CA1270381A - Copper-nickel-tin-cobalt spinodal alloy - Google Patents
Copper-nickel-tin-cobalt spinodal alloyInfo
- Publication number
- CA1270381A CA1270381A CA000589706A CA589706A CA1270381A CA 1270381 A CA1270381 A CA 1270381A CA 000589706 A CA000589706 A CA 000589706A CA 589706 A CA589706 A CA 589706A CA 1270381 A CA1270381 A CA 1270381A
- Authority
- CA
- Canada
- Prior art keywords
- alloy
- percent
- tin
- weight
- copper
- 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
Links
Landscapes
- Powder Metallurgy (AREA)
Abstract
COPPER-NICKEL-TIN-COBALT SPINODAL ALLOY
Abstract Disclosed is a copper base spinodal alloy prepared by powder metallurgy consisting essentially of from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 percent by weight cobalt and the balance copper, the said alloy having an unaged micro-structure characterized by an equiaxed grain structure of substantially all alpha, face-centered-cubic phase with a subs-tantially uniform dispersed concentration of tin and a substantial absence of tin segregation. The ductility and electrical conduc-tivity of an age hardened spinodally decomposed copper-nickel-tin 5 alloy can be improved, without detracting from the alloy's strength properties.
Abstract Disclosed is a copper base spinodal alloy prepared by powder metallurgy consisting essentially of from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 percent by weight cobalt and the balance copper, the said alloy having an unaged micro-structure characterized by an equiaxed grain structure of substantially all alpha, face-centered-cubic phase with a subs-tantially uniform dispersed concentration of tin and a substantial absence of tin segregation. The ductility and electrical conduc-tivity of an age hardened spinodally decomposed copper-nickel-tin 5 alloy can be improved, without detracting from the alloy's strength properties.
Description
` ~ 2701;313~
D.P.C.(Me) ~838/6859 COPPER-NICKEL-TIN-COBALT SPI~ODAL ALLOY
_ This is a divisional application of Serial No. 487,379 filed July 24, 19~5.
Background of the Invention The present invention relates to copper-base spinodal alloys and, in particular, copper-base spinodal alloys also containing nickel and tin.
Ternary copper-nickel-tin spinodal alloys are known in the metallurgical arts. As one example, U.S. Patent 4,373,970 discloses spinodal alloys containing from about 5 to 35 welght percent nickel, from about 7 to 13 weight percent tin, and the balance copper. The alloys disclosed by this prior art patent exhibit in the age hardened spinodally decomposed state a highly desirable combination of mechanical and electrical properties, i.e. good strength and good electrical conductivity, and thus have valuable utility as a material of construction for articles of manufactu~e such as electrical connectors and relay elements. One particular ternary spinodal alloy composi-tion falling within the scope of the disclosure of U.S. Patent 4,373,970 contains about 15 weight percent nickel and about 8 weight percent tin and is sold commercially under the trade name of Pfinodal ~trademark of Pfizer Inc., New York, N~). This alloy composition combines a sufficient strength for many commercial applications with a good ductility and an excellent electrical conductivity. When greater strength properties than those afforded by the Cu-15Ni-8Sn alloy composi-tion are required for certain other applications, this can be .
--``` 12~7038~
D.P.C.(Me) ~838/6859 COPPER-NICKEL-TIN-COBALT SPI~ODAL ALLOY
_ This is a divisional application of Serial No. 487,379 filed July 24, 19~5.
Background of the Invention The present invention relates to copper-base spinodal alloys and, in particular, copper-base spinodal alloys also containing nickel and tin.
Ternary copper-nickel-tin spinodal alloys are known in the metallurgical arts. As one example, U.S. Patent 4,373,970 discloses spinodal alloys containing from about 5 to 35 welght percent nickel, from about 7 to 13 weight percent tin, and the balance copper. The alloys disclosed by this prior art patent exhibit in the age hardened spinodally decomposed state a highly desirable combination of mechanical and electrical properties, i.e. good strength and good electrical conductivity, and thus have valuable utility as a material of construction for articles of manufactu~e such as electrical connectors and relay elements. One particular ternary spinodal alloy composi-tion falling within the scope of the disclosure of U.S. Patent 4,373,970 contains about 15 weight percent nickel and about 8 weight percent tin and is sold commercially under the trade name of Pfinodal ~trademark of Pfizer Inc., New York, N~). This alloy composition combines a sufficient strength for many commercial applications with a good ductility and an excellent electrical conductivity. When greater strength properties than those afforded by the Cu-15Ni-8Sn alloy composi-tion are required for certain other applications, this can be .
--``` 12~7038~
- 2 - 67839-63D
realized hy raising the nickel and tin levels within the ranges for -those elements disclosed in U.S. Patent 4,373,970. However, thls increased strength tends to be achieved at the expense of the valuable ductility, formability and electrical conductivity properties of the age hardened spinodally decomposed alloy.
Other copper base spinodal alloys containing nickel and tin are disc]osed in U.S. Patents 3,937,638; 4,012,240; 4,090,890;
4,130,~21; 4,1~2,918, 4,260,432 and 4,406,712, and U.S. Reissue Patent 31,180 (a reissue of U.S. Patent 4,052,20~).
Quaternary copper-nickel~tin-cobalt alloys are disclosed in U.~. Patents 3,940,290 and 3,953,249. These al]oys contain only 1.5% to 3.3~ -tin and thus do not appear to be spinoda]
alloys. Furthermore, these prior art patents -teach that the cobalt level in -the alloy should not exceed 3% in order to mini-mize impairment of ductility and hot workability.
Japanese Published Patent Application No. 5942/81 (published January 22, 1981) discloses a series o~ cast copper-base quaternary spinodal alloys containing 9 wt. % nickel and 6 wt. % tin, including, inter alia, alloys containing 0.5, 0.8 and 2.0 wt~ % cobalt, respectively, as the quaternary element.
It has now been discovered that the replacement of a portion of the weight percentage of nickel in a copper-nickel-tin spinodal alloy with an approximately equal weight percentage of cobalt gives rise to improved ductility, formability (~
bendability) and electrical conductivity in the age hardened spinodally decomposed state without substantial diminishment of strength properties in that state.
38~
realized hy raising the nickel and tin levels within the ranges for -those elements disclosed in U.S. Patent 4,373,970. However, thls increased strength tends to be achieved at the expense of the valuable ductility, formability and electrical conductivity properties of the age hardened spinodally decomposed alloy.
Other copper base spinodal alloys containing nickel and tin are disc]osed in U.S. Patents 3,937,638; 4,012,240; 4,090,890;
4,130,~21; 4,1~2,918, 4,260,432 and 4,406,712, and U.S. Reissue Patent 31,180 (a reissue of U.S. Patent 4,052,20~).
Quaternary copper-nickel~tin-cobalt alloys are disclosed in U.~. Patents 3,940,290 and 3,953,249. These al]oys contain only 1.5% to 3.3~ -tin and thus do not appear to be spinoda]
alloys. Furthermore, these prior art patents -teach that the cobalt level in -the alloy should not exceed 3% in order to mini-mize impairment of ductility and hot workability.
Japanese Published Patent Application No. 5942/81 (published January 22, 1981) discloses a series o~ cast copper-base quaternary spinodal alloys containing 9 wt. % nickel and 6 wt. % tin, including, inter alia, alloys containing 0.5, 0.8 and 2.0 wt~ % cobalt, respectively, as the quaternary element.
It has now been discovered that the replacement of a portion of the weight percentage of nickel in a copper-nickel-tin spinodal alloy with an approximately equal weight percentage of cobalt gives rise to improved ductility, formability (~
bendability) and electrical conductivity in the age hardened spinodally decomposed state without substantial diminishment of strength properties in that state.
38~
- 3 - 67839-63D
Thus, the parent application is directed to a copper base spinodal alloy consisting essentially of from about 5 to about 30 percent by weight nickel, from ahout 4 to about 13 per-cent by weight tin, from about 3.5 to about 7 percent by weight cobalt and the balance copper, with the sum of the nickel an~
cobalt contents being no more than 35 percent by weight of the alloy.
Of particular interest is an alloy of the inven-tion wherein the tin content is from about 8.5 percent by weight to about 13 percent by weight and the sum of the nickel and cobalt contents is at least 20 percent by weight. This alloy affords high strength properties while maintaining satisfactory ductility, formability and electrical conductivity properties for a wide variety oE applications.
This divisional application is directed to a novel copper base spinodal alloy prepared by powder metallurgy consist-ing essentially of from about 5 to about 30 percent by weigh-t nickel, from about 4 to about 13 percent by weigh-t tin, from about 0.5 to about 3.5 percent by weight cobalt and the balance copp~r.
This alloy af-fords an excellent combination of strength, ductili-ty, formability ~e.g. bendability) and electrical conductivity properties and has an unaged microstructure characterized by an equiaxed grain structure of substantially all alpha, face-centered-cubic phase with a substantially uniEorm dispersed concentration of tin and a substantial absence of tin segrega-tion.
This divisional application is further directed to a `` 3L~7~
Thus, the parent application is directed to a copper base spinodal alloy consisting essentially of from about 5 to about 30 percent by weight nickel, from ahout 4 to about 13 per-cent by weight tin, from about 3.5 to about 7 percent by weight cobalt and the balance copper, with the sum of the nickel an~
cobalt contents being no more than 35 percent by weight of the alloy.
Of particular interest is an alloy of the inven-tion wherein the tin content is from about 8.5 percent by weight to about 13 percent by weight and the sum of the nickel and cobalt contents is at least 20 percent by weight. This alloy affords high strength properties while maintaining satisfactory ductility, formability and electrical conductivity properties for a wide variety oE applications.
This divisional application is directed to a novel copper base spinodal alloy prepared by powder metallurgy consist-ing essentially of from about 5 to about 30 percent by weigh-t nickel, from about 4 to about 13 percent by weigh-t tin, from about 0.5 to about 3.5 percent by weight cobalt and the balance copp~r.
This alloy af-fords an excellent combination of strength, ductili-ty, formability ~e.g. bendability) and electrical conductivity properties and has an unaged microstructure characterized by an equiaxed grain structure of substantially all alpha, face-centered-cubic phase with a substantially uniEorm dispersed concentration of tin and a substantial absence of tin segrega-tion.
This divisional application is further directed to a `` 3L~7~
- 4 - 67839-63D
powder metallurgical process for preparing the novel alloy of the invention.
As used herein the term "spinodal a:LI.oy" refers to an alloy whose chemical composition is such that it is capable of undergoing spinodal decomposition. An alloy that has already undergone spinodal decomposition is referred to as an "age hardened spinodally decomposed alloy", a "spinodal hardened alloy", or the like. Thus, the term "spinodal alloy" refers to alloy chemistry rather than alloy physical state and a "spinodal alloy" may or may not be at any particular time in an "age hardened spinodally decomposed" state.
The spinodal alloy of the present invention consists essentially of copper, nickel, tin and cobalt. The alloy may optionally contain small amounts of additional elements as desired, ~ iron, maynesium, manganese, molyb~enum, niobium, tantalum, vanadium, aluminum, chromium, silicon, zinc and zirco-nium, as long as the basic and novel characteristics of the alloy are not materially affected in an adverse manner thereby.
The spinodal decomposition of the alloy is an age hardening operation carried out for at least about 15 seconds at a temperature of from about 500F to about 1000F. In any parti-cular case the upper limit of this temperature range is primarily established by the chemical composition of the alloy while the lower limlt of the range is primarily established by the nature and extent of working of the alloy performed immediately prior to the age hardening. Spinodal decomposition is characterized by the formation of a two-phase al.loy m.icrostructure i.n which the second phase is Einely dispersed throughout the first phase. Optimum ~'``
.,, "'~
~27~
powder metallurgical process for preparing the novel alloy of the invention.
As used herein the term "spinodal a:LI.oy" refers to an alloy whose chemical composition is such that it is capable of undergoing spinodal decomposition. An alloy that has already undergone spinodal decomposition is referred to as an "age hardened spinodally decomposed alloy", a "spinodal hardened alloy", or the like. Thus, the term "spinodal alloy" refers to alloy chemistry rather than alloy physical state and a "spinodal alloy" may or may not be at any particular time in an "age hardened spinodally decomposed" state.
The spinodal alloy of the present invention consists essentially of copper, nickel, tin and cobalt. The alloy may optionally contain small amounts of additional elements as desired, ~ iron, maynesium, manganese, molyb~enum, niobium, tantalum, vanadium, aluminum, chromium, silicon, zinc and zirco-nium, as long as the basic and novel characteristics of the alloy are not materially affected in an adverse manner thereby.
The spinodal decomposition of the alloy is an age hardening operation carried out for at least about 15 seconds at a temperature of from about 500F to about 1000F. In any parti-cular case the upper limit of this temperature range is primarily established by the chemical composition of the alloy while the lower limlt of the range is primarily established by the nature and extent of working of the alloy performed immediately prior to the age hardening. Spinodal decomposition is characterized by the formation of a two-phase al.loy m.icrostructure i.n which the second phase is Einely dispersed throughout the first phase. Optimum ~'``
.,, "'~
~27~
- 5 - 67839-63D
micros-tructures are ohtained when the alloy i9 annealed and rapidly cooled before it is age hardened.
The spinodal alloy of the present inventlon may be prepared by a variety of known techniques involving, for example, sintering a body of compacted alloy powder (powder metal]urgy) Because the use of casting processes tends to result in the presence of substantial tin segregation at grain boundaries in the spinodally decomposed product, the use of powder metallurgical techniques is preferred.
A part;cularly preferred powder metallurgical process for preparing an alloy of the present invention is the one set I
forth tfor -the Cu-Ni-Sn ternary system) in U.S. Patent 4,373,970.
Reference is made to that patent for a detailed description of this process, including guidelines for the proper selection of various operational parameters. It should be pointed out that this process may be readily adapted to prepare an alloy of the present invention in a wide variety of three-dimensional forms and not only in the form of a strip.
According to the process of U.S. Patent 4,373,970, as adapted to prepare the quaternary alloy of the present invention, an alloy powder containing appropriate proportions of copper, nickel, tin and cobalt is compacted, preferably to at least about twice its original uncompac-ted densi-ty, to form a green body having structural integrity and sufficient porosity to be penetra-ted by a reducing atmosphere, and preferably, a compacted density of from about 70 to 95 percent of the theoretical density. The green body is sintered in the reducing atmosphere, preferably for ~z~
micros-tructures are ohtained when the alloy i9 annealed and rapidly cooled before it is age hardened.
The spinodal alloy of the present inventlon may be prepared by a variety of known techniques involving, for example, sintering a body of compacted alloy powder (powder metal]urgy) Because the use of casting processes tends to result in the presence of substantial tin segregation at grain boundaries in the spinodally decomposed product, the use of powder metallurgical techniques is preferred.
A part;cularly preferred powder metallurgical process for preparing an alloy of the present invention is the one set I
forth tfor -the Cu-Ni-Sn ternary system) in U.S. Patent 4,373,970.
Reference is made to that patent for a detailed description of this process, including guidelines for the proper selection of various operational parameters. It should be pointed out that this process may be readily adapted to prepare an alloy of the present invention in a wide variety of three-dimensional forms and not only in the form of a strip.
According to the process of U.S. Patent 4,373,970, as adapted to prepare the quaternary alloy of the present invention, an alloy powder containing appropriate proportions of copper, nickel, tin and cobalt is compacted, preferably to at least about twice its original uncompac-ted densi-ty, to form a green body having structural integrity and sufficient porosity to be penetra-ted by a reducing atmosphere, and preferably, a compacted density of from about 70 to 95 percent of the theoretical density. The green body is sintered in the reducing atmosphere, preferably for ~z~
- 6 - 57839-63D
at least one minute at a temperature of from about 1~00F to about 1900F, more preferably from about 1600F t.o about 1700F. The sintered body is then cooled at a rate, typically at least about 200F per minute until the age hardening temperature range of the alloy has been traversed, such -that age hardening and embrittle-ment are prevented. As used herein, the term "alloy powder"
inc]udes both blended elemental powders and prealloyed powders, as well as mixtures thereof.
Although the sintered body can be subjected directly to age hardening spinodal decomposition, it is preferred to first subject the alloy body to working (with cold working preferred to hot working) and annealing. Thus, prior to age hardening, the sintered body may be bene~icially cold worked to approach the theoretical density and then annealed, preferably for at least about 15 seconds at a temperature of from about 1500F to about 1700F,and rapidly quenched after annealing at a rate, typically at least about 100F per second, sufficient to retain substantial-ly all alpha phase. If desired, the sintered alloy body may be cold worked in stages with intermediate anneal and rapid cooling between said stages. Also, the alloy body may be cold worked after the final anneal/cooling and immediately before age harden-ing in such a manner as to achieve a cross-sectional area reduc-tion of at least about 5 percent, more preferably at least about 15 percent.
The dura-tion of the age hardening spinodal decomposition operation should be carefully selected and controlled. The age hardening process proceeds in sequence through three time periods, ~.~7~3~
-
at least one minute at a temperature of from about 1~00F to about 1900F, more preferably from about 1600F t.o about 1700F. The sintered body is then cooled at a rate, typically at least about 200F per minute until the age hardening temperature range of the alloy has been traversed, such -that age hardening and embrittle-ment are prevented. As used herein, the term "alloy powder"
inc]udes both blended elemental powders and prealloyed powders, as well as mixtures thereof.
Although the sintered body can be subjected directly to age hardening spinodal decomposition, it is preferred to first subject the alloy body to working (with cold working preferred to hot working) and annealing. Thus, prior to age hardening, the sintered body may be bene~icially cold worked to approach the theoretical density and then annealed, preferably for at least about 15 seconds at a temperature of from about 1500F to about 1700F,and rapidly quenched after annealing at a rate, typically at least about 100F per second, sufficient to retain substantial-ly all alpha phase. If desired, the sintered alloy body may be cold worked in stages with intermediate anneal and rapid cooling between said stages. Also, the alloy body may be cold worked after the final anneal/cooling and immediately before age harden-ing in such a manner as to achieve a cross-sectional area reduc-tion of at least about 5 percent, more preferably at least about 15 percent.
The dura-tion of the age hardening spinodal decomposition operation should be carefully selected and controlled. The age hardening process proceeds in sequence through three time periods, ~.~7~3~
-
- 7 - 67839-63D
i.e., the underaged time range, the peak strength aging time range and, finally, the overaged time range. The duration oE these three phases will of course vary as the age hardening tempera-ture is varied, but the same general pattern prevaîls. The strength properties of the age hardenecl spinodally decomposed alloy are highest in the peak strength aging range and lower in the under-aged and overaged ranges, while the ductility of the alloy tends to vary in the opposite manner (i.e. lowest in the peak strength aging range). On the other hand, the electrical conductivity of the alloy tends to continuously increase with the time o-f age hardening. The optimum age hardening time will depend upon the combination of electrical and mechanical properties sought for the alloy being prepared, but will usually be within the pealc strength aging range and often, especially when a high electrical ccnauc-tivity is of particular importance, within the la~ter half of that range.
For purposes of definition, the peak strength aging time for a particular alloy at a particular age hardening temperature is that precise time of age hardening at which the yield stress of the spinodal hardened alloy is at its maximum value. The follow-ing examples are not to be construed as limiting the invention.
Elemental powders were blended in the proportions indicated in Table I for the six examples and then compacted into 3 in. by 0.5 in. by 0.125 in. rectangular bars at about 85 percent of theoretical density. Each bar was sintered in a dissociated ammonia atmosphere for about 60 minutes at 1625F and then about ~1~7V~L
i.e., the underaged time range, the peak strength aging time range and, finally, the overaged time range. The duration oE these three phases will of course vary as the age hardening tempera-ture is varied, but the same general pattern prevaîls. The strength properties of the age hardenecl spinodally decomposed alloy are highest in the peak strength aging range and lower in the under-aged and overaged ranges, while the ductility of the alloy tends to vary in the opposite manner (i.e. lowest in the peak strength aging range). On the other hand, the electrical conductivity of the alloy tends to continuously increase with the time o-f age hardening. The optimum age hardening time will depend upon the combination of electrical and mechanical properties sought for the alloy being prepared, but will usually be within the pealc strength aging range and often, especially when a high electrical ccnauc-tivity is of particular importance, within the la~ter half of that range.
For purposes of definition, the peak strength aging time for a particular alloy at a particular age hardening temperature is that precise time of age hardening at which the yield stress of the spinodal hardened alloy is at its maximum value. The follow-ing examples are not to be construed as limiting the invention.
Elemental powders were blended in the proportions indicated in Table I for the six examples and then compacted into 3 in. by 0.5 in. by 0.125 in. rectangular bars at about 85 percent of theoretical density. Each bar was sintered in a dissociated ammonia atmosphere for about 60 minutes at 1625F and then about ~1~7V~L
- 8 - 67839-63D
30 minutes at 1750F, cooled rapidly while still under the reduc-ing atmosphere to prevent age hardening and embrittlement, cold rolled in at least four steps (with intermittent homogenization or anneal in the reducing atmosphere) to a 0.01 i.nch thickness, solu-tion annealed for 5 minutes at 1650F in the reducing atmosphere and quenched rapidly in oil. Each bar was then age hardened in the ambient atmosphere at the time/tempera-ture conditions set forth in Table I, with the age hardening time in each example corresponding approximately to the peak strength aging time at the indicated age hardening temperature, and ' ' ~
~ '. : : '''"' :
~ 7~3~3~
30 minutes at 1750F, cooled rapidly while still under the reduc-ing atmosphere to prevent age hardening and embrittlement, cold rolled in at least four steps (with intermittent homogenization or anneal in the reducing atmosphere) to a 0.01 i.nch thickness, solu-tion annealed for 5 minutes at 1650F in the reducing atmosphere and quenched rapidly in oil. Each bar was then age hardened in the ambient atmosphere at the time/tempera-ture conditions set forth in Table I, with the age hardening time in each example corresponding approximately to the peak strength aging time at the indicated age hardening temperature, and ' ' ~
~ '. : : '''"' :
~ 7~3~3~
- 9 - 67839-63D
then cooled to ambient temperature. The yield stresS, ultimate tensile ~t~ess~ percent elongation at break~and electrical conductivlty of the re~ulting ~ix spinodally decomposed 3amples were measured and are al~o set forth S in Table I.
The data of Table I clear1y reveal that the replacement of a minor portiQn of nickel in a copper-nick~l-tin age hardened spinodally decomposcd alloy with an egual weight of cobalt provides a means of sub-stantially increasing thc ductility and electricalconductivity of ~he alloy without substantially altering the strength properties of the alloy.
- ~7~
o ~ 3 ~
r ~ r ~ N N t~
. o ~¦ @ ~ ~ ~ N ~
O ~
G~ ~
~ ~ .~ ~ ' ¦ ~ r rl r~ r o 81 ~) ~ ~
~ i~ ~ D
8 ~1 8~
a~ ~ .
~ ,~
then cooled to ambient temperature. The yield stresS, ultimate tensile ~t~ess~ percent elongation at break~and electrical conductivlty of the re~ulting ~ix spinodally decomposed 3amples were measured and are al~o set forth S in Table I.
The data of Table I clear1y reveal that the replacement of a minor portiQn of nickel in a copper-nick~l-tin age hardened spinodally decomposcd alloy with an egual weight of cobalt provides a means of sub-stantially increasing thc ductility and electricalconductivity of ~he alloy without substantially altering the strength properties of the alloy.
- ~7~
o ~ 3 ~
r ~ r ~ N N t~
. o ~¦ @ ~ ~ ~ N ~
O ~
G~ ~
~ ~ .~ ~ ' ¦ ~ r rl r~ r o 81 ~) ~ ~
~ i~ ~ D
8 ~1 8~
a~ ~ .
~ ,~
Claims (25)
PROPERTY OR PRIVILEGE IS CLAIMED ARE DEFINED AS FOLLOWS:
1. A copper base spinodal alloy prepared by powder metal-lurgy consisting essentially of from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 percent by weight cobalt and the balance copper, the said alloy having an unaged microstructure characterized by an equiaxed grain structure of substantially all alpha, face-centered-cubic phase with a substantially uniform dispersed concentration of tin and a substantial absence of tin segregation.
2. An alloy of claim 1 wherein the tin content thereof is at least about 6 percent by weight.
3. An alloy of claim 1 having an unaged microstructure further characterized by a substantial absence of grain boundary precipitation.
4. An alloy of claim 1, 2 or 3, wherein the tin content thereof is from about 6 to about 8.5 percent by weight.
5. A process for preparing a copper base spinodal alloy body which comprises:
(a) providing a copper base alloy powder containing from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 per-cent by weight cobalt, and the balance copper;
(b) compacting the alloy powder to form a green body having structural integrity and sufficient porosity to be penetrated by a reducing atmosphere;
(c) sintering the green body in the reducing atmosphere to form a metallurgical bond; and (d) cooling the sintered body at a rate such that age hardening and embrittlement are prevented.
(a) providing a copper base alloy powder containing from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 per-cent by weight cobalt, and the balance copper;
(b) compacting the alloy powder to form a green body having structural integrity and sufficient porosity to be penetrated by a reducing atmosphere;
(c) sintering the green body in the reducing atmosphere to form a metallurgical bond; and (d) cooling the sintered body at a rate such that age hardening and embrittlement are prevented.
6. A process of claim 5 wherein the alloy powder is compac-ted to at least about twice its original uncompacted density.
7. A process of claim 5 wherein the density of the green body is from about 70 to 95 percent of the theoretical density of said body.
8. A process of claim 5, 6 or 7, wherein the sintering is at a temperature of from about 1400°F to about 1900°F for at least about one minute.
9. A process of claim 5, 6 or 7, wherein the sintering is at a temperature of from about 1600°F to about 1700°F.
10. A process of claim 5, 6 or 7, wherein the sintered body is cooled below the age hardening temperature range of the alloy at a rate of at least about 200°F per minute.
11. A process of claim 5, 6 or 7, wherein the oxygen and carbon contents of the sintered body are each kept to less than about 100 ppm.
12. A process of claim 5, 6 or 7, wherein said green body, said sintered body and said alloy body are each in the form of a strip.
13. A process of claim 5 comprising additionally:
(e) working the sintered body to a substantially fully dense condition; and (f) annealing the worked body and quenching it at a rate sufficient to retain substantially all alpha phase.
(e) working the sintered body to a substantially fully dense condition; and (f) annealing the worked body and quenching it at a rate sufficient to retain substantially all alpha phase.
14. A process of claim 13 wherein the sintered body is cold worked in said step (e).
15. A process of claim 14 wherein said cold working results in a reduction of at least about 30 percent of cross-sectional area.
16. A process of claim 14 wherein the final anneal is at a temperature of from about 1500°F to about 1700°F for at least about 15 seconds, followed by quenching at a rate of at least about 100°F per second to retain substantially all alpha phase.
170 A process of claim 14 wherein the alloy body is age hardened following the final anneal and quench.
18. A process of claim 17 wherein the age hardening is at a temperature of from about 500°F to about 1000°F for at least about 15 seconds.
19. A process of claim 18 wherein the duration of the age hardening treatment is approximately equal to the peak strength aging time of the alloy at the age hardening temperature.
20. A process of claim 17 wherein the alloy body is cold worked to achieve at least about a 5 percent reduction in cross-sectional area after the final anneal and quench but before the age hardening.
21. A process of claim 20 wherein the alloy body is cold worked to achieve at least about a 15 percent reduction in cross-sectional area after the final anneal and quench but before the age hardening.
22. A process of claim 13 wherein said green body, said sintered body, said alloy body and said worked body are each in the form of a strip.
23. A process of claim 17 wherein said green body, said sintered body, said worked body and said alloy body are each in the form of a strip.
24. A process of claim 13 wherein the annealed and quenched body is characterized by an equiaxed grain structure of substan-tially all alpha, face-centered-cubic phase with a substantially uniform dispersed concentration of tin and a substantial absence of tin segregation, and by a substantial absence of grain boundary precipitation.
25. A process for preparing a copper base spinodal alloy body which comprises:
(a) providing a copper base alloy powder containing from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 per-cent by weight cobalt, and the balance copper;
(b) compacting the alloy powder to form a green body having structural integrity and sufficient porosity to be penetrated by a reducing atmosphere;
(c) sintering the green body in the reducing atmosphere to form a metallurgical bond, (d) hot working the sintered body to a substantially fully dense condition; and (e) rapidly cooling the hot worked body at a rate sufficient to retain substantially all alpha phase.
(a) providing a copper base alloy powder containing from about 5 to about 30 percent by weight nickel, from about 4 to about 13 percent by weight tin, from about 0.5 to about 3.5 per-cent by weight cobalt, and the balance copper;
(b) compacting the alloy powder to form a green body having structural integrity and sufficient porosity to be penetrated by a reducing atmosphere;
(c) sintering the green body in the reducing atmosphere to form a metallurgical bond, (d) hot working the sintered body to a substantially fully dense condition; and (e) rapidly cooling the hot worked body at a rate sufficient to retain substantially all alpha phase.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CA000589706A CA1270381A (en) | 1984-07-26 | 1989-01-31 | Copper-nickel-tin-cobalt spinodal alloy |
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US06/634,516 US4525325A (en) | 1984-07-26 | 1984-07-26 | Copper-nickel-tin-cobalt spinodal alloy |
| US634,516 | 1984-07-26 | ||
| CA000487379A CA1257788A (en) | 1984-07-26 | 1985-07-24 | Copper-nickel-tin-cobalt spinodal alloy |
| CA000589706A CA1270381A (en) | 1984-07-26 | 1989-01-31 | Copper-nickel-tin-cobalt spinodal alloy |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000487379A Division CA1257788A (en) | 1984-07-26 | 1985-07-24 | Copper-nickel-tin-cobalt spinodal alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1270381A true CA1270381A (en) | 1990-06-19 |
Family
ID=25670751
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000589706A Expired - Lifetime CA1270381A (en) | 1984-07-26 | 1989-01-31 | Copper-nickel-tin-cobalt spinodal alloy |
Country Status (1)
| Country | Link |
|---|---|
| CA (1) | CA1270381A (en) |
-
1989
- 1989-01-31 CA CA000589706A patent/CA1270381A/en not_active Expired - Lifetime
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US4260432A (en) | Method for producing copper based spinodal alloys | |
| EP0304181B1 (en) | High density tungsten-nickel-iron-cobalt alloys having improved hardness, and method for making them | |
| CA1172473A (en) | Copper alloys with small amounts of manganese and selenium | |
| CA1215865A (en) | Copper base spinodal alloy strip and process for its preparation | |
| CA1205728A (en) | Precipitation hardenable copper alloy and process | |
| US4589938A (en) | Single phase copper-nickel-aluminum-alloys | |
| JPS60215734A (en) | Al-base alloy and production of product therefrom | |
| US4732625A (en) | Copper-nickel-tin-cobalt spinodal alloy | |
| US4525325A (en) | Copper-nickel-tin-cobalt spinodal alloy | |
| CA1038205A (en) | Low expansion iron-nickel based alloys | |
| US4305762A (en) | Copper base alloy and method for obtaining same | |
| CA2215338C (en) | Lean, high conductivity, relaxation-resistant beryllium-nickel-copper alloys | |
| US4406712A (en) | Cu-Ni-Sn Alloy processing | |
| CA1119920A (en) | Copper based spinodal alloys | |
| US5882442A (en) | Iron modified phosphor-bronze | |
| CA2346635A1 (en) | Copper alloy | |
| US3880678A (en) | Processing copper base alloy | |
| EP0132371B1 (en) | Process for making alloys having a coarse elongated grain structure | |
| CA1270381A (en) | Copper-nickel-tin-cobalt spinodal alloy | |
| US3017268A (en) | Copper base alloys | |
| CA1101699A (en) | High-strength, high-expansion manganese alloy | |
| US3852121A (en) | Process for making a novel copper base alloy | |
| US4606889A (en) | Copper-titanium-beryllium alloy | |
| JP2618560B2 (en) | Production method of copper alloy | |
| JPS62267456A (en) | Manufacture of high strength copper alloy for lead frame having high electric conductivity |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MKLA | Lapsed |