EP1021575B1

EP1021575B1 - Copper based alloy featuring precipitation hardening and solid-solution hardening

Info

Publication number: EP1021575B1
Application number: EP98943252A
Authority: EP
Inventors: David H. Mandle; Daniel D. Farquharson
Original assignee: Miller Co
Current assignee: DUERER CORPORATION
Priority date: 1997-09-05
Filing date: 1998-08-21
Publication date: 2003-05-14
Anticipated expiration: 2018-08-21
Also published as: DE69814657T2; TW364019B; WO1999013117A1; JP2001515960A; AR017044A1; BR9811448A; ATE240413T1; EP1021575A1; CA2303164A1; DE69814657D1; CN1275171A; KR20010023699A; AU9108398A; CN1097095C

Description

This invention relates to a copper alloy, particularly a 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.

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 0.0001-1% boron (B), 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 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 obtainable according to the instant invention.

Another comparison alloy is disclosed by Kubosonc 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 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.

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 where Ni₂Si 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, 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; 0.1-0.8% P; 0.6-1.0% Si; optionally, 0.03 to 0.5% Zn; and Cu. Ni₅P₂ 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.

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; 1.0-6.0% 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 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 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.

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; 0.01-0.05% P; 0.0-0.35% manganese (Mn) or Si; and Cu. This alloy features 60 kg/mm² tensile strength and elongation of 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 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; less than 1% B; less than 2% P; less than 3% Mn; and Cu. 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 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 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 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), 0.25% Mn, 0.05% As, 0.05% S, 0.01% P, 0.55% Al, 0.25% Si and 57.0% minimum Cu.

The document JP-A-02 197 543 discloses a copper alloy for a connecting device comprising Ni : 1.5-6.0 wt% ; Si : 0.1-3.0 wt% ; P: 0.12-1.0 wt%; Sn : 1.2-4.2 wt%; O₂ : 20 ppm or less ; S: 10 ppm or less; balance Cu and unavoidable impurities.

In the electronics industry, phosphor bronzes with required strength and formability are known that can be used 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 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 superior durability especially at higher temperatures at an economic price.

BRIEF DESCRIPTION OF THE DRAWINGS

Figure 1 depicts softening behavior data curves for alloy 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

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 1.0% by weight; a P content of from 0.01-0.06% by weight; a Sn content of 3.0-11.0% by weight ; balance copper with unavoidable impurities. Sn 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 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, phosphorous and copper, while precipitation hardening resides in nickel silicide and nickel phosphides precipitated in the matrix.

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 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 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 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 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 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 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. 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.

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 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 a high thermal conductivity graphite die (minimum .29 cal/cm/sec) has been bolted as per current standard art. A high conductivity gas such as Helium or Hydrogen or mixtures thereof is introduced, or carrier gases with significant concentrations of Helium and/or Hydrogen, between the copper plates and graphite plates of the assembly. The high conductivity gas replaces atmospheric O₂/N; in the copper/graphite interface, thereby improving the cooling action.

The cast material is surface milled and then rolled down 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.

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 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 elevated temperatures at the cast stage, or at intermediate stages.

The process stages can include the following protocols:

One embodiment (for those mills so equipped)

Cast

Mill

Homogenize (= rapid heat up/homogenize/quench). The 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.

Roll to finish

Relief anneal for various tensile and yield strength conditions.

Another embodiment (for those mills so equipped)

Cast

Mill

Roll to intermediate gage

Homogenize anneal

Roll

Precipitation anneal

Roll to finish

Relief anneal

Another embodiment (for maximum strength at the expense of some conductivity)

Cast

Mill

Homogenize

Roll

Rapid anneal with quench (may need multiple "anneal with quench" steps in process to reach light gages)

Roll

Mill hardening anneal

Another embodiment

Cast

Mill

Roll to intermediate gage

Homogenize

Roll

Alternatively, a rapid cool can replace quenching in the above-described casting practice.

The process overcomes problems previously plaguing the 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 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 be 8% by weight or less, for example, 7%, 5%, and possibly approaching 3%. Alloys with Sn content below 3% will have lower potential strength levels and will not achieve the 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 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 consisting of by weight:

Sn	3.0-11.0%
Ni	0.4-3.0%
Si	0.1-1.0%
P	0.01-0.06%

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%, 4.7-5.3%, 7-11%, 7-8% or 7-9%, 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 of impurities that are not economically avoided will be present.

This alloy of the invention consists of, by weight:

Sn	3.0-11.0%
Ni	0.4-3.0%
Si	0.1-1.0%
P	0.01-0.06%,

or smaller preferred ranges of each element, with the balance being Cu.

In a more preferred embodiment, the inventive alloy consists essentially of:

Sn	3.0-7.0%
Ni	0.4-3.0%
Si	0.1-1.0%
P	0.01-0.06%,

with the balance being Cu. Again, smaller specific subranges are contemplated as applications dictate.

In yet other preferred embodiments of the invention, the alloy consists of, by weight:

Sn	3.0-11.0%
Ni	0.4-3.0%
Si	0.1-1.0%
P	0.01-0.06%, or especially,
Sn	3.0-7.0%
Ni	1.0-3.0%
Si	0.2-1.0%
P	0.02-0.06%,

in each case with the balance being Cu.

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 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.

EXAMPLE

The examples not falling within the scope of invention are for comparison.

In one embodiment, 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 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 (1 ksi = 6.895 MPa)
Yield strength @.2 84.4 ksi
Elongation on 2" 13.9%
Grain size .010mm
Conductivity 31.1% I.A.C.S.
Good way bend (180deg) Flat at .690" wide, bare
Bad way bend (180deg) Radius .006" at .690" wide, bare
Flat at .690" wide, tinned 40
microinches per side (1 inch = 1" = 25.4mm)
Bad way bend (180deg) Flat at .020" wide, bare.
Modulus of Elasticity 20 psi X 10⁶, tension (1 psi = 6895 Pa)
Density .323 lbs/cu inch at 68°F (1lbs = 453.6 g) (°F = 1.8°C + 32)

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 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.

Expected electronic application guide data for MHP101 and other alloys compared to similar UNS designated alloys are shown in Table 1.

ELECTRONIC APPLICATIONS ALLOY GUIDE
Alloy	Chemistry (Nominal%)	Conductivity (% IACS)	Tensile Strength (KSI)/n/mm²
			Hard	Spring
MHP
2	Cu, 1.5 Sn, 1.5 Ni, 0.30 Si, 0.2 P max	40	70/483 min	85/586 min
MHP
5	Cu, 2.4 Sn, 0.5 Ni, 0.10 Si, 0.2 P max	35	70/483 min	85/586 min
MHP 105	Cu, 5.0 Sn, 1.5 Ni, 0.3 Si, 0.2 P max	13	82/565	100/690
C 51000	Cu, 5 Sn, 0.2 P	15	76-91/ 524-628	95-110/ 655-759
MHP 101	Cu, 2.4 Sn, 1.5 Ni, 0.3 Si, 0.2 P max	30	75/517	90/620
C 51100	Cu, 4.2 Sn, 0.2 P	20	72-87/ 496-600	91-105/ 628-724
C 51900	Cu, 6 Sn, 0.2 P	14	80-96/ 552-662	99-114/ 683-786
MHP 108	Cu, 7.5 Sn, 1.5 Ni, 0.3 Si, 0.2 P max	10	90/620	110/758
C 52100	Cu, 8 Sn, 0.2 P	13	85-100/ 586-690	105-119/ 724-821
MHP 109	Cu, 7.5 Sn, 2.75 Ni, 0.45 Si, 0.2 P max	9	95/655	110/758
MHP 100	Cu, 1.5 Ni, 1.25 Sn, 0.3 Si, 0.2 P max	40	70/483	85/586
C50500	Cu, 1.3 Sn, 0.35 P max	48	59/407	70/483
MHP 4	Cu, 7.5 Sn, 0.5 Ni, 0.10 Si, 0.2 P max	12	85/586 min	105/724 min

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 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 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 use as a casting material.

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 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 applications. Such applications include those relating to integrated circuits and those encountered in the automotive industry such as engine compartment circuitry.

Claims

A phosphor bronze alloy consisting of 0.4 to 3.0 wt% Ni, 0.1 to 1.0 wt% Si, 0.01 to 0.06 wt% P, 3.0 to 11.0 wt% Sn and the remainder being Cu with unavoidable impurities.
The alloy of claim 1 wherein the Ni content is 1.0 to 3.0 wt%.
The alloy of claim 1 wherein the Sn content is below 8 wt%.
The alloy of claim 1 wherein the Si content is 0.22-0.30 wt%.
The alloy of claim 1 wherein the Si content is 0.4-0.5 wt%.
The alloy or claim 1 wherein the Sn content is 4.7-5.3 wt%.
The alloy of claim 1 wherein the Sn content is 7-11 wt%.
The alloy of claim 1 wherein the Sn content is 7-8 wt%.
The alloy of claim 1 wherein the P content is 0.05-0.06 wt%.
The alloy of claim 1 wherein the Ni content is 1.3-1.7 wt%.
The alloy of claim 1 wherein the Ni content is 2.5-3.0 wt%.
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%.
The alloy of claim 12 wherein the Sn content is 4.7-5.3 wt% or 7.0-8.0 wt%.
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%.
A phosphor bronze casting of the alloy of claim 1.