US3900349A - Silicon brass resistant to parting corrosion - Google Patents
Silicon brass resistant to parting corrosion Download PDFInfo
- Publication number
- US3900349A US3900349A US452618A US45261874A US3900349A US 3900349 A US3900349 A US 3900349A US 452618 A US452618 A US 452618A US 45261874 A US45261874 A US 45261874A US 3900349 A US3900349 A US 3900349A
- Authority
- US
- United States
- Prior art keywords
- corrosion
- parting
- silicon
- percent
- alloy
- 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
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C9/00—Alloys based on copper
- C22C9/04—Alloys based on copper with zinc as the next major constituent
Definitions
- valve stems The problem of dezincification in valve stems has been recognized for years and it was particularly severe when high zinc alloys, such as manganese bronze with 40 percent zinc, were used.
- high zinc alloys such as manganese bronze with 40 percent zinc
- manufacturers of valves turned to the silicon brasses which can contain from 5 to 22 percent zinc and over 0.5 percent silicon, but usually the range of 12 to percent zinc and 2.5 to 4.5 percent silicon has been used.
- This approach is based on the premise that the lower zinc content would deter dezincification and to some extent it has been successful.
- the parting corrosion problem is again becoming serious because of lower water quality as a consequence of the increasing demand for water due to increased population and industrial needs.
- the present invention comprises a silicon brass alloy whose thermal history is controlled in such a manner that the alloy includes substantial quantities of alpha and zeta phases and consists of about 3 to 20 percent zinc, about 2.5 to 6 percent silicon, from about 0.030 percent up to the percentage of solid solubility in the alloy of one or more elements of the group consisting of arsenic, antimony and phosphorus, and the remainder copper.
- an amount of lead to provide good machinability may be added to the alloy.
- the principal of operation of the present invention is the selection of proportions of copper, zinc, silicon and inhibitors within ranges depicted by areas bordered by dashed lines on the Figures.
- the dashed-lined areas disclose the alloys which under commercial conditions of heat treatment are protectible by inhibition addition.
- These areas of the Figures show the alphazeta phase for alloys held at temperature for short periods of time prior to quenching while the solid-line phase boundaries show the phases, including the alpha-zeta phase as indicated, obtained when the alloys are held for long periods, such as days, at selected temperatures to permit an equilibrium condition to be reached.
- the upper end of the range of inhibitor is the percentage just below that at which the inhibitor will start to precipitate and form compounds that may have deleterious effects. While percentages above about 0.10 percent are not generally required, the addition of amounts of inhibitors above 0.10 percent does not adversely affect the alloy until the percentage of solid solubility is passed.
- FIGS. 1, 2 and 3 of the drawings show parting corrosion behavior for three different alloy conditions plotted on the copper-rich comer of the ternary alloy system of the present invention.
- FIG. 4 shows the phases formed when the alloy is cooled from a temperature below 500C.
- FIGS. 1, 2 and 3 show the copper-rich corner of the ternary system of copper, zinc and silicon and whether an alloy having a particular composition undergoes parting corrosion with, or without, an inhibitor present in a specific water, and under electrochemical conditions that will be described below.
- the areas defined by the dashed lines denote compositions which were tested and found to suffer parting corrosion in the absence of an inhibitor.
- FIG. 1 it is seen that an alloy P, whose composition is 8 percent zinc, 3 percent silicon, and balance copper, and cast using normal commercial procedures, would suffer parting corrosion.
- the alloy P whose composition is 8 percent zinc, 3 percent silicon, and balance copper, and cast using normal commercial procedures
- FIGS. 2, 3 and 4 are the equilibrium phase boundaries as determined by Horace Pops (Trans. Met. Soc, AIME, 230, 813-820, 1964). The significance of these diagrams is that they define the phases that would exist if the alloys were allowed to remain at these temperatures for long periods of time such as days or weeks depending on the temperature. No equilibrium phase boundaries are shown in FIG. 1 since cast alloys are generally produced under nonequilibrium conditions.
- the alloys of this invention are cast, then heated and further processed by extrusion and drawing. Such treatments do involve high temperatures, such as 500 to 750C, but the length of time of treatment is generally only a few hours in duration and equilibrium is never attained. Thus, it is quite common to find, for example, alpha and zeta phases existing in alloys where only alpha would be predicted from the phase diagram. However, the phase diagram provides an excellent base on which to describe metallurgical phonomenon.
- zeta phase is no longer stable and transforms either into mu or chi as shown in FIG. 4. 1n the temperature range of 400-500C, the kinetics of the transformation of zeta are fast enough to produce significant amounts of mu or chi in minutes. These phases cannot be protected from parting corrosion, even with inhibitors present, and so they are highly undesirable from the corrosion resistance standpoint. Alpha, of course, can be protected by inhibitor as has been known for years. The unexpected discovery that zeta phase can also be inhibited is the basis for this invention. Thus, with proper inhibitor addition and temperature control, silicon brass alloys manufactured either in the cast or wrought form can be made resistant to parting corrosion so long as only alpha and zeta phases exist in the final state.
- the parting corrosion test used to develop the data herein employed an electronic potentiostat, an instrument which allows corrosion reactions to occur under carefully defined electrochemical parameters. This test more closely parallels actual service conditions than past procedures using hydrochloric acid or copper chloride solutions which are extremely aggressive and not therefore typical of conditions found in water distribution systems.
- the potentiostatic tests were carried out using a test water having similar composition and characteristics of Colorado River water which is an aggressive potable water used in large quantities in the Southwestern region of the United States.
- the composition of the test water and Colorado River In compiling the corrosion data set forth on F 16.
- alloys having the ranges of zero to 24 percent zinc, l to 6 percent silicon, up to about 0.06 percent of an inhibitor and with the remainder copper were cast into specimens which were then rapidly cooled to room temperature. Each specimen was thereafter tested to determine if the test water would cause any detectable parting corrosion.
- the criterion for determining the occurrence of parting was metallographic examination.
- the following table includes the composition of a number of specimens tested and states whether parting corrosion was detected.
- valve stem brass usually includes this element to improve machinability.
- lead was found to have no effect on the corrosion properties of the alloys of the present invention when added in quantities as required to give good machinability. For example, up to about 1.5 percent lead may be added to the alloys.
- the corrosion data depicted in the ternary phase diagrams of FIGS. 2 and 3 was obtained in the same manner as described in obtaining data for the diagram of FIG. 1, except that the cast specimens were swaged, encapsulated, annealed at 600C for days and 760C for 5 days and then quenched. Compositions of some of the specimens tested and the results of the tests are set forth below in Table 111.
- annealing specimens at 760C were to require the use of more inhibitor at the higher zinc and silicon contents to provide immunity to parting corrosion, as illustrated by the upper dashed area on the Figures.
- Annealing at 600C reduced the requirement of using a larger amount of inhibitor until the zinc content reached over 19 percent.
- Other samples were annealed at various temperatures between 550C and 760C and it was found that the immunity to parting obtained was substantially as illustrated on FIGS. 2 and 3. If, however, alloys are annealed or slowly cooled below about 500C, mu and chi phases will occur which are highly susceptible to parting. These phases, as mentioned earlier, cannot be protected by an inhibitor, thus it has been found essential to quickly cool castings or wrought material from over 500C to prevent these phases from forming.
- a silicon brass alloy resistant to parting corrosion consisting essentially of about 3-21 percent by weight zinc, an amount of silicon in the range of about 2.5 to about 7 percent, said amounts of zinc and silicon being sufficient to produce a structure consisting of alpha plus zeta phases in the brass, from about 0.030 percent up to the percentage by weight of solid solubility of one or more elements of the group consisting of arsenic, antimony and phosphorus remainder essentially copper, said alloy having been rapidly cooled to room temperature from a temperature in the range of 500c to 760C and consisting of alpha plus zeta micro structure.
Abstract
This disclosure relates to silicon brass alloys in which corrosion resistance is obtained by the addition of a small amount of an inhibitor, such as arsenic, to provide an alloy which when properly heat treated has substantial resistance to parting corrosion in waters which contain corrosiive ingredients such as are found in many public water supplies.
Description
United States Patent [191 Costas 1 SILICON BRASS RESISTANT TO PARTING CORROSION [75] Inventor: Louis P. Costas, Cheshire, Conn.
[73] Assignee: The Anaconda Company, New
York, NY.
[22] Filed: Mar. 19, 1974 [21] Appl. No.: 452,618
Related U.S. Application Data [63] Continuation-impart of Ser. No. 434,613, Jan. 18, 1974, abandoned, which is a continuation of Ser. No. 222,508, Feb. 1, 1972, abandoned, which is a continuation-in-part of Ser. No. 887,927, Dec. 24, 1969, abandoned.
52 us. Cl. 148/32; 75/1575; 148/325; 148/115 R; 148/l2.7 [51] Int. Cl. C22c 9/10; C22f 1/08 [58] Field of Search 75/1565, 157.5, 160; 148/11.5 R, 32, 32.5, 12.7
[56] References Cited UNITED STATES PATENTS 2,061,921 11/1936 Roath H 75/157.5 X
1 Aug. 19, 1975 2,075,005 3/1937 Bassctt 75/1575 2,118,688 5/1938 Webster..... 75/1575 2,369,813 2/1945 Wilkins.- 75/1575 2,394,673 2/1946 Edmunds 75/1575 3,402,043 9/1968 Smith 75/1575 OTHER PUBLICATIONS Horace Pops, "The Constitution of CopperRich Copper-Silicon-Zinc Alloys, Trans. of AIME, Vol, 230, June 1964, pp. 813-820.
Primary ExaminerC. Lovell Attorney, Agent, or Firm-Pennie & Edmonds 5 7 ABSTRACT This disclosure relates to silicon brass alloys in which corrosion resistance is obtained by the addition of a small amoun't'of an inhibitor, such as arsenic, to provide an alloy which when properly heat treated has substantial resistance to parting corrosion in waters which contain corrosiive ingredients such as are found in many public water supplies.
2 Claims, 4 Drawing Figures SILICON BRASS RESISTANT TO PARTING CORROSION RELATED APPLICATION This application is a continuation-in-part of my application Ser. No. 434,613 filed Jan. 18, 1974 now abandoned, which was a continuation of application Ser. No. 222,508 filed Feb. 1, 1972 now abandoned, which in turn was a continuation-in-part of my application now abandoned Ser. No. 887,927 filed Dec. 24, I969.
BACKGROUND OF THE INVENTION The addition of silicon to brasses increases the mechanical strength of the alloys making them more suitable for use as valve stems and other objects which are subjected to tensile and bending forces. Other desirable features of these alloys are machinability and their freedom from galling or seizing in operation.
However, the resistance of silicon brasses to the corrosive action of many waters and other corrosive fluids has not been satisfactory. For example, in some public water systems valve stems have failed within 1 to 2 years due to parting corrosion. This type of corrosion can be thought of as a leaching out of alloying agents leaving copper behind in a porous and weakened condition. This process of parting corrosion is usually referred to as dezincification when it occurs in the common copper-zinc brasses.
The problem of dezincification in valve stems has been recognized for years and it was particularly severe when high zinc alloys, such as manganese bronze with 40 percent zinc, were used. To combat this problem, manufacturers of valves turned to the silicon brasses which can contain from 5 to 22 percent zinc and over 0.5 percent silicon, but usually the range of 12 to percent zinc and 2.5 to 4.5 percent silicon has been used. This approach is based on the premise that the lower zinc content would deter dezincification and to some extent it has been successful. However, the parting corrosion problem is again becoming serious because of lower water quality as a consequence of the increasing demand for water due to increased population and industrial needs.
As a reaction to this corrosion problem, the trend once again is towards lower zinc levels. The disadvantages of smaller zinc contents are l increased cost of alloys and (2), what is more important, decreasing the zinc does not necessarily eliminate parting corrosion. I have discovered that parting corrosion in silicon brass is not solely a function of zinc content but rather of both zinc and silicon.
Another approach has been the addition of arsenic, antimony, or phosphorus inhibitors which is known to reduce parting corrosion in single phase copper-zinc brasses, but the use of such inhibitors had been found to be ineffective for twophased copper-zinc brasses. Since most silicon brasses depend upon multiphase structure to produce high mechanical strength, the benefits of these inhibitors would not have been predicted, nor would such additions have appeared promising. Furthermore, it has not been appreciated that silicon additions aid parting corrosion of even alpha phase, the primary structure, and therefore no prior attempts to negate the efiect of silicon have been made.
SUMMARY OF THE INVENTION Copper-zinc alloys containing small amounts of silicon in the range of 1 percent to about 2.5 percent silicon, depending on zinc content, are resistant to parting corrosion. However, when the silicon content is increased for strength purposes above these levels to amounts in the range of greater than about 2.5% to about 7 percent, depending on zinc content, parting corrosion will occur. To overcome the corrosion disadvantage of higher silicon levels, arsenic, antimony or phosphorus will provide the alloy with substantial immunity to parting corrosion, whether the alloy is single or multiphased, if proper heat treatment is performed on cast or wrought material.
Broadly stated, the present invention comprises a silicon brass alloy whose thermal history is controlled in such a manner that the alloy includes substantial quantities of alpha and zeta phases and consists of about 3 to 20 percent zinc, about 2.5 to 6 percent silicon, from about 0.030 percent up to the percentage of solid solubility in the alloy of one or more elements of the group consisting of arsenic, antimony and phosphorus, and the remainder copper. Optionally, an amount of lead to provide good machinability may be added to the alloy.
The principal of operation of the present invention is the selection of proportions of copper, zinc, silicon and inhibitors within ranges depicted by areas bordered by dashed lines on the Figures. The dashed-lined areas disclose the alloys which under commercial conditions of heat treatment are protectible by inhibition addition. These areas of the Figures show the alphazeta phase for alloys held at temperature for short periods of time prior to quenching while the solid-line phase boundaries show the phases, including the alpha-zeta phase as indicated, obtained when the alloys are held for long periods, such as days, at selected temperatures to permit an equilibrium condition to be reached.
The upper end of the range of inhibitor is the percentage just below that at which the inhibitor will start to precipitate and form compounds that may have deleterious effects. While percentages above about 0.10 percent are not generally required, the addition of amounts of inhibitors above 0.10 percent does not adversely affect the alloy until the percentage of solid solubility is passed.
BRIEF DESCRIPTION OF THE DRAWINGS FIGS. 1, 2 and 3 of the drawings show parting corrosion behavior for three different alloy conditions plotted on the copper-rich comer of the ternary alloy system of the present invention. FIG. 4 shows the phases formed when the alloy is cooled from a temperature below 500C.
DESCRIPTION OF THE PREFERRED EMBODIMENT FIGS. 1, 2 and 3 show the copper-rich corner of the ternary system of copper, zinc and silicon and whether an alloy having a particular composition undergoes parting corrosion with, or without, an inhibitor present in a specific water, and under electrochemical conditions that will be described below. The areas defined by the dashed lines denote compositions which were tested and found to suffer parting corrosion in the absence of an inhibitor. For example, in FIG. 1 it is seen that an alloy P, whose composition is 8 percent zinc, 3 percent silicon, and balance copper, and cast using normal commercial procedures, would suffer parting corrosion. However, in accordance with my invention, the
addition of at least about 0.03 percent inhibitor pro vides substantial immunity to parting corrosion.
The solid lines of FIGS. 2, 3 and 4 are the equilibrium phase boundaries as determined by Horace Pops (Trans. Met. Soc, AIME, 230, 813-820, 1964). The significance of these diagrams is that they define the phases that would exist if the alloys were allowed to remain at these temperatures for long periods of time such as days or weeks depending on the temperature. No equilibrium phase boundaries are shown in FIG. 1 since cast alloys are generally produced under nonequilibrium conditions.
In commercial operations, the alloys of this invention are cast, then heated and further processed by extrusion and drawing. Such treatments do involve high temperatures, such as 500 to 750C, but the length of time of treatment is generally only a few hours in duration and equilibrium is never attained. Thus, it is quite common to find, for example, alpha and zeta phases existing in alloys where only alpha would be predicted from the phase diagram. However, the phase diagram provides an excellent base on which to describe metallurgical phonomenon.
in FIGS. 2 and 3 it will be noted that the area bounded by the dashed lines involved three phases, alpha, beta, and zeta. However, beta in this region of composition is stable only at high temperatures and attempts to retain it by very rapid quenching fall; it quickly transforms to a mixture of alpha and zeta. On the other hand, alloys consisting of alpha or alpha and zeta at these higher temperatures can be quenched so that these same phases remain intact at room temperature. Thus commercial alloys quickly cooled or quenched from above about 500C commonly consist of alpha and zeta phases even though only alpha or alpha and beta would be predicted from the phase diagram.
Below about 500C, depending on the composition, zeta phase is no longer stable and transforms either into mu or chi as shown in FIG. 4. 1n the temperature range of 400-500C, the kinetics of the transformation of zeta are fast enough to produce significant amounts of mu or chi in minutes. These phases cannot be protected from parting corrosion, even with inhibitors present, and so they are highly undesirable from the corrosion resistance standpoint. Alpha, of course, can be protected by inhibitor as has been known for years. The unexpected discovery that zeta phase can also be inhibited is the basis for this invention. Thus, with proper inhibitor addition and temperature control, silicon brass alloys manufactured either in the cast or wrought form can be made resistant to parting corrosion so long as only alpha and zeta phases exist in the final state.
The parting corrosion test used to develop the data herein employed an electronic potentiostat, an instrument which allows corrosion reactions to occur under carefully defined electrochemical parameters. This test more closely parallels actual service conditions than past procedures using hydrochloric acid or copper chloride solutions which are extremely aggressive and not therefore typical of conditions found in water distribution systems.
The tests were carried out under an argon cover for 24 hours at zero millivolts referenced to a saturated calomel electrode. Cylindrical specimens were millimeters in diameter and about millimeters long. Room temperature test water was used, but, if no parting was detected, the test was again run at 52C and, if still no parting was found the specimen was categorized as showing no parting. These tests were found to correlate well with actual experience with a variety of uninhibited alloys which had been in service for years in aggressive potable waters. Where an alloy specimen passed both the room temperature and 52C test, it can be predicted that it would perform well in service in a corrosive water condition. The potentiostatic tests were carried out using a test water having similar composition and characteristics of Colorado River water which is an aggressive potable water used in large quantities in the Southwestern region of the United States. The composition of the test water and Colorado River In compiling the corrosion data set forth on F 16. l, alloys having the ranges of zero to 24 percent zinc, l to 6 percent silicon, up to about 0.06 percent of an inhibitor and with the remainder copper were cast into specimens which were then rapidly cooled to room temperature. Each specimen was thereafter tested to determine if the test water would cause any detectable parting corrosion. The criterion for determining the occurrence of parting was metallographic examination. The following table includes the composition of a number of specimens tested and states whether parting corrosion was detected.
Lead was added to some of the specimens since valve stem brass usually includes this element to improve machinability. lead was found to have no effect on the corrosion properties of the alloys of the present invention when added in quantities as required to give good machinability. For example, up to about 1.5 percent lead may be added to the alloys.
The corrosion data depicted in the ternary phase diagrams of FIGS. 2 and 3 was obtained in the same manner as described in obtaining data for the diagram of FIG. 1, except that the cast specimens were swaged, encapsulated, annealed at 600C for days and 760C for 5 days and then quenched. Compositions of some of the specimens tested and the results of the tests are set forth below in Table 111.
TABLE III Parting Cu 77.1 77.9 78.0 79.30 82.79 89.03 Zn 19.2 20.3 19.52 17.34 13.37 6.38 Si 34 1 83 2.50 3.35 3.83 4.59 Pb 024 No Parting Cu 76.96 78.79 82.58 89.07 Zn 19.66 17.24 13.47 6.28 Si 3.32 3.93 3.90 4.61 Pb As 0.06 0.03 0.05 0.04
Cu 82.06 Cu 82.1] Zn 19.94 Zn 13.82 Si 3.96 Si 3.98 P 0.04 Sb 0.088
The effect of annealing specimens at 760C was to require the use of more inhibitor at the higher zinc and silicon contents to provide immunity to parting corrosion, as illustrated by the upper dashed area on the Figures. Annealing at 600C reduced the requirement of using a larger amount of inhibitor until the zinc content reached over 19 percent. Other samples were annealed at various temperatures between 550C and 760C and it was found that the immunity to parting obtained was substantially as illustrated on FIGS. 2 and 3. If, however, alloys are annealed or slowly cooled below about 500C, mu and chi phases will occur which are highly susceptible to parting. These phases, as mentioned earlier, cannot be protected by an inhibitor, thus it has been found essential to quickly cool castings or wrought material from over 500C to prevent these phases from forming.
Field tests in public water supplies in major cities in the US have provided further evidence of the advantages of the present alloys. A cast ASTM B 198, CDA
TABLE IV Corrosion Rate (Millimeters per year) ASTM B 198 ASTM 371 (CDA 875) (CDA 697) Non Non- Sitc Inhibited Inhibited Inhibited Inhibited Washington, D.C. 1.6 0.06 0.4 0.06 Cleveland, Ohio 1.1 0.04 0.4 0.] Pasadena, Cal. 04 0.05 0.2 006 Philadelphia, Pa. 0.6 0.1 0.3 0.1
Metallographic examination revealed that in the cast alloy, zeta phase was heavily attacked in the noninhibited form whereas the inhibited counterpart was only superficially affected. In the wrought 697 alloy, both alpha and zeta suffered parting corrosion without an inhibitor present but when inhibited, this form of attack virtually disappeared.
I claim:
1. A silicon brass alloy resistant to parting corrosion consisting essentially of about 3-21 percent by weight zinc, an amount of silicon in the range of about 2.5 to about 7 percent, said amounts of zinc and silicon being sufficient to produce a structure consisting of alpha plus zeta phases in the brass, from about 0.030 percent up to the percentage by weight of solid solubility of one or more elements of the group consisting of arsenic, antimony and phosphorus remainder essentially copper, said alloy having been rapidly cooled to room temperature from a temperature in the range of 500c to 760C and consisting of alpha plus zeta micro structure.
2. The alloy of claim 1 having about 0.06% by weight arsenic as the element.
UNITED STATES PATENT AND TRADEMARK OFFICE CERTIFICATE OF CORRECTION PATENT NO.
DATED INVENTOR(S) I Column Column Column Column [SEAL] LOUIS P. COSTAS tt is certified that error appears in the above-identified patent and that said Letters Patent are hereby corrected as shown below:
line
line
line
line
line
"500C" should read -500C Signed and Scaled this twenty-third D3)! Of December I 975 Arrest:
RUTH C. MASON Arresting Officer C. MARSHALL DANN Commissioner nj'latenls and Trademarks
Claims (2)
1. A SILICON BRASS ALLOY RESISTANT TO PARTING CORROSION CONSISTING ESSENTIALLY OF ABOUT 3-21 PERCENT BY WEIGHT ZINC, AN AMOUNT OF SILICON IN THE RANGE OF ABOUT 2.5 TO ABOUT 7 PERCENT, SAID AMOUNTS OF ZINC AND SILICON BEING SUFFICIENT TO PRODUCE A STRUCTURE CONSISTING OF ALPHA PLUS ZETA PHASES IN THE BRASS, FROM ABOUT 0.030 PERCENT UP TO THE PERCENTAGE BY WEIGHT OF SOLID SOLUBILITY OF ONE MORE ELEMENTS OF THE GROUP CONSISTING OF ARSENIC, ANTIMONY AND PHOSPHORUS REMAINDER ESSENTIALLY COPPER, SAID ALLOY HAVING BEEN RAPIDLY COOLED TO ROOM TEMPERATURE FROM A TEMPERATURE IN THE RANGE OF 500*C TO 760*C AND CONSISTING OF ALPHA PLUS ZETA MICRO STRCTURE.
2. The alloy of claim 1 having about 0.06% by weight arsenic as the element.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US452618A US3900349A (en) | 1974-01-18 | 1974-03-19 | Silicon brass resistant to parting corrosion |
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US43461374A | 1974-01-18 | 1974-01-18 | |
| US452618A US3900349A (en) | 1974-01-18 | 1974-03-19 | Silicon brass resistant to parting corrosion |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| US3900349A true US3900349A (en) | 1975-08-19 |
Family
ID=27030248
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| US452618A Expired - Lifetime US3900349A (en) | 1974-01-18 | 1974-03-19 | Silicon brass resistant to parting corrosion |
Country Status (1)
| Country | Link |
|---|---|
| US (1) | US3900349A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3977913A (en) * | 1972-12-01 | 1976-08-31 | Essex International | Wrought brass alloy |
| US4113474A (en) * | 1974-09-12 | 1978-09-12 | Toyo Valve Company, Ltd. | Copper alloys of excellent corrosion resistance, moldability and workability |
| US4259124A (en) * | 1978-06-28 | 1981-03-31 | Olin Corporation | Modified brass alloys with improved stress relaxation resistance |
| EP1045041A1 (en) * | 1998-10-12 | 2000-10-18 | Sambo Copper Alloy Co., Ltd | Leadless free-cutting copper alloy |
| WO2012032155A3 (en) * | 2010-09-10 | 2013-02-28 | Raufoss Water & Gas As | Improved brass alloy and a method of manufacturing thereof |
| US20150368758A1 (en) * | 2014-06-23 | 2015-12-24 | Jiangxi Audy Brasswork Inc. | Low-lead brass alloy |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2061921A (en) * | 1936-03-20 | 1936-11-24 | Chase Companies Inc | Corrosion resistant tubes |
| US2075005A (en) * | 1933-11-25 | 1937-03-30 | Sarah H Bassett | Copper-silicon-zinc-lead alloy |
| US2118688A (en) * | 1937-06-25 | 1938-05-24 | Bridgeport Brass Co | Yellow brass pipe alloy |
| US2369813A (en) * | 1941-06-03 | 1945-02-20 | Revere Copper & Brass Inc | Brass pipe and tube |
| US2394673A (en) * | 1943-02-11 | 1946-02-12 | New Jersey Zinc Co | Brass |
| US3402043A (en) * | 1966-03-01 | 1968-09-17 | Olin Mathieson | Copper base alloys |
-
1974
- 1974-03-19 US US452618A patent/US3900349A/en not_active Expired - Lifetime
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2075005A (en) * | 1933-11-25 | 1937-03-30 | Sarah H Bassett | Copper-silicon-zinc-lead alloy |
| US2061921A (en) * | 1936-03-20 | 1936-11-24 | Chase Companies Inc | Corrosion resistant tubes |
| US2118688A (en) * | 1937-06-25 | 1938-05-24 | Bridgeport Brass Co | Yellow brass pipe alloy |
| US2369813A (en) * | 1941-06-03 | 1945-02-20 | Revere Copper & Brass Inc | Brass pipe and tube |
| US2394673A (en) * | 1943-02-11 | 1946-02-12 | New Jersey Zinc Co | Brass |
| US3402043A (en) * | 1966-03-01 | 1968-09-17 | Olin Mathieson | Copper base alloys |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3977913A (en) * | 1972-12-01 | 1976-08-31 | Essex International | Wrought brass alloy |
| US4113474A (en) * | 1974-09-12 | 1978-09-12 | Toyo Valve Company, Ltd. | Copper alloys of excellent corrosion resistance, moldability and workability |
| US4259124A (en) * | 1978-06-28 | 1981-03-31 | Olin Corporation | Modified brass alloys with improved stress relaxation resistance |
| EP1045041A1 (en) * | 1998-10-12 | 2000-10-18 | Sambo Copper Alloy Co., Ltd | Leadless free-cutting copper alloy |
| EP1045041A4 (en) * | 1998-10-12 | 2003-05-07 | Sambo Copper Alloy Co Ltd | Leadless free-cutting copper alloy |
| EP1559802A1 (en) * | 1998-10-12 | 2005-08-03 | Sambo Copper Alloy Co., Ltd | Lead-free, free-cutting copper alloys |
| EP1600516A2 (en) * | 1998-10-12 | 2005-11-30 | Sambo Copper Alloy Co., Ltd | Lead-free, free-cutting copper alloys |
| EP1600517A2 (en) * | 1998-10-12 | 2005-11-30 | Sambo Copper Alloy Co., Ltd | Lead-free, free-cutting copper alloys |
| EP1600516A3 (en) * | 1998-10-12 | 2005-12-14 | Sambo Copper Alloy Co., Ltd | Lead-free, free-cutting copper alloys |
| EP1600517A3 (en) * | 1998-10-12 | 2005-12-14 | Sambo Copper Alloy Co., Ltd | Lead-free, free-cutting copper alloys |
| WO2012032155A3 (en) * | 2010-09-10 | 2013-02-28 | Raufoss Water & Gas As | Improved brass alloy and a method of manufacturing thereof |
| US9217191B2 (en) | 2010-09-10 | 2015-12-22 | Raufoss Water & Gas As | Brass alloy comprising silicon and arsenic and a method of manufacturing thereof |
| US20150368758A1 (en) * | 2014-06-23 | 2015-12-24 | Jiangxi Audy Brasswork Inc. | Low-lead brass alloy |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US4434016A (en) | Precipitation hardenable copper alloy and process | |
| EP1287175A1 (en) | Corrosion resistant aluminium alloy | |
| US4417929A (en) | Special brass with dezincification corrosion resistance | |
| US5637160A (en) | Corrosion-resistant bismuth brass | |
| US3703367A (en) | Copper-zinc alloys | |
| US3900349A (en) | Silicon brass resistant to parting corrosion | |
| GB2147915A (en) | Stress corrosion resistant al-mg-li-cu alloy | |
| US3816187A (en) | Processing copper base alloys | |
| US4242132A (en) | Copper base alloy containing manganese and nickle | |
| Costas | Effect of Phosphorus on the Embrittlement of Copper-Nickel Alloys by Mercury | |
| US4148635A (en) | High temperature softening resistance of alloy 688 and modified 688 through the addition of Nb | |
| JPS6086233A (en) | High-strength conductive copper alloy | |
| US3893851A (en) | Corrosion-resistant alloys | |
| US4715910A (en) | Low cost connector alloy | |
| US4180398A (en) | Modification of leaded brasses to improve hot workability | |
| US4242133A (en) | Copper base alloy containing manganese | |
| US3684496A (en) | Solder having improved strength at high temperatures | |
| US4407776A (en) | Shape memory alloys | |
| JP2841270B2 (en) | Copper base alloy excellent in corrosion resistance and hot workability and valve parts using the alloy | |
| US4202708A (en) | Corrosion resistant copper base alloys for heat exchanger tube | |
| US4650650A (en) | Copper-based alloy with improved conductivity and softening properties | |
| US2744822A (en) | Copper base alloys | |
| Skidmore et al. | Corrosion and dezincification of brasses in water | |
| KR0141858B1 (en) | Method for manufacturing copper alloy with resistant corrosion | |
| JP3483773B2 (en) | Hot water related equipment and electrical / mechanical parts using a copper-based alloy with excellent corrosion resistance and hot workability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| AS | Assignment |
Owner name: ATLANTIC RICHFIELD COMPANY, A PA CORP. Free format text: ASSIGNMENT OF ASSIGNORS INTEREST.;ASSIGNOR:ANACONDA COMPANY THE, A DE CORP;REEL/FRAME:003992/0218 Effective date: 19820115 |
|
| STCF | Information on status: patent grant |
Free format text: PATENTED FILE - (OLD CASE ADDED FOR FILE TRACKING PURPOSES) |
|
| AS | Assignment |
Owner name: AMERICAN BRASS COMPANY, L.P., A DELAWARE LIMITED P Free format text: ASSIGNMENT OF ASSIGNORS INTEREST. SUBJECT TO LICENSE RECITED;ASSIGNOR:ATLANTIC RICHFIELD COMPANY, A CORP. OF DE.;REEL/FRAME:004492/0486 Effective date: 19851129 |
|
| AS | Assignment |
Owner name: HELLER FINANCIAL CENTRAL, INC., 105 WEST ADAMS STR Free format text: SECURITY INTEREST;ASSIGNOR:AMERICAN BRASS COMPANY, L.P., A DELAWARE LIMITED PARTNERSHIP;REEL/FRAME:004510/0187 Effective date: 19851206 Owner name: CONTINENTAL BANK OF CANADA, NEW YORK BRANCH, 245 P Free format text: SECURITY INTEREST;ASSIGNOR:AMERICAN BRASS COMPANY, L.P., A DELAWARE LIMITED PARTNERSHIP;REEL/FRAME:004510/0187 Effective date: 19851206 |
|
| AS | Assignment |
Owner name: ANSONIA COPPER & BRASS, INC., 75 LIBERTY STREET, A Free format text: LICENSE;ASSIGNOR:AMERICAN BRASS COMPANY;REEL/FRAME:004539/0570 Effective date: 19860212 |
|
| AS | Assignment |
Owner name: BANCBOSTON FINANCIAL COMPANY, ONE LANDMARK SQUARE, Free format text: SECURITY INTEREST;ASSIGNOR:ANSONIA COPPER & BRASS, INC.,;REEL/FRAME:004760/0875 Effective date: 19870716 Owner name: BANCBOSTON FINANCIAL COMPANY,CONNECTICUT Free format text: SECURITY INTEREST;ASSIGNOR:ANSONIA COPPER & BRASS, INC.,;REEL/FRAME:004760/0875 Effective date: 19870716 |
|
| AS | Assignment |
Owner name: NORSTAR BANK, NATIONAL ASSOCIATION, A NATIONAL BAN Free format text: SECURITY INTEREST;ASSIGNOR:AMERICAN BRASS COMPANY, L.P., A DE. LIMITED PARTNERSHIP;REEL/FRAME:005237/0717 Effective date: 19891228 |
|
| AS | Assignment |
Owner name: OUTOKUMPU AMERICAN BRASS, INC., A CORP. OF DE, NEW Free format text: ASSIGNMENT OF ASSIGNORS INTEREST.;ASSIGNOR:AMERICAN BRASS COMPANY, L.P., A DE LIMITED PARTNERSHIP;REEL/FRAME:005426/0646 Effective date: 19900830 |
|
| AS | Assignment |
Owner name: AMERICAN BRASS COMPANY, L.P., A DELAWARE LIMITED P Free format text: RELEASED BY SECURED PARTY;ASSIGNOR:CONTINENTAL BANK OF CANADA, NEW YORK BRANCH;REEL/FRAME:005505/0315 Effective date: 19900828 |
|
| AS | Assignment |
Owner name: AMERICAN BRASS COMPANY, L.P., A DE LIMITED PARTNER Free format text: RELEASED BY SECURED PARTY;ASSIGNOR:NORSTAR BANK, NATIONAL ASSOCIATION;REEL/FRAME:005573/0710 Effective date: 19900828 Owner name: AMERICAN BRASS COMPANY, L.P., A DE LIMITED PARTNER Free format text: RELEASED BY SECURED PARTY;ASSIGNOR:HELLER FINANCIAL, INC. AS SUCCESSOR BY MERGER TO HELLER FINANCIAL CENTRAL, INC.;REEL/FRAME:005573/0702 Effective date: 19900828 |
|
| AS | Assignment |
Owner name: BANCBOSTON FINANCIAL COMPANY A MA CORPORATION, CO Free format text: SECURITY INTEREST;ASSIGNOR:ANSONIA COPPER & BRASS, INC., A DE CORPORATION;REEL/FRAME:005748/0076 Effective date: 19870716 |
|
| AS | Assignment |
Owner name: BANK OF BOSTON CONNECTICUT A CORP. OF CONNECTIC Free format text: SECURITY INTEREST;ASSIGNOR:ANSONIA COPPER & BRASS, INC. A CORP. OF DELAWARE;REEL/FRAME:005947/0393 Effective date: 19910828 |
|
| AS | Assignment |
Owner name: ANSONIA COPPER & BRASS, INC., CONNECTICUT Free format text: RELEASE BY SECURED PARTY;ASSIGNOR:FLEET NATIONAL BANK FKA A BANK OF BOSTON CT;REEL/FRAME:012463/0809 Effective date: 20010328 Owner name: ANSONIA COPPER & BRASS, INC., CONNECTICUT Free format text: TERM. OF SECURITY INTEREST;ASSIGNOR:FLEET NATIONAL BANK F/K/A BANK OF BOSTON CT;REEL/FRAME:012463/0815 Effective date: 20010424 Owner name: GENERAL ELECTRIC CAPITAL CORPORATION, CONNECTICUT Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:ANSONIA COPPER & BRASS, INC.;REEL/FRAME:012463/0855 Effective date: 20010330 |