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30th SEMI-THERM Symposium
The Effect of Improper Conformal Coating on SnPb and Pb-free BGA Solder Joints during
Thermal Cycling: Experiments and Modeling
Maxim Serebreni1*, Ross Wilcoxon2, Dave Hillman2, Nathan Blattau1, Craig Hillman1
1DfR Solutions
9000 Virginia Manor Rd #290
Beltsville, MD 20705
2Rockwell Collins
400 Collins Road NE
Cedar Rapids, IA 52498 *Maxim Serebreni, [email protected]
Abstract
Application of chip scale packages (CSPs) and bottom
terminated components (BTCs) in harsh use environments
often requires the use of conformal coatings to meet reliability
requirements. In certain coating application methods, the
conformal coating materials can flow underneath the
component and cause solder joint failure during thermal
expansion and contraction of the electronic assembly. In this
study, Ball Grid Array (BGA) components were coated with an
acrylic conformal coating materials using two application
methods and subjected to two thermal cycling profiles to assess
the integrity of SnPb and Pb-free BGA components. To better
understand the observed failure modes, Finite Element
Analysis (FEA) was performed on the conformally coated
BGA packages. Material characterization was performed using
Dynamic Mechanical Analysis (DMA) and Thermal
Mechanical Analysis (TMA) to capture the temperature
dependent properties of the conformal coating to better
correlate simulation and experimental results. Failure modes
were found to greatly depend on the conformal coating material
properties around the glass transition temperature (Tg) rather
than temperature range. Significant difference in the failure
mode was found between the Pb-free and SnPb BGA
components with acrylic conformal coating materials and
temperatures profiles.
Keywords
Conformal Coating, Thermal Cycling, Ball Grid Arrays,
Solder fatigue, Finite Element Modeling
1. Introduction
Conformal coatings are used on Printed Circuit Boards
(PCB) with the intent of providing protection from harsh
environments containing moisture and contamination such as
dust and metallic debris that could cause shorts in electronic
components. In addition, some conformal coatings are
designed to provide thermal insulation, shock vibration
attenuation and electrical insulation for high voltage
components at high altitudes [1]. Conformal coatings are also
being used to help mitigate the risk of tin whiskers on pure tin
surface finishes [2]. These attributes make conformal coatings
especially attractive for high reliability application
environments of avionic and aerospace electronics. Previous
studies have shown that the application of conformal coating to
surface mount resistors and CSPs can reduce the thermal strain
in solder joints and thus extend the thermo-mechanical fatigue
life of components [3-5].
Potential concerns regarding solder joint integrity arise
when the conformal coating material is allowed to flow
underneath the package. Recent investigations have show that
letting conformal coating flow underneath plastic quad-flat no
lead package (PQFN) dramatically reduces the thermo-
mechanical fatigue (TMF) life of the device by changing the
equivalent plastic strain of solder joints from predominantly
shear to an axial loading mode [6]. In such a condition, the
conformal coating expands and contracts in the vertical
direction. As thermal cycling progresses, failure in solder joints
could result from the lifting of the component that causes
excessive tensile and compressive stresses. The amount of axial
stress will greatly depend on the leverage of the conformal
coating on the particular component and the variation of
coefficient of thermal expansion (CTE) and elastic modulus (E)
of the coating with temperature. In addition, conformal coating
materials with a Tg that is within the thermal cycle range could
drastically reduce fatigue life of solder interconnects. As
temperature approaches the materials Tg, large expansion
occurs along with reduction of material stiffness. In cases when
the conformal coating material expansion occurs prior to
adequate softening, large stresses would be applied to solder
joints. This behavior is inherent in thermoset polymers since
materials expansion tends to bedriven by the changes in the free
volume while changes in the modulus tends to be driven by the
increases in movement of the polymer chains. Due to the
intrinsic properties of conformal coating and the large variety
of coating materials used by the electronics industry, the effect
conformal coatings on solder joint TMF life needs to be
investigated.
This research aims to investigate the impact conformal
coatings and their application method can have on Pb-free and
SnPb area array components under thermal cycling condition.
Experimental procedure follows that of previous study
conducted by authors in which components with only SnPb
solder were used [7]. Results from mechanical characterization
of the acrylic conformal coating were used in finite element
simulation to capture the effect of acrylic conformal coating
and their application method on ball grid (BGA) components
and provide further insight into the associated failure mode in
each of the tested solder alloys under various thermal cycling
ranges.
Wesling, Test Structures in Thermal Test Chips for Optimum …
30th SEMI-THERM Symposium
2. Experimental Approach
Simulations in the current study were based on
experimental conditions performed in a previous investigation
that included ball grid array (BGA) components, with tin-lead
(63Sn37Pb) solder balls, that were subjected to thermal
cycling. Figure 1 shows an assembled test vehicle from that
study that included 60 components with half of them
conformally coated. In the experimental study of reference [7],
an Anatech event detector system continuously monitored the
continuity of the daisy-chain BGA components to determine
the number of thermal cycles at which solder joint failure
occurred.
2.1 Material Properties
Acrylic conformal coating is widely used in a large variety
of electronic assemblies. To understand the temperature
dependent mechanical behavior of the material bulk samples of
the acrylic conformal coating were prepared and characterized
using TMA and DMA to measure the materials CTE and
modulus as a function of temperature as shown in Figure 1 and
are implemented in FE modeling. Characterization identified
the Tg of the material to be around 15°. The glass transition
temperature corresponds to the midpoint of a region in which
the material’s modulus decreases and material expansion
rapidly increases rather than a single data point in which an
abrupt transition occurs.
Figure 1. Measured material properties
2.2 Test Vehicle
Test vehicles comprised of daisy chained BGA components
with a package size of 17mm x 17mm, 1mm pitch, 256 IO.
Each test board was populated with 60 individual components.
Test boards selected with FR4 material laminate with 0.081
inch thickness and 8 dummy inner layers. BGA components
assembled using 0.005 inch thick stencil. Two conformal
coating configuration were applied to the two halves of each
test vehicle. The left half of each board was coated using
“standard” production spray process and the right half of the
boards coated by a manual process using pneumatic syringe to
completely fill the conformal coating material under each BGA
referred to as “thick” application. This approach represents a
worst-case scenario of conformal coating application that can
occur in dipping method and heavy spray coating applications.
Figure 2. Assembled test vehicle showing two halves of the
board with two conformal application methods [7].
3. Thermal Cycle Testing
Two thermal cycle conditions were used in testing, one
with a temperature range of -55°C to +125°C and the second
with –20°C to +80°C as shown in Figure 7. Both profiles have
a minimum of 15 minute dwell time at each temperature
extreme and a ramp rate of 5-10°C/minute according to IPC-
9701.
Figure 3. Thermal cycles used in experiment and modeling.
4. Test Results
Reliability data of BGA component were analyzed using
regression analysis to determine the Weibull shape factor (β)
and characteristic life (η) for each configuration. The Weibull
function correlates the cumulative failure distribution F(t) to
the number of thermal cycles at which failure occurs shown in
equation (1).
F(t) = 1 − exp (−t
η)β
(1)
The reported characteristic life corresponds to number of cycles
at which 63.2% of the population is expected to have failed.
4.1 Failure Data Analysis
Failure data for each of the component configuration is
analyzed for the two thermal cycles and displayed in Table1.
Cycles to first failure are indicated for configuration in which
only sufficient thermal cycles progressed to cause an “early
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30th SEMI-THERM Symposium
failure” event; however, in slots indicated by “N/A”, the
characteristic life occurs past the experimental time frame.
Control samples with SAC305 alloy exhibit shorter fatigue life
than the SnPb components under equivalent thermal profiles.
As standard acrylic conformal coating is introduced,
characteristic life of the two alloys under temperature profile
with -20°C to +80°C falls within a narrower range.
Table 1. Weibull coefficients for experimental data
Alloy
Applicati
on
method
Temp Profile
β η First
failure
SAC305
control 1 7.92 256 173
standard 1 5.74 448 243
Heavy 1 17.09 197 171
control 2 N/A N/A N/A
standard 2 N/A N/A 935
Heavy 2 3.78 191 88
63Sn37Pb
control 1 17 629 514
standard 1 14.6 567 472
Heavy 1 6.14 568 364
control 2 N/A N/A N/A
Standard 2 N/A N/A N/A
Heavy 2 7.21 1234 756
The differences between standard and control samples are not
consistent from the SAC305 to SnPb alloys but are shown to
match under temperature profile 2 with a range of –20°C to
+80°C. With an increase in the thermal cycling range, a larger
discrepancy between the two solder alloy characteristic life is
evident from the cycles to first failure. First failure with
standard conformal coating surpassed the initial 1600 thermal
cycles for the -55°C to 125°C profile for the SnPb alloy with a
much lower first failure observed for the SAC305 alloy.
Figure 4 represents the cumulative failure distribution for
the SAC305 components with thick and standard coating for
the two temperature profiles. It is evident that the application
method impacts fatigue life significantly more than the
temperature range. A similar trend is evident for the SnPb
components.
Figure 4. Cumulative failure distribution for the Pb-free
acrylic samples with thick and standard coating
Figure 5 displays the cumulative failure distribution for the
SnPb components performed in the previous study along with
the standard acrylic coating performed in the current study.
Failure rates for the standard and thick coating under profile 1
show close resemblance to that of the SAC305 components
with earlier failures in the thick coated components. Initial
failures of the standard coated components are displayed for
profile 2 and illustrate the drastic increase in fatigue life with
standard coating between the two solder alloys and temperature
profiles.
Figure 5. Cumulative failure distribution for the SnPb acrylic
samples with thick and standard coating from previous study
[7]
4.2 Cross-sectional Failure Analysis
Metallographic cross section assessment performed on
both Pb-free and SnPb BGA components post thermal cycling
to reveal damage and crack location in solder jonits with and
without conformal coating.
Figure 6. Pb-free control sample showing cracking along
bottom pad.
Control components with Pb-free solder show cracking along
the solder joint/board pad interface as shown in Figure 6;
however; SnPb control components exhibit cracks along the
upper solder joints/component pad interface. This initial
difference in failure site between the control samples indicates
Wesling, Test Structures in Thermal Test Chips for Optimum …
30th SEMI-THERM Symposium
that additional factors such as component warping, pitch size,
ball height, local CTE mismatch, package configuration and
intermetallic layer all affect fatigue life of components and are
inherent factors in each solder alloy and component selection.
Figure 7. Failure of Pb-free BGA with acrylic conformal
coating (-55 to 125C) a) standard b) heavy coating application
Cross-sections of failed Pb-free solder joints are shown in
Figure 7 for both the standard and thick coated components.
Standard Pb-free components exhibit similar cracking location
as those in the control components with corner joints cracking
before joints at the center due to distance to neutral point effect.
Since a similar characteristic life between the control and
standard coated components was observed, the failure location
was as expected to be comparable. Introduction of the thick
conformal coating was found to have a different failure mode
than the standard coating. Since the acrylic conformal coating
represents a much larger area than the effective area of the
solder joints between the PCB and substrate, the mechanical
strains placed on the solder joints were imposed by the thermal
expansion of the conformal coating. Figure 8b) shows severe
plastic deformation in the Pb-free solder joints and no evident
distance to neutral effect. Similar cracking at the board pad is
observed for the -20°C to 80°C thermal cycle with less plastic
deformation as in Figure 7. Large compressive strains caused
solder joint to be extruded outwards. This failure mode is also
attributed to the lack of adhesion and interaction between the
conformal coating and solder alloy during the low and high
temperature extremes. At the high temperature dwell, solder
joints creep and conformal coating softens and eliminates any
possible adhesion between solder and the acrylic material. At
the cold temperature, extreme, the solder is compresses and
squeezed outward in the normal direction to the applied load.
The lack of hydrostatic stress on solder joints during low
temperature dwell implies that no physical constraint is being
placed on the solder and allows for the deformation to occur.
This solder/conformal coating interaction is greatly dependent
on the conformal coating CTE and modulus at the dwell
temperature. It is important to note that the cross-section shown
in Figure 7 is that after 1000 thermal cycles, and electrical
failure was detected in a fraction of the number of cycles took
to severely deform the Pb-free solder alloy to the one shown.
Failure analysis of the Pb-free solder joints exhibits similar
failure location on the upper solder/component pad interface as
the control components. Figure 8 displays SnPb BGA with
standard acrylic coating post 1600 thermal cycles with slight
cracking and grain coarsening under temperature profile 2.
Figure 8. SnPb BGA with Acrylic standard coating showing
cracking in upper left size of solder joint at 1600 cycles.
Cross-sections of the SnPb components reveals that the
magnitude of damage closely correlate to the characteristic life
variation found in the BGA solder joints under both thermal
cycles. A different failure mechanism with the thick acrylic
coating between the SnPb and the Pb-free solder joints was
observed along with a phenomenon that explains the difference
in cycles to failure primarily between the thick coated
components. Figure 9 displays the SnPb solder joints with thick
acrylic coating post thermal cycling for a) corner joint and b)
joints at the center of the row for the -20°C to 80°C thermal
cycles. Cracking along the diagonal of the SnPb solder is found
along with grain coarsening at the crack area and similar
extrusion as seen in the Pb-free components. Whoever; unlike
the Pb-free components, electrical failures in the SnPb
components were detected as cracking along the diagonal of the
solder joints propagated prior to the severe compressive
deformation took place. Unlike the Pb-free solder, distance to
neutral point in the thick coated SnPb components remains
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30th SEMI-THERM Symposium
dominant and is evident from the lack of damage in solder
joints at the center of the row with progressively lower damage
in solder joints closer to the neutral point of the component.
This phenomenon can be attributed to the lower stiffness of the
SnPb solder joints which allow for more components warpage
and load sharing between neighboring solder joints.
Figure 9. SnPb BGA with thick conformal coating failed at
1055 thermal cycles (-20 to 80C) a) Corner joint b) joints in
middle of row.
Variation in the characteristic life between the Pb-free and
SnPb components is also strongly dependent on the local CTE
mismatch between solder alloy and component. Due to a
different microstructure and mechanical properties, the stress
distribution in SnPb corner joints is subjected under lower axial
strain but with larger shear strains than the Pb-free solder. In
conjunction with the axial compression due to the thick acrylic
coating, solder joints are placed under mixed-mode thermo-
mechanical loading which progresses cracking along the
diagonal of the solder joint.
In a few instances, no failure was recorded in SnPb
components with thick acrylic coating. Figure 10 displays
corner and middle row SnPb components with thick coating
cycles from -20°C to 80°C for 1600 cycles with not an evident
change in resistance. Both locations along the row show
severely compressed solder joints with cracks running along
the diagonal of the component. It is believed that in this
instance the large compressive stresses caused crack closure to
overate the rate of crack propagation and avoid an open to
occur. This process is not fully explained and its exact
contribution to the observed increase in cycles to failure in
SnPb components is not yet known.
Figure 10. SnPb BGA with thick acrylic coating survived
1600 cycles a) corner joint b) joint in middle row
5. Finite Element Modeling
BGA package is modeled using commercial finite element
software ABAQUS 16.4. Global/local modeling approach is
used to create a quarter symmetric finite element model of the
BGA package and has proven to provide accurate results in
modeling solder in electronic packaging [9]. Copper pads on
both the PCB and substrate are modeled without solder mask.
Plugs of fine mesh were created to model corner solder joints
and plugs with coarse mesh used to model the rest of the solder
joints as shown in Figure 11.
Figure 11. Local model (a) joint with coarse mesh (b) jonit
with fine mesh
Wesling, Test Structures in Thermal Test Chips for Optimum …
30th SEMI-THERM Symposium
To capture creep and plasticity deformation of solder joints,
Schubert’s constitutive model based on a hyperbolic sine
function was implemented for both Pb-free and SnPb solder
shown in equation (1) [8]. Where 𝜀̇𝑐𝑟 is the steady state creep
strain rate, 𝐴1 constant, 𝐻1 is the apparent activation energy, k
is the Boltzmann’s constant, T is the absolute temperature, 𝜎 is
the applied stress, 𝛼 and n prescribe the power law relationship
between creep strain rate and applied stress.
𝜀̇𝑐𝑟 = 𝐴1(𝑠𝑖𝑛ℎ𝛼𝜎)𝑛 exp (−
𝐻1
𝑘𝑇) (2)
Solder A1 α n H1 k
SAC305 277984 0.02447 6.41 54041 8.314
63Sn37Pb 23343483 0.06699 3.3 67515 8.13
Modeling of the components with standard conformal coating
was omitted from the analysis since failure rates of standard
coated components matches those with the control components
in both solder alloys and thermal cycles. Figure 12 shows the
global view of the quarter symmetric BGA model.
Figure 12. Global model without underfill
Material properties used in the analysis are presented in Table
2. These values are a culmination of both published and
measured quantities and are assumed to be linear elastic except
solder alloy
Table 2. Material Properties
Local BGA plugs and a single quarter symmetric model were
merged and tie constrains generated between plug surfaces and
global model. To avoid incorrect results in the thick coated
model, a 20 µm gap was placed between solder and conformal
coating as shown in Figure 13 to avoid potential over
constraining of the solder joint during thermal cycling.
Figure 13. FE model structure with conformal coating
5.1 Pb-free BGA
Figure 14 shows the Von Mises stress contour plot for the
corner and die shadow joints at the beginning of the hot dwell
period. Stresses do not correspond to the directionality of
the load but imply that the location of maximum stress is
found at the solder/copper pad interface along with a slight
Figure 14. Von Mises stress distribution in SAC305 BGA
with thick conformal coating at 125°C.
Material Elastic
Modulus
(GPa)
Poisson’s
ratio
CTE
(ppm/ºc)
PCB 33.9 0.13 17
Substrate 28 0.13 13
Copper 118.5 0.326 16.7
Silicon 130 0.28 2.6
SAC305 20
63Sn37Pb 24
Wesling, Test Structures in Thermal Test Chips for Optimum …
30th SEMI-THERM Symposium
distance to neutral point effect at the corner joint which is not
presented in joints along the die shadow and is characteristic of
predominantly axial loading. The location of maximum stress
changes from the upper to lower interface during high and low
dwell periods, respectively. To illustrate the effect of the thick
conformal coating on the stress-strain state of the solder, a 25
µm layer of elements directly above the board copper pad is
volume averaged. Figure 15 illustrates the average maximum
principal strain for the Pb-free BGA for temperature profile 1
with and without conformal coating. largest average strain
value in BGA solder joints occurs at the center and graduate
decreases toward the solder/copper interface while average
Figure 15. Maximum principal strain with time and
temperature with and without conformal coating for Pb-free
BGA under temperature profile 1.
stress values are largest at the interface and decrease toward the
center of the joint. Since solder displacement is driven by
thermal expansion of the conformal coating, solder joints are
placed under displacement control loading conditions. With the
thick conformal coating, larger axial strains accumulate during
cold temperature dwell. This values occurs at a point at which
the acrylic material still maintains rigidity with high modulus.
More damage is accumulating at the start of the glass transition
temperature region rather than after the glass transition. At the
onset of the transition region, the elastic modulus of the acrylic
has not sufficiently decreased to allow even for a small increase
in the CTE.
To illustrate the difference in compressive loading caused
by conformal coating contraction during cold temperature
dwell the average axial strains are compared. Figure 16
illustrated the axial strains with time for the Pb-free BGA with
and without conformal coating for the same layer of elements.
It can be seen that the first high temperature dwell, both the
control and thick coated joints reach an equivalent state;
however, thick coated joints reach a much larger compressive
strain than the control. This cause a shift from positive to
negative axial mean strain which correlates to the failure mode
observed in cross-sectional analysis.
At the start of the subsequent thermal cycle, the strain state
at the interface of the Pb-free solder joint is under compressive
loading. The existence of a compressive preload has been
previously shown to contribute to larger accumulation of
plastic work per thermal cycle [10]. In this experimental
condition, the compressive preload occurs at the cold
temperature dwell and continues up to the glass temperature at
which the acrylic material softens. A similar trend is observed
at both temperature profiles with higher strain obtained for
profile with higher temperature extremes.
Figure 16. Axial stress distribution with time for Pb-free
corner BGA under temperature profile 1 with and without
conformal coating.
5.2 SnPb BGA
The stress-strain behavior of the SnPb solder joints at the
interface is similar to that observed in Pb-free components only
with noticale difference in magnitude. Figure 17 illustrates the
maximum principal strains at the corner SnPb BGA with and
without conformal coating at the high temperature dwell.
Figure 17. SnPb Max. principal strain at 125°C for the corner
BGA (a) with conformal coating (b) without conformal
coating.
Temperature
No coat
With coat
No coat
with coat
Wesling, Test Structures in Thermal Test Chips for Optimum …
30th SEMI-THERM Symposium
The strain distribution confirms the dominance of distance to
neutral point effect in SnPb components. Figure 18 illustrates
the same SnPb components during the cold temperature dwell
in which a noticeable difference is observed due to the thick
conformal coating.
Figure 18. SnPb BGA Min. principal strains at -55°C for corner
joint (a) with conformal coating (b) without conformal coating.
Larger strains are concentrated along the diagonal of the joint
with thick coating compared to a more uniform distribution of
the control component. This simulation assists in correlating
the failure model observed in cross-sectional analysis to the
temperature dependent material behavior of the acrylic coating.
6. Conclusions
This study resulted in identifying the effect of conformal
coating materials on solder joint fatigue life in Pb-free and
SnPb BGA packages. Experimental testing of acrylic
conformal coating materials with various temperature
dependent CTE and E exhibited failure modes ranging from
fatigue to overstress in Pb-free and SnPb solder joints. Finite
element simulation proved to be correlate well with associated
stress-strain state to the observed failure mechanism. An
accurate characterization of the conformal coating temperature
dependent properties has shown that the glass transition
temperature of the conformal coatings is a critical factor
affecting fatigue life. Thermal cycling profiles which crosses
the glass transition temperature of the material proven to be
more damaging than the temperature range with thick
conformal coating application. SnPb BGA components have
proven to be more robust to acrylic conformal coating under
both temperature extremes and application method. This results
is supported by the mechanical behavior inherent to SnPb
solder and the package type used in this study. Additional
experimentation is required to fully investigate the influence of
conformal coating BGA components by altering the conformal
coating materials and package type along with thermal cycling
conditions.
Acknowledgments
The authors would like to thank Gil Sharon for his fruitful
discussion of the modeling results as well as technical staff of
DfR Solutions and Rockwell Collins for assisting with sample
preparation, test setup and material characterization.
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