CA1247505A - Process for treating copper-nickel alloys for use in brazed assemblies - Google Patents
Process for treating copper-nickel alloys for use in brazed assembliesInfo
- Publication number
- CA1247505A CA1247505A CA000473821A CA473821A CA1247505A CA 1247505 A CA1247505 A CA 1247505A CA 000473821 A CA000473821 A CA 000473821A CA 473821 A CA473821 A CA 473821A CA 1247505 A CA1247505 A CA 1247505A
- Authority
- CA
- Canada
- Prior art keywords
- alloy
- copper
- providing
- nickel
- thickness
- 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
Links
Classifications
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12861—Group VIII or IB metal-base component
- Y10T428/12903—Cu-base component
- Y10T428/1291—Next to Co-, Cu-, or Ni-base component
Abstract
ABSTRACT
The present invention relates to a process for maintaining the fine grain size of and providing excellent bend formability, hot ductility and strength properties to a copper-nickel-manganese alloy to be exposed to elevated temperatures. The process of the present invention includes a final cold working step during which the material to be fabricated into a desired article and/or exposed to the elevated temperatures has its thickness reduced by about 4% to about 30%, preferably from about 5% to about 25%. The alloys described herein have particular utility in brazed articles or assemblies.
The present invention relates to a process for maintaining the fine grain size of and providing excellent bend formability, hot ductility and strength properties to a copper-nickel-manganese alloy to be exposed to elevated temperatures. The process of the present invention includes a final cold working step during which the material to be fabricated into a desired article and/or exposed to the elevated temperatures has its thickness reduced by about 4% to about 30%, preferably from about 5% to about 25%. The alloys described herein have particular utility in brazed articles or assemblies.
Description
~2~'7505 PROCESS FOR TREATING COPPER-NICKEL ALLOYS
FOR USE IN BRAZED ASSEMBLIES
:
The present invention relates to a process for treating copper-nickel alloys to enable them to 5 retain a relatively fine grain structure and exhibit excellent bend formability, ductility and strength properties after exposure to elevated temperatures.
¦ It is well known that copper~nickel alloys are ' particularly well adapted for use in those ¦ 10 en~ironments where resistance to corrosion and mechanical strength are required. Applications for these alloys include tubing for heat exchangers such as radiators and oil coolers, salt water lines such as fire lines and sanitary lines, sheathing for t 15 lifeboats, fuel lines and pressure-containing parts in valves and fittings which are used at elevated : temperatures. Often during fabrication into a final product~ the alloys are subjected to elevated s temperatures such as those associated with bra~ing.
20 One particular family of copper-nickel alloys that have been used in a variety of applications because of their ductility and ability to withstand high temperatures are copper-nickel-manganese alloys.
U.S. Patent Nos. 1,525,047 to Rath, 2,074,604 to Bolton et al., 2,144,279 to Whitman, 2,215,905 to Kihlgren and 4,169,729 to Popplewell et al. illustrate several copper-nickel-manganese alloys and their applications. In addition to being exposed to elevated temperatures, these copper-nickel-manganese alloys often undergo fabrication operations such as stamping and ~4~75~5
FOR USE IN BRAZED ASSEMBLIES
:
The present invention relates to a process for treating copper-nickel alloys to enable them to 5 retain a relatively fine grain structure and exhibit excellent bend formability, ductility and strength properties after exposure to elevated temperatures.
¦ It is well known that copper~nickel alloys are ' particularly well adapted for use in those ¦ 10 en~ironments where resistance to corrosion and mechanical strength are required. Applications for these alloys include tubing for heat exchangers such as radiators and oil coolers, salt water lines such as fire lines and sanitary lines, sheathing for t 15 lifeboats, fuel lines and pressure-containing parts in valves and fittings which are used at elevated : temperatures. Often during fabrication into a final product~ the alloys are subjected to elevated s temperatures such as those associated with bra~ing.
20 One particular family of copper-nickel alloys that have been used in a variety of applications because of their ductility and ability to withstand high temperatures are copper-nickel-manganese alloys.
U.S. Patent Nos. 1,525,047 to Rath, 2,074,604 to Bolton et al., 2,144,279 to Whitman, 2,215,905 to Kihlgren and 4,169,729 to Popplewell et al. illustrate several copper-nickel-manganese alloys and their applications. In addition to being exposed to elevated temperatures, these copper-nickel-manganese alloys often undergo fabrication operations such as stamping and ~4~75~5
-2- 13063-MB
bending. Consequently, it becornes desirable that the alloy being processed exhibit both good formability and du~tillty. When fabr~cated into articles such as tubing, it is also desirable that the alloy exhibit relatively high strength properties.
bending. Consequently, it becornes desirable that the alloy being processed exhibit both good formability and du~tillty. When fabr~cated into articles such as tubing, it is also desirable that the alloy exhibit relatively high strength properties.
3 In order to maintaln the lowest possible cost, 3 cupro-nic~el strip materials are often processed directly to finish gage and annealed. The materials processed in this manner often show extreme grain growth a~ter exposure to elevated temperatures. It ls not unusual for brazed cupro-nickel materials to exhibit grain growth in excess of 2mm. Materials having such a grain size may be undesirably low in strength.
It is an ob~ect of the present invention to provide a copper-nlckel alloy having the ability to maintain a relatively fine grain structure when exposed to elevated temperatures.
It is a further object of the present invention to provide a copper-nickel alloy as above having improved ductility and bend formability.
It is a further ob~ect of the present invention to provide a process for providing such a copper-nickel alloy.
j It is a further object of the present invention to provide a copper-nickel alloy as above which has particular utility in brazed assemblies.
~/ Further objects and advantages of the present , 30 invention will become apparent from a consideration 3` of the following speci~ication.
'~ Alloys in accordance with the present invention consist essentially o~ from about 5% to about 45%
nickel, from about 0.1% to about 1.1% manganese and .
o~
_3_ 13063-MB
the balance essentially copper. The higher nickel contents are generally used where strength is required and/or more aggressive envlronments are encountered in service. Whlle not mandatory, the alloys may-also contain phosphorous in an amount less than about .002%. As used hereln, the percentages for each addition are weight percentages. In a preferred embodiment, the alloys of the present inventlon consist essentially of from about 5% to about 35% nickel, from about 0.6~ to about 1%
manganese and the balance essentially copper.
The alloys may be processed ln any desired manner to a strip material having a desired thickness, a desired temper and a desired grain slze.
Preferably, the strip material posse~ses an average grain size of about 10 ~ to about 100 ~ prior to the treatment of the present invention. In accordance wlth the present invention, the strip material is then sub~ected to a final cold working step which reduces its thickness from about 4% to about 30%. I~ has been discovered that such a final cold working step enables the materlal to substantially maintain a relatively fine grain structure when exposed to elevated temperatures during subsequent processing.
This is surprislng because relatively low reductions normally cause exaggerated grain growth during conventional heat treatments such as annealing. As well as maintaining a relatively fine grain structure, alloys processed in accordance with the present lnvention exhibit excellent bend formability, ductility and strength during and after exposure to elevated temperatures. This combination of propertles and grain structure ls highly desirable in a materlal to be brazed.
s
It is an ob~ect of the present invention to provide a copper-nlckel alloy having the ability to maintain a relatively fine grain structure when exposed to elevated temperatures.
It is a further object of the present invention to provide a copper-nickel alloy as above having improved ductility and bend formability.
It is a further ob~ect of the present invention to provide a process for providing such a copper-nickel alloy.
j It is a further object of the present invention to provide a copper-nickel alloy as above which has particular utility in brazed assemblies.
~/ Further objects and advantages of the present , 30 invention will become apparent from a consideration 3` of the following speci~ication.
'~ Alloys in accordance with the present invention consist essentially o~ from about 5% to about 45%
nickel, from about 0.1% to about 1.1% manganese and .
o~
_3_ 13063-MB
the balance essentially copper. The higher nickel contents are generally used where strength is required and/or more aggressive envlronments are encountered in service. Whlle not mandatory, the alloys may-also contain phosphorous in an amount less than about .002%. As used hereln, the percentages for each addition are weight percentages. In a preferred embodiment, the alloys of the present inventlon consist essentially of from about 5% to about 35% nickel, from about 0.6~ to about 1%
manganese and the balance essentially copper.
The alloys may be processed ln any desired manner to a strip material having a desired thickness, a desired temper and a desired grain slze.
Preferably, the strip material posse~ses an average grain size of about 10 ~ to about 100 ~ prior to the treatment of the present invention. In accordance wlth the present invention, the strip material is then sub~ected to a final cold working step which reduces its thickness from about 4% to about 30%. I~ has been discovered that such a final cold working step enables the materlal to substantially maintain a relatively fine grain structure when exposed to elevated temperatures during subsequent processing.
This is surprislng because relatively low reductions normally cause exaggerated grain growth during conventional heat treatments such as annealing. As well as maintaining a relatively fine grain structure, alloys processed in accordance with the present lnvention exhibit excellent bend formability, ductility and strength during and after exposure to elevated temperatures. This combination of propertles and grain structure ls highly desirable in a materlal to be brazed.
s
-4- 13063-MB
In a preferred manner of performing the present invention, the final cold worklng step ls per~ormed by cold rolling the strip material in a single pass through a rolling mill to obtain the strip material thlckness reduction. In a most preferred embodiment, the final cold working step comprises reduclng the strip ma~erial thickness by about 5% to about 25%.
A11QYS processed in accordance with the present invention have utllity in assemblies sub~ected to high temperature processes and techniques, part~cularly brazed assemblies. Good brazing materials need to exhlbit good bend formability, hot ductility and strength properties. Alloys processed in accordance with the present invention exhibit such properties. In addition, alloys processed in accordance with the present invention are abie to substantially maintain relatively fine grain structures after exposure to elevated temperatures.
This is directly attributable to the final cold working step which acts as a grain refinement treatment.
As previously discussed, alloys in accordance with the present invention consist essentially of from about 5% to about 45% nickel, from about 0.1% to about 1.1% manganese and the balance essentially copper. In a preferred embodiment, the copper-base alloys consist essentially of from about 5% to about 35% nickel~ from about o.6~ to about 1% manganese and the balance essentially copper. I~ desired, the alloys may contain phosphorous in an amount less than about .002%; however, this is not required.
Conventional brass ~ill impurities may be tolerated .
~ 75(~S
In a preferred manner of performing the present invention, the final cold worklng step ls per~ormed by cold rolling the strip material in a single pass through a rolling mill to obtain the strip material thlckness reduction. In a most preferred embodiment, the final cold working step comprises reduclng the strip ma~erial thickness by about 5% to about 25%.
A11QYS processed in accordance with the present invention have utllity in assemblies sub~ected to high temperature processes and techniques, part~cularly brazed assemblies. Good brazing materials need to exhlbit good bend formability, hot ductility and strength properties. Alloys processed in accordance with the present invention exhibit such properties. In addition, alloys processed in accordance with the present invention are abie to substantially maintain relatively fine grain structures after exposure to elevated temperatures.
This is directly attributable to the final cold working step which acts as a grain refinement treatment.
As previously discussed, alloys in accordance with the present invention consist essentially of from about 5% to about 45% nickel, from about 0.1% to about 1.1% manganese and the balance essentially copper. In a preferred embodiment, the copper-base alloys consist essentially of from about 5% to about 35% nickel~ from about o.6~ to about 1% manganese and the balance essentially copper. I~ desired, the alloys may contain phosphorous in an amount less than about .002%; however, this is not required.
Conventional brass ~ill impurities may be tolerated .
~ 75(~S
-5- 13063-MB
ln the alloys of the present lnvention but should preferably be kept at a minimum.
Ordinarily, copper nickel alloys that are exposed to high temperatures such as those associated with brazing experience grain coarsenlng. This graln coarsening adversely impacts the material and reduces the overall strength of the material. It has been ~ound that alloys processed in accordance with the process of the present invention are able to maintain relatively fine grain structures after exposure to elevated temperatures. As a result, the alloys exhibit improved strength and improved ductility at elevated temperatures. The improved ductility ls partlcularly desirable because greater elongation percentages may be obtained at the elevated temperatures. As a result, cracking in assemblies sub~ected to relatively high temperature heat treatments such as brazing is significantly reduced.
As well as exhibiting improved strength and ductillty, alloys processed in accordance with the present invention exhibit excellent bend formability.
This is particularly desirable where the material is to be subje~ted during fabrication to formlng operations such as stamping and bending. For good bend formability, a minimum bend radius of lt is desirable where t is the thickness of the material being bent.
The alloys of the present invention may be cast 30 in any desired manner. For example, they mav be cast using continuous casting3 direct chill casting or Durville casting. Any suitable pouring temperature ~2~5~)5
ln the alloys of the present lnvention but should preferably be kept at a minimum.
Ordinarily, copper nickel alloys that are exposed to high temperatures such as those associated with brazing experience grain coarsenlng. This graln coarsening adversely impacts the material and reduces the overall strength of the material. It has been ~ound that alloys processed in accordance with the process of the present invention are able to maintain relatively fine grain structures after exposure to elevated temperatures. As a result, the alloys exhibit improved strength and improved ductility at elevated temperatures. The improved ductility ls partlcularly desirable because greater elongation percentages may be obtained at the elevated temperatures. As a result, cracking in assemblies sub~ected to relatively high temperature heat treatments such as brazing is significantly reduced.
As well as exhibiting improved strength and ductillty, alloys processed in accordance with the present invention exhibit excellent bend formability.
This is particularly desirable where the material is to be subje~ted during fabrication to formlng operations such as stamping and bending. For good bend formability, a minimum bend radius of lt is desirable where t is the thickness of the material being bent.
The alloys of the present invention may be cast 30 in any desired manner. For example, they mav be cast using continuous casting3 direct chill casting or Durville casting. Any suitable pouring temperature ~2~5~)5
-6- 13063-MB
may be used during casting. Generally, the pouring temperature will preferably be in the range of about 1000C to about 1300C. Most preferably, the pouring temperature is in the range of about 1050C
to about 1150C.
After castlng, the alloys may be processed in any de3ired manner into a strip material having a desired thicknes~, a desired temper and a desired graln structure. In a preferred embodiment, the strip material has an average grain size in the range of about 10 ~ ~o about 100 ~. Preferably, the alloys will be processed by breaking down the cast lngot into a strip material such as a sheet or plate using a hot working operation such as hot rolling followed by a cold working operation such as cold rolling. During cold rolling, the alloy may be sub~ected to one or more passes through a rolling mill until it reaches the deslred thickness or gage. If necessary, one or more interanneals may be performed during the cold rolling operation. To provide the desired temper, the strip material may be annealed after cold working to the desired thickness. The various hot rolling, cold rolling and/or annealing steps may be performed using any conventional technique and apparatus known in the art.
The hot rolling step may be performed with any suitable initial temperature. Preferably, the initlal hot rolling temperature is in the range of about 700C to about 1050C. Most preferably, the inltial hot rolling temperature is in the range of about 780~C to about 1000C. Any suitable cooling rate may be used to cool the strip material from hot rolling.
~L2~5~
may be used during casting. Generally, the pouring temperature will preferably be in the range of about 1000C to about 1300C. Most preferably, the pouring temperature is in the range of about 1050C
to about 1150C.
After castlng, the alloys may be processed in any de3ired manner into a strip material having a desired thicknes~, a desired temper and a desired graln structure. In a preferred embodiment, the strip material has an average grain size in the range of about 10 ~ ~o about 100 ~. Preferably, the alloys will be processed by breaking down the cast lngot into a strip material such as a sheet or plate using a hot working operation such as hot rolling followed by a cold working operation such as cold rolling. During cold rolling, the alloy may be sub~ected to one or more passes through a rolling mill until it reaches the deslred thickness or gage. If necessary, one or more interanneals may be performed during the cold rolling operation. To provide the desired temper, the strip material may be annealed after cold working to the desired thickness. The various hot rolling, cold rolling and/or annealing steps may be performed using any conventional technique and apparatus known in the art.
The hot rolling step may be performed with any suitable initial temperature. Preferably, the initlal hot rolling temperature is in the range of about 700C to about 1050C. Most preferably, the inltial hot rolling temperature is in the range of about 780~C to about 1000C. Any suitable cooling rate may be used to cool the strip material from hot rolling.
~L2~5~
-7- 13063-MB
The alloys of the present invention are believed to be capable of cold rolling reductions ln excess of 90%; however, the cold rolllng reduction preferably is between 10% and 80%o The cold rolling operation may 5 be performed in one or more rolling passes.
Annealing temperatures in the range of about 550C to about 900C for at least one minute to about 24 hours may be used for the lnteranneals and/or the final anneal to a desirecl temper. Preferably, the final anneal and/or the interanneals are performed at an annealing temperature in the range of about 700C
to about 850C for at least about one hour to about 12 hours.
After the strip material has been processed to have a desired thickness~ a desired temper and a desired grain structure, it is sub~ected to a final cold working step. The final cold wo~king step preferably reduces the strip material thickness from about 4% to about 30%. In a most preferred embodiment~ the strip material thickness is reduced from about 5% to about 25%. The final cold worklng step may be performed in any desired manner using any conventional technique and apparatus known in the art. Preferably, the cold working step comprises cold rolling the strip material to obtain the reduction in thickness. The cold rolling step may be performed by one or more passes of the strip material through a conventional rolling mill~
It has been discovered that performing this ~inal cold working step as the last processing step be~ore fabrication into a desired article and/or exposure to elevated temperatures enables the copper alloys of the present invention to maintain a relatively fine grain structure. It is believed that grain structures having an average grain size in the ~L2~750S
The alloys of the present invention are believed to be capable of cold rolling reductions ln excess of 90%; however, the cold rolllng reduction preferably is between 10% and 80%o The cold rolling operation may 5 be performed in one or more rolling passes.
Annealing temperatures in the range of about 550C to about 900C for at least one minute to about 24 hours may be used for the lnteranneals and/or the final anneal to a desirecl temper. Preferably, the final anneal and/or the interanneals are performed at an annealing temperature in the range of about 700C
to about 850C for at least about one hour to about 12 hours.
After the strip material has been processed to have a desired thickness~ a desired temper and a desired grain structure, it is sub~ected to a final cold working step. The final cold wo~king step preferably reduces the strip material thickness from about 4% to about 30%. In a most preferred embodiment~ the strip material thickness is reduced from about 5% to about 25%. The final cold worklng step may be performed in any desired manner using any conventional technique and apparatus known in the art. Preferably, the cold working step comprises cold rolling the strip material to obtain the reduction in thickness. The cold rolling step may be performed by one or more passes of the strip material through a conventional rolling mill~
It has been discovered that performing this ~inal cold working step as the last processing step be~ore fabrication into a desired article and/or exposure to elevated temperatures enables the copper alloys of the present invention to maintain a relatively fine grain structure. It is believed that grain structures having an average grain size in the ~L2~750S
-8- 13063-MB
range of about 100 ~ to about 200 ~ are achievable using the final cold working step of the present invention. Further, alloys processed ln accordance with the present invention exhiblt excellent bend formabillty, hot ductility and strength berore, during and after exposure to elevated temperatures. Ihis renders the alloys particularly suitable for use in brazed ass mblies such as tubing for radiat~rs or heat exchangers.
After the processing has been completed~ the strip material may be fabricated into any desired art~cle. As previously stated, alloys processed in accordance with the present invention readlly lend themselves for use in brazed assemblies such as tubing. When used in such assemblie~, the alloys of the present invention demonstrate excellent brazing characteristics and may be used with any suitable filler material. For example, they may be used with filler materials such as copper alloys CllO00 and C12200. Of course, the temperatures used ln brazing depend upon the filler material being used. For copper alloys such as C11000 and C12200, the brazing temperature is typically in the range of about 1065C
to about 1120C, generally about 1090C. At these temperatures, alloys processed in accordance with the present invention are able to maintain relatively fine grain structures as well as excellent ductility, formabillty and strength properties. It should be noted that the ductility at elevated temperatures property, or hot ductility, exhibited by the present alloys facilitate fabrication oper~tions in general.
The present lnvention and improvements resulting therefrom wlll be more readily apparent from a consideration-of the following illustrative examples.
~2~
_9- 13063-MB
EXAMPLE I
Two alloys were prepared having the nominal compositions set forth in Table I below.
TABLE I
5 Allo~ Ni(g) Mn (%) Cu(%) A 21 o.6 bal.
B 21 1.0 bal.
.. ........ .
The alloys were Durville cast and processed in the following manner. ~le alloys were soaked at 980C for 40 mlnutes and then hot rolled to 0.3".
The plates were then coil milled and cold rolled down to 0.050" gage. Samples of each alloy were then given one of the following three treatments.
The first treatment comprised further cold rolling the samples down to 0.020" gage and then annealing each sample at 700C for 1 hour to a soft temper. The second treatment comprised cold rolling the samples down to 0.020" gage, annealing each sample at 700C for 1 hour to a soft temper and per~orming a final 10% cold reduction. The third treatment comprised first annealing each sample at 700C for 1 hour and then performing the second treatment. All of the treated samples were then braze heat treated at 1090C for 30 minutes and the grain si2e was recorded. The brazing heat treatment consisted of placing the test samples in a chamber and heating them to the desired temperature.
The results of the grain size measurements are recorded in Table II.
os TABLE II
-Graln Size After Brazing Heat Treatment Alloy Treatment ~mm) 1 h > 1 l B > 1 2 A ~ 0.2 2 ~ ~ 0.2 3 A ~ 0.2 3 B ~ 0.2 _ ~ rom thi~s data, it can be seen that treatment 1 resulted in excessive undesirable grain growth whereas the alloys processed by treatments 2 and 3 exhibted a fine grain structure. The data also shows that the grain refinement effect after brazing using the final cold working step of the present invention may be obtained irrespective of the number of previous anneals employed.
EX~MPLE II
To demonstrate the bend formability properties of materials treated in accordance with the present invention3 bend formability tests were carried out on a manganese modified copper-nickel alloy. The alloy had the same nominal composition as alloy B
in Example I.
Samples of the alloy were given different final cold reductions ranging from 5% to 37%. m ereafter, standard 90 bend tests were carried out in good and bad way dlrections. The results are given in Table III.
1L~ 9Lr7S05i ~ 13063-MB
TABLE III
Cold Rolling (%) 5 10 20 25 37 Minlmum Bend sharp sharp 0.550.6 0.7 Radius~Thlckness (L)*
Minimum Bend sharp 0.24 0.550.6 1.4 Radius/Thickness ~T)*~
.. .. _ ... . . .
*(L) = good way **~T) = bad way For good bend formability, a minimum bend radius of lt is the maximum limit where t is the thlckness of the material being tested. The results at the 5%, 10%, 20% and 25% cold reductions were acceptable while the results at the 37% cold reduction were unacceptable.
It is believed that these examples demonstrate the benefits, e.g. improved ductility, bend formability and strength, the ability to maintain a fine grain structure when exposed to elevated temperatures and improved brazing ability which can be obtained by processing copper-nickel-manganese alloys in accordance with the present invention.
A~oys processed in accordance with the present invention readily lend themselves to applications~
such as tubing for heat exchangers, radiators, and transmission oil coolersg where such properties are required.
While the nickel content of the alloys of the present invention has been described as being from about 5% to about 45%, the nickei content ~ay be as great as about 65% without adversely affecting the desirable properties of the alloys.
75()$
It is apparent that there has been provided in accordance with this invention a process for treating copper-nickel alloys for use in brazed assemblies which fully satisfy the ob~ects, means and advantages set forth hereinbefore. While the inventlon has been described in combination wlth specific embodiments thereof, it is evident that many alternatives, modifications and varlations will be apparent to those skilled in the art in light of the foregolng description. Accordingly, it is intended to embrace all such alternatives, modificatlons and variations as fall within the spirit and broad scope of the appended claims.
range of about 100 ~ to about 200 ~ are achievable using the final cold working step of the present invention. Further, alloys processed ln accordance with the present invention exhiblt excellent bend formabillty, hot ductility and strength berore, during and after exposure to elevated temperatures. Ihis renders the alloys particularly suitable for use in brazed ass mblies such as tubing for radiat~rs or heat exchangers.
After the processing has been completed~ the strip material may be fabricated into any desired art~cle. As previously stated, alloys processed in accordance with the present invention readlly lend themselves for use in brazed assemblies such as tubing. When used in such assemblie~, the alloys of the present invention demonstrate excellent brazing characteristics and may be used with any suitable filler material. For example, they may be used with filler materials such as copper alloys CllO00 and C12200. Of course, the temperatures used ln brazing depend upon the filler material being used. For copper alloys such as C11000 and C12200, the brazing temperature is typically in the range of about 1065C
to about 1120C, generally about 1090C. At these temperatures, alloys processed in accordance with the present invention are able to maintain relatively fine grain structures as well as excellent ductility, formabillty and strength properties. It should be noted that the ductility at elevated temperatures property, or hot ductility, exhibited by the present alloys facilitate fabrication oper~tions in general.
The present lnvention and improvements resulting therefrom wlll be more readily apparent from a consideration-of the following illustrative examples.
~2~
_9- 13063-MB
EXAMPLE I
Two alloys were prepared having the nominal compositions set forth in Table I below.
TABLE I
5 Allo~ Ni(g) Mn (%) Cu(%) A 21 o.6 bal.
B 21 1.0 bal.
.. ........ .
The alloys were Durville cast and processed in the following manner. ~le alloys were soaked at 980C for 40 mlnutes and then hot rolled to 0.3".
The plates were then coil milled and cold rolled down to 0.050" gage. Samples of each alloy were then given one of the following three treatments.
The first treatment comprised further cold rolling the samples down to 0.020" gage and then annealing each sample at 700C for 1 hour to a soft temper. The second treatment comprised cold rolling the samples down to 0.020" gage, annealing each sample at 700C for 1 hour to a soft temper and per~orming a final 10% cold reduction. The third treatment comprised first annealing each sample at 700C for 1 hour and then performing the second treatment. All of the treated samples were then braze heat treated at 1090C for 30 minutes and the grain si2e was recorded. The brazing heat treatment consisted of placing the test samples in a chamber and heating them to the desired temperature.
The results of the grain size measurements are recorded in Table II.
os TABLE II
-Graln Size After Brazing Heat Treatment Alloy Treatment ~mm) 1 h > 1 l B > 1 2 A ~ 0.2 2 ~ ~ 0.2 3 A ~ 0.2 3 B ~ 0.2 _ ~ rom thi~s data, it can be seen that treatment 1 resulted in excessive undesirable grain growth whereas the alloys processed by treatments 2 and 3 exhibted a fine grain structure. The data also shows that the grain refinement effect after brazing using the final cold working step of the present invention may be obtained irrespective of the number of previous anneals employed.
EX~MPLE II
To demonstrate the bend formability properties of materials treated in accordance with the present invention3 bend formability tests were carried out on a manganese modified copper-nickel alloy. The alloy had the same nominal composition as alloy B
in Example I.
Samples of the alloy were given different final cold reductions ranging from 5% to 37%. m ereafter, standard 90 bend tests were carried out in good and bad way dlrections. The results are given in Table III.
1L~ 9Lr7S05i ~ 13063-MB
TABLE III
Cold Rolling (%) 5 10 20 25 37 Minlmum Bend sharp sharp 0.550.6 0.7 Radius~Thlckness (L)*
Minimum Bend sharp 0.24 0.550.6 1.4 Radius/Thickness ~T)*~
.. .. _ ... . . .
*(L) = good way **~T) = bad way For good bend formability, a minimum bend radius of lt is the maximum limit where t is the thlckness of the material being tested. The results at the 5%, 10%, 20% and 25% cold reductions were acceptable while the results at the 37% cold reduction were unacceptable.
It is believed that these examples demonstrate the benefits, e.g. improved ductility, bend formability and strength, the ability to maintain a fine grain structure when exposed to elevated temperatures and improved brazing ability which can be obtained by processing copper-nickel-manganese alloys in accordance with the present invention.
A~oys processed in accordance with the present invention readily lend themselves to applications~
such as tubing for heat exchangers, radiators, and transmission oil coolersg where such properties are required.
While the nickel content of the alloys of the present invention has been described as being from about 5% to about 45%, the nickei content ~ay be as great as about 65% without adversely affecting the desirable properties of the alloys.
75()$
It is apparent that there has been provided in accordance with this invention a process for treating copper-nickel alloys for use in brazed assemblies which fully satisfy the ob~ects, means and advantages set forth hereinbefore. While the inventlon has been described in combination wlth specific embodiments thereof, it is evident that many alternatives, modifications and varlations will be apparent to those skilled in the art in light of the foregolng description. Accordingly, it is intended to embrace all such alternatives, modificatlons and variations as fall within the spirit and broad scope of the appended claims.
Claims (13)
PROPERTY OR PRIVILEGE IS CLAIMED ARE DEFINED AS FOLLOWS:
1. A process for providing a copper-nickel alloy capable of maintaining its bend formability properties and a relatively fine grain structure when exposed to elevated tenperatures, said process comprising:
providing a copper-nickel alloy having a first thickness, a desired temper and a desired grain size, said alloy containing from about 5% to about 45%
nickel; and subjecting said alloy to a final working step prior to said exposure to elevated temperatures, said working step comprising reducing said thickness from about 4% to about 30%.
providing a copper-nickel alloy having a first thickness, a desired temper and a desired grain size, said alloy containing from about 5% to about 45%
nickel; and subjecting said alloy to a final working step prior to said exposure to elevated temperatures, said working step comprising reducing said thickness from about 4% to about 30%.
2 The process of claim 1 wherein said working step comprises:
cold rolling said alloy to said reduced thickness.
cold rolling said alloy to said reduced thickness.
3. The process of claim 1 wherein said working step comprises:
reducing said thickness from about 5% to about 25%.
reducing said thickness from about 5% to about 25%.
4. The process of claim 1 wherein said alloy providing step comprises:
providing an alloy consisting essentially of about 5% to about 45% nickel, about 0.1% to about 1.1% manganese and the balance essentially copper.
providing an alloy consisting essentially of about 5% to about 45% nickel, about 0.1% to about 1.1% manganese and the balance essentially copper.
5. The process of claim 1 wherein said alloy providing step comprises:
providing an alloy consisting essentially of about 5% to about 35% nickel, about 0.6% to about 1.0% manganese and the balance essentially copper.
providing an alloy consisting essentially of about 5% to about 35% nickel, about 0.6% to about 1.0% manganese and the balance essentially copper.
6. The process of claim 1 wherein said alloy providing step comprises:
casting said copper alloy into an ingot;
hot working said ingot;
cold working said alloy into a strip material having said first thickness; and subjecting said alloy to at least one heat treatment.
casting said copper alloy into an ingot;
hot working said ingot;
cold working said alloy into a strip material having said first thickness; and subjecting said alloy to at least one heat treatment.
7. The process of claim 1 wherein said alloy providing step comprises:
providing an alloy having a grain size in the range of about 10 µ to about 100 µ.
providing an alloy having a grain size in the range of about 10 µ to about 100 µ.
8. A copper alloy produced by the process of claim 1.
9. A brazing process comprising:
providing an article formed from a copper base alloy consisting essentially of about 5% to about 45% nickel 3 about 0.1% to about 1.1% manganese and the balance essentially copper;
applying a filler material to said article, and heating said article and said filler material to a temperature sufficient to melt said filler material;
wherein the improvement comprises:
said article providing step including processing said alloy into a material having a desired thickness, a desired temper and a relatively fine grain structure; and subjecting said material to a final cold working step comprising reducing said material thickness from about 4% to about 30% to enable said alloy forming said material to substantially maintain said grain structure during said heating step.
providing an article formed from a copper base alloy consisting essentially of about 5% to about 45% nickel 3 about 0.1% to about 1.1% manganese and the balance essentially copper;
applying a filler material to said article, and heating said article and said filler material to a temperature sufficient to melt said filler material;
wherein the improvement comprises:
said article providing step including processing said alloy into a material having a desired thickness, a desired temper and a relatively fine grain structure; and subjecting said material to a final cold working step comprising reducing said material thickness from about 4% to about 30% to enable said alloy forming said material to substantially maintain said grain structure during said heating step.
10. The process of claim 9 wherein said final cold working step comprises reducing said thickness from about 5% to about 25%.
11. The process of claim 9 wherein:
said alloy consists essentially of about 5%
to about 35% nickel, about 0.6% to about 1%
manganese and the balance essentially copper; and said alloy processing step including providing said material with an average grain size in the range of about 10 µ to about 100 µ.
said alloy consists essentially of about 5%
to about 35% nickel, about 0.6% to about 1%
manganese and the balance essentially copper; and said alloy processing step including providing said material with an average grain size in the range of about 10 µ to about 100 µ.
12. The process of claim 9 wherein:
said filler material comprises a copper containing material; and said heating step comprises heating said article and said filler material to a temperature in the range of about 1065°C to about 1125°C.
said filler material comprises a copper containing material; and said heating step comprises heating said article and said filler material to a temperature in the range of about 1065°C to about 1125°C.
13. A brazed assembly, said assembly being formed by the process of claim 9.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US06/596,182 US4799973A (en) | 1984-04-02 | 1984-04-02 | Process for treating copper-nickel alloys for use in brazed assemblies and product |
| US596,182 | 1984-04-02 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1247505A true CA1247505A (en) | 1988-12-28 |
Family
ID=24386285
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA000473821A Expired CA1247505A (en) | 1984-04-02 | 1985-02-07 | Process for treating copper-nickel alloys for use in brazed assemblies |
Country Status (2)
| Country | Link |
|---|---|
| US (1) | US4799973A (en) |
| CA (1) | CA1247505A (en) |
Families Citing this family (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2644714A1 (en) * | 1989-03-22 | 1990-09-28 | Commissariat Energie Atomique | PROCESS FOR OBTAINING COPPER LARGE SIZE PARTS AND VERY FINE STRUCTURE FROM A CONTINUOUSLY CONTINUOUS LOPIN |
| US5213638A (en) * | 1990-07-27 | 1993-05-25 | Olin Corporation | Surface modified copper alloys |
| US5209787A (en) * | 1990-07-27 | 1993-05-11 | Olin Corporation | Surface modification of copper alloys |
| US5096508A (en) * | 1990-07-27 | 1992-03-17 | Olin Corporation | Surface modified copper alloys |
| US5320689A (en) * | 1990-07-27 | 1994-06-14 | Olin Corporation | Surface modified copper alloys |
| WO2000052516A2 (en) * | 1999-03-01 | 2000-09-08 | Boston Innovative Optics, Inc. | System and method for increasing the depth of focus of the human eye |
| US7628810B2 (en) * | 2003-05-28 | 2009-12-08 | Acufocus, Inc. | Mask configured to maintain nutrient transport without producing visible diffraction patterns |
| US20050046794A1 (en) * | 2003-06-17 | 2005-03-03 | Silvestrini Thomas A. | Method and apparatus for aligning a mask with the visual axis of an eye |
| EP1734884B1 (en) * | 2004-03-16 | 2021-06-16 | Guidance Endodontics, LLC | Endodontic files |
| US20060124283A1 (en) * | 2004-12-14 | 2006-06-15 | Hind Abi-Akar | Fluid-handling apparatus with corrosion-erosion coating and method of making same |
| US7976577B2 (en) * | 2005-04-14 | 2011-07-12 | Acufocus, Inc. | Corneal optic formed of degradation resistant polymer |
| CA2770735C (en) * | 2009-08-13 | 2017-07-18 | Acufocus, Inc. | Masked intraocular implants and lenses |
| USD656526S1 (en) | 2009-11-10 | 2012-03-27 | Acufocus, Inc. | Ocular mask |
| EP2322890A1 (en) * | 2009-11-16 | 2011-05-18 | Thermex Ltd. | A marine heat exchanger |
| CA2857306C (en) | 2011-12-02 | 2017-07-25 | Acufocus, Inc. | Ocular mask having selective spectral transmission |
| US9204962B2 (en) | 2013-03-13 | 2015-12-08 | Acufocus, Inc. | In situ adjustable optical mask |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US1525047A (en) * | 1923-04-12 | 1925-02-03 | Non Corrosive Metal Co | Alloy and method for producing same |
| US2052139A (en) * | 1931-09-21 | 1936-08-25 | American Brass Co | Fabricated structure and method of making the same |
| US2058887A (en) * | 1931-10-21 | 1936-10-27 | American Brass Co | Fabricated structure and method of making |
| US2074604A (en) * | 1934-12-28 | 1937-03-23 | Lunkenheimer Co | Alloy |
| US2144279A (en) * | 1937-12-07 | 1939-01-17 | Henry L Whitman | Alloy |
| US2215905A (en) * | 1939-03-29 | 1940-09-24 | Int Nickel Co | Pressure casting |
| US3053511A (en) * | 1957-11-15 | 1962-09-11 | Gen Motors Corp | Clad alloy metal for corrosion resistance and heat exchanger made therefrom |
| 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 |
| US4169729A (en) * | 1978-02-21 | 1979-10-02 | Olin Corporation | Corrosion resistant copper base alloys for heat exchanger tube |
| JPS56116846A (en) * | 1980-02-18 | 1981-09-12 | Furukawa Kinzoku Kogyo Kk | Copper alloy for fin of automobile radiator |
| JPS6045698B2 (en) * | 1982-01-20 | 1985-10-11 | 日本鉱業株式会社 | Lead material for semiconductor equipment |
-
1984
- 1984-04-02 US US06/596,182 patent/US4799973A/en not_active Expired - Fee Related
-
1985
- 1985-02-07 CA CA000473821A patent/CA1247505A/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| US4799973A (en) | 1989-01-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CA1247505A (en) | Process for treating copper-nickel alloys for use in brazed assemblies | |
| JPH0841612A (en) | Copper alloy and its preparation | |
| EP2562280A1 (en) | Copper alloy | |
| WO2010064547A1 (en) | Cu-ni-si-co based copper ally for electronic materials and manufacturing method therefor | |
| JPH08325681A (en) | Production of copper-based alloy having improved combinationof ultimate tensile strength, electrical conductivity and stress relaxation resistance | |
| JPH0625388B2 (en) | High strength, high conductivity copper base alloy | |
| CN1327016C (en) | Copper base alloy with improved punchin and impacting performance and its preparing method | |
| CN110157945B (en) | Softening-resistant copper alloy and preparation method and application thereof | |
| EP0189637B1 (en) | Copper alloy and production of the same | |
| JP3797882B2 (en) | Copper alloy sheet with excellent bending workability | |
| WO2005083137A1 (en) | Copper alloy | |
| JP3896422B2 (en) | Copper alloy for backing plate and manufacturing method thereof | |
| JP3334157B2 (en) | Copper alloy strip with less wear on stamping mold | |
| JP2000328157A (en) | Copper alloy sheet excellent in bending workability | |
| JPH09125175A (en) | Copper alloy | |
| JPS6231059B2 (en) | ||
| EP0299605B1 (en) | Iron-copper-chromium alloy for high-strength lead frame or pin grid array and process for preparation thereof | |
| JPS61272339A (en) | Lead material for electronic parts excelled in repeated bendability and its production | |
| JPH10130754A (en) | Heat resistant copper base alloy | |
| JP3980808B2 (en) | High-strength copper alloy excellent in bending workability and heat resistance and method for producing the same | |
| US4715910A (en) | Low cost connector alloy | |
| JP3835004B2 (en) | Copper alloy processing method | |
| JP3274175B2 (en) | Copper base alloy for heat exchanger and method for producing the same | |
| JP3274177B2 (en) | Copper base alloy for heat exchanger and method for producing the same | |
| JP3274178B2 (en) | Copper base alloy for heat exchanger and method for producing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MKEX | Expiry |