EP1888798A1 - Alliage d'aluminium pour paliers lisses - Google Patents

Alliage d'aluminium pour paliers lisses

Info

Publication number
EP1888798A1
EP1888798A1 EP05756177A EP05756177A EP1888798A1 EP 1888798 A1 EP1888798 A1 EP 1888798A1 EP 05756177 A EP05756177 A EP 05756177A EP 05756177 A EP05756177 A EP 05756177A EP 1888798 A1 EP1888798 A1 EP 1888798A1
Authority
EP
European Patent Office
Prior art keywords
alloy
plain bearing
bismuth
aluminum
heat treatment
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
EP05756177A
Other languages
German (de)
English (en)
Other versions
EP1888798B1 (fr
Inventor
Babette Tonn
Juri Moiseev
Hennadiy Zak
Lorenz Ratke
Heinz Palkowski
Hubert Schwarze
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.)
Deutsches Zentrum fuer Luft und Raumfahrt eV
Technische Universitaet Clausthal
Original Assignee
Deutsches Zentrum fuer Luft und Raumfahrt eV
Technische Universitaet Clausthal
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 Deutsches Zentrum fuer Luft und Raumfahrt eV, Technische Universitaet Clausthal filed Critical Deutsches Zentrum fuer Luft und Raumfahrt eV
Publication of EP1888798A1 publication Critical patent/EP1888798A1/fr
Application granted granted Critical
Publication of EP1888798B1 publication Critical patent/EP1888798B1/fr
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/003—Aluminium alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/40—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rings; for bearing races
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/053—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with zinc as the next major constituent

Definitions

  • the invention relates to a heavy-duty aluminum sliding bearing alloy, in particular for multilayer bearings, a method for their preparation and associated plain bearing shells and plain bearings.
  • Highly stressed plain bearings are constructed of several layers to meet the variety of requirements placed on the bearings and partly contradictory. Usually steel-aluminum composites are used.
  • the sliding bearing materials While the steel support shell ensures the absorption of the mechanical stress and the tight fit, the sliding bearing materials must withstand the manifold tribological stresses and be fatigue-proof. To meet this requirement, the sliding bearing materials in the aluminum matrix on the one hand contain hard phases, such as silicon and intermetallic precipitates, and on the other soft phases, such as lead or tin.
  • Multi-layer bearings often additionally have a highly lead-containing sliding layer applied galvanically on the functional layer.
  • This soft sliding layer ensures the good emergency running properties of the bearing. It can embed abrasion particles and thus remove from the sliding surface.
  • bismuth has some advantages as a soft phase in the aluminum matrix.
  • bismuth has a higher melting point and can be used at higher temperatures.
  • an aluminum alloy comprises one or more of the components 1 to 50% by weight, preferably 5 to 30% by weight lead, 3 to 50% by weight, preferably 5 to 30% by weight.
  • This alloy known from DE 4003018 A1 is cast in continuous casting vertically to a strip or wire of 5 to 20 mm thickness or diameter, wherein the melt is cast at a cooling rate of 300 to 1500 K / s. Due to the rapid cooling rate, it is intended to prevent large-volume precipitations of a minority phase from being formed in the period between when the demixing temperature has fallen below and after complete solidification of the matrix metal. From the practice of continuous casting of aluminum alloys, however, it is known that, as a result of the very high cooling rates, there is a considerable risk of crack formation and the process stability required for series production is difficult to ensure.
  • a cast aluminum difficult to control monotectic aluminum sliding bearing alloy with up to 15 wt .-% bismuth and with at least one element selected from the group silicon, tin, lead in total from 0.5 to 15 wt .-% and possible additives from the group of copper, manganese, magnesium, nickel, chromium, zinc and antimony in a total amount of up to 3% in reproducible quality by casting tapes are cast.
  • a homogeneous distribution of the minority phase is achieved in this case by intensive stirring of the melt in the electromagnetic field.
  • the texture of this alloy is softened by addition of fining agents.
  • this has an advantageous effect on the size of the drop-shaped bismuth precipitates, which in casting a Diameter of 40 microns maximum.
  • the addition amount of the grain refining agent is calculated according to EP 0 940 474 A1 with a formula which takes into account the bismuth content in the melt.
  • This invention contains no indication of the type of Komfeinungszu accounts used, leading to the results described in the patent.
  • EP 0 190 691 discloses an alloy containing 4 to 7% by weight bismuth, 1 to 4.5% by weight silicon, 0 to 1, 7% by weight copper, 0 to 2.5% by weight Lead and at least one element from the group nickel, manganese, chromium in a total amount of up to 1% and additionally at least one element from the group tin, zinc, antimony of a total of up to 5 wt .-% known.
  • high silicon contents reinforce the aluminum matrix, they have a negative influence on the size of the minority phase and lead to a significant worsening of the droplet distribution in the strand.
  • the originally spherical lead or bismuth phase is deformed into very thick threads which considerably reduce the mechanical strength and the tribological properties of the material.
  • One possible solution for setting the desired material properties is the transformation of the elongated precipitates of the minority phase into compact structural forms by a subsequent heat treatment.
  • DE 4014430 A1 is a monotectic aluminum-silicon bismuth alloy heat-treated at temperatures of 575 0 C to 585 0 C, in order to achieve a fine distribution of the plate-like elongated after rolling bismuth.
  • the heat treatment offers the possibility of improving the strength values of the aluminum sliding bearing alloy by means of hardening effects.
  • the elements suitable for achieving the possible curing effects are, for example, silicon, magnesium, zinc and zirconium.
  • the addition of copper increases the cure rate and can be used in combination with these elements. From US Pat. No. 5,286,445 an aluminum sliding bearing alloy with a bismuth content of 2 to 15% by weight, 0.05 to 1% by weight of zirconium and a copper content and / or magnesium content of up to 1.5% is known.
  • this alloy contains at least one element from the group of tin, lead and indium in the sum of 0.05 to 2 wt .-% or at least one element selected from the group silicon, manganese, vanadium, antimony, niobium, molybdenum, cobalt, iron, Titanium, chromium in the sum of 0.05 to 5 wt .-%.
  • tin, lead and indium support the re-coagulation of stretched bismuth drops to finer precipitates at temperatures of 200 0 C to 350 0 C.
  • the elements zirconium, silicon and magnesium cause after annealing in the temperature range 480 0 C to 525 0 C, the is carried out shortly before the Walzplattiervorgang after US 5,286,445, the actual hardening effect.
  • the transition elements should ensure an additional increase in the mechanical strength of the material.
  • the unfavorable effect of silicon on the size and distribution of the minority phase has already been reported.
  • the addition of magnesium additionally has the disadvantage that magnesium with bismuth preferably forms the intermetallic compound Mg 3 Bi 2 . This accumulates in the bismuth drops and significantly reduces the embedding capacity of the bismuth drops for abrasive particles. By adding tin, the mechanical strength of the sliding bearing material is significantly impaired at higher temperatures.
  • DE 4014430 A1 and US 5,286,445 proposed in the heat treatment temperatures of about 480 0 C in view of the formation of brittle intermetallic phases between the steel shell contactor and aluminum are very unfavorable selected. According to the state of the art, the temperature range acceptable for the cladding of aluminum with steel is below 400 ° C.
  • aluminum sliding bearing alloys In addition to a fine distribution of the minority phase in the casting state, aluminum sliding bearing alloys also have the option of following the necessary forming and Walzplattiervor réellen to produce a fine distribution of the minority phase can. Other requirements are high strength, mechanical strength - including at high temperatures - wear resistance of the aluminum matrix and a good formability.
  • the invention is therefore an object of the invention to provide a heavy-duty aluminum sliding bearing alloy, which avoids the disadvantages of the prior art, and makes it possible to achieve a uniform and fine distribution of the bismuth phase and to obtain during the subsequent processing of the tapes in the manufacturing phase to slide bearing shell and possibly to improve.
  • an aluminum sliding bearing alloy containing the following constituents: about 5 to 20 wt .-% bismuth, about 3 to 20 wt .-% zinc, about 1 to 4 wt .-% copper and additionally one or several of the components manganese, vanadium, niobium, nickel, molybdenum, cobalt, iron, tungsten, chromium, silver, calcium, scandium, cerium, antimony, boron, beryllium, titanium, carbon, zirconium in total up to about 5% by weight. % and remainder aluminum, but without tin, lead and silicon, except in quantities caused by melting-induced impurities, or in a quantity of not more than 1% by weight each.
  • the alloy according to the invention should in principle not contain tin and silicon as alloying constituents. In contamination-related amounts up to about 0.3 wt .-% or otherwise in small amounts up to about 1 wt .-%, but better to about 0.5 wt .-% can both tin (Sn), lead (Pb) as well as silicon (Si), however, without unduly compromising the advantages of the invention.
  • the plain bearing alloy according to the invention is preferably continuously cast and is already characterized in the cast state by a fine distribution of the bismuth phase, which is largely independent of the withdrawal and cooling rate.
  • long bismuth plates may subsequently be fully re-coagulated by heat treatment at temperatures of 270 0 C to 400 0 C to finely divided spherical droplets, which are present at a corresponding procedure less than 20 microns.
  • the alloy contains between about 7 and 12 weight percent bismuth.
  • the proportion of zinc may preferably be between about 3 and 6 wt .-%, of copper between about 2 and 4, in particular between about 2 and 3 wt .-%.
  • the proportions of the different elements are independently variable within the given limits.
  • the alloy of the invention differs from the known by the use of bismuth as the only soft phase, ie there is no combination of bismuth with lead and / or tin, and by a max. 20 wt .-% increased zinc and up to max. 4 wt .-% increased copper content.
  • zinc and copper lead to a slight deterioration in the size of the bismuth drops in the cast state compared to binary Al-Bi alloys, but allow complete re-coagulation of bismuth strands strongly stretched after the cladding into fine up to 20 microns large spherical droplets. These anneals are provided up to 400 0 C. The glow time depends on the chemical composition.
  • increased copper contents increase the strength of the aluminum matrix and, according to our own experience, improve the corrosion resistance of the bismuth-containing plain bearing material.
  • the invention further comprises a process for producing an aluminum sliding bearing alloy using the composition of the invention as described above.
  • the alloying ingredients are combined in a casting process to form an alloy in which the cooling rate is 5 to 1000 K / s.
  • the alloy can also be produced by other customary production methods, in particular by other casting methods.
  • production by continuous casting is preferred.
  • the conditions are then adapted so that preferably drop-shaped Bismuteinlagerungen arise.
  • the take-off speed is preferably 2 to 15 mm / s.
  • the alloy obtained by casting is subjected to at least one heat treatment at temperatures between about 270 and 400 0 C according to the preferred embodiment of this invention in the course of subsequent forming processes.
  • Such heat treatment preferably follows a rolling and / or roll plating process, wherein multiple rolling and / or plating operations may be performed within the manufacturing process between the casting of the alloy and the final product and at least one heat treatment at the final rolling and / or roll plating operation or connect to several or all of these operations.
  • the cast alloy can be provided with at least one support layer.
  • the support layer may in particular be a steel layer.
  • Other layers, e.g. Adhesive layers or coatings may be added.
  • the invention further comprises a sliding bearing shell which contains or consists of an alloy according to the invention as one of the materials used therein.
  • the invention comprises a sliding bearing with such a plain bearing shell or the use of the sliding bearing shell according to the invention in a sliding bearing.
  • the invention is explained in more detail below with reference to an embodiment.
  • Fig. 1 cast structure of a AIZn5Cu3Bi7 alloy
  • the sliding bearing material cast strips with a cross-section of 10 mm ⁇ 100 mm with the addition of 0.6% by weight of AITi5B1 are produced in this example on a vertical continuous casting plant, as known in the prior art.
  • the take-off speed is 8 mm / s and the cooling speed is 600 K / s.
  • the strands are milled horizontally on the broad sides to a thickness of about 8 mm.
  • a brushed and degreased aluminum alloy primer is first roll-coated onto the brushed and degreased AIZn5Cu3Bi7 alloy in the mill stand.
  • the thickness of the plated starting material strip is 4 mm. This is then rolled to 1, 3 mm in several rolling passes. For this purpose 5 rolling passes are necessary.
  • To improve the plating capability of the aluminum bearing material strip it is subjected to a Erhohlungsglühung at 370 0 C of up to 3 hours duration.
  • the steel strip and the aluminum bearing material strip are joined together in a plating mill.
  • the produced material compound is subjected to a 3 hour heat treatment at a temperature of 360 ° C., wherein the bond between the steel and the aluminum bearing material is increased by a diffusion process and that after plating in the aluminum-zinc-copper matrix is strong stretched bismuth threads to fine up to 20 microns large spherical droplets are completely transformed.
  • the likewise from the Heat treatment resulting high hardness of at least 43 HB 2.5 / 62.5 / 30 is also beneficial.
  • the plated strip can be divided and formed into bearing shells.
  • FIGS. 1 to 3 show, by way of example, how an alloy according to the invention, in this case an AIZn5Cu3Bi7 alloy, changes its structure during processing.
  • FIG. 1 shows the structure of the alloy after production by continuous casting.
  • the bismuth phase which is in the form of droplets, is shown in the dark.
  • FIG. 2 shows the structure of the alloy after rolling.
  • the bismuth plates elongated by the rolling can be recognized.
  • Figure 3 shows the rolled structure after a heat treatment at 360 0 C for 3 hours.
  • the elongated Bi plates could be effectively recoagulated by the heat treatment.
  • Figure 1 still occasionally to be recognized larger drops were divided by the stretching and re-coagulation, so that the degree of fine distribution by the treatment is increased overall.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Sliding-Contact Bearings (AREA)
EP05756177A 2005-06-07 2005-06-07 Alliage d'aluminium pour paliers lisses Not-in-force EP1888798B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/EP2005/006091 WO2006131129A1 (fr) 2005-06-07 2005-06-07 Alliage d'aluminium pour paliers lisses

Publications (2)

Publication Number Publication Date
EP1888798A1 true EP1888798A1 (fr) 2008-02-20
EP1888798B1 EP1888798B1 (fr) 2008-12-10

Family

ID=34971668

Family Applications (1)

Application Number Title Priority Date Filing Date
EP05756177A Not-in-force EP1888798B1 (fr) 2005-06-07 2005-06-07 Alliage d'aluminium pour paliers lisses

Country Status (6)

Country Link
US (1) US20100221141A1 (fr)
EP (1) EP1888798B1 (fr)
JP (1) JP2008542548A (fr)
AT (1) ATE417132T1 (fr)
DE (1) DE502005006241D1 (fr)
WO (1) WO2006131129A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018228640A1 (fr) * 2017-06-15 2018-12-20 Zollern Bhw Gleitlager Gmbh & Co. Kg Alliage monotectique pour palier lisse à base d'aluminium et son procédé de fabrication ainsi que palier lisse ainsi fabriqué

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US8403027B2 (en) * 2007-04-11 2013-03-26 Alcoa Inc. Strip casting of immiscible metals
ES2330713B2 (es) * 2008-06-11 2010-04-19 Abinash Banerji Afinador de grano de base aluminio.
CN101838783B (zh) * 2010-02-05 2012-01-04 新星化工冶金材料(深圳)有限公司 通过控制压缩比来控制铝钛碳合金晶粒细化能力的变化量的方法
CN103031459B (zh) * 2012-12-05 2015-03-04 安徽徽铝铝业有限公司 一种掺杂有粉煤灰的铝合金熔炼用精炼剂制备方法
KR101526659B1 (ko) * 2013-05-07 2015-06-05 현대자동차주식회사 복합 미세조직을 갖는 내마모성 합금
US9963770B2 (en) 2015-07-09 2018-05-08 Ut-Battelle, Llc Castable high-temperature Ce-modified Al alloys
DE102015112550B3 (de) * 2015-07-30 2016-12-08 Zollern Bhw Gleitlager Gmbh & Co. Kg Verfahren zur Herstellung einer monotektischen Legierung
JP7249105B2 (ja) * 2018-03-22 2023-03-30 大同メタル工業株式会社 摺動部材
CN110157935B (zh) * 2019-06-28 2021-05-07 上海大学 铸造铝硅合金用Al-V-B细化剂、其制备方法及应用
CN110578075A (zh) * 2019-10-24 2019-12-17 沈阳航空航天大学 一种高性能均质铝铋难混溶合金及其制备方法
CN111057911A (zh) * 2020-01-06 2020-04-24 高品质特殊钢冶金与制备国家重点实验室张家港产业中心 一种Al-Bi偏晶合金及其制备方法

Family Cites Families (1)

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EP0947260A1 (fr) * 1998-02-04 1999-10-06 Deutsches Zentrum für Luft- und Raumfahrt e.V. Palier à glissement en alliage monotectic

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO2006131129A1 *

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2018228640A1 (fr) * 2017-06-15 2018-12-20 Zollern Bhw Gleitlager Gmbh & Co. Kg Alliage monotectique pour palier lisse à base d'aluminium et son procédé de fabrication ainsi que palier lisse ainsi fabriqué
CN110730827A (zh) * 2017-06-15 2020-01-24 卓轮Bhw滑动轴承两合公司 偏晶铝滑动轴承合金及其制造方法和借助该方法制造的滑动轴承

Also Published As

Publication number Publication date
DE502005006241D1 (de) 2009-01-22
JP2008542548A (ja) 2008-11-27
EP1888798B1 (fr) 2008-12-10
US20100221141A1 (en) 2010-09-02
WO2006131129A1 (fr) 2006-12-14
ATE417132T1 (de) 2008-12-15

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