US3464865A - Process for treating copper base alloys - Google Patents

Process for treating copper base alloys Download PDF

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Publication number
US3464865A
US3464865A US629927A US3464865DA US3464865A US 3464865 A US3464865 A US 3464865A US 629927 A US629927 A US 629927A US 3464865D A US3464865D A US 3464865DA US 3464865 A US3464865 A US 3464865A
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Prior art keywords
annealing
cold
present
temperature
alloy
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US629927A
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English (en)
Inventor
George H Eichelman Jr
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Olin Corp
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Olin Corp
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    • 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
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon
    • 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

Definitions

  • the annealing and cold rolling steps are employed in accordance with the process of US. Patent 3,297,497 in order to obtain the desired gage material and the desired physical properties. It is highly desirable to provide a process which enables the greatest possible cold reduction without inordinate loss of physical properties. The advantages of greater cold reduction are significant in a commercial process. This will enable the reduction of production costs and the reduction of the number of anneals which are necessary.
  • the process of the present invention comprises:
  • aluminum from 1.0 to 5.0% iron and the balance essentially copper.
  • the preferred iron content is from 3 to 4% and the preferred aluminum content is from 9.4 to 10.4%, optimally from 9.4 to 10.0%.
  • the alloys may contain from 0.05 to 5.0% of at least one additional element having a solid solubility in copper of less than 4.0% and which forms at least one intermetallic compound with aluminum.
  • the total amount of the additional elements should be less than 10.0%.
  • the additional element is preferably selected from the following group of elements, although the alloys are not necessarily limited to these elements: chromium; titanium; zirconium; molybdenum; columbium; vanadium and mixtures thereof in the preferred amounts set forth hereinbelow. Chromium, titanium, molybdenum, oolumbium, and vanadium are each preferably present in an amount of from 0.4 to 2.0%, and optimally in an amount of from 1 to 2%. Zirconium is preferably present in an amount of from 0.05 to 0.2% and optimally from 0.1 to 0.2%.
  • the additional element must, as discussed above, have limited solid solubility in copper and be an intermetallic compound former with aluminum.
  • the additional element and/or intermetallic compounds formed should preferably form a dispersion in copper with limited solid solubility at temperatures up to 1800 F. The presence of this dispersion acts to prevent grain growth at high heat treatment temperatures.
  • the remainder or balance of the alloy is essentially copper, i.e., the alloy may contain incidental impurities or other materials which do not materially degrade the physical characteristics of the alloy.
  • incidental impurities or other materials which do not materially degrade the physical characteristics of the alloy. Examples of such elements which can be present include tin, zinc, lead, nickel, silicon, silver, phosphorus, magnesium, antimony, bismuth, and arsenic.
  • the alloy is provided in plate or sheet form having a gage of at least 0.70". It is preferred to start with plate or sheet material having a thicker gage of at least 0.2" since the primary purpose of the present invention is to enable greater cold rollability, particularly at the heavier gages. It is noted that cold rollability may be defined as the amount of reduction in gage at which the first signs of edge cracking occur.
  • the material may be cast by conventional commercial methods and hot rolled at a temperature of from 1850 to 1000 F.
  • the process of the present invention may be performed on the as hot rolled plate or, if desired, the hot rolled plate may be cold rolled prior to the process of the present invention.
  • cold rolling should be performed at a temperature below 500 F. and preferably from 0 to 200 F.
  • the plate or sheet product is annealed at a temperature of from 1100 to 1500 F. for a period of at least 15 minutes and preferably from 1 to 6 hours. It is preferred in accordance with the present invention to anneal the material at the higher end of the annealing temperature range, with the preferred range being from 1300 to 1400 F.
  • the material is critically slowly cooled to a temperature of 1000 F. at a rate slower than F. per hour, and preferably slower than 50 F. per hour. If desired, the slow cooling may be continued below 1000 F., but no particular advantage is had thereby. Also,
  • the slow cooling rate may be slower than 50 F. per hour. This slow cooling step is necessary in order to prevent the iron dissolved at elevated temperatures from precipitating as the non-equilibrium Fe Al intermetallic compound.
  • the material is cold rolled as desired.
  • a plurality of annealing and cold rolling cycles may be performed depending on particular gage requirements, with from 2 to 5 cycles of annealing and cold rolling being preferred.
  • the material it is preferred to heat the material to the annealing temperature at a rate faster than 200 F. per hour. It is still more preferred to use a still faster heat-up rate of faster than 100 F. per minute.
  • the material may be formed or brazed in accordance with conventional practices.
  • the alloy has a uniformly fine metallographic grain structure with a particle size less than 0.065 mm., and generally less than 0.040 mm.
  • the alloys of the present invention possess properties which are unexpected and surprising in alloys of this type, especially with regard to strength and ductility. For example, tensile strengths, ranging from 120,000 to 160,000 p.s.i. and yield strengths from 60,000 to 80,000 p.s.i. (0.2 percent offset) may be developed in combination with elongations ranging from 12 to 9 percent.
  • the electrical conductivities are good for alloys of this type, ranging from 10 to 16 percent IACS.
  • modifications of the present invention improve the properties still further.
  • tempering increases the yield strength considerably, e.g., to from 60,000 to 110,000 p.s.i., at the expense, however, of ductility.
  • yield strength values as high as 115,000 p.s.i. and higher may be achieved together with tensile strengths as high as 148,000 p.s.i.
  • Example I Alloys containing 9.7% aluminum, 4.0% iron, balance essentially copper, were prepared from a charge of cathode copper, aluminum-iron master alloy and commercial purity aluminum in the form of commercial size DC cast bars.
  • the alloy was hot rolled in the temperature range of from 1600 to 1300 F., using a thirteen (13) pass schedule, in reducing the gage from 5" to 0.25".
  • Example 11 Fol-lowing hot rolling the alloy of Example I was annealed at 1150 F. for 5 hours, followed by a water quench to room temperature. The material was then cold rolled and it was found that the material could be cold rolled 40% to the start of edge cracking.
  • Example IV The material of Example I following the treatment of Example I was treated in the following manner: The ma terial was cold rolled 29% followed by annealing at 1375 F. for 5 hours, with a heat-up rate to annealing temperature of about 150 F. per hour. After annealing the material was slowly cooled to 1000 F. at a rate of about 50 F. per hour followed by water quenching to room temperature. The material was then cold rolled, with a cold rollability value-of 52% being obtained. This cold rollability value should be sharply contrasted to the lower cold rollability obtained in Examples II and III.
  • Example V The procedure of Example IV was repeated with the exception that the material was rapidly heated to annealing temperature at a rate of approximately 100 F. per minute. In this case, a cold rollability value of 58% was obtained.
  • Example VI The procedure of Example IV was repeated with the following exceptions: The annealing temperature was 1450 F. for 24 hours. In this case the cold rollability was 55%.
  • Example VII The procedure of Example VI was repeated except that the material was held at temperature for 43 hours. In this case the cold rollability value was 55%.
  • each succeeding annealing step is conducted at a lowerv temperature.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Conductive Materials (AREA)
  • Metal Rolling (AREA)
US629927A 1967-04-11 1967-04-11 Process for treating copper base alloys Expired - Lifetime US3464865A (en)

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US62992767A 1967-04-11 1967-04-11

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US (1) US3464865A (esLanguage)
BE (1) BE713546A (esLanguage)
DE (1) DE1758158A1 (esLanguage)
FR (1) FR1573083A (esLanguage)
GB (1) GB1183655A (esLanguage)
SE (1) SE339114B (esLanguage)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3653980A (en) * 1970-06-11 1972-04-04 Olin Corp Method of obtaining exceptional formability in aluminum bronze alloys
US3656945A (en) * 1970-06-11 1972-04-18 Olin Corp High strength aluminum bronze alloy
US3841921A (en) * 1973-03-02 1974-10-15 Olin Corp Process for treating copper alloys to improve creep resistance
US4025367A (en) * 1976-06-28 1977-05-24 Olin Corporation Process for treating copper alloys to improve thermal stability
US5039355A (en) * 1989-03-22 1991-08-13 Daumas Marie T Process for obtaining parts made of copper of very fine texture from a billet made by continuous casting

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
ES2641016T3 (es) * 2010-07-05 2017-11-07 Ykk Corporation Producto de aleación de cobre-cinc y procedimiento para producir el producto de aleación de cobre-cinc

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3287180A (en) * 1963-12-05 1966-11-22 Olin Mathieson Method of fabricating copper base alloy
US3290182A (en) * 1965-05-25 1966-12-06 Olin Mathieson Method of making aluminum bronze articles
US3297497A (en) * 1964-01-29 1967-01-10 Olin Mathieson Copper base alloy

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3287180A (en) * 1963-12-05 1966-11-22 Olin Mathieson Method of fabricating copper base alloy
US3297497A (en) * 1964-01-29 1967-01-10 Olin Mathieson Copper base alloy
US3290182A (en) * 1965-05-25 1966-12-06 Olin Mathieson Method of making aluminum bronze articles

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3653980A (en) * 1970-06-11 1972-04-04 Olin Corp Method of obtaining exceptional formability in aluminum bronze alloys
US3656945A (en) * 1970-06-11 1972-04-18 Olin Corp High strength aluminum bronze alloy
US3841921A (en) * 1973-03-02 1974-10-15 Olin Corp Process for treating copper alloys to improve creep resistance
US4025367A (en) * 1976-06-28 1977-05-24 Olin Corporation Process for treating copper alloys to improve thermal stability
US5039355A (en) * 1989-03-22 1991-08-13 Daumas Marie T Process for obtaining parts made of copper of very fine texture from a billet made by continuous casting

Also Published As

Publication number Publication date
GB1183655A (en) 1970-03-11
BE713546A (esLanguage) 1968-10-11
DE1758158A1 (de) 1971-01-14
SE339114B (esLanguage) 1971-09-27
FR1573083A (esLanguage) 1969-07-04

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