The present invention relates to an alloy, in particular to a lead-free solder alloy.
A number of lead-free solder alloys are known, which provide non-toxic alternatives to the most widely used solder alloy—eutectic 37% Pb-63% Sn alloy. Examples of such lead-free alloys include the binary eutectic 58% Bi-42% Sn alloy (see, for example, U.S. Pat. No. 5,569,433 B) and the binary 40% Bi-60% Sn alloy (see, for example, U.S. Pat. No. 6,574,411 A). Such alloys exhibit a loss of ductility at high strain rates, which can be improved by the addition of up to 1% by weight silver (see, for example, U.S. Pat. No. 5,569,433 B). However, the impact energies exhibited by these alloys, measured using the Charpy Impact Test, are relatively low. Accordingly, there is a need to develop lead-free solder alloys which exhibit improved impact toughness.
Furthermore, in order for such lead-free alloys to be used in soldering methods such as wave and reflow soldering, the alloys must exhibit good wettability in relation to a variety of substrate materials such as copper, nickel and nickel phosphorus (“electroless nickel”). Such substrates may be coated to improve wetting, for example by using tin alloys, silver, gold or organic coatings (OSP). Good wetting also enhances the ability of the molten solder to flow into a capillary gap, and to climb up the walls of a through-plated hole in a printed wiring board, to thereby achieve good hole filling.
The present invention aims to solve at least some of the problems associated with the prior art, or to provide commercially acceptable alternatives thereto.
In a first aspect the present invention provides an alloy, preferably a lead-free solder alloy, comprising:
- from 35 to 59% wt Bi;
- from 0 to 1.0 wt % Ag;
- from 0 to 1.0% wt Au;
- from 0 to 1.0% wt Cr;
- from 0 to 2.0% wt In;
- from 0 to 1.0% wt P;
- from 0 to 1.0% wt Sb;
- from 0 to 1.0% wt Sc;
- from 0 to 1.0% wt Y;
- from 0 to 1.0% wt Zn;
- from 0 to 1.0% wt rare earth elements;
- one or more of:
- from greater than 0 to 1.0% wt Al;
- from 0.01 to 1.0% wt Ce;
- from greater than 0 to 1.0% wt Co;
- from greater than 0 to 1.0% wt Cu;
- from 0.001 to 1.0% wt Ge;
- from greater than 0 to 1.0% wt Mg;
- from greater than 0 to 1.0% wt Mn;
- from 0.01 to 1.0% wt Ni; and
- from greater than 0 to 1.0% wt Ti,
- and the balance Sn, together with any unavoidable impurities.
Surprisingly, it has been found that incorporation of small amounts of one or more of Ce, Ni and Ge results in the alloy exhibiting increased impact energy in comparison to the corresponding Sn—Bi base alloy or, if the alloy contains Ag, the corresponding Sn—Bi—Ag base alloy. This indicates improved strength and ductility of the alloy. Further advantages provided to the alloys by incorporation of these elements include improved wettability, increased thermal conductivity, increased yield strength and increased tensile strength.
In addition, the presence of Ni results in lowering of the Cu dissolution rate, improvements in the thermal fatigue properties, increased aging stability (in particular when combined with Cu) and refinement of the alloy's microstructure. The presence of Ge reduces oxidation and, when used as a solder alloy, results in lustrous joints. The presence of Al and/or Mg can increase oxidation resistance of the alloy and improves the wetting. The presence of Co results in higher toughness, lower Cu dissolution, higher tensile strength and a more refined microstructure (in particular when combined with Cu). When used as a solder alloy, the presence of Co results in lustrous joints and lower levels of dross formed on the top of an open tank of the solder. The presence of Cu in the alloy increases ductility, reduces the occurrence of copper leaching and increases resistance to thermal fatigue. These properties caused by the presence of Cu are particularly pronounced in the absence of Ag. In particular, substituting Ag for Cu in am SnBiAg base alloy results in particularly reduced Cu dissolution, particularly improved mechanical properties (in particular when combined with Co), particularly improved drop shock resistance (in particular when combined with Ni) and particularly improved creep rupture resistance. The presence of Mn and/or Ti results in improved drop shock performance of the alloy. The presence of Ti results in increased thermal conductivity and increased thermal fatigue life.
Definitions
The term “solder alloy” used herein refers to a fusible metal alloy with a melting point in the range of from 90-400 degrees C.
The “Charpy impact test” referred to herein, also known as the Charpy v-notch test, is a standardized high strain-rate test which determines the amount of energy absorbed by a material during fracture. This absorbed energy is a measure of a given material's toughness and acts as a tool to study temperature-dependent brittle-ductile transition. Further details regarding this test can be found in Charpy Impact Test: Factors and Variables, J. M. Holt, ASTM STP 1072, the contents of which is hereby incorporated by reference.
The term “wettability” used herein refers to the degree to which solder spread on a wettable surface. Wettability is determined by surface tension of the liquid solder and its ability to react with the wettable surface. Wetting can also be described in terms of the contact angle of the molten, and subsequently frozen solder alloy on a substrate, with lower contact angles being favoured over high contact angles.
The term “wave soldering” used herein refers to the large-scale soldering process by which electronic components are soldered to a printed circuit board (PCB) to form an electrical assembly.
The term “reflow soldering” used herein refers to the process where solder paste is printed or dispensed, or a solder perform is placed on the surface of a printed circuit board, components are placed in or near the deposited solder, and the assembly is heated to a temperature above the liquidus of the solder alloy.
The term “rare earth element” used herein refers to an element selected from Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb and Lu.
The present invention will now be further described. In the following passages different aspects of the invention are defined in more detail. Each aspect so defined may be combined with any other aspect or aspects unless clearly indicated to the contrary. In particular, any feature indicated as being preferred or advantageous may be combined with any other feature or features indicated as being preferred or advantageous.
The alloy may comprise from 35 to 55% wt Bi, preferably from 35 to 50% wt Bi, more preferably from 35 to 45% wt Bi and even more preferably about 40% wt Bi. Advantageously, such Bi contents result in the alloy exhibiting increased ductility compared to alloys with higher levels of Bi. Alternatively, the alloy may comprise from 57 to 59% wt Bi, preferably about 58% wt Bi. Advantageously, such Bi contents reduce the melting point of the alloy compared to alloys containing lower levels of Bi.
Preferably the alloy comprises from 0.01 to 0.5% wt Ce, more preferably from 0.05 to 0.1% wt Ce.
Preferably the alloy comprises from 0.01 to 0.5% wt Ni, more preferably from 0.025 to 0.1% wt Ni, even more preferably from 0.025 to 0.05% wt Ni, most preferably about 0.03% wt Ni.
Preferably the alloy comprises from 0.001 to 0.1% wt Ge, more preferably from 0.001 to 0.01% wt Ge.
Preferably the alloy comprises from 0.01 to 0.8% wt Ag, more preferably from 0.3 to 0.7% wt Ag, even more preferably 0.4 to 0.6% wt Ag, still even more preferably about 0.5% wt Ag. The presence of Ag increases the ductility of the alloy and also reduces surface oxidation.
Preferably, the alloy comprises one or more of:
- from 0 to 0.7% wt Al, more preferably from 0.003 to 0.6 Al, even more preferably from 0.003 to 0.5% wt Al;
- from 0.001 to 1.0% wt Au, more preferably from 0.003 to 0.7 Au, even more preferably from 0.005 to 0.5% wt Au;
- from 0 to 0.5% wt Co, more preferably from 0.003 to 0.5% wt Co, even more preferably from 0.01 to 0.07% wt Co, still even more preferably from 0.02 to 0.04% wt Co, still even more preferably about 0.03% wt Co;
- from 0.001 to 1.0% wt Cr, more preferably from 0.003 to 0.7 Cr, even more preferably from 0.005 to 0.5% wt Cr;
- from 0 to 0.5% wt Cu, more preferably from 0.05 to 0.4% wt Cu, even more preferably from 0.1 to 0.3% wt Cu, still even more preferably about 0.2% wt Cu;
- from 0 to 1.5% wt In, more preferably from 0.1 to 1.0% wt In, even more preferably from 0.2 to 1.0% wt In, still even more preferably about 1.0% wt In;
- from 0 to 0.2% wt Mg, more preferably from 0.05 to 0.18% wt Mg, even more preferably from 0.05 to 0.1% wt Mg;
- from 0 to 0.2% wt Mn, more preferably from 0.05 to 0.18% wt Mn, even more preferably from 0.05 to 0.1% wt Mn;
- from 0 to 0.01% wt P, more preferably from 0.001 to 0.01% wt P, even more preferably from 0.005 to 0.01% wt P;
- from 0.001 to 1.0% wt Sb, more preferably from 0.003 to 0.7 Sb, even more preferably from 0.005 to 0.5% wt Sb;
- from 0.001 to 1.0% wt Sc, more preferably from 0.003 to 0.7 Sc, even more preferably from 0.005 to 0.5% wt Sc;
- from 0 to 0.2% wt Ti, more preferably from 0.05 to 0.18% wt Ti, even more preferably from 0.05 to 0.1% wt Ti;
- from 0.001 to 1.0% wt Y, more preferably from 0.003 to 0.7 Y, even more preferably from 0.005 to 0.5% wt Y;
- from 0.001 to 1.0% wt Zn, more preferably from 0.003 to 0.7 Zn, even more preferably from 0.005 to 0.5% wt Zn; and
- from 0.001 to 1.0% wt rare earth elements, more preferably from 0.003 to 0.7 rare earth elements, even more preferably from 0.005 to 0.5% wt rare earth elements;
The presence of In increases the ductility of the alloy and reduces surface oxidation. The presence of Au in the alloy increases the ductility of the alloy. The presence of Zn in the alloy refines and redistributes the Bi rich phase. An interfacial IMC layer forms, which prevents a Bi-rich segregation layer forming. The presence of P reduces oxidation of the alloy. The presence of Sb improves the ductility of the alloy.
Preferably, the alloy comprises only one of Al and Ni.
Preferably the alloy comprises Cu and one or more of Co and Ni. A particularly preferred alloy comprises:
- from 57 to 59% wt Bi;
- from 0.1 to 0.3% wt Cu;
one or more of:
- from 0.02 to 0.04% wt Co; and
- from 0.02 to 0.04% wt Ni,
- and the balance Sn, together with any unavoidable impurities.
Preferably, the alloy comprises:
- about 58% wt Bi;
- about 0.2% wt Cu
one or more of:
- about 0.03% wt Co; and
- about 0.03% wt Ni,
- and the balance Sn, together with any unavoidable impurities. The above-described alloys containing Cu and one or more of Ni and Co may optionally include one or more of the optional elements described above.
The above-described alloys containing Cu and Ni and/or Co advantageously exhibit superior mechanical properties to the corresponding SnBi base alloy. For example, these alloys exhibit approximately 9% higher tensile strengths, approximately 11% higher elastic moduli, approximately 8.4% higher toughness (based on Charpy Impact Resistance Test), approximately 8% higher creep elongation and approximately 11% longer creep rupture time (80° C., 2.3 kg load) in comparison to the SnBi base alloy.
The above-described alloys containing Cu and Ni and/or Co advantageously exhibit superior thermal fatigue resistance to the SnBi base alloy. For example, when carrying out Accelerated Thermal Cycling (conditions: TC3/NTC-C, −40° C. to 125° C., 10 minute dwell) no cracks are observed for chip components up to 1000 cycles. In addition, no cracks are observed for Ball Grid Array (BGA) components for up to 500-800 cycles in comparison to the cracks observed on the SnBi base alloy after only 200 cycles.
The above-described alloys containing Cu and Ni and/or Co advantageously exhibit improved drop shock resistance, in particular an increase of approximately 40% in the number of drops in a standard drop shock resistance test compared to the SnBi base alloy.
The above-described alloys containing Cu and Ni and/or Co advantageously exhibit, in comparison to the SnBi base alloy, approximately 4% higher thermal and electrical conductivities and approximately 30 times lower Cu dissolution. Accordingly, these alloys are particularly suitable for photovoltaic ribbon applications. The alloys are eutectics with melting points of approximately 138° C. and, in contrast to the SnBi base alloy, do not exhibit ageing degradation. The alloys also exhibit improved, more refined microstructures, which presumably contribute to their improved mechanical properties.
The above described properties of the alloys containing Cu and Ni and/or Co are also exhibited when the alloys or alloy powders are produced on the 400 kg and 50 kg scales, respectively, indicating the industrial viability of manufacturing these alloys on an industrial scale.
The alloy may be a solder alloy.
Preferably the alloy is lead-free or essentially lead-free. Lead-free solder alloys are advantageous due to the toxic nature of lead.
The alloys of the present invention may be in the form of a bar, a stick, a solid or flux cored wire, a foil or strip, a film, a preform, or a powder or paste (powder plus flux blend), or solder spheres for use in ball grid array joints, or a pre-formed solder piece or a reflowed or solidified solder joint, or pre-applied on any solderable material such as a copper ribbon for photovoltaic applications.
Preferably the alloy exhibits an impact energy when measured using the Charpy Impact Test of at least 5% greater than that of the corresponding Sn—Bi base alloy or, if the alloy contains Ag, the corresponding Sn—Bi—Ag base alloy.
Preferably the impact energy is at least 8% greater, more preferably at least 10% greater, even more preferably at least 12% greater.
It will be appreciated that the alloys according to the present invention may contain unavoidable impurities, although, in total, these are unlikely to exceed 1 wt % of the composition. Preferably, the alloys contain unavoidable impurities in an amount of not more than 0.5 wt % of the composition, more preferably not more than 0.3 wt % of the composition, still more preferably not more than 0.1 wt % of the composition.
The alloys according to the present invention may consist essentially of the recited elements. It will therefore be appreciated that in addition to those elements which are mandatory (i.e. Sn, Bi and at least one of Ce, Ni, Ge, Ti, Mn, Mg, Al, Cu and Co) other non-specified elements may be present in the composition provided that the essential characteristics of the composition are not materially affected by their presence.
In a second aspect, the present invention provides an alloy comprising:
- from 41 to 43% wt Sn;
- one or more of:
- from 0 to 1.0 wt % Ag;
- from 0 to 1.0% wt Al;
- from 0 to 1.0% wt Au;
- from 0 to 1.0% wt Co;
- from 0 to 1.0% wt Cr;
- from 0 to 1.0% wt Cu;
- from 0 to 2.0% wt In;
- from 0 to 1.0% wt Mn;
- from 0 to 1.0% wt P;
- from 0 to 1.0% wt Sb;
- from 0 to 1.0% wt Sc;
- from 0 to 1.0% wt Ti;
- from 0 to 1.0% wt Y;
- from 0 to 1.0% wt Zn;
- from 0 to 1.0% wt rare earth elements;
- from 0.01 to 1.0% wt Ce;
- from 0.01 to 1.0% wt Ni; and
- from 0.001 to 1.0% wt Ge;
- and the balance Bi, together with any unavoidable impurities.
In a third aspect, the invention provides an alloy comprising:
- from 41 to 43% wt Sn;
- from 0 to 1.0 wt % Ag;
- one or more of:
- from 0 to 1.0% wt Al;
- from 0 to 1.0% wt Au;
- from 0 to 1.0% wt Co;
- from 0 to 1.0% wt Cr;
- from 0 to 1.0% wt Cu;
- from 0 to 2.0% wt In;
- from 0 to 1.0% wt Mn;
- from 0 to 1.0% wt P;
- from 0 to 1.0% wt Sb;
- from 0 to 1.0% wt Sc;
- from 0 to 1.0% wt Ti;
- from 0 to 1.0% wt Y;
- from 0 to 1.0% wt Zn;
- from 0 to 1.0% wt rare earth elements;
- from 0.01 to 1.0% wt Ce;
- from 0.01 to 1.0% wt Ni; and
- from 0.001 to 1.0% wt Ge;
- and the balance Bi, together with any unavoidable impurities.
In a fourth aspect, the present invention provides an alloy comprising:
- from 50 to 65% wt Sn;
- one or more of:
- from 0 to 1.0 wt % Ag;
- from 0 to 1.0% wt Al;
- from 0 to 1.0% wt Au;
- from 0 to 1.0% wt Co;
- from 0 to 1.0% wt Cr;
- from 0 to 1.0% wt Cu;
- from 0 to 2.0% wt In;
- from 0 to 1.0% wt Mn;
- from 0 to 1.0% wt P;
- from 0 to 1.0% wt Sb;
- from 0 to 1.0% wt Sc;
- from 0 to 1.0% wt Ti;
- from 0 to 1.0% wt Y;
- from 0 to 1.0% wt Zn;
- from 0 to 1.0% wt rare earth elements;
- from 0.01 to 1.0% wt Ce;
- from 0.01 to 1.0% wt Ni; and
- from 0.001 to 1.0% wt Ge;
- and the balance Bi, together with any unavoidable impurities.
In a fifth aspect, the present invention provides an alloy comprising:
- from 50 to 65% wt Sn;
- from 0 to 1.0 wt % Ag;
- one or more of:
- from 0 to 1.0% wt Al;
- from 0 to 1.0% wt Au;
- from 0 to 1.0% wt Co;
- from 0 to 1.0% wt Cr;
- from 0 to 1.0% wt Cu;
- from 0 to 2.0% wt In;
- from 0 to 1.0% wt Mn;
- from 0 to 1.0% wt P;
- from 0 to 1.0% wt Sb;
- from 0 to 1.0% wt Sc;
- from 0 to 1.0% wt Ti;
- from 0 to 1.0% wt Y;
- from 0 to 1.0% wt Zn;
- from 0 to 1.0% wt rare earth elements;
- from 0.01 to 1.0% wt Ce;
- from 0.01 to 1.0% wt Ni; and
- from 0.001 to 1.0% wt Ge;
- and the balance Bi, together with any unavoidable impurities.
In a sixth aspect, the present invention provides a soldered joint comprising an alloy selected from the first to fifth aspects.
In a seventh aspect, the present invention provides the use of an alloy of the first to fifth aspects in a soldering method. Such soldering methods include, but are not restricted to, wave soldering, Surface Mount Technology (SMT) soldering, die attach soldering, thermal interface soldering, hand soldering, laser and RF induction soldering, and rework soldering.
In an eighth aspect the present invention provides an alloy comprising:
- from 0 to 10% wt Ag;
- from 35 to 59% wt Bi; and
- one or more of:
- from 0.01 to 1.0% wt Ce;
- from 0.01 to 1.0% wt Ni; and
- from 0.001 to 1.0% wt Ge;
- from 0.001 to 1.0% wt Al;
The invention will now be described, by way of example only, with reference to the following drawings in which:
FIG. 1 is a plot showing the results of the Charpy Impact Test on three alloys according to the first aspect of the invention and a reference example;
FIG. 2 is a plot showing the results of the Charpy Impact Test on three alloys according to the first aspect of the invention and three reference examples;
FIG. 3 is a plot of linear spread in mm on a copper organic solderability preservative (OSP) of a number of alloys according to the present invention and a reference example.
FIG. 4 is a plot showing the results of the Bulk Shear Test for a number of alloys according to the present invention and a number of reference examples.
FIG. 5 is a plot showing the results of the Hardness Test for a number of alloys according to the present invention and a number of reference examples.
FIG. 6 is a plot of yield strengths of a number of alloys according to the present invention and a number of reference examples.
FIG. 7 is a plot of tensile strengths of a number of alloys according to the present invention and a number of reference examples.
FIG. 8 is a plot showing the results of the Bulk Shear Test for a number of alloys according to the present invention when incorporated onto a chip component and a number of reference examples.
FIG. 9 is a plot showing the results of the Lead Pull Test for a number of alloys according to the present invention when incorporated onto a Quad Flat Package (QFP) component and a number of reference examples.
FIG. 10 is a plot of thermal conductivities of a number of alloys according to the present invention and a number of reference examples.
FIGS. 11-13 show electron microscope images of the microstructures of Sn57.6Bi0.4Ag, Sn57.45Bi0.5Ag0.05Ni and Sn57.4Bi0.5Ag0.1Ce, respectively.
FIG. 14 shows the time for Cu dissolution of a number of alloys according to the present invention and a number of reference examples.
FIG. 15 shows the results of drop shock testing for a number of alloys according to the present invention and a reference example.
FIG. 16 shows the results of thermal fatigue testing for a number of alloys according to the present invention and a number of reference examples.
FIG. 17 shows the results of thermal fatigue testing for a number of alloys according to the present invention and a number of reference examples.
Referring to FIG. 1, the Charpy Impact Test was carried out (sample size 55×10×15 mm) on four alloys (from left to right): Sn57.5Bi0.5Ag, Sn57.4Bi0.5Ag0.1Ce, Sn57.495Bi0.5Ag0.005Ge and Sn57.45Bi0.5Ag0.05Ni. The results indicate that the presence of Ce, Ge and Ni results in the alloys exhibiting an increase in impact energy of from approximately 10 to 12% compared to the Sn57.5Bi0.5Ag base alloy.
Referring to FIG. 2, the Charpy Impact Test was carried out (sample size 55×10×10 mm) on six alloys (from left to right): Sn58Bi, Sn57.5Bi0.5Ag, Sn45Bi, Sn57.4Bi0.5Ag0.1Ce, Sn57.4555Bi0.5Ag0.005Ge and Sn57.45Bi0.5Ag0.05Ni. The results indicate that a reduction in the level of Bi and the addition of Ag, Ce, Ge and Ni improves the toughness of the alloys. Charpy Impact Tests carried out on the alloys Sn57.54Bi0.4Ag0.03Ni0005Mn, Sn57.75Bi0.2Cu0.03Ni, Sn57.7Bi0.2Cu0.03Co, Sn45Bi0.03Ni and Sn45Bi0.1Cu0.034Co indicated that each of these alloys exhibit an impact energy in excess of 225 kJ. Sn57.7Bi0.2Cu0.03Co exhibited an impact energy in excess of 230 kJ.
Referring to FIG. 3, linear spreads were determined for the alloys (from left to right): Sn57.6Bi0.4Ag, Sn57.5Bi0.5Ag0.005Ge, Sn57.5Bi0.5Ag0.05Ni and Sn57.5Bi0.5Ag0.05Ce. the results demonstrate that the alloys of the present invention exhibit improved wettability compared to their base Sn—Bi—Ag alloy. Similar results were obtained for the alloys Sn58Bi0.2Cu0.03Ni, Sn58Bi0.2Cu0.03Co and Sn58Bi0.4Ag0.03Ni, for both samples manufactured on the laboratory and 400 kg scales.
Referring to FIGS. 4-7, it is demonstrated that the alloys of the present invention exhibit increased shear strength, hardness, yield strength and tensile strength in comparison to their base Sn—Bi—Ag alloy. In FIG. 4, the bulk shear test results are shown for the following alloys (from left to right): Sn45Bi, Sn58Bi, Sn57.6Bi0.4Ag, Sn58Bi0.5Ag0.5Ce, Sn58Bi0.5Ag0.005Ge, Sn57.6Bi0.4Ag0.02Ti, Sn57.6Bi0.4Ag0.02Ti0.05Ni. Sn45Bi0.2Cu0.005Mn, Sn58Bi0.005Al, Sn58Bi0.005Mn and Sn57.75Bi0.2Cu0.05Ni. In FIG. 5, the hardness values are shown for the following alloys (from left to right): Sn58Bi, Sn58Bi0.4Ag0.02Ti, An58Bi0.4Ag0.02Ti0.05Ni, Sn58Bi0.005Al, Sn58Bi0.2Cu0.02Ni, Sn58Bi0.2Cu0.02Ni0.005Ge, Sn58Bi0.005Mn, Sn58Bi0.4Ag0.005Mn and Sn58Bi0.4Ag0.05Ni0.005Mn. In FIG. 6 the yield strength values are shown for the following alloys (from left to right) Sn57.5Bi0.5Ag, Sn45Bi, Sn57.5Bi0.5Ag0.05Ce, Sn57.5Bi0.5Ag0.005Ge, Sn57.5Bi0.5Ag0.05Ni and Sn57.5Bi0.5Ag0.05(Ce, Ni)0.005Ge. In FIG. 7 the tensile strengths are shown for the following alloys (from left to right) Sn57.5Bi0.5Ag, Sn45Bi, Sn57.5Bi0.5Ag0.05Ce, Sn57.5Bi0.5Ag0.005Ge, Sn57.5Bi0.5Ag0.05Ni and Sn57.5Bi0.5Ag0.05(Ce, Ni)0.005Ge.
Referring to FIG. 8, it is demonstrated that the improvement in shear strength is also exhibited by the alloys when incorporated onto a chip component. The results are shown for the following alloys (from left to right): Sn57.6Bi0.4Ag, Sn57.6Bi0.4Ag0.05Ni, Sn57.6Bi0.4Ag0.005Ge and Sn57.6Bi0.4Ag0.05Ce
Referring to FIG. 9, it is demonstrated that the when the alloys are incorporated onto QFP components, the force required to pull the lead from the chip after soldering increases in comparison to their base Sn—Bi—Ag alloy. In FIG. 9 the results are shown for the following alloys (from left to right) Sn57.6Bi0.4Ag, Sn57.6Bi0.4Ag0.05Ni, Sn57.6Bi0.4Ag0.005Ge and Sn57.6Bi0.4Ag0.05Ce.
Referring to FIG. 10, it is demonstrated that the alloys of the present invention exhibit improved thermal conductivity in comparison to their base Sn—Bi/Sn—Bi—Ag alloy. The results are shown for the alloys Sn58Bi (smaller squares), Sn57.5Bi0.5Ag (triangles), Sn57.5Bi0.5Ag0.05Ce (larger squares) and Sn57.5Bi0.5Ag0.05Ni (diamonds).
Referring to FIGS. 11-13, it is demonstrated that small additions of certain elements have the advantageous effect of refining the microstructure, leading to, for example, enhanced mechanical properties. Electron micrograph images of the alloys Sn57.8Bi0.2Cu0.03Ni and Sn57.8Bi0.2Cu0.03Co show microstructures which are still further refined.
Referring to FIG. 14, it is demonstrated that the alloys Sn58Bi0.2Cu0.06 and Sn58Bi0.2Cu0.03Co exhibit very low Cu dissolution. Accordingly, since these alloys also exhibit high electrical conductivity, they are particularly suitable for photovoltaic applications. The results in FIG. 14 are shown for the alloys (from left to right): Sn58Bi0.4Ag, Sn58Bi0.4Ag0.03Ni, Sn58Bi0.4Ag0.03Ti, Sn58Bi0.4Ag0.007Mn, Sn58Bi0.2Cu0.06Ni, Sn58Bi0.2Cu0.03Co, Sn45Bi, Sn45Bi0.1Cu, Sn45Bi0.02Ni and Sn45Bi0.1Cu0.06Co.
Referring to FIG. 15, drop shock test results are indicated for the alloys Sn58BiCu0.2Ni0.06 (circles, average number of drops to failure: 324.5), Sn58BiCu0.2Co0.03 (squares, average number of drops to failure 289.9), Sn58Bi0.04Ag (diamonds, average number of drops to failure 174.7) and Sn58Bi0.4Ag0.05Ni (triangles, average number of drops to failure 259.0). The drop shock test followed JEDEC standard JESD22-B111 (test conditions: 1500 Gs, 0.5 millisecond duration, half-sine pulse). Boards were populated with Ball Grid Array (BGA) components on all 15 available positions. The results indicate that the alloys of the present invention exhibit improved drop shock resistance compared to the Sn58Bi0.4Ag alloy.
Referring to FIG. 16, thermal fatigue testing was carried out on the alloys Sn58Bi (diamonds), Sn57.6Bi0.4Ag (filled triangles), Sn57.6Bi0.4Ag0.03Ni (hollow circles), Sn57.6Bi0.4Ag0.0033Ge (hollow triangles), Sn57.6Bi0.4Ag0.056Ce (squares) and Sn45Bi (crosses). The thermal cycling conditions corresponded to standard TC3/NTC-C (−40 to 125° C.; 10 minute dwell time). The alloys of the present invention exhibited very little variation in shear strength after 1500 cycles compared to those of the Sn58Bi and Sn45Bi alloys. In addition, no cracks were observed after 1500 cycles for any of the alloys of the present invention.
Referring to FIG. 17, thermal fatigue testing was carried out on the alloys Sn57.6Bi0.4Ag (diamonds, 3rd highest shear force after 1000 cycles), Sn58Bi (squares, 5th highest shear force after 1000 cycles), Sn57.6Bi0.2Cu0.03Ni (triangles, highest shear force after 1000 cycles), Sn57.6Bi0.2Cu0.03Co (dark circles, 2nd highest shear force after 1000 cycles), Sn57.6Bi0.4Ag0.03Ni (crosses, lowest shear force after 1000 cycles) and Sn57.1Bi0.9Ag (light circles, 4th highest shear force after 1000 cycles). The thermal cycling conditions were the same as those used for the testing shown in FIG. 16. 36 BGA84 boards were used for testing per alloy. Only 26 of the SnBi0.4Ag boards and 24 of the Sn58Bi boards survived 1000 cycles. In comparison, all 36 boards of Sn57.6Bi0.2Cu0.03Ni, Sn57.1Bi0.9Ag and Sn57.6Bi0.4Ag0.03Ni, and 35 board of Sn57.6Bi0.2Cu0.03Co, survived 1000 cycles.
The foregoing detailed description has been provided by way of explanation and illustration, and is not intended to limit the scope of the appended claims. Many variations in the presently preferred embodiments illustrated herein will be apparent to one of ordinary skill in the art, and remain within the scope of the appended claims and their equivalents.
Patent Application
20170304955
