EP1063310B1 - Utilisation d'une alliage riche en étain de cuivre-étain-fer - Google Patents

Utilisation d'une alliage riche en étain de cuivre-étain-fer Download PDF

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Publication number
EP1063310B1
EP1063310B1 EP00111778A EP00111778A EP1063310B1 EP 1063310 B1 EP1063310 B1 EP 1063310B1 EP 00111778 A EP00111778 A EP 00111778A EP 00111778 A EP00111778 A EP 00111778A EP 1063310 B1 EP1063310 B1 EP 1063310B1
Authority
EP
European Patent Office
Prior art keywords
weight
tin
iron
alloy
manufacture
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP00111778A
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German (de)
English (en)
Other versions
EP1063310A1 (fr
Inventor
Andreas Dr. Bögel
Stephan Dr. Hansmann
Uwe Dr. Hofmann
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.)
Wieland Werke AG
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Wieland Werke AG
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Publication date
Application filed by Wieland Werke AG filed Critical Wieland Werke AG
Publication of EP1063310A1 publication Critical patent/EP1063310A1/fr
Application granted granted Critical
Publication of EP1063310B1 publication Critical patent/EP1063310B1/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Classifications

    • 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
    • C22C9/02—Alloys based on copper with tin as the next major constituent

Definitions

  • the invention relates to the use of a Cu-Sn-Fe alloy for mechanical stressed components of machine or vehicle construction.
  • the Cu-Sn-Fe alloy consists of Sn 12 - 20 wt .-%, Fe 0.2 - 5.0 wt .-%, balance Cu and the usual Impurities.
  • the alloy is cooled down sufficiently quickly from the molten state at room temperature in one Get structural condition that the preform available for the semi-finished product (Cast strip, cast block, cast bolt) is technically free of coarse, brittle phases and therefore in a special way for the production of semi-finished products Bands, profiles, wires, hollow profiles or pipes - suitable for kneading.
  • This Semi-finished products are ideal for the production of various mechanical Functional parts of precision engineering, vehicle or general mechanical engineering. Because of their chemical composition and manufacturing method draws the above Alloy high mechanical strength or high wear resistance with excellent ductility. She also has one good corrosion resistance and thermal conductivity.
  • CuSn materials are because of their high mechanical strength, their large Resistance to sliding stress or wear and their corrosion resistance for various mechanical components of the general Mechanical engineering used.
  • CuSn wrought alloys with typically 8% by weight Sn are very easy to form and are therefore also suitable for the production of complex ones Functional parts.
  • Sn cast alloys are preferred with Sn contents above 10% by weight.
  • Sn contents above 10% by weight.
  • the cast bronze has the required strength, but it is also bad formable.
  • the Material is said to be the chemical and mechanical properties of the cast bronze combine with the processing properties of the kneading materials, which is why the setting of the cold deformability and at the same time securing a high mechanical strength and hardness is necessary.
  • JP-A-04 017 635 offers a sintered alloy that acts as a sliding element to be used.
  • the material is a tin-rich CuSn alloy with about 12-20% by weight Sn, the rest Cu.
  • the high Sn content ensures the strength of the material.
  • Spray compacting 2 is a suitable method for the primary shaping of this alloy or strip casting 3 ,
  • the material cools so quickly from the molten state that the segregation that is customary in castings is suppressed.
  • the primary structure of this alloy is therefore free of macroscopic segregation at room temperature 4 ,
  • the preforms produced using these processes can be shaped very well either warm or cold.
  • the material so produced is mainly due to its excellent mechanical Properties versatile in the field of mechanical engineering. Yet some shortcomings can be identified.
  • the process of master shaping is difficult for the following reasons: As with conventional, comparatively low tin wrought wrought alloys also in the present case the need to deoxidize the melt. at The conventional alloys are therefore more oxygen-sensitive to the melt Elements such as B. phosphorus added. These additions are usually like this selected that in addition to melt deoxidation also the material properties (e.g. strength) can be influenced favorably. Because of the high affinity for oxygen the added elements tend to burn off when they melt and pour and slagging. As a result, complex process control is required for compliance of defined concentrations necessary. Generally affect the oxides The deoxidizer in the melt also sensitive to the melt viscosity and thus the procedural boundary conditions of the master molding process of spray compacting. Ideally, therefore, a vacuum oven comes for the Melting process used so that oxidation of the additives is largely prevented can be. However, the process engineering effort required is not always expedient and economical.
  • Oxides from admixtures with an affinity for oxygen can also be used in hot forming of the tin-rich CuSn alloys. They deteriorate the surface quality of the formed material and lead to tool contamination and as a result for a shorter tool life. When cutting or cutting these oxides are also undesirable in the volume of materials because they are due to their Hardness promote increased tool wear.
  • JP-A-63235455 is a phosphorus-containing copper alloy for electrical engineering Known components that have good fatigue properties.
  • the melt is produced with high cooling rate in the form of thin preforms and then rolled into 0.3 mm thick strips.
  • the object thereby achieved is achieved by the present invention according to claim 1 solved that for mechanical components of machine or vehicle construction an alloy is used, which in addition to copper has a tin content of 12 to 20% Sn and a Contains 0.2 to 5% Fe and / or Co.
  • the primary shaping of the alloy should be carried out again using a casting process, at which prevents the formation of brittle phases by a high cooling rate. It is surprising that when casting the alloy according to the invention with a such processes to a large extent on the complex vacuum or protective gas technology can be dispensed with.
  • the alloy particularly achieves Fe and Sn contents good mechanical properties. On the one hand, they express themselves in a high degree of firmness or hardness, in a high creep or softening resistance and in one high wear resistance.
  • the materials have a sufficiently high toughness which enables a related shape change through cold forming of more than 20%.
  • Sn also ensures the corrosion resistance of the material.
  • the Sn content should not exceed 20% because then - even with an unconventional casting process - The increased occurrence of brittle phases cannot be prevented.
  • iron Due to its metal-related relationship, iron can go through in whole or in part Cobalt to be replaced.
  • aluminum can contain up to 2% by weight. be added. Higher levels are not useful as they are surface processing or impair the joining of the material.
  • Nickel additives up to 5 wt .-% improve the strength properties and Corrosion resistance. Higher levels promote curing mechanisms, which means the further processing of the alloy is difficult.
  • phosphorus can be used to deoxidize the melt.
  • a significant one Effect occurs from 0.01% P.
  • the structure of the phosphorus should be matched to the iron concentration, the Fe content / P content> 2.
  • P contents above 0.5% by weight should be avoided because thereby reducing the ductility of the material on the one hand and in Loose layers of heat adhere to the heat, especially during hot forming to disturb.
  • the invention is illustrated by the following example.
  • the structure in the sprayed state was uniform and metallographically free from Segregations. After the bolt had been machined, it was hot-worked by extrusion into a rod with a diameter of 20 mm. The temperature the material was 650 ° C. The bar stock was straightened.
  • the material was in the soft state after hot forming.
  • the bars were pickled for surface leveling.
  • the further processing was carried out using cold drawing processes to increase the strength properties.
  • the use according to the invention clearly achieves the use of 0.7% by weight of Fe better mechanical properties than the Fe-free variant and is therefore the known tin arms are also more suitable for mechanically stressed components CuSn alloys.
  • the ductility parameters are for both materials similarly, from which it can be concluded that Fe additions are suitable for the formation of To complicate pores and embrittling oxide lines during the primary shaping. This was not to be expected because of this effect of iron in a CuSn alloy was not known.
  • the low level of softening of the alloys according to the invention is striking: the strength parameters clearly exceed those of a conventionally shaped tin bronze with 8% by weight of Sn 6 , which was similarly shaped and heat treated. This leads to the conclusion that the tin-rich alloys have much better mechanical properties at high temperatures (ie softening resistance, relaxation resistance, creep or creep resistance) than the conventional CuSn wrought alloys. This is the invention

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Sliding-Contact Bearings (AREA)
  • Electroplating And Plating Baths Therefor (AREA)
  • Conductive Materials (AREA)
  • Compositions Of Macromolecular Compounds (AREA)

Claims (6)

  1. Utilisation d'un alliage cuivre-étain-fer compacté par pulvérisation, qui consiste en 12 à 20 % en masse d'étain, 0,2 à 5 % en masse de fer et/ou de cobalt, au choix jusqu'à 2 % en masse d'aluminium et jusqu'à 5 % en masse de nickel, au choix du manganèse et/ou du zinc jusqu'à 5 % en masse au total, au choix encore jusqu'à 3 % en volume de plomb et/ou de phases intermétalliques et/ou de graphite comme brise-copeaux, le reste étant du cuivre et des impuretés habituelles, pour la production de pièces sollicitées mécaniquement de la construction des véhicules automobiles et de la construction mécanique générale, où le rapport teneur en Fe et/ou Co/teneur en P > 2.
  2. Utilisation selon la revendication 1 pour la production d'éléments fonctionnels de la construction mécanique, en particulier pour la production de leviers, de ressorts, de roues dentées, de roues-vis, de cylindres, d'écrous de broches, de boulons et de vis.
  3. Utilisation selon la revendication 1 pour la production d'éléments d'accouplement ou de disques de friction de la construction des véhicules automobiles ou de la construction mécanique.
  4. Utilisation d'un alliage de cuivre selon la revendication 1 avec 12 à 14 % en masse d'étain, 1 à 5 % en masse de fer pour le but selon une ou plusieurs des revendications 1 à 3.
  5. Utilisation d'un alliage de cuivre selon la revendication 1 avec 15 à 17 % en masse d'étain, 0,3 à 4 % en masse de fer pour le but selon une ou plusieurs des revendications 1 à 3.
  6. Utilisation d'un alliage de cuivre selon la revendication 1 avec 16 à 20 % en masse d'étain, 0,3 à 3 % en masse de fer, pour le but selon une ou plusieurs des revendications 1 à 3.
EP00111778A 1999-06-21 2000-06-03 Utilisation d'une alliage riche en étain de cuivre-étain-fer Expired - Lifetime EP1063310B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19928330A DE19928330C2 (de) 1999-06-21 1999-06-21 Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Knetlegierung
DE19928330 1999-06-21

Publications (2)

Publication Number Publication Date
EP1063310A1 EP1063310A1 (fr) 2000-12-27
EP1063310B1 true EP1063310B1 (fr) 2004-09-15

Family

ID=7911986

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00111778A Expired - Lifetime EP1063310B1 (fr) 1999-06-21 2000-06-03 Utilisation d'une alliage riche en étain de cuivre-étain-fer

Country Status (5)

Country Link
EP (1) EP1063310B1 (fr)
JP (1) JP2001064741A (fr)
AT (1) ATE276378T1 (fr)
DE (2) DE19928330C2 (fr)
ES (1) ES2228344T3 (fr)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10107601B4 (de) * 2001-02-17 2006-01-12 Bühler Motor GmbH Schneckenbauteil
DE102006052384A1 (de) * 2006-11-07 2008-05-08 BÖGRA Technologie GmbH Lagerschalenpaar und Verfahren zu seiner Herstellung
CN103964617B (zh) * 2014-05-09 2015-04-08 张志雄 一种外螺纹铜合金海水淡化装置
DE102015012095A1 (de) 2015-09-16 2017-03-16 Audi Ag Verfahren zur Herstellung eines Bauteils, Bauteil und Kraftfahrzeug mit einem derartigen Bauteil

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US1928747A (en) * 1928-10-11 1933-10-03 Int Nickel Co Nonferrous alloy
DE659207C (de) * 1935-12-10 1938-04-28 Aeg Verfahren zur Erhoehung der elektrischen Leitfaehigkeit von Zinnbronzen
US2128954A (en) * 1936-10-31 1938-09-06 American Brass Co Hot workable bronze
US2128955A (en) * 1937-11-26 1938-09-06 American Brass Co Hot workable phosphor bronze
US2210670A (en) * 1939-02-18 1940-08-06 Westinghouse Electric & Mfg Co Copper alloy
GB1002966A (en) * 1963-11-15 1965-09-02 Philip Edward Hustwitt Improvements in or relating to wire cloths
DE1758501A1 (de) * 1968-06-14 1971-01-21 Wangner Fa Hermann Papiermaschinensieb
CA980223A (en) * 1972-10-10 1975-12-23 John T. Plewes Method for treating copper-nickel-tin alloy compositions and products produced therefrom
US4016010A (en) * 1976-02-06 1977-04-05 Olin Corporation Preparation of high strength copper base alloy
US4732625A (en) * 1985-07-29 1988-03-22 Pfizer Inc. Copper-nickel-tin-cobalt spinodal alloy
JPH07113143B2 (ja) * 1987-03-20 1995-12-06 三菱電機株式会社 高強度銅合金の製造方法
JP2695031B2 (ja) * 1990-05-10 1997-12-24 日立粉末冶金株式会社 耐摩耗性銅系焼結合金
JPH0688156A (ja) * 1992-09-08 1994-03-29 Honda Motor Co Ltd 耐摩耗性Ｃｕ系焼結合金

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
DIES K.: "kupfer und Kupfrlegierungn in der Technik", 1967, SPRINGER VERLAG BERLIN, DEUTSCHLAND, pages: 507 - 508 *

Also Published As

Publication number Publication date
ES2228344T3 (es) 2005-04-16
JP2001064741A (ja) 2001-03-13
DE19928330A1 (de) 2001-01-04
DE50007736D1 (de) 2004-10-21
DE19928330C2 (de) 2003-01-16
ATE276378T1 (de) 2004-10-15
EP1063310A1 (fr) 2000-12-27

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