CA2303164A1 - Copper based alloy featuring precipitation hardening and solid-solution hardening - Google Patents
Copper based alloy featuring precipitation hardening and solid-solution hardening Download PDFInfo
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- CA2303164A1 CA2303164A1 CA002303164A CA2303164A CA2303164A1 CA 2303164 A1 CA2303164 A1 CA 2303164A1 CA 002303164 A CA002303164 A CA 002303164A CA 2303164 A CA2303164 A CA 2303164A CA 2303164 A1 CA2303164 A1 CA 2303164A1
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C9/00—Alloys based on copper
- C22C9/02—Alloys based on copper with tin as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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Abstract
A phosphor bronze alloy consisting of: 0.4 to 3.0 wt.% Ni, 1.0 to 11.0 wt.%
Sn, 0.1 to 1.0 wt.% Si, 0.01 to 0.35 wt.% P, the remainder being substantially Cu. The alloy is suitable for electrical lead conductors and for electrical or electronic interconnections.
Sn, 0.1 to 1.0 wt.% Si, 0.01 to 0.35 wt.% P, the remainder being substantially Cu. The alloy is suitable for electrical lead conductors and for electrical or electronic interconnections.
Description
WO 99/13117 PG"T/US98/17196 COPPER BASED ALLOY FEATURING PRECIPITATION
HARDENING AND SOLID-SOLUTION HARDENING
This application claims priority to U.S. Application No.
60/057,777 filed September 5, 1997, the entire contents of which are incorporated by reference.
This invention relates to a copper alloy, particularly a s copper alloy that is especially useful in electrical and electronic interconnection components and switch applications, including high temperature switching. This alloy shows special promise in "spring type" applications.
to BACKGROUND OF THE INVENTION
Several families of copper alloys are known in various arts. For example, Mikawa et al., U.S. Patent No. 5,041,176 discloses a copper alloy including from 0.1-10~ nickel (Ni);
0.1-10~ tin (Sn); 0.05-5~ silicon (Si); 0.01-5~ iron (Fe); and ~s 0.0001-l~ boron (H), by weight. This disclosure requires formation of an Ni-Si intermetallic compound homogeneously dispersed in the alloy. Fe is required for age hardening.
However, at Fe concentrations greater than 5~, electrical conductivity is compromised and corrosion becomes a serious problem. B is incorporated into the alloy to improve corrosion resistance, hardness and strength. High hardness is achieved by precipitation hardening at a tempering temperature of 400° to 450°C. Si also serves as a deoxidizer.
Although the Mikawa alloy is suitable for use in zs electronic parts where good electrical conductivity, heat conductivity, strength, hardness, plating ability, soldering ability, elasticity, and corrosion resistance including resistance to acids are required, this alloy is of a different composition and displays different characteristics from those ao obtainable according to the instant invention.
Another comparison alloy is disclosed by Kubosono et al . , U.S. Patent No. 5,516,484. Kubosono et al. discloses copper-nickel based alloys that are processed using horizontal continuous casting with a graphite mold. The Ni-Cu alloy as system is essentially a different alloy than the alloy of the instant invention. In this alloy copper (Cu) is an undesired impurity whose content must be kept below 0.02%. Kubosono et al., teaches that effects obtainable by addition of Si cannot be recognized if no B is present.
s U.S. Patent No. 5,334,346 to Kim et al. discloses a high performance copper alloy for electrical and electronic parts.
The Kim alloy consists essentially of copper and 0.5 to 2.4%
by weight Ni; 0.1-0.5% Si; 0.02 to 0.16% P; and 0.02 to 0.2%
magnesium (Mg). Kim et al. discusses precipitation hardening ~o where NiZSi and Ni3P precipitate in the copper matrix. Any excess of free Si and P, is taught as causing formation of brittle intermetallic compounds which lead to peeling and cracking. Mg is proposed as a scavenger element to remove free Si and P. However, as content of Mg increases, ~s conductivity and utility of the alloy are compromised. Zinc (Zn) and Fe are also disclosed as possible scavengers. This alloy does not contain Sn.
Hashizume et al., U.S. Patent No. 5,064,611 discloses a process for producing a copper alloy that contains 1-8% Ni;
zo 0.1-0.8% P; 0.6-1.0% Si; optionally, 0.03 to 0.5% Zn; and Cu.
NisP2 and Ni2Si are disclosed as intermetallic compounds for increasing mechanical strength of the alloy with minimal decrease in electrical conductivity. Sn is not present in this alloy.
s As an example of a copper-tin alloy, i.e., bronze, Asai et al., U.S. Patent No. 5,021,105, discloses an alloy comprising 2.0-7.0% Sn; l.0-6.0% Ni, cobalt (Co) or chromium (Cr) ; 0.1-2.0% Si; and Cu. This alloy may be processed to exhibit elongation of 3-20%; strength of 70-100 kg/mm2; and so electroconductivity from 10-30% IACS. Ni is disclosed as being important for strengthening; Cr is disclosed as improving hot rolling properties and heat resistance; and Co is disclosed as contributing to effective heat resistance.
According to Asai et al. Sn content is limited to 7% by the 3s hot rolling method used to process the alloy. Asai et al.
does not disclose phosphorus (P) as a constituent.
Accordingly, this alloy suffers similar limitations to Mikawa et al., as discussed above.
HARDENING AND SOLID-SOLUTION HARDENING
This application claims priority to U.S. Application No.
60/057,777 filed September 5, 1997, the entire contents of which are incorporated by reference.
This invention relates to a copper alloy, particularly a s copper alloy that is especially useful in electrical and electronic interconnection components and switch applications, including high temperature switching. This alloy shows special promise in "spring type" applications.
to BACKGROUND OF THE INVENTION
Several families of copper alloys are known in various arts. For example, Mikawa et al., U.S. Patent No. 5,041,176 discloses a copper alloy including from 0.1-10~ nickel (Ni);
0.1-10~ tin (Sn); 0.05-5~ silicon (Si); 0.01-5~ iron (Fe); and ~s 0.0001-l~ boron (H), by weight. This disclosure requires formation of an Ni-Si intermetallic compound homogeneously dispersed in the alloy. Fe is required for age hardening.
However, at Fe concentrations greater than 5~, electrical conductivity is compromised and corrosion becomes a serious problem. B is incorporated into the alloy to improve corrosion resistance, hardness and strength. High hardness is achieved by precipitation hardening at a tempering temperature of 400° to 450°C. Si also serves as a deoxidizer.
Although the Mikawa alloy is suitable for use in zs electronic parts where good electrical conductivity, heat conductivity, strength, hardness, plating ability, soldering ability, elasticity, and corrosion resistance including resistance to acids are required, this alloy is of a different composition and displays different characteristics from those ao obtainable according to the instant invention.
Another comparison alloy is disclosed by Kubosono et al . , U.S. Patent No. 5,516,484. Kubosono et al. discloses copper-nickel based alloys that are processed using horizontal continuous casting with a graphite mold. The Ni-Cu alloy as system is essentially a different alloy than the alloy of the instant invention. In this alloy copper (Cu) is an undesired impurity whose content must be kept below 0.02%. Kubosono et al., teaches that effects obtainable by addition of Si cannot be recognized if no B is present.
s U.S. Patent No. 5,334,346 to Kim et al. discloses a high performance copper alloy for electrical and electronic parts.
The Kim alloy consists essentially of copper and 0.5 to 2.4%
by weight Ni; 0.1-0.5% Si; 0.02 to 0.16% P; and 0.02 to 0.2%
magnesium (Mg). Kim et al. discusses precipitation hardening ~o where NiZSi and Ni3P precipitate in the copper matrix. Any excess of free Si and P, is taught as causing formation of brittle intermetallic compounds which lead to peeling and cracking. Mg is proposed as a scavenger element to remove free Si and P. However, as content of Mg increases, ~s conductivity and utility of the alloy are compromised. Zinc (Zn) and Fe are also disclosed as possible scavengers. This alloy does not contain Sn.
Hashizume et al., U.S. Patent No. 5,064,611 discloses a process for producing a copper alloy that contains 1-8% Ni;
zo 0.1-0.8% P; 0.6-1.0% Si; optionally, 0.03 to 0.5% Zn; and Cu.
NisP2 and Ni2Si are disclosed as intermetallic compounds for increasing mechanical strength of the alloy with minimal decrease in electrical conductivity. Sn is not present in this alloy.
s As an example of a copper-tin alloy, i.e., bronze, Asai et al., U.S. Patent No. 5,021,105, discloses an alloy comprising 2.0-7.0% Sn; l.0-6.0% Ni, cobalt (Co) or chromium (Cr) ; 0.1-2.0% Si; and Cu. This alloy may be processed to exhibit elongation of 3-20%; strength of 70-100 kg/mm2; and so electroconductivity from 10-30% IACS. Ni is disclosed as being important for strengthening; Cr is disclosed as improving hot rolling properties and heat resistance; and Co is disclosed as contributing to effective heat resistance.
According to Asai et al. Sn content is limited to 7% by the 3s hot rolling method used to process the alloy. Asai et al.
does not disclose phosphorus (P) as a constituent.
Accordingly, this alloy suffers similar limitations to Mikawa et al., as discussed above.
SUBSTITUTE SHEET (RULE 26) Similarly, Arita et al., U.S. Patent No. 4,337,089, discloses a Cu-Ni-Sn alloy containing 0.5-3.0% Ni; 0.3-0.9%
Sn; 0.01-0.2% P; 0.0-0.35% manganese (Mn) or Si; and Cu. This alloy features 60 kg/mm= tensile strength and elongation of s more than 6% (i.e., to provide the mechanical property necessary for bend working) by combining heat treatment and cold rolling in its processing. In Arita et al., Si or Mn is incorporated to, enhance strength. The low Sn content disclosed in Arita et al., however, does not provide the ~o combined formability-strength properties of the instant invention.
Takeda et al., U.S. Patent No. 5,132,083 teaches a laser padding material which is a powder containing 1-5% Ni; 0.2-5%
Si; leas than 1% B; less than 2% P; less than 3% Mn; and Cu.
~s Sn and lead (Pb) are optional ingredients, at 8-15% for each.
This powder can be laser processed to produce a copper laser padding material excellent in sliding-abrasion resistance.
The chemistries involved in laser padding are not the same as in the alloy of the instant invention. For example, no io rolling, hot or cold, is used to process the padding material.
A designation system for providing a means for defining and identifying coppers and copper alloys is known as UNS
(Unified Numbering System). This system is in common use in North America and uses a five digit (recently expanded from a three digit) numbering following a C prefix. The numbering system is not a specification, but rather a useful number code for identifying mill and foundry products. The C designations appearing below refer to the UNS numbers. The general art that includes alloys thus includes many patentable alloys that so are similar in some respects in composition, but that display different desired properties depending on the specific content and processing of the alloy.
UNS alloy C85800 is a leaded yellow brass containing 1.5%
Sn, 1.5% Pb, 31-41% Zn, 0.5% Fe, 0.05%Sb, 0.5% Ni (incl Co), 3s 0.25% Mn, 0.05% As, 0.05% S, 0.01% P, 0.55% A1, 0.25% Si and 57.0% minimum Cu.
In the electronics industry, phosphor bronzes with required strength and formability are known that can be used SUBSTITUTE SHEET (RULE 26) up to 100°C. However, the need exists for alloys resistant to higher temperatures, e.g., of 120°C, 140°C and temperatures up to or exceeding 150°C. Higher temperature applications will allow faster speed in electronic processing and allow the s alloy to be used in higher temperature environments.
Accordingly, the present invention provides a phosphor bronze alloy with characteristics much improved over those known in the art. The invention provides an alloy that when processed has desired spring and strength properties and io superior durability especially at higher temperatures at an economic price.
BRIEF DESCRIPTION OF THE DRAWINGS
Figure 1 depicts softening behavior data curves for alloy ~s MHP101 of the Example and of comparative alloys.
Figure 2 depicts stress relaxation data curves for alloy MHP101 of the Example and of comparative alloys.
THE INVENTION
zo A particle dispersion enhanced phosphor bronze in accordance with the present invention includes a nickel content of from 0.4 to 3.0% by weight; a Si content of from 0.1 to I.0% by weight; a P content of from 0.01-0.35% by weight; a Sn content of 1.0-11.0% by weight and copper. Sn zs enhances formability at a given level of strength. P helps impart optimal spring and strength properties as well as providing fluidity in casting copper based alloys. P also aids in deoxidation of the melt. P is the primary deoxidizer of the melt. Si is not lost in uncontrolled quantities in the ~o melting process, which permits maintaining a stoichiometrical relationship between Si and Ni in the alloy.
Sn content of below 8% and P content of 0.01-0.2% by wt.
are especially preferred in some embodiments.
Solid solution hardening is contributed by tin, 3s phosphorous and copper, while precipitation hardening resides in nickel silicide and nickel phosphides precipitated in the matrix.
Sn; 0.01-0.2% P; 0.0-0.35% manganese (Mn) or Si; and Cu. This alloy features 60 kg/mm= tensile strength and elongation of s more than 6% (i.e., to provide the mechanical property necessary for bend working) by combining heat treatment and cold rolling in its processing. In Arita et al., Si or Mn is incorporated to, enhance strength. The low Sn content disclosed in Arita et al., however, does not provide the ~o combined formability-strength properties of the instant invention.
Takeda et al., U.S. Patent No. 5,132,083 teaches a laser padding material which is a powder containing 1-5% Ni; 0.2-5%
Si; leas than 1% B; less than 2% P; less than 3% Mn; and Cu.
~s Sn and lead (Pb) are optional ingredients, at 8-15% for each.
This powder can be laser processed to produce a copper laser padding material excellent in sliding-abrasion resistance.
The chemistries involved in laser padding are not the same as in the alloy of the instant invention. For example, no io rolling, hot or cold, is used to process the padding material.
A designation system for providing a means for defining and identifying coppers and copper alloys is known as UNS
(Unified Numbering System). This system is in common use in North America and uses a five digit (recently expanded from a three digit) numbering following a C prefix. The numbering system is not a specification, but rather a useful number code for identifying mill and foundry products. The C designations appearing below refer to the UNS numbers. The general art that includes alloys thus includes many patentable alloys that so are similar in some respects in composition, but that display different desired properties depending on the specific content and processing of the alloy.
UNS alloy C85800 is a leaded yellow brass containing 1.5%
Sn, 1.5% Pb, 31-41% Zn, 0.5% Fe, 0.05%Sb, 0.5% Ni (incl Co), 3s 0.25% Mn, 0.05% As, 0.05% S, 0.01% P, 0.55% A1, 0.25% Si and 57.0% minimum Cu.
In the electronics industry, phosphor bronzes with required strength and formability are known that can be used SUBSTITUTE SHEET (RULE 26) up to 100°C. However, the need exists for alloys resistant to higher temperatures, e.g., of 120°C, 140°C and temperatures up to or exceeding 150°C. Higher temperature applications will allow faster speed in electronic processing and allow the s alloy to be used in higher temperature environments.
Accordingly, the present invention provides a phosphor bronze alloy with characteristics much improved over those known in the art. The invention provides an alloy that when processed has desired spring and strength properties and io superior durability especially at higher temperatures at an economic price.
BRIEF DESCRIPTION OF THE DRAWINGS
Figure 1 depicts softening behavior data curves for alloy ~s MHP101 of the Example and of comparative alloys.
Figure 2 depicts stress relaxation data curves for alloy MHP101 of the Example and of comparative alloys.
THE INVENTION
zo A particle dispersion enhanced phosphor bronze in accordance with the present invention includes a nickel content of from 0.4 to 3.0% by weight; a Si content of from 0.1 to I.0% by weight; a P content of from 0.01-0.35% by weight; a Sn content of 1.0-11.0% by weight and copper. Sn zs enhances formability at a given level of strength. P helps impart optimal spring and strength properties as well as providing fluidity in casting copper based alloys. P also aids in deoxidation of the melt. P is the primary deoxidizer of the melt. Si is not lost in uncontrolled quantities in the ~o melting process, which permits maintaining a stoichiometrical relationship between Si and Ni in the alloy.
Sn content of below 8% and P content of 0.01-0.2% by wt.
are especially preferred in some embodiments.
Solid solution hardening is contributed by tin, 3s phosphorous and copper, while precipitation hardening resides in nickel silicide and nickel phosphides precipitated in the matrix.
SUBSTITUTE SHEET (RULE 26) Solid solution of a copper base occurs when the alloying element is dissolved to form a homogenous liquid solution.
When the solution is frozen and subsequently rolled/annealed, the alloying metal goes into solution to form a solid s solution. The alloying element thereby becomes an integral part of the matrix crystal.
Substitution of elements in solid solution tends to increase the strength of the metal as it decreases electrical conductivity. The increased strength is related to a greater io resistance to slip. The solute atoms are different in size from the copper atoms, causing a distortion of the lattice structure that imparts slip resistance. That is, greater energy is required to distort the lattice.
Preliminary analysis indicates that this alloy is is resistant to stress relaxation, i.e., time dependent decrease in stress in a solid under given constant constraints especially at elevated temperatures encountered in some applications. The phosphor bronze according to the instant invention has consistent mechanical properties, optimum yield xo strength and excellent formability. The alloy is especially useful in high temperature applications, e.g., where operational temperatures may reach 140°C, 150°C or higher, for example, up to 200°C in specific applications. The alloy is designed to be a high strength alloy with moderate a conductivity. In these applications, no comparable alloy has been previously available.
The alloy family will have the strength and formability of known phosphor bronzes, but will exhibit superior resistance to stress relaxation especially at elevated ~o temperatures.
In an exemplary process, the material for the alloy is mixed according to desired concentrations and melted in channel or coreless electric induction furnaces. The obtained melt is horizontally continuous cast through a graphite die.
ss This process is sometimes referred to as horizontal thin strip continuous casting. Special enhanced cooling can be employed to assure proper quenching of solidified material, to maintain all solute in solution.
When the solution is frozen and subsequently rolled/annealed, the alloying metal goes into solution to form a solid s solution. The alloying element thereby becomes an integral part of the matrix crystal.
Substitution of elements in solid solution tends to increase the strength of the metal as it decreases electrical conductivity. The increased strength is related to a greater io resistance to slip. The solute atoms are different in size from the copper atoms, causing a distortion of the lattice structure that imparts slip resistance. That is, greater energy is required to distort the lattice.
Preliminary analysis indicates that this alloy is is resistant to stress relaxation, i.e., time dependent decrease in stress in a solid under given constant constraints especially at elevated temperatures encountered in some applications. The phosphor bronze according to the instant invention has consistent mechanical properties, optimum yield xo strength and excellent formability. The alloy is especially useful in high temperature applications, e.g., where operational temperatures may reach 140°C, 150°C or higher, for example, up to 200°C in specific applications. The alloy is designed to be a high strength alloy with moderate a conductivity. In these applications, no comparable alloy has been previously available.
The alloy family will have the strength and formability of known phosphor bronzes, but will exhibit superior resistance to stress relaxation especially at elevated ~o temperatures.
In an exemplary process, the material for the alloy is mixed according to desired concentrations and melted in channel or coreless electric induction furnaces. The obtained melt is horizontally continuous cast through a graphite die.
ss This process is sometimes referred to as horizontal thin strip continuous casting. Special enhanced cooling can be employed to assure proper quenching of solidified material, to maintain all solute in solution.
SUBSTITUTE SHEET (RULE 26) The preferred casting practice employs special enhanced cooling within the graphite die assembly to assure a sufficiently rapid quench of the just-solidified metal from its solidus temperature to a temperature below 450°C. This s assures that the solute remains to a high degree (estimated at approx. 90%) in solution, and does not have time to significantly precipitate during the cooling phase.
This enhanced cooling involves the use of high thermal conductivity (minimum .77 cal/cm/sec) copper plates to which io a high thermal conductivity graphite die (minimum .29 cal/cm/sec) has been bolted as per current standard art. The invention introduces a high conductivity gas such as Helium or Hydrogen or mixtures thereof, or carrier gases with significant concentrations of Helium and/or Hydrogen, between ~s the copper plates and graphite plates of the assembly. The high conductivity gas replaces atmospheric OZ/N2 in the copper/graphite interface, thereby improving the cooling action.
The cast material is surface milled and then rolled down zo to thinner gages. Heat treatments are imposed in the course of rolling to assure 1) maximum solution of alloying elements, and 2) precipitation of the dissolved alloying elements. The precipitate provides strength and resistance to stress relaxation.
a Less cold rolling is required to achieve the same tensile strength as Sn concentration (solid solution content) of the alloy increases. Less cold rolling permits more subsequent forming operations.
After heat treatment, the material is for some so applications further rolled to attain increased strength, and may or may not be stress relieved thermally and/or mechanically at finish.
In a further embodiment of the invention, improved solutioning of the solute is obtained by heat treating at 3s elevated temperatures at the cast stage, or at intermediate stages.
The process stages in accordance with the instant invention can include the following protocols:
This enhanced cooling involves the use of high thermal conductivity (minimum .77 cal/cm/sec) copper plates to which io a high thermal conductivity graphite die (minimum .29 cal/cm/sec) has been bolted as per current standard art. The invention introduces a high conductivity gas such as Helium or Hydrogen or mixtures thereof, or carrier gases with significant concentrations of Helium and/or Hydrogen, between ~s the copper plates and graphite plates of the assembly. The high conductivity gas replaces atmospheric OZ/N2 in the copper/graphite interface, thereby improving the cooling action.
The cast material is surface milled and then rolled down zo to thinner gages. Heat treatments are imposed in the course of rolling to assure 1) maximum solution of alloying elements, and 2) precipitation of the dissolved alloying elements. The precipitate provides strength and resistance to stress relaxation.
a Less cold rolling is required to achieve the same tensile strength as Sn concentration (solid solution content) of the alloy increases. Less cold rolling permits more subsequent forming operations.
After heat treatment, the material is for some so applications further rolled to attain increased strength, and may or may not be stress relieved thermally and/or mechanically at finish.
In a further embodiment of the invention, improved solutioning of the solute is obtained by heat treating at 3s elevated temperatures at the cast stage, or at intermediate stages.
The process stages in accordance with the instant invention can include the following protocols:
SUBSTITUTE SHEET (RULE 26) One embodiment (for those mills so equipped) Cast Mill Homogenize (= rapid heat up/homogenize/quench). The s homogenization assures maximum solutioning of alloying elements. The quench assures maximum solution is retained. Temperature attained is 800-950°C.
Roll Precipitate anneal at 375-550°C.
~a Roll to finish Relief anneal for various tensile and yield strength conditions.
Another embodiment (for those mills so equipped) ~s Cast Mill Roll to intermediate gage Homogenize anneal Roll zo Precipitation anneal Roll to finish Relief anneal Another embodiment (for maximum strength at the expense a of some conductivity) Cast Mill Homogenize Roll so Rapid anneal with quench (may need multiple "anneal with quench" steps in process to reach light gages) Roll Mill hardening anneal 3s Another embodiment Cast Mill Roll to intermediate gage _ 7 _ SUBSTITUTE SHEET (RULE 26) Homogenize Roll Rapid anneal with quench (may need multiple "anneal with quench" steps in process to reach light gages) s Roll Alternatively, a rapid cool can replace quenching in the above-described casting practice.
The invention overcomes problems previously plaguing the ~o art wherein hot rolling technologies did not permit P to be used at levels as instantly claimed. Also the instant invention provides an alloy that can contain if desired, a wide range of Sn content, for example, greater than 7% Sn, (including 8-11% Sn in several embodiments) with excellent as working properties and product characteristics. Although below 8% Sn content is preferred for greater electrical conductivity desired in some applications, higher levels of Sn will provide greater strength desired in other applications.
In contrast, many applications will demand that the Sn content zo be 8% by weight or less, for example, 7%, 5%, and possibly approaching 3%. For some applications, a 1% Sn content may prove advantageous due to its high electrical conductivity and moderate strength. Alloys with Sn content below 1% will have lower potential strength levels and will not achieve the zs contact forces required in some more demanding spring contact applications.
P levels of 0.01-0.20 may prove particularly advantageous in many applications.
Ni and Si in the phosphor bronze according to the so invention allow improved strengths and will increase the alloy's resistance to stress relaxation at elevated temperatures where the alloy may be used.
The instant invention provides a metal alloy comprising by weight:
3s Sn 1.0-11.0%
Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%
Roll Precipitate anneal at 375-550°C.
~a Roll to finish Relief anneal for various tensile and yield strength conditions.
Another embodiment (for those mills so equipped) ~s Cast Mill Roll to intermediate gage Homogenize anneal Roll zo Precipitation anneal Roll to finish Relief anneal Another embodiment (for maximum strength at the expense a of some conductivity) Cast Mill Homogenize Roll so Rapid anneal with quench (may need multiple "anneal with quench" steps in process to reach light gages) Roll Mill hardening anneal 3s Another embodiment Cast Mill Roll to intermediate gage _ 7 _ SUBSTITUTE SHEET (RULE 26) Homogenize Roll Rapid anneal with quench (may need multiple "anneal with quench" steps in process to reach light gages) s Roll Alternatively, a rapid cool can replace quenching in the above-described casting practice.
The invention overcomes problems previously plaguing the ~o art wherein hot rolling technologies did not permit P to be used at levels as instantly claimed. Also the instant invention provides an alloy that can contain if desired, a wide range of Sn content, for example, greater than 7% Sn, (including 8-11% Sn in several embodiments) with excellent as working properties and product characteristics. Although below 8% Sn content is preferred for greater electrical conductivity desired in some applications, higher levels of Sn will provide greater strength desired in other applications.
In contrast, many applications will demand that the Sn content zo be 8% by weight or less, for example, 7%, 5%, and possibly approaching 3%. For some applications, a 1% Sn content may prove advantageous due to its high electrical conductivity and moderate strength. Alloys with Sn content below 1% will have lower potential strength levels and will not achieve the zs contact forces required in some more demanding spring contact applications.
P levels of 0.01-0.20 may prove particularly advantageous in many applications.
Ni and Si in the phosphor bronze according to the so invention allow improved strengths and will increase the alloy's resistance to stress relaxation at elevated temperatures where the alloy may be used.
The instant invention provides a metal alloy comprising by weight:
3s Sn 1.0-11.0%
Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%
SUBSTITUTE SHEET (RULE 26) Cu comprises the balance. Preferred embodiments of this invention may be limited to preferred subranges of various components, e.g., Sn content of below 8%, 1.0 to 1.5%, 2.1 to 2.7%, 4.7-5.3%, 1-7%, 7-11%, 7-8% or 7-9%, etc. Similarly, s other constituents such as P may be preferably limited to, for example, O.OI-0.2%, 0.01 to 0.06%, 0.05-0.18 or 0.2, etc. Si content can be 0 .22-0 .30% or 0 .4-0 . 5% . Ni content can be 1.3-1.7%, 2.5-3.0%, or 1.0-3.0%, etc.
Of course, the inventors contemplate that a small amount io of impurities that are not economically avoided will be present.
In other preferred embodiments of the invention, this alloy consists essentially of, by weight:
Sn 1.0-11.0% .
~s Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%, or smaller preferred ranges of each element, with the balance being Cu.
In a more preferred embodiment, the inventive alloy zo consists essentially of:
Sn 1.0-7.0%
Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.2%, with the balance being Cu. Again, zs smaller specific subranges are contemplated as applications dictate.
In yet other preferred embodiments of the invention, the alloy consists of, by weight:
Sn 7..0-11.0%
3o Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%, or especially, Sn 1.0-7.0%
Ni 1.0-3.0%
3s Si 0.2-1.0%
P 0.02-0.2%, in each case with the balance being Cu.
_ g SUBSTITUTE SHEET (RULE 26) W O 99/131 i 7 PCT/US98/17196 Based on preliminary analysis, the alloys according to the instantly claimed invention will demonstrate improved properties, for example, conductivity and tensile strength, over those alloys known in the art. Devices incorporating the s alloy will be more economical to produce and maintain and will demonstrate improved durability. Table 1 shows a comparison of exemplary alloys according to the invention, with several standard phosphor bronze alloys.
~o EXAMPLE
In one embodiment of the instant invention, an alloy designated alloy MHP101 was cast with the chemistry as follows:
Cu 95.67%, Sn 2.46%, P .057%, Ni 1.50%, Si .28% together ~s with unavoidable impurities.
The material was processed to .0070" thick and had mechanical properties as follows in the bare conditions unless otherwise stated:
- Tensile strength 91.9 ksi ~o - Yield strength Q.2 84.4 ksi - Elongation on 2" 13.9%
- Grain size .OlOmm - Conductivity 31.1% I.A.C.S.
- Good way bend (180deg) Flat at .690" wide, bare zs - Bad way bend (180deg) Radius .006" at .690" wide, bare Flat at .690" wide, tinned 40 microinches per side - Bad way bend (180deg) Flat at .020" wide, bare.
- Modulus of Elasticity 20 psi X 106, tension ~o - Density .323 lbs/cu inch at 68°F
The softening behavior is shown in Figure 1 compared with data of C51100 alloy (4% Sn Phosphor Bronze) and C52100 (8% Sn Phosphor Bronze). The time at temperature was one hour.
The stress relaxation behavior is shown in Figure 2 3s compared with C51100 alloy. The test stress was 80% of initial stress, and the initial stress in the test sample was 88ksi. The test temperature was 150°C.
SUBSTITUTE SHEET (RULE 26) WO 99/13117 PCT/US9$/17196 Expected electronic application guide data for MHP101 and other alloys according to the instant invention compared to similar UNS designated alloys are shown in Table 1.
SUBSTITUTE SHEET (RULE 26) ELECTRONIC APPLICATIONS ALLOY GUIDE
Alloy Ch~sistry ConductivityTensile Streacth (Nomniasl%) (% IACS) fRBI) /a/~
Hard Spring *MHP 2 Cu, 1.5 Sn, 1.5 40 70/483 85/586 Ni, 0.30 Si, 0.2 P min** min max *MHP 5 Cu, 2.4 Sn, 0.5 35 70/483 85/586 Ni, 0.10 Si, 0.2 P min min max *MHP 105 Cu, 5.0 Sn, 1.5 13 82/565 100/690 Ni, 0.3 Si, 0.2 P max C 51000 Cu, 5 Sn, 0.2 P 15 76-91/ 95-110/
*MHP 101 Cu, 2.4 Sn, 1.5 30 75/517 90/620 Ni, 0.3 Si, 0.2 P max C 51100 Cu, 4.2 Sn, 0.2 20 72-87/ 91-105/
P
C 51900 Cu, 6 Sn, 0.2 P 14 BO-96/ 99-114/
*MHP 108 Cu, 7.5 Sn, 1.5 10 90/620 110/758 Ni, 0.3 Si, 0.2 P max C 52100 Cu, 8 Sn, 0.2 P 13 85-100/ 105-119/
*MFIP 109 Cu, 7.5 Sn, 2.75 9 95/655 110/758 Ni, 0.45 Si. 0.2 P
max *MHP 100 Cu, 1.5 Ni, 1.25 40 70/483 85/586 Sn, 0.3 Si, 0.2 P
max C50500 Cu. 1.3 Sn, 0.35 48 59/407 70/483 P
max *MHP 4 Cu, 7.5 Sn, 0.5 12 85/586 105/724 Ni, 0.10 Si, 0.2 P min ~n max ~.e y.,~e~artt e.. oQ
- a~cw ~a~.~rv1 ......._......~..-.... ..._ ._-r----.~ r__r ** min = minimum °MHP~~ is a trademark of The Miller Company, the assignee of the invention of the subject patent application.
SUBSTITUTE SHEET (RULE 26) WO 99/13117 PCT/US9$/17196 The data collected for MHP101 confirm that alloy formulations of the instant invention provide resistance to stress relaxation at higher temperatures than the current offering to standard Phosphor Bronze alloys such as the C51100 s used in the comparison. In addition, strengths equal to higher tin-containing Phosphor Bronzes can be achieved with increased electrical conductivity.
The alloy MHP101, an example of the alloys of the instant invention, is thus shown to have excellent formability ~o properties.
It also has a higher modulus of elasticity which offers the connector designer a material with increased contact forces for a given deflection.
The invention also provides the above described alloy for ~s use as a casting material.
The invention also includes embodiments for certain applications that may demand smaller ranges of constituents, e.g., 0.02-0.2% P, than described above. All subranges within the above-described ranges are contemplated as part of the ~o invention.
Sn over 7%, for example, nominal Sn content of 8%, 9%, or 10% will add strength to the alloy. The alloy will also have better formability at a given tensile strength.
The invention especially includes embodiments where the ~s alloy displays properties of solid solution hardening, and precipitation hardening, and dispersion hardening.
Another aspect of the invention is a phosphor bronze casting. The product resulting from the processing of the casting is useful as a material for electrical lead conductor ~o applications. Such applications include those relating to integrated circuits and those encountered in the automotive industry such as engine compartment circuitry.
SUBSTITUTE SHEET (RULE 26)
Of course, the inventors contemplate that a small amount io of impurities that are not economically avoided will be present.
In other preferred embodiments of the invention, this alloy consists essentially of, by weight:
Sn 1.0-11.0% .
~s Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%, or smaller preferred ranges of each element, with the balance being Cu.
In a more preferred embodiment, the inventive alloy zo consists essentially of:
Sn 1.0-7.0%
Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.2%, with the balance being Cu. Again, zs smaller specific subranges are contemplated as applications dictate.
In yet other preferred embodiments of the invention, the alloy consists of, by weight:
Sn 7..0-11.0%
3o Ni 0.4-3.0%
Si 0.1-1.0%
P 0.01-0.35%, or especially, Sn 1.0-7.0%
Ni 1.0-3.0%
3s Si 0.2-1.0%
P 0.02-0.2%, in each case with the balance being Cu.
_ g SUBSTITUTE SHEET (RULE 26) W O 99/131 i 7 PCT/US98/17196 Based on preliminary analysis, the alloys according to the instantly claimed invention will demonstrate improved properties, for example, conductivity and tensile strength, over those alloys known in the art. Devices incorporating the s alloy will be more economical to produce and maintain and will demonstrate improved durability. Table 1 shows a comparison of exemplary alloys according to the invention, with several standard phosphor bronze alloys.
~o EXAMPLE
In one embodiment of the instant invention, an alloy designated alloy MHP101 was cast with the chemistry as follows:
Cu 95.67%, Sn 2.46%, P .057%, Ni 1.50%, Si .28% together ~s with unavoidable impurities.
The material was processed to .0070" thick and had mechanical properties as follows in the bare conditions unless otherwise stated:
- Tensile strength 91.9 ksi ~o - Yield strength Q.2 84.4 ksi - Elongation on 2" 13.9%
- Grain size .OlOmm - Conductivity 31.1% I.A.C.S.
- Good way bend (180deg) Flat at .690" wide, bare zs - Bad way bend (180deg) Radius .006" at .690" wide, bare Flat at .690" wide, tinned 40 microinches per side - Bad way bend (180deg) Flat at .020" wide, bare.
- Modulus of Elasticity 20 psi X 106, tension ~o - Density .323 lbs/cu inch at 68°F
The softening behavior is shown in Figure 1 compared with data of C51100 alloy (4% Sn Phosphor Bronze) and C52100 (8% Sn Phosphor Bronze). The time at temperature was one hour.
The stress relaxation behavior is shown in Figure 2 3s compared with C51100 alloy. The test stress was 80% of initial stress, and the initial stress in the test sample was 88ksi. The test temperature was 150°C.
SUBSTITUTE SHEET (RULE 26) WO 99/13117 PCT/US9$/17196 Expected electronic application guide data for MHP101 and other alloys according to the instant invention compared to similar UNS designated alloys are shown in Table 1.
SUBSTITUTE SHEET (RULE 26) ELECTRONIC APPLICATIONS ALLOY GUIDE
Alloy Ch~sistry ConductivityTensile Streacth (Nomniasl%) (% IACS) fRBI) /a/~
Hard Spring *MHP 2 Cu, 1.5 Sn, 1.5 40 70/483 85/586 Ni, 0.30 Si, 0.2 P min** min max *MHP 5 Cu, 2.4 Sn, 0.5 35 70/483 85/586 Ni, 0.10 Si, 0.2 P min min max *MHP 105 Cu, 5.0 Sn, 1.5 13 82/565 100/690 Ni, 0.3 Si, 0.2 P max C 51000 Cu, 5 Sn, 0.2 P 15 76-91/ 95-110/
*MHP 101 Cu, 2.4 Sn, 1.5 30 75/517 90/620 Ni, 0.3 Si, 0.2 P max C 51100 Cu, 4.2 Sn, 0.2 20 72-87/ 91-105/
P
C 51900 Cu, 6 Sn, 0.2 P 14 BO-96/ 99-114/
*MHP 108 Cu, 7.5 Sn, 1.5 10 90/620 110/758 Ni, 0.3 Si, 0.2 P max C 52100 Cu, 8 Sn, 0.2 P 13 85-100/ 105-119/
*MFIP 109 Cu, 7.5 Sn, 2.75 9 95/655 110/758 Ni, 0.45 Si. 0.2 P
max *MHP 100 Cu, 1.5 Ni, 1.25 40 70/483 85/586 Sn, 0.3 Si, 0.2 P
max C50500 Cu. 1.3 Sn, 0.35 48 59/407 70/483 P
max *MHP 4 Cu, 7.5 Sn, 0.5 12 85/586 105/724 Ni, 0.10 Si, 0.2 P min ~n max ~.e y.,~e~artt e.. oQ
- a~cw ~a~.~rv1 ......._......~..-.... ..._ ._-r----.~ r__r ** min = minimum °MHP~~ is a trademark of The Miller Company, the assignee of the invention of the subject patent application.
SUBSTITUTE SHEET (RULE 26) WO 99/13117 PCT/US9$/17196 The data collected for MHP101 confirm that alloy formulations of the instant invention provide resistance to stress relaxation at higher temperatures than the current offering to standard Phosphor Bronze alloys such as the C51100 s used in the comparison. In addition, strengths equal to higher tin-containing Phosphor Bronzes can be achieved with increased electrical conductivity.
The alloy MHP101, an example of the alloys of the instant invention, is thus shown to have excellent formability ~o properties.
It also has a higher modulus of elasticity which offers the connector designer a material with increased contact forces for a given deflection.
The invention also provides the above described alloy for ~s use as a casting material.
The invention also includes embodiments for certain applications that may demand smaller ranges of constituents, e.g., 0.02-0.2% P, than described above. All subranges within the above-described ranges are contemplated as part of the ~o invention.
Sn over 7%, for example, nominal Sn content of 8%, 9%, or 10% will add strength to the alloy. The alloy will also have better formability at a given tensile strength.
The invention especially includes embodiments where the ~s alloy displays properties of solid solution hardening, and precipitation hardening, and dispersion hardening.
Another aspect of the invention is a phosphor bronze casting. The product resulting from the processing of the casting is useful as a material for electrical lead conductor ~o applications. Such applications include those relating to integrated circuits and those encountered in the automotive industry such as engine compartment circuitry.
SUBSTITUTE SHEET (RULE 26)
Claims (20)
1. A phosphor bronze alloy consisting essentially of 0.9 to 3.0 wt% Ni, 0.1 to 1.0 wt% Si, 0.01 to 0.06 wt% P, 1.0 to 11.0 wt% Sn and the remainder being substantially Cu.
2. The alloy of claim 1 wherein the Ni content is 1.0 to 3.0 wt%.
3. The alloy of claim 1 wherein the Sn content is below 8 wt%.
4. The alloy of claim 1 wherein the Si content is 0.22-0.30 wt%.
5. The alloy of claim 1 wherein the Si content is 0.4-0.5 wt%.
6. The alloy of claim 1 wherein the Sn content is 1-7 wt%.
7. The alloy of claim 1 wherein the Sn content is 1.0-3.5 wt%.
8. The alloy of claim 1 wherein the Sn content is 2.1-2.7 wt%.
9. The alloy of claim 1 wherein the Sn content is 4.7-5.3 wt%.
10. The alloy of claim 1 wherein the Sn content is 7-11 wt%.
11. The alloy of claim 1 wherein the Sn content is 7-8 wt%.
12. The alloy of claim 1 wherein the P content is 0.05-0.06 wt%.
13. The alloy of claim 1 wherein the Ni content is 1.3-1.7 wt%.
14. The alloy of claim 1 wherein the Ni content is 2.5-3.0 wt%.
15. The alloy of claim 1 wherein the Ni content is 1.3-1.7 wt%, the Si content is 0.22-0.30 wt%, the P content is 0.01-0.06 wt%.
16. The alloy of claim 15 wherein the Sn content is 1.0-1.5 wt%, 2.1-2.7 wt%, 4.7-5.3 wt% or 7.0-8,0 wt%.
17. The alloy of claim 1 wherein the Ni content is 2.5-3.0 wt%, the Si content is 0.4-0.5 wt%, the P content is 0.01-0.06 wt% and the Sn content is 7.0-8.0 wt%.
18. The alloy of claim 1 consisting essentially of 1.5 wt% Ni, 0.28 wt% Si, 0,057 wt% P, 2.46 wt% Sn and the remainder being substantially Cu.
19. A phosphor bronze casting of the alloy of claim 1.
20. The alloy of claim 1 wherein the Sn content is 1.25 wt% nominal to 11.0 wt%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US5777997P | 1997-09-05 | 1997-09-05 | |
| US60/057,779 | 1997-09-05 | ||
| PCT/US1998/017196 WO1999013117A1 (en) | 1997-09-05 | 1998-08-21 | Copper based alloy featuring precipitation hardening and solid-solution hardening |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2303164A1 true CA2303164A1 (en) | 1999-03-18 |
Family
ID=22012718
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002303164A Abandoned CA2303164A1 (en) | 1997-09-05 | 1998-08-21 | Copper based alloy featuring precipitation hardening and solid-solution hardening |
Country Status (12)
| Country | Link |
|---|---|
| EP (1) | EP1021575B1 (en) |
| JP (1) | JP2001515960A (en) |
| KR (1) | KR20010023699A (en) |
| CN (1) | CN1097095C (en) |
| AR (1) | AR017044A1 (en) |
| AT (1) | ATE240413T1 (en) |
| AU (1) | AU9108398A (en) |
| BR (1) | BR9811448A (en) |
| CA (1) | CA2303164A1 (en) |
| DE (1) | DE69814657T2 (en) |
| TW (1) | TW364019B (en) |
| WO (1) | WO1999013117A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1329541C (en) * | 2004-04-16 | 2007-08-01 | 日矿金属株式会社 | High strength high conductive copper alloy |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7163753B2 (en) | 2002-04-15 | 2007-01-16 | Sumitomo Wiring Systems, Ltd. | Arc-resistant terminal, arc-resistant terminal couple and connector or the like for automobile |
| EP2426225B1 (en) * | 2006-05-26 | 2015-12-02 | Kabushiki Kaisha Kobe Seiko Sho | Copper alloy with high strength, high electrical conductivity, and excellent bendability |
| WO2009098810A1 (en) * | 2008-02-08 | 2009-08-13 | Mitsui Mining & Smelting Co., Ltd. | Process for producing precipitation-hardened copper alloy strip |
| CN102149833B (en) * | 2008-09-10 | 2013-07-17 | 大丰工业株式会社 | Sliding component consisting of Pb-free Cu-Bi type sintered material |
| CN106435250A (en) * | 2009-04-08 | 2017-02-22 | 瑞士金属-Ums瑞士金属加工有限公司 | Machinable copper base alloy and production method thereof |
| WO2020160682A1 (en) * | 2019-02-07 | 2020-08-13 | Equispheres Inc. | Alloys with a low density of precipitates for use in applications that include remelting processes, and preparation process thereof |
| KR102107585B1 (en) * | 2019-11-22 | 2020-05-07 | 주식회사 풍산 | Copper alloy material with excellent wear resistance and method for producing same |
| CN110923505B (en) * | 2019-12-31 | 2021-11-02 | 内蒙古工业大学 | Cu-Ni-Mn alloy and preparation method and application thereof |
| CN113249612A (en) * | 2021-04-21 | 2021-08-13 | 铁岭富兴铜业有限公司 | Novel contact copper alloy and preparation method thereof |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SU219368A1 (en) * | 1966-07-16 | 1968-05-30 | Припой Пайки Меди | |
| JPS5727051A (en) * | 1980-07-25 | 1982-02-13 | Nippon Telegr & Teleph Corp <Ntt> | Copper nickel tin alloy for integrated circuit conductor and its manufacture |
| JPS61143564A (en) * | 1984-12-13 | 1986-07-01 | Nippon Mining Co Ltd | Manufacture of high strength and highly conductive copper base alloy |
| JPH02122039A (en) * | 1988-10-31 | 1990-05-09 | Nippon Mining Co Ltd | High strength and high conductivity copper alloy having excellent adhesion of oxidized film |
| JPH02197543A (en) * | 1989-01-26 | 1990-08-06 | Furukawa Electric Co Ltd:The | Copper alloy for connecting apparatus |
| JPH0776397B2 (en) * | 1989-07-25 | 1995-08-16 | 三菱伸銅株式会社 | Cu alloy electrical equipment connector |
| JP2780584B2 (en) * | 1992-11-13 | 1998-07-30 | 三菱伸銅株式会社 | Cu alloy for electrical and electronic parts with excellent hot workability and punching workability |
-
1998
- 1998-08-21 AU AU91083/98A patent/AU9108398A/en not_active Abandoned
- 1998-08-21 KR KR1020007002353A patent/KR20010023699A/en not_active Application Discontinuation
- 1998-08-21 DE DE69814657T patent/DE69814657T2/en not_active Expired - Fee Related
- 1998-08-21 WO PCT/US1998/017196 patent/WO1999013117A1/en not_active Application Discontinuation
- 1998-08-21 AT AT98943252T patent/ATE240413T1/en not_active IP Right Cessation
- 1998-08-21 JP JP2000510901A patent/JP2001515960A/en not_active Withdrawn
- 1998-08-21 CA CA002303164A patent/CA2303164A1/en not_active Abandoned
- 1998-08-21 CN CN98810040A patent/CN1097095C/en not_active Expired - Fee Related
- 1998-08-21 EP EP98943252A patent/EP1021575B1/en not_active Expired - Lifetime
- 1998-08-21 BR BR9811448-4A patent/BR9811448A/en not_active Application Discontinuation
- 1998-08-27 TW TW087114229A patent/TW364019B/en active
- 1998-09-01 AR ARP980104367A patent/AR017044A1/en unknown
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1329541C (en) * | 2004-04-16 | 2007-08-01 | 日矿金属株式会社 | High strength high conductive copper alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| AU9108398A (en) | 1999-03-29 |
| WO1999013117A1 (en) | 1999-03-18 |
| ATE240413T1 (en) | 2003-05-15 |
| TW364019B (en) | 1999-07-11 |
| DE69814657T2 (en) | 2004-03-25 |
| CN1097095C (en) | 2002-12-25 |
| DE69814657D1 (en) | 2003-06-18 |
| BR9811448A (en) | 2000-08-22 |
| CN1275171A (en) | 2000-11-29 |
| KR20010023699A (en) | 2001-03-26 |
| AR017044A1 (en) | 2001-08-22 |
| EP1021575A1 (en) | 2000-07-26 |
| JP2001515960A (en) | 2001-09-25 |
| EP1021575B1 (en) | 2003-05-14 |
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