metal Co A thrust bearing for a turbocharger of an internal combustion engine
WO2017198698A1 (de) * 2016-05-20 2017-11-23 Otto Fuchs - Kommanditgesellschaft - Bleifreie sondermessinglegierung sowie sondermessinglegierungsprodukt
US10570484B2 (en) 2016-05-20 2020-02-25 Otto Fuchs Kommanditgesellschaft High tensile brass alloy and high tensile brass alloy product
US11427890B2 (en) 2014-02-04 2022-08-30 Otto Fuchs Kommanditgesellschaft Lubricant-compatible copper alloy

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP5253440B2 (ja) * 2010-03-01 2013-07-31 大同メタル工業株式会社 内燃機関用過給機のすべり軸受
JP6753647B2 (ja) * 2015-01-07 2020-09-09 大豊工業株式会社 すべり軸受用銅合金およびすべり軸受

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH03215642A (ja) 1990-01-22 1991-09-20 Daido Metal Co Ltd 非焼付性、耐摩耗性および耐蝕性に優れた摺動用銅基合金
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
JP2004137512A (ja) 2002-10-15 2004-05-13 Daido Metal Co Ltd 摺動用銅基合金

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58177430A (ja) * 1982-04-12 1983-10-18 Furukawa Electric Co Ltd:The 導電用銅合金
JP3335002B2 (ja) * 1994-05-12 2002-10-15 中越合金鋳工株式会社 熱間加工性に優れた無鉛快削黄銅合金
JP3333654B2 (ja) * 1995-02-02 2002-10-15 矢崎総業株式会社 伸び特性及び屈曲特性に優れた導電用高力銅合金、及びその製造方法

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH03215642A (ja) 1990-01-22 1991-09-20 Daido Metal Co Ltd 非焼付性、耐摩耗性および耐蝕性に優れた摺動用銅基合金
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
JP2004137512A (ja) 2002-10-15 2004-05-13 Daido Metal Co Ltd 摺動用銅基合金

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB2489609A (en) * 2011-03-31 2012-10-03 Daido Metal Co A thrust bearing for a turbocharger of an internal combustion engine
GB2489609B (en) * 2011-03-31 2013-03-27 Daido Metal Co Thrust bearing for turbocharger of internal combustion engine
US8790574B2 (en) 2011-03-31 2014-07-29 Daido Metal Company, Ltd. Thrust bearing for turbocharger of internal-combustion engine
US11427890B2 (en) 2014-02-04 2022-08-30 Otto Fuchs Kommanditgesellschaft Lubricant-compatible copper alloy
WO2017198698A1 (de) * 2016-05-20 2017-11-23 Otto Fuchs - Kommanditgesellschaft - Bleifreie sondermessinglegierung sowie sondermessinglegierungsprodukt
US10570484B2 (en) 2016-05-20 2020-02-25 Otto Fuchs Kommanditgesellschaft High tensile brass alloy and high tensile brass alloy product
RU2732139C2 (ru) * 2016-05-20 2020-09-11 Отто Фукс - Коммандитгезельшафт Бессвинцовый высокопрочный латунный сплав и изделие из высокопрочного латунного сплава
US11359263B2 (en) 2016-05-20 2022-06-14 Otto Fuchs Kommanditgesellschaft Lead-free high tensile brass alloy and high tensile brass alloy product

Also Published As

Publication number Publication date
JP2010001532A (ja) 2010-01-07
EP2135964B1 (de) 2014-03-12
JP5111253B2 (ja) 2013-01-09
EP2135964A3 (de) 2013-01-23

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