Rapidly solidifying Pb-free Sn-Ag-Cu-Al or Sn-Cu-Al solder

Abstract

A solder alloy includes Sn, optional Ag, Cu, and Al wherein the solder alloy composition together with the solder alloy superheat temperature and rapid cooling rate from the superheat temperature are controlled to provide a dispersion of fine hard CuAl intermetallic particles in an as-solidified solder alloy microstructure wherein the particles are retained even after multiple solder reflow cycles often used in modern electronic assembly procedures to provide a particle strengthening to the solder joint microstructure as well as exert a grain refining effect on the solder joint microstructure, providing a strong, impact- and thermal aging-resistant solder joint that has beneficial microstructural features and is substantially devoid of Ag.sub.3Sn blades.

Claims

1. A solder comprising an alloy comprising aluminum, copper, optionally silver, and tin with copper present in an amount of about 0.7 to about 3.5 weight %, with aluminum present in an amount of 0.10 to 0.25 weight %, with silver optionally present in an amount of about 3 to about 4 weight %, and with the balance of the solder alloy consisting essentially of tin, said solder including, before solder reflow, a dispersion of Cu.sub.33Al.sub.17 intermetallic particles in a solder alloy matrix whose largest particle dimension, averaged, is about 0.1 micron to about 0.5 micron.

2. The solder of claim 1 in the form of a solder ball before solder reflow.

3. The solder of claim 1 in the form of a solder ribbon or foil before solder reflow.

4. The solder of claim 1 wherein the alloy consists essentially of about 3 to about 4 weight % Ag, about 0.7 to about 1.7 weight % Cu, and about 0.10 to about 0.25 weight % Al, and balance consisting essentially of Sn.

5. The solder of claim 1 wherein the alloy also intentionally comprises about 3 to about 4 weight % Ag.

6. A solder comprising a SnCuAl alloy consisting essentially of about 3.2 minus y weight % Cu, y weight % Al, and balance consisting essentially of Sn wherein y is about 0.15 to about 0.25 weight %, said solder including, before solder reflow, a dispersion of Cu.sub.33Al.sub.17 intermetallic particles in a solder alloy matrix whose largest particle dimension, averaged, is about 0.1 micron to about 0.5 micron.

Description

DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 is a graph illustrating the effect of cooling rate (from the superheat temperature of 1200 C.) on average maximum and minimum particle sizes of Cu.sub.33Al.sub.17 phase particles in the as-solidified matrix of two similar SnCuAl solder alloys (Sn-1.25Cu-0.20Al and Sn-3.0Cu-0.40Al, in wt. %). The data from the 5 slowest cooling rates were produced from Sn-1.25Cu-0.20Al samples that were subject to DSC measurements using a Pegasus, heat flux, DSC 404C by Netzsch. Approximately 100 mg of the alloy wire was used for each DSC run and a linear heating rate of 10 C./min (0.17 C./s) was used to bring the sample up to 1200 C. A hold time of 10 min at 1200 C. was used and each sample was cooled to room temperature using linear cooling rates of 0.017, 0.17, 0.33, 0.83, 1.65 (C/s). The data for 110.sup.3 C/s cooling rate was from the same alloy sample that was sealed in a quartz tube, in an argon atmosphere, and held at 1200 C., for 60 min during melting from elemental constituents (with periodic agitation) before being quenched in a water bath. The solder ingot was drawn into a 1.7 mm dia. wire for microstructural analysis. The data point for 110.sup.5 C/s cooling rate was from a chill cast ingot sample of Sn-3.0Cu-0.4Al that was melted and held in a quartz tube in an argon atmosphere at 1200 C. for several seconds during melting. Then, Ar gas over-pressure ejected the alloy through a pre-made (0.8 mm dia.) orifice onto a Cu chill wheel that was rotating at 5 m/s.

(2) FIG. 2 illustrates a copper wheel melt spinning apparatus to produce the melt spun ribbon of Example 1.

(3) FIG. 3a (low magnitude) and FIG. 3b (higher magnitude) contain SEM photomicrographs in backscattered image mode of a representative as-solidified microstructure of the particular Sn-3.0Cu-0.4Al melt spun (at 5 m/sec) showing the dispersion of Cu.sub.33Al.sub.17 phase particles (see arrow for example) in the as-rapidly solidified solder alloy matrix with 0.2 m average particle diameter in this field of view.

(4) FIG. 4 is an optical photomicrograph of a representative as-solidified microstructure of a solder joint on a Cu substrate (Cu substrate is in the top portion) made from the Sn-3.0Cu-0.4Al melt spun ribbon (at 5 m/sec) showing (at this lower magnification) the interfacial Cu.sub.6Sn.sub.5 intermetallic phase attached to the substrate and an array of pro-eutectic Cu.sub.6Sn.sub.5 phase that is thought to be associated with Cu.sub.33Al.sub.17 phase particles with 0.2 m average particle diameter.

DESCRIPTION OF THE INVENTION

(5) For purposes of illustration, the present invention is described in connection with the rapid solidification of a Sn-optional AgCuAl solder alloy of the type described in copending U.S. patent application Ser. No. 13/066,748 filed Apr. 22, 2011, the teachings of which are incorporated herein by reference, although the invention can be practiced with other SnCuAl solder alloys with or without Ag or other alloying elements in a manner to impart the aforementioned beneficial properties thereto.

(6) The Sn-optional AgCuAl solder alloys of copending patent application Ser. No. 13/066,748 are alloyed with aluminum to reduce the unusually high undercooling of SAC (SnAgCu) solder joints described above, where there can be difficulty in nucleating Sn solidification as a pro-eutectic phase, especially during slow cooling, such as existing for ball grid array (BGA) joints. As mentioned above, increased undercooling of the solder joints can promote formation of undesirable pro-eutectic intermetallic phases, specifically Ag.sub.3Sn blades, that tend to coarsen radically, leading to embrittlement of as-solidified solder joints for impact stresses. To this end, the present invention provides a solder alloy comprising Sn, Ag, Cu, and Al having an alloy composition controlled to provide a strong, impact- and thermal aging-resistant solder joint having beneficial microstructural features described below and substantially devoid of Ag.sub.3Sn blades. The solder alloy has a relatively low liquidus temperature and a narrow liquid-solid mushy zone for solderability.

(7) In one embodiment, such solder alloys consist essentially of about 3 to about 4 weight % Ag, about 0.7 to about 1.7 weight % Cu, about 0.01 to about 0.25 weight % Al, and balance consisting essentially of Sn. The solder alloy preferably exhibits a relatively low solidus temperature of about 217 C.1 C. and narrow liquid-solid mushy zone with a liquidus temperature not exceeding about 5 C., often less than 3 C., above the solidus temperature. Other alloying elements may be present in the solder alloy that do not substantially affect the melting temperature thereof.

(8) A preferred solder alloy consists essentially of about 3.4 to about 3.6 weight % Ag, about 0.8 to about 1.1 weight % Cu, about 0.03 to about 0.20 weight % Al, and balance consisting essentially of Sn.

(9) A still more preferred solder alloy consists essentially of about 3.45 to about 3.55 weight % Ag, about 0.9 to about 1.0 weight % Cu, about 0.04 to about 0.10 weight % Al, and balance consisting essentially of Sn.

(10) A still more preferred solder alloy consists essentially of about 3.45 to about 3.55 weight % Ag, about 0.75 to about 1.0 weight % Cu, about 0.04 to about 0.15 weight % Al, and balance consisting essentially of Sn.

(11) In another embodiment, such Pb-free solder alloy consists essentially of about 3 to about 4 weight % Ag, 0.95-y weight % Cu, and y weight % Al and balance consisting essentially of Sn wherein y is about 0.01 to about 0.25 weight %.

(12) Another embodiment of the invention provides a still more preferred solder alloy consists essentially of about 3.45 to about 3.55 weight % Ag, about 0.80 to about 1.0 weight % Cu, about 0.10 to about 0.20 weight % Al, and balance consisting essentially of Sn, especially for BGA applications that involve thermal-mechanical fatigue environments, like avionics.

(13) Such solder alloys also can be modified in composition to eliminate the Ag component for situations where higher solder melting alloys can be tolerated. Such modified solder alloy embodiments are described below and comprise a solder alloy consisting essentially of about 3.20-y weight % Cu, y weight % Al, and balance consisting essentially of Sn wherein y is about 0.15 to about 0.25 weight %.

(14) An embodiment of the present invention provides a method of making a rapidly solidified solder alloy comprising Sn, Cu and Al, wherein the alloy composition together with the solder alloy superheat temperature and rapid cooling rate from the superheat temperature are controlled to provide a dispersion of hard CuAl intermetallic particles in the as-solidified solder alloy microstructure and wherein the particles are retained even after multiple solder reflow cycles often used in modern electronic assembly procedures to provide a particle strengthening to the solder joint microstructure as well as exert a grain refining effect on the solder joint microstructure. An impact- and thermal aging-resistant solder joint having beneficial microstructural features and completely devoid of Ag.sub.3Sn blades (due to the omission of Ag in the alloy composition) can be produced using the rapidly solidified solder product.

(15) The rapidly solidified solder alloy product can be rapidly solidified in the form of thin ribbon, foil, flakes, fine wire, atomized spheres (typically for BGA assemblies), atomized particles/powder (typically for solder paste), or other forms.

(16) For purposes of illustration and not limitation, a method embodiment of the invention involves heating the Sn-optional AgCuAl solder alloy to a superheat temperature above the liquidus temperature of the solder alloy high enough, preferably at least 50 degrees C. above the liquidus temperature, to produce a homogeneous (single phase) melt. For purposes of illustration and not limitation, for solder alloy comprising Sn-3.0Cu-0.4Al (in weight %), the liquidus temperature has been determined to be about 1080 degrees C. such that a preferred superheat temperature is about 50 degrees or more above that liquidus temperature.

(17) The superheat temperature and time at that temperature are controlled to produce a homogenous, single phase melt of the solder alloy that can be subsequently rapidly solidified. For the above-mentioned solder alloy comprising Sn-3.0Cu-0.4Al, the superheat temperature and time at that temperature can be 1200 degrees C. for 30 minutes to produce a homogenous, single phase melt of the solder alloy. The melting and heating of the solder alloy to the superheat temperature can be conducted in an atmosphere including, but not limited to, ultra-high purity (99.99%) Ar gas.

(18) Typically, elemental alloying elements of the solder alloy are placed in a crucible, such as an alumina crucible, or other melting vessel, and melted and heated by any suitable heating method/apparatus, such as by induction heating using one or more induction coils, electrical resistance heating using heating elements, gas firing, and the like to achieve the superheat temperature. Alternatively, the alloying elements can be placed in the crucible in the form of prealloyed crucible charge components (e.g. a binary SnCu alloy, CuAl alloy, etc.) and then melted and heated to the desired superheat temperature. The Examples set forth below provide exemplary melting and heating parameters for a solder alloy comprising Sn-3.0Cu-0.4Al, for purposes of further illustration and not limitation.

(19) The superheated melt then is rapidly solidified at a cooling rate high enough to produce an as-solidified solder alloy having a dispersion of CuAl intermetallic particles, such as for example relatively hard Cu.sub.33Al.sub.17 particles, in a rapidly solidified solder alloy matrix. The Cu.sub.33Al.sub.17 particles are hard (e.g. 30-50 GPa hardness by a nano-indention hardness test) compared to the matrix hardness (0.2 GPa hardness by same test). The CuAl particles preferably have an average maximum particle size (major dimension such as diameter) of 1 micron or less, preferably from about 0.1 to less than 1 micron average maximum particle size, even more preferably from about 0.1 to about 0.5 micron average maximum particle size. The rapidly solidified solder alloy matrix can have a cellular or dendritic solidification microstructure with a micron-scale grain size.

(20) Such CuAl intermetallic particles form first upon rapid cooling through the particular phase field (e.g. the Cu.sub.33Al.sub.17 phase field) and subsequently nucleate Cu.sub.6Sn.sub.5 phase (apparent from microstructural evidence), which in turn nucleates the Sn dendritic phase. Such CuAl intermetallic particles are retained in the solder joint microstructure even after multiple solder reflow cycles often used in modern electronic assembly procedures to provide a particle strengthening effect to the solder joint as well as exert a grain refining effect on the solder joint. An impact- and thermal aging-resistant solder joint having beneficial microstructural features and completely devoid of Ag.sub.3Sn blades (from an absence of Ag in the alloy) can be produced using the rapidly solidified solder.

(21) Rapid cooling rates greater than 110.sup.3 degrees C./second, preferably at least about 110.sup.4 to about 110.sup.6 degrees C./second and greater preferably are used to this end. For example, referring to FIG. 1, the dependence of particle size on cooling rate is shown for 2 SnCuAl solder alloys comprising Sn-1.25Cu-0.20Al and Sn-3.0Cu-0.4Al (weight %). The former alloy was used for generating samples (in a DSC) from linear cooling rates of 0.017, 0.17, 0.33, 0.83, 1.65 (C/s) and for generating a (water quenched) chill cast alloy sample at an uncontrolled cooling rate of about 110.sup.3 C/second that were subject to quantitative metallography to determine the size ranges of Cu.sub.33Al.sub.17 particles that are shown in FIG. 1, all of which are far greater than 1 micron. The later alloy (Sn-3.0Cu-0.4Al) was melt spun at a wheel speed of 5 m/second (about 110.sup.5 degrees C./second) and was shown to produce dispersed Cu.sub.33Al.sub.17 intermetallic particles having a size of less than 1 micron. A cooling rate of 110.sup.6 degrees C./second or greater is predicted by FIG. 1 to produce dispersed Cu.sub.33Al.sub.17 intermetallic particles having a size of about 0.1 to about 0.5 micron. To achieve the cooling rate of 110.sup.5 degrees C./second, the solder alloy was melt spun using the apparatus shown in FIG. 2 and parameters of Example 1 pursuant to the invention.

(22) In FIG. 1, the effects on the desired intermetallic phase size at the rapid cooling rates of about 110.sup.4 to about 110.sup.6 degrees C./second and greater employed in practice of the present invention are contrasted to the effects at the much slower cooling rate of about 110.sup.3 degrees C./second that is typically associated with water quenching as described in connection with FIG. 1. It is apparent from the figure that the effect of the water quenching cooling rate (1-2 orders of magnitude slower than the preferred cooling rates) on the size of the desired intermetallic particles is very significant, increasing the size of the particles by at least 5 times. The effects on the desired intermetallic particle size of the much slower cooling rates, below of about 210.sup.0 degrees C./second and less, are also shown for purposes of comparison where the minimum average diameter of about 25 microns is far above the 1 micron average maximum diameter produced at the lower end of the cooling rate range of this invention. The values from these much slower cooling rates are precisely labeled, since these samples were cooled at a controlled linear rate in an automated DSC system.

(23) In practicing the present invention, a melt spinning process can be used to achieve cooling rates of 110.sup.4 degrees C./second and above using a rotatable copper wheel 10, FIG. 2, cooled by mass quenching (using the heat capacity of the heavy copper wheel) and rotated at different wheel speeds to vary the cooling rate achievable. For most typical experimental melt spinning (small total melt quantities, about 5-10 g) higher wheel speeds provide higher cooling rates at a given (starting) wheel temperature and solder alloy superheat temperature and discharge rate on the wheel. For larger melt quantities, active wheel cooling is typically employed. In our experiments, the molten solder alloy at the superheat temperature is discharged onto the rotating copper wheel 10 at a controlled rate and wheel speed to form rapidly solidified solder alloy ribbon or foil typically having a thickness in the range of 25 to 50 microns for purposes of illustration and not limitation. The parameters of melt spinning, such as wheel speed (e.g., very high speeds, above 30 m/second) or wheel surface finish (with scribed line patterns) also can be controlled to fragment and rapidly solidify the melt in a manner to form rapidly solidified solder alloy flake particles having flake particle sizes within a controllable size distribution. FIG. 2 illustrates a copper wheel 10 to produce the melt spun ribbon of Example 1.

(24) The parameters of melt spinning can be chosen to achieve and vary the desired cooling rate to form the desired CuAl intermetallic particles in the rapidly solidified solder alloy matrix, see FIG. 1. The Examples set forth below provide exemplary melt spinning parameters for a solder alloy comprising wheel speeds of 5-25 m/second with a smooth wheel surface for purposes of further illustration but not limitation.

(25) The present invention can also be practiced by gas atomization processes to achieve typical cooling rates of 110.sup.5 degrees C./second, typically ranging up to 110.sup.6 degrees C./second and above, to produce fine solder alloy powder particles within controlled powder particle size distributions (e.g. particle size range of 1 to 100 microns) wherein the solder alloy melt stream at the superheat temperature is atomized by gas jets or a gas curtain discharged from a gas atomizing nozzle so that the melt is atomized into small particles which are rapidly cooled at the desired preferred cooling rate of at least 110.sup.4 degrees C. or greater. For purposes of illustration and not limitation, high pressure gas atomization processes and apparatus for practicing the invention are described in U.S. Pat. Nos. 5,125,574; 5,228,620; and 6,142,382, the teachings of which are incorporated herein by reference to this end, although other atomization apparatus and processes can be used.

(26) The parameters of gas atomization can be chosen to achieve and vary the desired cooling rate to form the desired CuAl intermetallic particles in the rapidly solidified solder alloy matrix, see FIG. 1. For example, such gas atomization parameters as gas manifold (upstream supply) pressure that controls the gas velocity in the melt disintegration zone and gas mass flow rate relative to melt flow rate that promotes atomization process uniformity can be varied to this end.

(27) Practice of the present invention is not limited to melt spinning processes and gas atomization processes since other rapid solidification processes can be employed including, but not limited to, melt drip/quench atomization to produce small spheres (about 500 microns or less) and melt surface extraction to produce fine wire or filaments, to achieve a cooling rate high enough to produce an as-solidified solder alloy having a dispersion of CuAl intermetallic particles, such as for example hard Cu.sub.33Al.sub.17 particles, in a rapidly solidified solder alloy matrix wherein the CuAl particles preferably have an average maximum particle size (major dimension such as diameter) of 1 micron or less, preferably from about 0.1 to less than 1 micron average maximum particle size, even more preferably from about 0.1 to about 0.5 micron average maximum particle size.

(28) The beneficial properties of rapidly solidified solder alloy embodiments of the invention provide several advantages for solder assembly of electronic circuits and electrical systems. In the type of solder paste reflow and ball grid array (BGA) applications that are envisioned for use with the SnAgCuAl solder, every single degree of reduced reflow temperature is a precious advantage for reducing damage to temperature sensitive electronic components and to the circuit board material, itself. In fact, a reason that SAC solder came into broad use as a Pb-free alternative to SnPb solder is that the minimum reflow temperature of SAC solder for most applications, about 240 C., is just below the threshold for significant damage of one of the most popular circuit board materials, a fiberglass/epoxy composite, i.e., FR-4. Thus, the rapidly solidified SnAgCuAl solder alloy pursuant to the present invention should permit a more comfortable margin for preventing thermal damage of most components and common circuit board materials while producing an impact- and thermal aging-resistant solder joint having beneficial microstructural features discussed above and substantially devoid of Ag.sub.3Sn blades.

(29) The rapidly solidified SnAgCuAl solder alloy of the type discussed above produces a solder joint having a microstructure that comprises tin dendrites, interdendritic multi-phase ternary eutectic (between the tin dendrites), and pro-eutectic Cu.sub.6Sn.sub.5 particles adjacent and/or within the tin dendrites and that is devoid of Ag.sub.3Sn blades as described in copending U.S. patent application Ser. No. 13/066,748 filed Apr. 22, 2011, the teachings of which are incorporated herein by reference. The as-solidified solder joint microstructure includes an interfacial layer comprising Cu.sub.6Sn.sub.5 and preferably an adjacent metastable, intermediate Al-containing rejected solute region as a zone of intermediate hardness between the hard, brittle interfacial layer and the softer tin matrix of the solder microstructure to provide a beneficial hardness gradient therebetween. The interfacial layer resides between the copper substrate and the solder of the solder joint.

(30) This microstructure is achievable at the relatively slow cooling rates employed for solder paste reflow and BGA solder processing. The controlled dispersion of hard CuAl intermetallic particles in the as-solidified solder alloy microstructure of the solder alloy are retained even after multiple solder reflow cycles often used in modern electronic assembly procedures to provide a particle strengthening effect to the solder joint microstructure as well as to exert a grain refining effect on the solder joint microstructure. For example, the Cu.sub.33Al.sub.17 intermetallic particles are retained primarily in either the tin matrix or Cu.sub.6Sn.sub.5 phases of the solidified solder joint. An impact- and thermal aging-resistant solder joint having beneficial microstructural features and substantially devoid of Ag.sub.3Sn blades thereby can be produced using the rapidly solidified solder product.

(31) The solder joint is formed by the rapidly solidified solder alloy being melted and solidified on an electrical wiring board and/or about copper electrical conductors in illustrative embodiments of the invention by various conventional soldering processes including, but not limited to, solder paste reflow and BGA attachments. A thermally-aged solder joint (e.g. aged for 1000 hours at 150 C.) will have an interfacial layer thickness that is about the same as the thickness as the interfacial layer thickness in the as-solidified solder joint condition (e.g. no more than 30% greater in thickness). As a result, the solder joint is resistant to thermal aging-induced embrittlement.

EXAMPLE

(32) The following Example is offered to illustrate practice of the invention is more detail without limiting the scope of the invention.

Example 1

(33) The data point for 110.sup.5 C/s cooling rate in FIG. 1 was from a chill cast ingot sample of Sn-3.0Cu-0.4Al (weight %) that was held and melted (using an induction heating coil 14, FIG. 2) in a quartz tube (melting vessel) 12 in an argon atmosphere at 1200 C. for several seconds during melting. The induction coil was a water-cooled copper tube operating at a frequency greater than 10 kHz. Surface tension effects of the liquid melt prevent any leaking before the solder alloy melt is forced out of the tube orifice by sudden application of the Ar over-pressure of about 20 psi applied to the top of the solder alloy melt to eject the solder alloy melt through a pre-made tube orifice 12a (0.8 mm diameter tube hole) onto a Cu chill wheel 10 that was rotating at 5 m/second. In this same manner, melt spun ribbon of the same solder alloy was made by ejecting the melt onto a copper wheel that was spinning a 25 m/second. The ribbons from the 5 m/second and the 25 m/second runs were mounted in epoxy and polished to a mirror finish for metallographic examination. At this time, microstructural analysis, including a quantitative analysis of the average size of the intermetallic CuAl particles, has been performed only on the 5 m/second ribbon sample on an FEI field emission SEM, since the spatial resolution limits are well within the resulting particle sizes that were imaged. The results of this analysis are shown in FIG. 1 for the cooling rate of about 110.sup.5 C/second, which is estimated to be about the cooling rate for this wheel speed. The 5 m/second ribbon sample was also used to produce a prototype solder joint with a fluxed copper substrate by reflowing to a peak temperature of 250 C and cooling at a rate of 0.17 C/second, typical of BGA solder joints. An optical photomicrograph of this solder joint is included in FIG. 4 and shows (at lower magnification) the interfacial Cu.sub.6Sn.sub.5 intermetallic phase attached to the Cu substrate and an array of darker pro-eutectic Cu.sub.6Sn.sub.5 phase regions that are thought to be associated with Cu.sub.33Al.sub.17 phase particles with 0.2 m average particle diameter.

(34) While the invention has been described in terms of specific embodiments thereof, those skilled in the art will appreciate that modifications and changes can be made thereto within the scope of the appended claims.