EP1063311B1 - Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Legierung - Google Patents

Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Legierung Download PDF

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Publication number
EP1063311B1
EP1063311B1 EP00111779A EP00111779A EP1063311B1 EP 1063311 B1 EP1063311 B1 EP 1063311B1 EP 00111779 A EP00111779 A EP 00111779A EP 00111779 A EP00111779 A EP 00111779A EP 1063311 B1 EP1063311 B1 EP 1063311B1
Authority
EP
European Patent Office
Prior art keywords
tin
alloy
iron
copper
joined
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
EP00111779A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP1063311A1 (de
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
Original Assignee
Wieland Werke AG
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 Wieland Werke AG filed Critical Wieland Werke AG
Publication of EP1063311A1 publication Critical patent/EP1063311A1/de
Application granted granted Critical
Publication of EP1063311B1 publication Critical patent/EP1063311B1/de
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 CuSn alloys with tin contents above 12% 1 for components joined under the influence of heat.
  • CuSn alloys are widely used both as cast materials and as wrought materials. This class of materials can be found in numerous applications in electrical engineering, in machine and apparatus construction as well as in precision engineering, but also in the jewelry industry.
  • the usual compositions are in the range from 0.1 to 11% Sn, 0.01 to 0.4% P, balance Cu.
  • the advantages of these so-called phosphor bronzes are that they are very readily available and inexpensive worldwide and, in addition to very good physical properties, also offer the designer excellent characteristics for mechanical strength and ductility. They have sufficient corrosion resistance for a wide variety of applications.
  • the industries mentioned above provide their components for use under high mechanical loads. This naturally results in the demand for high-strength construction materials.
  • the conventional CuSn wrought alloys already occupy an outstanding position among the Cu materials with regard to the mechanical properties:
  • the common phosphor bronze with approx. 8% Sn typically reaches yield strength values of approx. 800 MPa 2 by cold forming with a large change in shape ,
  • the conventional wrought CuSn alloys can no longer be used as construction materials.
  • solder When using an additional material, namely the solder, its strength plays a role for the mechanical stability of the bonded composite. Therefore there is a desire for unbreakable solders.
  • the strength of a solder scales usually with its solidus or working temperature, i.e. high strength brazing alloys only melt at high temperatures. This relationship is not a disadvantage because this gives the designer the opportunity to create brazed components for the To be used at higher temperatures.
  • the use is more melting Solders also desirable from a manufacturing point of view, because it is, for example, expanded with working temperatures that are too high Range of different brazing alloys possible, several joining operations on one component to be carried out one after the other.
  • an alloy is used for the components to be joined in the case of the basic composition of copper has an Sn content of 12 to 20% Sn and a Fe content of 0.1 to 4% is alloyed.
  • the high Sn content and the Fe admixtures ensure particularly high strength and resistance to softening. Contrary to the conventional view, deoxidation, for example with P, is described above, not necessary. When setting Fe contents in the Alloy obviously becomes the occurrence of the dreaded Sn oxide prevented that additional deoxidizing measures are dispensed with can.
  • the Fe additives also surprisingly provide an improvement resistance to heat discoloration.
  • the primary shaping of an alloy according to the invention is expediently carried out using a casting process in which the formation of brittle phases is suppressed from the molten state by a sufficiently rapid cooling.
  • a casting process in which the formation of brittle phases is suppressed from the molten state by a sufficiently rapid cooling.
  • Such high cooling rates are used, for example, in strip casting 3 or when spray compacting 4 reached.
  • the preforms produced with these processes are characterized by uniform, low-segregation primary structures. In addition to the high strength, this structural state ensures a releasable kneadability, so that the preforms shaped in this way can be handled without problems using the classic forming processes.
  • the alloy is outstandingly hard-solderable with a wide variety Soldering. Obviously, none of the Fe contents according to the invention arise of those oxides on the surface which have poor wettability or would cause poor solder flow. The use of the proposed Alloy for joined components thus fulfills the wishes formulated above in an excellent way.
  • P can be added to the CuSnFe alloy according to the invention up to about 0.5%.
  • P causes a moderate increase in mechanical strength after cold working.
  • a P content of at least 0.01% should be used.
  • Levels of more than 0.5% should be avoided since the scale layers formed during soldering in an oxygen-containing atmosphere tend to flake off 5 .
  • high P concentrations reduce the ductility of the CuSn alloys 6 .
  • high P contents lead to the formation of coarse Fe phosphide particles, which are undesirable for many applications. They permanently disrupt the structure. Therefore, P must be set in a mass ratio Fe / P ⁇ 2/1 in order to ensure a favorable formation of the structure due to the freely separating Fe.
  • the alloy can lead to intermetallic phases or graphite can be added up to a volume fraction of 3 volume%.
  • compositions of the tapes are summarized below: alloy Cu /% Sn /% Fe /% P /% A 84.03 15.24 0.73 B 84.69 15.00 0.31 CuSn8P 91.88 7.95 0.17 (Alloy A and B according to the invention)
  • Alloys A and B according to the invention differ from the alloy of conventional phosphor bronze by their significantly higher strength values. Nevertheless, the measured values for the elongation at break A 10 and the yield point ratio R p0.2 / R m , which were determined on the alloys according to the invention, are in good agreement with the corresponding values obtained after comparable processing steps for the CuSn8P alloy deoxidized with P receives. Since one can deduce the effectiveness of deoxidation from the amount of elongation at break 7 , it can be concluded from this agreement that Fe has a positive influence on the primary and forming of CuSn alloys in the same way as P.
  • soldering behavior two hard-rolled, 1 mm thick strip strips of the same alloy were brazed after their surfaces were degreased and mechanically cleaned. A commercially available silver solder with a working temperature of 710 ° C was used. Soldering was carried out under protective gas without the use of a flux. The result of the soldering was evaluated both by mechanical torsion testing and by metallographic inspection. The strength of the joined materials in the immediate vicinity of the soldering gap - that is, in the heat affected zone (HAZ) - was characterized by the Vickers hardness HV. The table below shows the results obtained.
  • the amount of residual hardness of alloy A or B was evaluated after five minutes of annealing in relation to the usual phosphor bronze alloy: HV (alloy A or B, 700 ° C, 300 s) / HV (CuSnP, 700 ° C, 300 s) - 1.
  • HV alloy A or B, 700 ° C, 300 s
  • HV CuSnP, 700 ° C, 300 s
  • the alloys A and B were compared with the alloy CuSn8P in terms of reducing the difference between the hardness after 60 s and 300 s: 1 - [HV (Leg. A or B, 700 ° C, 60 s) - HV (Leg.
  • the microstructure of the alloys according to the invention is mentioned above To characterize heat treatment as follows: There is a low-segregation structure before, which is free of oxides, although - as is common in the prior art considered necessary - no phosphorus was alloyed. It can only Excretions are detected in which the alloying elements according to the invention Fe and Sn are enriched. The average grain sizes are in the alloys according to the invention after the above heat treatment only about 25 microns. This is due to the grain-refining effect of Fe. If desired, it is also possible to add the alloys according to the invention after joining reshape without creating roughness on the component surface, how to this is known from prior art tin bronze alloys.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Adornments (AREA)
  • Eyeglasses (AREA)
  • Electroplating And Plating Baths Therefor (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Arc Welding In General (AREA)
  • Contacts (AREA)
EP00111779A 1999-06-17 2000-06-03 Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Legierung Expired - Lifetime EP1063311B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE19927646 1999-06-17
DE19927646A DE19927646C5 (de) 1999-06-17 1999-06-17 Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Legierung

Publications (2)

Publication Number Publication Date
EP1063311A1 EP1063311A1 (de) 2000-12-27
EP1063311B1 true EP1063311B1 (de) 2002-07-03

Family

ID=7911553

Family Applications (1)

Application Number Title Priority Date Filing Date
EP00111779A Expired - Lifetime EP1063311B1 (de) 1999-06-17 2000-06-03 Verwendung einer zinnreichen Kupfer-Zinn-Eisen-Legierung

Country Status (5)

Country Link
EP (1) EP1063311B1 (es)
JP (1) JP2001049368A (es)
AT (1) ATE220121T1 (es)
DE (2) DE19927646C5 (es)
ES (1) ES2178986T3 (es)

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10133144A1 (de) 2001-07-07 2003-01-30 Rheinmetall Landsysteme Gmbh Gepanzertes Fahrzeug
DE20211557U1 (de) * 2002-07-12 2002-09-26 Berkenhoff GmbH, 35452 Heuchelheim Legierung, insbesondere für Brillengestelle

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
US3655367A (en) * 1970-07-15 1972-04-11 Albert B Bleecker Copper alloy
CA1045010A (en) * 1976-04-30 1978-12-26 Michael J. Pryor Copper base alloy
DE2620733C2 (de) * 1976-05-11 1978-03-23 W.C. Heraeus Gmbh, 6450 Hanau Verwendung von Legierungen auf Kupfer-Basis für dentaltechnische Zwecke
US4116686A (en) * 1976-05-13 1978-09-26 Olin Corporation Copper base alloys possessing improved processability
US4478651A (en) * 1982-12-03 1984-10-23 Olin Corporation Protective film on Cu-Sn alloys
DE19927136C1 (de) * 1999-06-15 2001-03-01 Wieland Werke Ag Verwendung einer Kupfer-Zinn-Eisen-Legierung

Also Published As

Publication number Publication date
DE50000258D1 (de) 2002-08-08
DE19927646C1 (de) 2001-03-01
DE19927646C5 (de) 2006-05-11
EP1063311A1 (de) 2000-12-27
ES2178986T3 (es) 2003-01-16
JP2001049368A (ja) 2001-02-20
ATE220121T1 (de) 2002-07-15

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