EP2215278A1 - Copper tin nickel phosphorus alloys with improved strength and formability - Google Patents
Copper tin nickel phosphorus alloys with improved strength and formabilityInfo
- Publication number
- EP2215278A1 EP2215278A1 EP08837615A EP08837615A EP2215278A1 EP 2215278 A1 EP2215278 A1 EP 2215278A1 EP 08837615 A EP08837615 A EP 08837615A EP 08837615 A EP08837615 A EP 08837615A EP 2215278 A1 EP2215278 A1 EP 2215278A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- copper base
- alloys
- base alloy
- iacs
- 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.)
- Withdrawn
Links
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
-
- 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
-
- 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
- C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
-
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/026—Alloys based on copper
Definitions
- This invention relates to copper alloys, and in particular to copper-tin-nickel-phosphorus alloys with improved strength and formabiiity.
- Table 1 shows currently available Cu-Sn-Ni-P alloys: Table 1 : Available connector alloys in the Cu-Sn-Ni-P family
- C19025 comes close to achieving the desired properties but lacks the strength with acceptable formability; C40820 has the strength and superior formability but does not have the electrical conductivity.
- Embodiments of the present invention provide a copper-tin- nickel-phosphorus alloy with an improved combination or properties, and in particular improved combination of yield strength and formability.
- the alloy comprises between about 1 % and about 2% Sn; between about 0.3% and about 1 %Ni; between about 0.05% and about 0.15% P, and at least one of between about 0.01% and about 0.20% Mg and about 0.02% and about 0.4% Fe, the balance being copper.
- the addition of iron can be used as a low cost substitute for of Mg if good stress relaxation is not required for the application.
- the alloy comprises between about 1.1% and about 1.8% Sn, between about 0.4% and about 0.9% Ni, between about 0.05% and about 0.14% P, and between about 0.05 and about 0.15 Mg. Fe may be substituted for some of the Mg. Most preferably the alloy comprises, between about 1.2% and about 1.5% Sn; between about 0.5% and about 0.7%Ni; between about 0.09% and about 0.13% P, and between about 0.02% and about 0.06% Mg, the balance being copper.
- the alloy is preferably processed to have a yield strength of at ieast about 77 KSI, electrical conductivity of at least about 37 %IACS, and formability (90° GW/BW) of 1.0/1.0.
- the alloy preferably also has a stress relaxation of 65% at 150 0 C.
- the Sn gives the alloy solid solution strengthening. Ni and Mg are added to form precipitates of phosphorus with the added benefit of Mg increasing strength without lowering the electrical conductivity.
- the metal (Ni+Mg) to P ratio (the M/P ratio) is preferably controlled to a range of 4 to 8.5. If the ratio falls below 4 strengthening is not obtained and if is greater that 8.5 the material does not achieve 40% IACS.
- the alloy is processed by melting and casting, hot rolling from about 850 -C to about 1000 Q C cold rolling up to about 75% annealing between about 450 Q C - about 600 Q C, cold roiling up to about a 60% reduction followed by annealing at 425 2 C to about 600 5 C, cold rolling to about 50% prior to the final anneal between about 400 S C and 550 e C.
- a final cold roll reduction is given to achieve the desired thickness and mechanical strength prior to a thermal stress relief treatment.
- the processing includes a double final anneal treatment and the eiimination of an upstream anneal which improves formability and strength respectively.
- Fig. 1 is a photomicrograph of the alloy in Exarnpie 1 ;
- Fig. 2 is a graph showing the relationship between YS and M/P ratio, and illustrating the preferred M/P ratio for a Cu-Sn-Ni-P-Mg alloy;
- Fig. 3 is a graphs showing the relationship between %IACS and M/P ratio, and illustrating the preferred M/P ratio of 4-8.5 ratio for a Cu- Sn-Ni-P-Mg alloy;
- Fig. 4A is a flow chart of a preferred embodiment of a method of processing alloys in accordance with the principles of the present invention.
- Fig. 4B is a flow chart of an alternate preferred embodiment of processing alloys in accordance with the principles of this present invention.
- Fig. 4C is a flow chart of an alternate preferred embodiment of processing alloys in accordance with the principles of this present invention.
- Fig. 5 is a photomicrograph of an alloy 4 after double anneal, showing a grain size of between 6 - 7 ⁇ m, with some areas appearing to have not fully recrystailized grains;
- Fig. 6 is a photomicrograph of an alloy 4 from the process 3 after strip anneal, showing a grain size of 4 - 5 ⁇ m.
- Embodiments of the present invention provide a copper-tin- nickel-phosphorus alloy with an improved combination or properties, and in particular improved combination of yield strength and formabiiity.
- the alloy comprises between about 1% and about 2% Sn; between about 0.3% and about 1%Ni; between about 0.05% and about 0.15% P, and at least one of between about 0.01% and about 0.20% Mg and about 0.02% and about 0.4% Fe, the balance being copper.
- the addition of iron can be used as a low cost substitute for of Mg if good stress reiaxation is not required for the application.
- the alloy comprises, between about 1.2% and about 1.5% Sn; between about 0.5% and about 0.7%Ni; between about 0.09% and about 0.13% P, and between about 0.02% and about 0.06% Mg, the balance being copper.
- the alloy is preferably processed to have a yield strength of at least about 77 KSI, electrical conductivity of at least about 37 %IACS, and formabiiity (90° GW/BW) of 1.0/1.0.
- the alloy preferably also has a stress relaxation of 65% at 150 0 C.
- the Sn gives the alloy soiid solution strengthening. Ni and Mg are added to form precipitates of phosphorus with the added benefit of Mg increasing strength without lowering the electrical conductivity.
- the M/P ration is preferably controlied to a range of 4 to 8.5. If the ratio falls below 4 strengthening is not obtained and if is greater that 8.5 the material does not achieve 40% IACS.
- the alloy is processed by melting and casting, hot rolling from 850- 1000 s C cold rolling up to about 75% annealing between 450- 600 5 C, cold roliing about 60% followed by annealing at 425-600 Q C, cold rolling about 50% prior to the final anneal between 400-550 s C.
- a final coid roll reduction is given to achieve the desired thickness and mechanical strength prior to a thermal stress relief treatment.
- the processing includes a double final anneal treatment and the elimination of an upstream anneal which improves formability and strength respectively.
- the alioys were cleaned and coid rolled to 0.048" and annealed at 525-C for 2 hours.
- the alloys were cold rolied to 0.030" and annealed at 500 s C for 2 hours.
- the final coid roll was 60% to 0.012" and a stress relief heat treatment was performed at 250 s C for 2 hours.
- the Ni level is preferably at least 0.5 and the best overall alloys had a Ni/P ratio of 7-9. All the bends were poor due to the presence of contamination of sulfur forming long stringers as shown in Figure 1.
- the alloys were cleaned and cold rolled to 0.048" and annealed at 525 S C for 2 hours.
- the alloys were cold rolled to 0.024" and annealed at 450 s C for 8 hours.
- the final cold roll was 50% to 0.012" and a stress relief heat treatment was performed at 250-C for 2 hours.
- the strengths are low with the exception of alloys K293 and K294. Both these alloys contained more Sn than any of the others by about 0.5% correlating higher Sn levels to higher strength.
- the strengths of K286, K287 and K288 indicate the benefit of Mg as opposed to alloys of very close composition but without Mg, K282 and K284. It is notable that there is no drop in conductivity (the %IACS) accompanying the increase in yield strength. There was an increase in strength with the addition of iron to K291 and Mg in K289 both without Ni. The conductivity for the iron containing alloy is lower than the Mg containing alloy by about 4 %iACS.
- the alloys were cleaned and cold rolled to 0.048" and annealed at 525 S C for 2 hours.
- the alloys were cold rolled to 0.024" and annealed at 450 6 C for 4 hours only for the single anneal condition and for 450 9 C for 4 hours plus 375°C for another 4 hours constituting the double anneal condition.
- the final cold roll was 50% to 0.012" and a stress relief heat treatment was performed at 250 Q C for 2 hours for both conditions.
- the alloys were cleaned and cold rolled to 0.048" and annealed at 525 Q C for 2 hours.
- the alloys were cold rolled to 0.024" and annealed at 450 9 C for 4 hours only plus 375 0 C for another 4 hours.
- the final cold roll was 50% to 0.012" and a stress relief heat treatment was performed at 250 a C for 2 hours.
- the Mg containing alloy with an M/P ratio below 9 was the only one to improve YS whiie maintaining or improving conductivity.
- YS is in KSI
- YS is in KSI
- the chemistry given in the Table 12 is the analyzed chemistry for the cast bars. Alloy 6 lies within the CDA range for C19025 and is present as a comparative example. Ail alloys were processed the same way: They were all hot rolled from 900 0 C, coil milled and then cold rolled to 0.125 or 0.100 gauge.
- Processes 3 and 4 generally gave the best results.
- the results for Processes 1 and 2 on alloys 1 and 4 show slightly different results if the process is conducted in the plant (Process 2) rather than in the lab (Process 1) may have caused grain growth.
- Table 15 shows that the double anneal process (Process 2) gives good bends when simulated in
- Plant processed alloys were subjected to stress relaxation testing at 15O 0 C.
Landscapes
- 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)
Abstract
Description
Claims
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US97906407P | 2007-10-10 | 2007-10-10 | |
US12/249,530 US20090098011A1 (en) | 2007-10-10 | 2008-10-10 | Copper Tin Nickel Phosphorus Alloys With Improved Strength and Formability and Method of Making Same |
PCT/US2008/079573 WO2009049201A1 (en) | 2007-10-10 | 2008-10-10 | Copper tin nickel phosphorus alloys with improved strength and formability |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2215278A1 true EP2215278A1 (en) | 2010-08-11 |
EP2215278A4 EP2215278A4 (en) | 2015-09-02 |
Family
ID=40534408
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08837615.7A Withdrawn EP2215278A4 (en) | 2007-10-10 | 2008-10-10 | Copper tin nickel phosphorus alloys with improved strength and formability |
Country Status (8)
Country | Link |
---|---|
US (1) | US20090098011A1 (en) |
EP (1) | EP2215278A4 (en) |
JP (1) | JP5752937B2 (en) |
CN (1) | CN101874122A (en) |
CA (1) | CA2702358A1 (en) |
MX (1) | MX2010003995A (en) |
TW (1) | TW200934882A (en) |
WO (1) | WO2009049201A1 (en) |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8821655B1 (en) | 2010-12-02 | 2014-09-02 | Fisk Alloy Inc. | High strength, high conductivity copper alloys and electrical conductors made therefrom |
CN110462091B (en) * | 2017-02-04 | 2022-06-14 | 美题隆公司 | Method for producing copper-nickel-tin alloy |
CN113981265A (en) * | 2021-09-07 | 2022-01-28 | 铜陵有色金属集团股份有限公司金威铜业分公司 | Copper alloy having excellent hot rolling properties and method for producing same |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0616522B2 (en) * | 1987-03-04 | 1994-03-02 | 日本鉱業株式会社 | Copper alloy foil for tape carrier |
US4908275A (en) * | 1987-03-04 | 1990-03-13 | Nippon Mining Co., Ltd. | Film carrier and method of manufacturing same |
US5322575A (en) * | 1991-01-17 | 1994-06-21 | Dowa Mining Co., Ltd. | Process for production of copper base alloys and terminals using the same |
US6254702B1 (en) * | 1997-02-18 | 2001-07-03 | Dowa Mining Co., Ltd. | Copper base alloys and terminals using the same |
US7182823B2 (en) * | 2002-07-05 | 2007-02-27 | Olin Corporation | Copper alloy containing cobalt, nickel and silicon |
JP4660735B2 (en) * | 2004-07-01 | 2011-03-30 | Dowaメタルテック株式会社 | Method for producing copper-based alloy sheet |
JP4810703B2 (en) * | 2005-09-30 | 2011-11-09 | Dowaメタルテック株式会社 | Copper alloy production method |
JP4984108B2 (en) * | 2005-09-30 | 2012-07-25 | Dowaメタルテック株式会社 | Cu-Ni-Sn-P based copper alloy with good press punchability and method for producing the same |
JP4680765B2 (en) * | 2005-12-22 | 2011-05-11 | 株式会社神戸製鋼所 | Copper alloy with excellent stress relaxation resistance |
JP5075438B2 (en) * | 2007-03-20 | 2012-11-21 | Dowaメタルテック株式会社 | Cu-Ni-Sn-P copper alloy sheet and method for producing the same |
-
2008
- 2008-10-10 JP JP2010529100A patent/JP5752937B2/en active Active
- 2008-10-10 WO PCT/US2008/079573 patent/WO2009049201A1/en active Application Filing
- 2008-10-10 CN CN200880113779A patent/CN101874122A/en active Pending
- 2008-10-10 CA CA2702358A patent/CA2702358A1/en not_active Abandoned
- 2008-10-10 EP EP08837615.7A patent/EP2215278A4/en not_active Withdrawn
- 2008-10-10 US US12/249,530 patent/US20090098011A1/en not_active Abandoned
- 2008-10-10 MX MX2010003995A patent/MX2010003995A/en unknown
- 2008-10-13 TW TW097139291A patent/TW200934882A/en unknown
Non-Patent Citations (1)
Title |
---|
See references of WO2009049201A1 * |
Also Published As
Publication number | Publication date |
---|---|
EP2215278A4 (en) | 2015-09-02 |
US20090098011A1 (en) | 2009-04-16 |
JP2011500963A (en) | 2011-01-06 |
MX2010003995A (en) | 2010-09-30 |
CA2702358A1 (en) | 2009-04-16 |
TW200934882A (en) | 2009-08-16 |
WO2009049201A1 (en) | 2009-04-16 |
JP5752937B2 (en) | 2015-07-22 |
CN101874122A (en) | 2010-10-27 |
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RA4 | Supplementary search report drawn up and despatched (corrected) |
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RIC1 | Information provided on ipc code assigned before grant |
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