Modified brass alloys with improved stress relaxation resistance

Abstract

An alloy system which exhibits improved resistance to stress relaxation at elevated temperatures utilizes additions of tin or silicon, or mixtures of each of these elements, along with magnesium or magnesium plus aluminum to a copper-zinc base to attain the stress relaxation performance. The composition and processing of this alloy system maintains at least 90% by weight alpha-phase within the alloy.

Description

BACKGROUND OF THE INVENTION

Material used for spring connection devices must exhibit the ability to maintain adequate contact pressure for the design life of any part formed from the material. This ability to maintain adequate contact pressure is the ability to resist stress relaxation over a period of time, especially at temperatures elevated above normal room temperture. The current trend in connector design has been to place greater emphasis upon the maintenance of high contact pressure on connector parts at mildly elevated tempertures to reduce problems which might develop as the service temperature of the parts increases. Alloy 260 is currently widely used for electrical connectors but tends to exhibit a rather poor stress relaxation resistance at tempertures of 75.degree. C. or higher. Accordingly, it is important that this widely used alloy be modified in such a manner so as to improve its elevated temperature stress relaxation performance.

It is important to any modifications of Alloy 260 that high conductivity alloy be maintained along with improved stress relaxation performance. Furthermore, bend formability should be maintained while any cost increase in the alloy should be held down as low as possible to keep such an alloy competitive in the market. Other performance characteristics such as stress corrosion, solderability, sofening resistance and others should not be significantly degraded below those properties shown by Commercial Alloy 260. It is desirable in the present invention that the performance of such an alloy exhibit approximately a 10-30% increase over projected stress remaining after 100,000 hours at 75.degree. C. or higher relative to Alloy 260. It is also desirable in the present invention that such an alloy maintain approximately a 20% IACS conductivity.

One alloy system which has been developed in the prior art is an improved beta-brass alloy as shown in U.S. Pat. No. 4,055,445 to Horace Pops. This particular patent teaches a brass alloy which exhibits a shape memory effect and which may contain from 25 to 40% by weight zinc along with 0.25 to 3.0% by weight silicon. It should be noted that the only useful alloy system within this broad range is shown by the cross hatched area in FIG. 3 of said patent, wherein the alloy should have a minimum amount of 25% by weight beta-phase up to 75%. Apparently, not only the particular alloy system itself but its specific processing is important in preparing the improved alloy of this particular patent. It is quite important to this patent that an annealing be performed so as to provide the above-mentioned minimum amount of beta-phase material within the alloy system.

It is a principal object of the present invention to provide an alloy system which exhibits improved stress relaxation resistance, particularly at the elevated temperatures, when compared to Commercial Alloy 260.

It is a further object of the present invention to provide an alloy system as aforesaid which exhibits improved stress relaxation resistance and maintains approximate conductivity values found in Alloy 260.

It is an additional object of the present invention to provide an alloy system as aforesaid which is essentially an all alpha-phase alloy with up to 10% beta-phase within the alloy.

It is an additional object of the present invention to provide an alloy system as aforesaid which provides the noted benefits without appreciably increasing the cost of such an alloy.

Further objects and advantages will become apparent from a consideration of the following specification.

SUMMARY OF THE INVENTION

The alloy system of the present invention utilizes unique additions of silicon or tin or any combinations thereof to an alpha-brass containing 8 to 32.8% by weight zinc and magnesium or magnesium plus aluminum to provide improvements in the stress relaxation behavior of such an alloy particularly at large degrees of cold reduction. The alloy system of the present invention meets these objectives without appreciably detrimentally affecting the electrical conductivity of the base copper-zinc alloy system. The elemental additions made to the base alloy also provide these increases in performance without appreciably affecting the processing of the alloy system, which contributes to keeping down the cost of such an alloy.

DETAILED DESCRIPTION

The alloy system of the present invention accomplishes its objectives by adding from 0.05 to 0.5% by weight magnesium and an element selected from the group consisting of 0.1 to 2.0% by weight tin, 0.05 to 3.0% by weight silicon, and combinations thereof, to an alpha-brass containing 8 to 32.8% by weight zinc. The magnesium may be in combination with 0.02 to 0.5% by weight aluminum. The preferred compositional ranges for these particular additions should range from 0.1 to 0.5% by weight magnesium and from 0.1 to 2.0% by weight tin, or from 0.1 to 2.0% by weight silicon, and combinations thereof. The preferred aluminum addition, if utilized, ranges from 0.05 to 0.5% by weight. The optimal magnesium range for this alloy should be from 0.1 to 0.5% by weight. It should be noted that the total amount of magnesium in the alloy system should be limited by the effect of the magnesium upon the processing of the alloy.

It should also be noted that these additions exhibit an inverse relationship according to the amount of zinc in the alpha-brass base material. In other words, the higher amount of zinc in the base alloy, generally the lower the amount of silicon or tin. The maximum zinc content should be selected in accordance with the following equation: wt.% zinc=32.8-4.8.times.(wt.% Al) -2.3.times.(wt.% Sn) -6.5.times.(wt.% Si). This would assure that the alloy is essentially a single-phase alpha alloy even at elevated temperatures approaching the solidus temperature of the alloy.

The elemental additions discussed above maintain an essentially single-phase alpha alloy. It should be stressed that beta-phase formation should be avoided as much as possible. Although immediately after casting and solidification non-equilibrium beta-phase may be present within the alloy system, further processing of the alloy should try to keep the beta-phase to a maximum of 10 wt. percent. The alloy system of the present invention is compositionally selected so that it cannot be annealed in an alpha plus beta or a beta-phase region since it remains essentially alpha-phase up to within about 25.degree. C. of its solidus temperature. The presence of the beta-phase adversely affects the cold workability of the alloy as well as its stress corrosion resistance.

Various other elements may be added to the alloy of the present invention to suit various purposes. For example, a grain refining element selected from the group consisting of 0.001 to 5.0% by weight iron, 0.001 to 5.0% by weight cobalt, 0.001 to 1.0% by weight chromium, 0.001 to 1.0% by weight zirconium, 0.001 to 1.0% by weight nickel, 0.001 to 1.0% by weight titanium, combination thereof may be added to the alloy. Various other elements such as lead may be added to improve the machinability of the alloy and elements such as arsenic may be added to improve the stress corrosion performance of the alloy. Naturally, the alloy of the present invention may also contain impurities common for alloys of this type and additional additives may be employed in the alloy, as desired, in order to emphasize particular characteristics or to obtain particularly desirable results.

It has normally been expected in this art that an increase in the yield strength of such an alloy should provide an improvement in the stress relaxation performance of the alloy. The improvements brought about by the alloy system of the present invention are considerably greater than those improvements which can be realized by increasing the yield stress alone. These modifications made in the present invention do raise the yield strength of Alloy 260 brass by as much as 13% while they raise the stress remaining values of the alloy by as much as 30%. It is this unexpected increase in the stress remaining value of the alloy system which provides the surprising benefits of the present invention.

The processing of the alloys of the present invention includes various stages of hot and cold working along with various annealing stages. The hot working of this alloy system should be done at a minimum temperature which is above the recrystallization temperature of the particular alloy being worked and which is below the solidus temperature of the alloy. This temperature will range between 500.degree. and 1000.degree. C. or preferably between 600.degree. and 900.degree. C. An optional step after hot working in the processing can be a diffusion annealing step. This annealing will utilize a temperature range of from 200.degree. to 800.degree. C. for 1 to 24 hours or preferably a range of 400.degree. to 700.degree. C. for 1 to 12 hours. The alloy can then be subjected to a milling step, whether or not it undergoes the annealing step, in order to clean the surface of the worked alloy and prepare it for further working. The alloy may then be cold worked with up to but not including a 100% reduction in area and preferably a 10 to 98% reduction in cross-sectional area. The cold worked material can then be subjected to an annealing step at 150.degree. to 900.degree. C. for enough time to recrystallize the alloy to a grain size of 0.005 to 0.05 mm. This annealing can be accomplished in cycles with cold working steps providing that cold working is the last step of the cycle. Cleaning of the worked material can be performed after any one of the annealing steps and not necessarily after each annealing step.

The present invention will be more readily understood from a consideration of the following illustrative examples.

EXAMPLE I

Alloys of the present invention were all made by adding the elemental additions to molten cooper at approximately 1100.degree. C. The zinc was added at approximately 1050.degree. C. and all ingots were poured at 950.degree. to 1050.degree. C. These ingots were then soaked at 800.degree. C. for 2 hours prior to hot working by rolling down to a 0.48" gage and then both rolled surfaces were milled to a final gage of 0.4". Subsequent processing consisted of cold working up to a 90% reduction with interanneals of 550.degree. C. for one hour in air between each cold working pass. The material utilized in this processing was given a final anneal such that the grain size of the alloy was approximately 0.010 mm.

Various alloys were cast in air as 10 lb. ingots with the compositions in weight percent as shown in Table I. Four control alloys of copper-30% zinc were cast and the average properties of the four controls were utilized as subsequent measurements. An additional alloy of commercially processed copper-30% zinc brass was also utilized. The appropriate amounts of the required elements were added to molten copper and the melts were poured through a tundish into a chilled mold. The processing of the alloys consisted of soaking at 800.degree. C. for 2 hours followed by hot rolling to 0.48" and surface milling down to 0.4". The alloy were subsequently cold rolled with intermediate annealing. This annealing was utilized to provide a grain size in the alloy prior to a final cold reduction of 0.01 mm. The final cold rolling reductions were either 35% or 60%, which values were selected for property measurement at each point.

Samples were machined from the 0.03" final gage material after cold working and were tested for their stress relaxation behavior in the longitudinal direction at 75.degree. C. Initial loading was set at 80% of the 0.2% offset yield stress for each alloy. Data for percent stress remaining at 1,000 or more hours of testing were extrapolated to 100,000 hours. The logarithm of stress remaining versus the logarithm of time and hours was assumed to be a linear relationship. The results are presented in Table II.

TABLE I______________________________________NOMINAL COMPOSITIONS OF ALLOYS CompositonAlloy No. % Zn % Mg % Al % Sn % Si % Cu______________________________________Control 30 -- -- -- -- Rem.Commercial 30 -- -- -- -- Rem.Alloy 260C249 27 0.2 -- -- 0.4 Rem.C250 27 0.2 0.1 -- 0.4 Rem.C251 30 0.2 0.1 0.5 -- Rem.______________________________________ TABLE II__________________________________________________________________________ALLOY PROPERTIES Stress Relaxation Behavior Actual Extrapolated Extrapolated 1000 H. 100,000 H. 100,000 H. MBR (in Initial % Stress % stress StressAlloy % CW 0.2% YS UTS % Elong. 1/64")* Stress Remaining Remaining Remaining__________________________________________________________________________Control 35 71.4 79.7 7.7 4 57.1 76.8 66.9 38.2 60 86.1 99.6 2.8 16 68.9 70.4 59.4 40.9CommercialAlloy 260 60 85.8 102.0 2.5 N.A. 68.6 68.1 56.9 39.0C249 35 80.6 94.4 4.5 7 64.5 83.4 77.6 50.1 60 93.8 109.6 1.5** 28 75.0 77.4 69.6 52.2C250 35 81.1 95.2 5.5 8 64.9 84.4 79.4 51.5 60 96.7 111.1 1.5** 28 77.3 78.0 70.5 54.5C251 35 80.0 89.6 5.5 5 64.0 83.0 77.0 49.3 60 91.5 104.5 1.0 28 73.2 74.6 64.7 47.4__________________________________________________________________________ *In transverse direction **Broke outside gage marks N.A. Not Available YS, UTS, Initial Stress and Stress Remaining values are all in ksi.

As can be seen from Table II, the alloys according to the present invention exhibit surprising stress relaxation resistance behavior when compared to either Commercial Alloy 260 or a similar laboratory manufactured material. The Stress Remaining portion of Table II extrapolated to 100,000 hours indicates that the benefits derived from the present invention are more than can be expected from a simple increase in yield strength compared to the base alloys. For example, while the yield strength of Alloy C249, the composition of which falls within the present invention, is only 9.2 ksi and 7.7 ksi at 35% cold worked and 60% cold worked greater than the Control Alloy, the stress remaining at 100,000 hours is 11.9 and 11.3 ksi greater at these cold working reductions than the Control Alloy. This clearly demonstrates the unexpected and surprising improvement in stress relaxation resistance brought about by the alloys of the present invention.

EXAMPLE II

The alloys listed in Table I were processes as described in Example I and the Stress Remaining after 100,000 hours was determined based on Initial Stress levels of 60 ksi and 70 ksi corresponding to hard temper brass and spring temper brass, respectively. The percentage difference over the average Cu-30 Zn base alloy was also measured. The results are shown in Table III.

Electrical conductivities for each of these alloys were measured in various degrees of worked and annealed conditions. These results are shown in Table IV.

TABLE III__________________________________________________________________________STRESS REMAINING AFTER 100,000 HOURS AND IMPROVEMENT OVER BRASS CONTROLSBASED ON INITIAL STRESS LEVELS OF 60 AND 70 KSI 60 ksi Initial Stress 70 ksi Initial Stress % Difference % Difference Nominal 100,000 H. Over Average 100,000 H. Over AverageAlloy No. Composition % SR SR Cu-30 Zn % SR SR Cu-30 Zn__________________________________________________________________________Average ofCu-30 Zn Cu-30-Zn 65.4 39.2 -- 60.0 42.0 --ControlsC249 Cu-27 Zn-0.2 Mg-0.4 Si 81.0 48.6 +24 73.4 51.4 +22C250 Cu-27 Zn-0.2 Mg-0.4 Si- 82.9 49.8 +27 75.7 53.0 +26 0.1 AlC251 Cu-30 Zn-0.2 Mg-0.5 Sn- 82.3 49.4 +26 69.0 48.3 +15 0.1 Al__________________________________________________________________________ TABLE IV______________________________________CONDUCTIVITY PROPERTIES*Alloy No. Condition Conductivity (% IACS)______________________________________Control 35% CW 26.1C249 Annealed 21.2C250 Annealed 20.7C251 Annealed 26.0______________________________________ *Values for conductivity in the cold worked condition are typically 1.5 t 2.5% IACS lower than the annealed values.

The results shown in Table III indicate that the alloys of the present invention provide a significant improvement in stress relaxation resistance at both levels of initial stress when compared to the average of the copper-30 zinc controls. The results shown in Table IV indicate that the conductivity values for the alloys of the present invention compare quite favorably with the conductivity of the control material. There appears to be a trade off point between desired conductivity and desired resistance to stress relaxation. The range percentage improvements demonstrated by the magnesium plus silicon and magnesium plus silicon plus aluminum additions to the base alloy in Table III offset somewhat the relatively small decrease in conductivity exhibited by these same alloys in Table IV. It therefore becomes necessary for a user of material formed from the alloys of the present invention to determine the stress relaxation resistance values and electrical conductivity values desired in the final product. This determination includes the specific additions and amounts of these additions to the base alloy. These particular silicon-containing alloys, however, also exhibit the highest average difference at initial stress levels displayed by all of the alloys in Table III which falls within the present invention. Therefore, it becomes necessary for a user of this specific embodiment of the present invention to determine a trade off point between desired high stress relaxation resistance and desired maintenance of electrical conductivity.

This invention may be embodied in other forms or carried out in other ways without departing from the spirit or essential characteristics thereof. The present embodiment is therefore to be considered as in all respects illustrative and not restrictive, the scope of the invention being indicated by the appended claims, and all changes which come within the meaning and range of equivalency are intended to be embraced therein.

Claims

1. An essentially single-phase alpha alloy which is particularly resistant to stress relaxation at elevated temperatures, said alloy consisting essentially of one component selected from the group consisting of 0.05 to 0.5% by weight magnesium or 0.05 to 0.5% by weight magnesium in combination with 0.02 to 0.5% by weight aluminum, a second component selected from the group consisting of 0.05 to 3.0% by weight silicon or 0.05 to 0.3% by weight silicon in combination with 0.1 to 2.0% by weight tin, from 8 to 32.8% by weight zinc, balance copper, with the amount of said aluminum, silicon or tin being inversely related to the amount of said zinc and with the maximum wt.% zinc=32.8 -4.8.times.(wt.% Al) -2.3.times.(wt.% Sn) -6.5.times.(wt.% Si).

2. An alloy according to claim 1, wherein said one component is selected from the group consisting of 0.1 to 0.5% by weight magnesium or 0.1 to 0.5% magnesium in combination with 0.05 to 0.5% by weight aluminum and said second component is selected from the group consisting of 0.1 to 2.0% by weight for each of tin or silicon and combinations thereof.

3. An alloy according to claim 1, wherein the magnesium portion of said one component ranges from 0.1 to 0.2% by weight.

4. An alloy according to claim 1, wherein said alpha-phase within the alloy accounts for at least 90% by weight of the alloy.

5. An alloy according to claim 1, wherein said alloy is in worked condition and has a grain size of approximately 0.005 to 0.050 mm.

6. An alloy according to claim 1, which maintains its single-phase alpha structure at elevated temperatures approaching the solidus temperature of said alloy.

7. A method for producing an essentially single-phase alpha alloy which is particularly resistant to stress relaxation at elevated temperatures, said method comprising the steps of:

(a) casting an alloy consisting essentially of one component selected from the group consisting of 0.05 to 0.5% by weight magnesium or 0.05 to 0.5% by weight magnesium in combination with 0.02 to 0.5% by weight aluminum, a second component selected from the group consisting of 0.05 to 3.0% by weight silicon or 0.05 to 3.0% by weight silicon in combination with 0.1 to 2.0% by weight tin, from 8 to 32.8% by weight zinc, balance copper, with the amount of said aluminum, silicon or tin being inversely related to the amount of said zinc and with the maximum wt.% zinc =32.8 -4.8 .times.(wt.% Al) -2.3.times.(wt.% Sn) -6.5.times.(wt.% Si);

(b) hot working said alloy at a temperature above the recrystallization temperature of the alloy and below the solidus temperature of the alloy;

(c) cold working said alloy with up to but not including a 100% reduction in area; and

(d) annealing the worked alloy at 150.degree. to 900.degree. C. to recrystallize the alloy to a grain size of 0.005 to 0.050 mm.

8. A method according to claim 7, wherein said cold working is accomplished in cycles with said annealing, provided that a cold working step is the last step of the cycle.

9. A method according to claim 7, wherein said beta-phase in the alloy is kept to a maximum of 10% by weight throughout the processing of the alloy.

10. A method according to claim 7, wherein said alloy is annealed at 200.degree. to 800.degree. C. for 1 to 24 hours after said hot working but before said cold working.

11. A method according to claim 7, wherein said hot working is at 500.degree. to 1000.degree. C.

12. A method according to claim 7, wherein said cold working utilizes a 10 to 98% reduction in cross-sectional area of said alloy.

13. A method according to claim 7, wherein the surface of said alloy is milled or cleaned after said hot working but before said cold working.

14. A method according to claim 7, wherein said one component is selected from the group consisting of 0.1 to 0.5% by weight magnesium or 0.1 to 0.5% by weight magnesium in combination with 0.05 to 0.5% by weight aluminum and said second component is selected from the group consisting of 0.1 to 0.2% by weight for each of tin or silicon and combinations thereof.

15. A method according to claim 7, wherein said alpha-phase within the alloy accounts for at least 90% by weight of the alloy.

16. A method according to claim 7, which maintains its single-phase alpha structure at elevated temperatures approaching the solidus temperature of said alloy.