Effect of Aging Treatment on Microstructural Evolution of Rapidly Solidified Eutectic Sn-Pb Alloy Powders

The microstructural stability of rapidly solidified eutectic Sn–Pb alloy solder powders was investigated through aging at room temperature (25 ◦C) and temperatures of 40 ◦C–120 ◦C. The coarsening behavior of the Pb-rich phase both at room and elevated temperatures was observed. The evident coarsening of the Pb-rich phase was detected upon storage after 40 days. At elevated temperatures, a similar sequence of Pb-rich phase coarsening was observed; however, it occurred substantially more quickly. Pb-rich coarsening rate kinetics at different temperatures were estimated using the Arrhenius equation. The apparent activation energy was 45.53 ± 4.23 KJ/mol, which indicates that grain boundary diffusion is a crucial mass transport mechanism controlling Pb-rich phase coarsening under annealing.


Introduction
Eutectic Sn-Pb is the most crucial solder alloy with excellent electrical conductivity, good wettability, acceptable plasticity and low melting point properties [1].In previous decades, it has been used as a joining material for the packaging and interconnection of electronic components and devices, and as solders for temperature-sensitive components, optoelectronics modules, printed circuit, plumbing and assembly of sheet metal parts [2][3][4].It has also played an important role in a number of other industrial applications, such as water piping, beverage cans, and automobile bodies [5][6][7].Chu et al. proposed a new technology for quenching Sn-Pb droplets, and a higher cooling rate was obtained using this method [8].Li et al. predicted the nucleation kinetics of Sn-Pb droplets through combining the nucleation temperature and droplet motion [9].The solidification behavior of Sn-Pb droplets was investigated based on the microstructure and solidification path [10].Melt atomization is a dominant technique and commercially used to yield metal and alloy powders, including electronic grade solder powders [11][12][13].Before preparing a solder paste by mixing solder powders with flux, storage or transport is generally necessary.During this period, microstructural coarsening of the solder powder is observed.However, few studies have investigated the microstructural evolution of rapidly solidified eutectic Sn-Pb alloy powders.
Reducing the free energy is the driving force behind coarsening for obtaining a more stable microstructure [14,15].Gan et al. reported the size effect of Sn-Pb microstructures on microdevices, and they indicated that stable microstructures are crucial in several applications [16].The effect of the two primary phases on Sn-Pb microstructures was studied using thermal analysis method [17].Zhao et al. investigated the effect of processing conditions on the particle formation of Sn-37 wt% Pb, and adequate clearance is essential based on the results [18].
Because a solder paste is affected by the quality of the powder, studying the microstructural evolution of rapidly solidified solder powders at room or elevated temperature is essential.However, little information presently exists on the morphology evolution of eutectic Sn-Pb alloy powders.Therefore, in this study, the microstructures and stability of eutectic Sn-Pb alloy powders generated through atomization were investigated.The microstructural evolution of eutectic Sn-Pb alloy powders at ambient and elevated temperature was studied.Moreover, the Pb-rich coarsening rate kinetics and diffusion mechanism in Sn-Pb alloy powders produced through atomization were discussed.

Experimental Procedure
A Sn-Pb eutectic solder (Sn-37 wt% Pb) used for atomization in this study was purchased from commercially Sn and Pb (purity of 99.99%).A master alloy was obtained through melting in an induction furnace.Atomization was performed in a centrifugal atomizer at a cooling rate of 103-105 • C/s under the protection of nitrogen atmosphere.Sn-Pb solder powders were obtained after the rapid solidification of alloy droplets.
An aging treatment was performed in air at room temperature for different numbers of days and at temperatures of 40 • C, 60 • C, 90 • C, and 120 • C.After rapid solidification, the powder samples were immediately placed in an oven.
Microstructures of Sn-Pb were prepared using the following metallographic procedure.The powders were encased in epoxy resin and then sectioned, polished, and etched for microstructure examination.The polished samples were etched using a solution of 5 vol.%HCl + 95 vol.%C 2 H 5 OH.The microstructures of both the powders and polished and etched specimens were examined through scanning electron microscopy (SEM).SEM micrographs were obtained in secondary-electron and backscattered-electron (BSE) modes.

Results and Discussion
The general features of the microstructure of Sn-Pb alloy solders can be understood from the Sn-Pb binary alloy phase diagram (Figure 1).With decreasing melt temperature, the first precipitated solids are lead primaries, which contained approximately 19 wt% of dissolved Sn.Moreover, undercooling is generally required to nucleate Sn, and the solidification of the primary eutectic matrix may occur at temperatures less than the equilibrium temperature of the eutectic Sn-Pb alloy (183 • C) [19].The solid solubility between Sn and Pb is limited, and Sn-rich and Pb-rich phases are separated.In general, a lamellar eutectic structure, which comprises alternating plates of Sn-rich and Pb-rich phases, appears through the slow solidification of binary alloys.
The solidified microstructure can be altered by changing the solidification rate or undercooling degree.With increasing melt undercooling, the lamellar eutectic structure may transform into an anomalous eutectic microstructure [20].During centrifugal atomization, the melt droplets are solidified at strong undercooling, and the formation of a lamellar structure is suppressed.The resulting microstructure is a mixture of fine Pb-rich and Sn-rich solid phases.Figure 2 presents an SEM micrograph of the centrifugally atomized eutectic Sn-Pb powders, which exhibit a fine structure immediately after solidification.Dark and light regions in the micrograph are Sn-rich and Pb-rich phases, respectively.The Pb-rich phase is finely dispersed in the Sn-rich matrix.

Effect of Aging on the Microstructure of Solder Powder
Figure 3 displays SEM images of the rapidly solidified eutectic Sn-Pb37 powder after aging at ambient temperature for different numbers of days.Even for aging at room temperature, coarsening of the microstructure is observed.A microstructure with an evident increase in the Pb-rich phase is observed after aging for 40 days.Moreover, some small particles are observed around the large particles in the Pb-rich-phase-coarsened microstructure.This observation indicates that the large Pbrich phase particles grow at the expense of other particles rather than through a continuous nucleation and growth process.Structures formed during atomization generally have high interfacial areas and nonequilibrium solute concentration, because of the rapid solidification that occurs.This behavior is observed because of the need to reduce the overall energy of the system by decreasing the interfacial area.Sufficient thermal energy is required to reduce the energy of the system through diffusion even at room temperature.
Figure 4 presents the cross-sectional microstructure of rapidly solidified Sn-Pb37 powder aged for different numbers of days.No microsegregation of the Pb-rich phase was detected during growth.This observation illustrates that the Pb-rich phase in Sn-Pb37 powder coarsened through atom diffusion, with Pb particles becoming fewer in number, more spherical, and much larger during room

Effect of Aging on the Microstructure of Solder Powder
Figure 3 displays SEM images of the rapidly solidified eutectic Sn-Pb37 powder after aging at ambient temperature for different numbers of days.Even for aging at room temperature, coarsening of the microstructure is observed.A microstructure with an evident increase in the Pb-rich phase is observed after aging for 40 days.Moreover, some small particles are observed around the large particles in the Pb-rich-phase-coarsened microstructure.This observation indicates that the large Pbrich phase particles grow at the expense of other particles rather than through a continuous nucleation and growth process.Structures formed during atomization generally have high interfacial areas and nonequilibrium solute concentration, because of the rapid solidification that occurs.This behavior is observed because of the need to reduce the overall energy of the system by decreasing the interfacial area.Sufficient thermal energy is required to reduce the energy of the system through diffusion even at room temperature.
Figure 4 presents the cross-sectional microstructure of rapidly solidified Sn-Pb37 powder aged for different numbers of days.No microsegregation of the Pb-rich phase was detected during growth.This observation illustrates that the Pb-rich phase in Sn-Pb37 powder coarsened through atom diffusion, with Pb particles becoming fewer in number, more spherical, and much larger during room

Effect of Aging on the Microstructure of Solder Powder
Figure 3 displays SEM images of the rapidly solidified eutectic Sn-Pb37 powder after aging at ambient temperature for different numbers of days.Even for aging at room temperature, coarsening of the microstructure is observed.A microstructure with an evident increase in the Pb-rich phase is observed after aging for 40 days.Moreover, some small particles are observed around the large particles in the Pb-rich-phase-coarsened microstructure.This observation indicates that the large Pb-rich phase particles grow at the expense of other particles rather than through a continuous nucleation and growth process.Structures formed during atomization generally have high interfacial areas and nonequilibrium solute concentration, because of the rapid solidification that occurs.This behavior is observed because of the need to reduce the overall energy of the system by decreasing the interfacial area.Sufficient thermal energy is required to reduce the energy of the system through diffusion even at room temperature.
Figure 4 presents the cross-sectional microstructure of rapidly solidified Sn-Pb37 powder aged for different numbers of days.No microsegregation of the Pb-rich phase was detected during growth.This observation illustrates that the Pb-rich phase in Sn-Pb37 powder coarsened through atom diffusion, with Pb particles becoming fewer in number, more spherical, and much larger during room temperature aging, indicating that the microstructure of the Sn-Pb37 powder evolves even at room temperature.Because some material properties depend on the material's microstructure, the effect of microstructure coarsening at room temperature should be considered.
temperature aging, indicating that the microstructure of the Sn-Pb37 powder evolves even at room temperature.Because some material properties depend on the material's microstructure, the effect of microstructure coarsening at room temperature should be considered.

Effect of Heat Treatment on the Microstructure of Solder Powder
To evaluate the effect of heating on microstructure evolution, the aging process was performed at elevated temperatures.Figure 5 presents SEM images of the eutectic Sn-Pb37 powder after heat temperature aging, indicating that the microstructure of the Sn-Pb37 powder evolves even at room temperature.Because some material properties depend on the material's microstructure, the effect of microstructure coarsening at room temperature should be considered.

Effect of Heat Treatment on the Microstructure of Solder Powder
To evaluate the effect of heating on microstructure evolution, the aging process was performed at elevated temperatures.Figure 5 presents SEM images of the eutectic Sn-Pb37 powder after heat

Effect of Heat Treatment on the Microstructure of Solder Powder
To evaluate the effect of heating on microstructure evolution, the aging process was performed at elevated temperatures.Figure 5 presents SEM images of the eutectic Sn-Pb37 powder after heat treatment for 1 day in air at temperatures from 40 • C to 120 • C. Figure 6 shows the corresponding SEM micrographs of a cross-section through the powder.Microstructure coarsening similar to that caused by aging at room temperature occurs.However, the coarsening occurs more rapidly at elevated temperatures.The microstructure is coarsened to the same degree after aging at 120 • C for 1 day as in aging for more than 1 month at room temperature.
The aging process in the alloy powder is the same at elevated temperatures as at room temperature; however, it occurs considerably more quickly at elevated temperatures.This indicates that the thermal diffusion coefficient between tin and lead is considerably higher for a higher aging temperature.
Precipitation occurs with a further increase in aging temperature.Figure 7 shows SEM images of Sn-Pb37 powder after aging at 150 • C for 3 days, wherein several small particles were precipitated.The solubility of tin in lead at 150 • C is approximately 10 wt%, and thus some redissolution of the tin phase may be observed.After cooling to room temperature, the new precipitates are observed to have reduced tin solubility in lead.
treatment for 1 day in air at temperatures from 40 °C to 120 °C. Figure 6 shows the corresponding SEM micrographs of a cross-section through the powder.Microstructure coarsening similar to that caused by aging at room temperature occurs.However, the coarsening occurs more rapidly at elevated temperatures.The microstructure is coarsened to the same degree after aging at 120 °C for 1 day as in aging for more than 1 month at room temperature.
The aging process in the alloy powder is the same at elevated temperatures as at room temperature; however, it occurs considerably more quickly at elevated temperatures.This indicates that the thermal diffusion coefficient between tin and lead is considerably higher for a higher aging temperature.
Precipitation occurs with a further increase in aging temperature.Figure 7 shows SEM images of Sn-Pb37 powder after aging at 150 °C for 3 days, wherein several small particles were precipitated.The solubility of tin in lead at 150 °C is approximately 10 wt%, and thus some redissolution of the tin phase may be observed.After cooling to room temperature, the new precipitates are observed to have reduced tin solubility in lead.The coarsening kinetics of Pb-rich particles at different aging temperatures can be interpreted using the Arrhenius law.The Pb-rich phase size is measured using the intercept method [21].Similar to that of conventional materials, the growth of Pb-rich particles can be described using the following equation: where D and Do are the average size of the Pb-rich phase and initial Pb-rich phase size before aging treatment, respectively; k, T, and t represent a constant, the temperature, and time, respectively.The grain growth constant is temperature dependent: where Q and kb are the activation energy and Boltzmann constant, respectively.
Therefore, the grain growth models for Pb-rich phase coarsening can be expressed using the following equation, which is in agreement with the models [22]:   The coarsening kinetics of Pb-rich particles at different aging temperatures can be interpreted using the Arrhenius law.The Pb-rich phase size is measured using the intercept method [21].Similar to that of conventional materials, the growth of Pb-rich particles can be described using the following equation: where D and Do are the average size of the Pb-rich phase and initial Pb-rich phase size before aging treatment, respectively; k, T, and t represent a constant, the temperature, and time, respectively.The grain growth constant is temperature dependent: where Q and kb are the activation energy and Boltzmann constant, respectively.
Therefore, the grain growth models for Pb-rich phase coarsening can be expressed using the following equation, which is in agreement with the models [22]: The coarsening kinetics of Pb-rich particles at different aging temperatures can be interpreted using the Arrhenius law.The Pb-rich phase size is measured using the intercept method [21].Similar to that of conventional materials, the growth of Pb-rich particles can be described using the following equation: where D and D o are the average size of the Pb-rich phase and initial Pb-rich phase size before aging treatment, respectively; k, T, and t represent a constant, the temperature, and time, respectively.The grain growth constant is temperature dependent: where Q and k b are the activation energy and Boltzmann constant, respectively.
Therefore, the grain growth models for Pb-rich phase coarsening can be expressed using the following equation, which is in agreement with the models [22]: where D and D o are the phase size after annealing for different durations and the initial phase size, respectively.T, n, K o , and Q are the temperature, phase size exponent, pre-exponential factor, and activation energy, respectively.According to coarsening theory [23,24], the growth exponent n = 4 is used for the coarsening of Pb-rich particles, in which the coarsening process is controlled through grain boundary solution diffusion.The growth kinetics of Pb-rich phase particles are provided by Figure 8 plots ln(D 4 − D o 4 ) versus 1/T for the annealing of Sn-Pb37 powder based on the Pb-rich particle coarsening analysis.A straight line through the data points provides an activation energy of Q = 45.53 ± 4.23 kJ/mol, which is consistent with the activation energy of grain boundary diffusion in Sn and Pb [21].This observation is also consistent with the value reported for the thermal annealing of Pb-phase growth, which is controlled by grain boundary diffusion.
where D and Do are the phase size after annealing for different durations and the initial phase size, respectively.T, n, Ko, and Q are the temperature, phase size exponent, pre-exponential factor, and activation energy, respectively.According to coarsening theory [23,24], the growth exponent n = 4 is used for the coarsening of Pb-rich particles, in which the coarsening process is controlled through grain boundary solution diffusion.The growth kinetics of Pb-rich phase particles are provided by Figure 8 plots ln(D 4 − Do 4 ) versus 1/T for the annealing of Sn-Pb37 powder based on the Pb-rich particle coarsening analysis.A straight line through the data points provides an activation energy of Q = 45.53 ± 4.23 kJ/mol, which is consistent with the activation energy of grain boundary diffusion in Sn and Pb [21].This observation is also consistent with the value reported for the thermal annealing of Pb-phase growth, which is controlled by grain boundary diffusion.

Conclusions
The effects of aging treatment on the microstructural evolution of rapidly solidified eutectic Sn-Pb solder powder were investigated.The rapidly solidified eutectic Sn-Pb solder powder exhibited instability after aging at different temperatures.Pb-rich phase coarsening was observed, during which the small particles congregated to form large particles in the microstructure.At elevated temperatures, similar coarsening of the Pb-rich phase occurred considerably more rapidly, because of the increase in mass transport.The relationship between Pb-rich phase coarsening and the aging temperature was estimated using the Arrhenius law.The activation energy obtained for the processes was 45.53 ± 4.23 kJ/mol, indicating that the rapid diffusion mechanism has a low activation barrier for Pb-rich phase coarsening.Moreover, the estimated value of the activation energy indicates that mass transport controlled through grain boundary diffusion is crucial for Pb-rich coarsening under aging treatment.

Conclusions
The effects of aging treatment on the microstructural evolution of rapidly solidified eutectic Sn-Pb solder powder were investigated.The rapidly solidified eutectic Sn-Pb solder powder exhibited instability after aging at different temperatures.Pb-rich phase coarsening was observed, during which the small particles congregated to form large particles in the microstructure.At elevated temperatures, similar coarsening of the Pb-rich phase occurred considerably more rapidly, because of the increase in mass transport.The relationship between Pb-rich phase coarsening and the aging temperature was estimated using the Arrhenius law.The activation energy obtained for the processes was 45.53 ± 4.23 kJ/mol, indicating that the rapid diffusion mechanism has a low activation barrier for Pb-rich phase coarsening.Moreover, the estimated value of the activation energy indicates that mass transport controlled through grain boundary diffusion is crucial for Pb-rich coarsening under aging treatment.

Figure 7 .
Figure 7. SEM images show the precipitate particles in the powders after aging at 150 °C for 3 days.

Figure 7 .
Figure 7. SEM images show the precipitate particles in the powders after aging at 150 °C for 3 days.

Figure 7 .
Figure 7. SEM images show the precipitate particles in the powders after aging at 150 • C for 3 days.