investigation of fiber orientation states in injection-compression molded short-fiber-reinforced...
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Investigation of Fiber Orientation States inInjection-Compression MoldedShort-Fiber-Reinforced Thermoplastics
Can Yang, Han-Xiong Huang, Kun LiLaboratory for Micro Molding and Polymer Rheology, South China University of Technology, Guangzhou510640, People’s Republic of China
Injection-compression molding (ICM) has receivedincreased attention because of its advantages over con-ventional injection molding (CIM). This article aims toinvestigate the effects of five dominating ICM process-ing parameters on fiber orientation in short-fiber-rein-forced polypropylene (SFR-PP) parts. A five-layer struc-ture of fiber orientation is found across the thicknessunder most conditions in ICM parts. This is quite differ-ent from the fiber orientation patterns in CIM parts. Thefibers orient orderly along the flow direction in the shellregion, whereas most fibers arrange randomly in theskin and the core regions. Additionally, the fiber orienta-tion changes in the width direction, with most fibersarranging orderly along the flow direction at positionsnear the mold cavity wall. The results also show that thecompression force, compression distance, and com-pression speed play important roles in determining thefiber states. Thicker shell regions, in which most fibersorient remarkably along the flow direction, can beobtained under larger compression force or compres-sion speed. Moreover, the delay time has an obviouseffect on the fiber orientation at positions far fromthe gate. However, the effect of compression time isfound to be negligible. POLYM. COMPOS., 31:1899–1908,2010. ª 2010 Society of Plastics Engineers
INTRODUCTION
Compared with conventional injection molding (CIM),
injection-compression molding (ICM) possesses the
advantages of decreased molding pressure, reduced resid-
ual stress, minimized molecular orientation, reduced
uneven shrinkage, overcome sink mark and warpage,
reduced density variation, and increased dimensional
accuracy [1]. Because of these advantages, ICM is often
employed to produce parts with high-dimensional accu-
racy or heavily reinforced parts for which the fiber orien-
tation is an issue.
To date, numerous researchers have reported on the
fiber orientation patterns in thermoplastics parts molded
by CIM. Among them, some studies [2–4] were con-
cerned with the typical skin-core structure of fiber orienta-
tion. This involves two skin layers with the fibers highly
orienting along the flow direction and a core layer con-
taining fibers generally aligning normal to the flow direc-
tion. Shokri and Bhatnagar [5] investigated the effect of
packing pressure on the fiber orientation in fiber-rein-
forced parts. Their results showed that the packing pres-
sure at the instant of complete filling tries to reduce the
degree of fiber alignment in the flow direction. Silva
et al. [6] compared the fiber orientation patterns of short
glass fiber (SGF)-reinforced polypropylene (PP) in con-
ventional and nonconventional molding (using a mold
involving rotation, compression, and expansion). The
results showed that the induced high-fiber orientation
transverse to the radial flow direction is very pronounced
in the expansion mold. Malzahn and Schultz [7] investi-
gated the development of fiber orientation during the
mold-filling process by examining the through-thickness
microstructures in a series of controlled short shots. The
transverse orientation of fibers throughout the core layer
was found only after the mold was fully packed. They
attributed this phenomenon to stresses developed during
the packing stage of the injection molding process. Exper-
imental and numerical simulation work performed by Lee
et al. [8] focused on the three-dimensional fiber orienta-
tion states in injection-molded parts, with a conclusion
that the predicted fiber orientation tensors and orientation
states showed good agreement with the measured ones.
Additionally, they attributed some differences between the
predicted and measured results at the end of cavity to the
fact that the fountain flow phenomenon is not considered
in the numerical analysis. Han and Im [9] carried out the
simulation of the fiber orientation distribution in short-
fiber-reinforced injection-molded parts with consideration
Correspondence to: Han-Xiong Huang; e-mail: [email protected]
Contract grant sponsors: Major Project of Key Fields in Guangdong-
Hong Kong; contract grant number: 2004A10402003.
Contract grant sponsors: Scientific Research Foundation for the Returned
Overseas Chinese Scholars, State Education Ministry.
DOI 10.1002/pc.20986
Published online in Wiley Online Library (wileyonlinelibrary.com).
VVC 2010 Society of Plastics Engineers
POLYMER COMPOSITES—-2010
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of fountain flow effects. By comparing simulation results
with experimental data from literatures, they found that
the orientation components in shell structure can be accu-
rately predicted.
From the literatures, it is found that although research
on fiber orientation has been reported, it mainly focused
on those parts molded by CIM. However, the fiber orien-
tation patterns often seem quite complicated because of
their dependence on the mold geometry, material proper-
ties, and processing parameters. The fiber orientation
states in ICM parts may be quite different from those in
CIM parts. Therefore, the effects of processing parameters
on fiber orientation states in ICM parts were experimen-
tally investigated in this work.
EXPERIMENTAL
Materials
The short-fiber-reinforced PP (SFR-PP) with 30 wt %
SGF used in this work was prepared by compounding PP
with SGF in a twin-screw extruder (with a diameter of 35
mm and a length-to-diameter ratio of 40) and then pellet-
ized. The PP used in this experiment was grade J501
(Sinopec Group Guangzhou, Guangdong, China) with a
melt index of 2.7 g/10 min (at 2308C and 2.16 kg). The
SGF had an average length of 3.0 6 1.0 mm, a diameter
of 11 6 1.0 lm, and was manufactured by Jushi Group
(Zhejiang, China).
ICM Part Molding
ICM experiments were conducted on an 80-ton injec-
tion molding machine (CJ80HE, Chende, China), which
can perform the function of ICM by changing its control
program. Both compression force and speed of the mova-
ble mold platen can be adjusted. To prevent back-flow of
the polymer melt, a special shut-off nozzle was connected
to the end of injection molding machine. Table 1 lists all
processing parameters as well as their values used in this
work. Only one parameter was changed at a time, while
the others were kept at a constant value (shown in bold in
Table 1). An injection-compression mold with an adjusta-
ble shim block that allowed a maximum compression dis-
tance of 3 mm was used to mold the rectangular parts
with the dimensions of 150 3 20 3 2 mm3.
Microscopic Observation
To observe the orientation of the glass fibers in the
ICM parts molded under various processing parameters,
or at different positions in the ICM parts molded under
the same processing parameters, small specimens were
cut at four different positions on the part, denoted as posi-
tions A, B, C, and D as shown in Fig. 1. Specimens were
studied from positions A and B for all the parts molded
in this work. Positions C and D were only analyzed from
parts molded under different compression distances and
compression speeds to better understand the fiber orienta-
tion along and transverse to the flow direction. The speci-
mens were deeply cooled in liquid nitrogen, and then bro-
ken parallel to the flow direction to prepare a surface for
scanning electron microscope (SEM) observation. A Phi-
lips XL-30FEG SEM was utilized to observe the fracture
surface at an acceleration voltage of 10 kV. All specimen
surfaces were gold coated before observation. Considering
the symmetry of each section across the thickness, only
half of the broken surface was observed for the specimen
under each condition.
RESULTS AND DISCUSSION
Fiber Orientation within ICM Parts
Figure 2 demonstrates the typical fiber orientation at
positions A and B within an ICM part. Clearly, three dif-
ferent regions across the thickness of the ICM part can be
found: a thin skin region located below the mold cavity
wall, a core region, and a shell region between the skin
and the core regions. By closer examination, it can be
seen that for positions A and B, there are more grooves
than holes in the shell region, whereas a contrary phe-
nomenon can be observed in the skin and the core
regions. This reveals that more fibers in the shell region
orient remarkably along the flow direction whereas more
fibers in the skin and core regions arrange randomly. It
can be observed that the boundaries between different
regions at position B are not as clear as those at position
A. Moreover, the thickness of the shell region at position
B is smaller than that at position A. The difference in
fiber state at positions A and B is due to the fact that the
dominant fiber orientation pattern originates from the
injection stage for position A, whereas from the compres-
sion stage for position B. Details are discussed later.
Considering the fact that the SEM images shown in
Fig. 2 only cover half of the part thickness, it is under-
standable that, despite some difference in fiber orientation
between positions A and B, a five-layer structure of fiber
TABLE 1. Values for various parameters used in this work.
Parameters Values
Melt temperature (8C) 210
Mold temperature (8C) 50
Injection pressure (MPa) 30
Injection time (s) 1.5
Cooling time (s) 30
Compression force (t) 1 3
Compression distance (mm) 1 2.5
Compression speed (mm/s) 1 3
Delay time (s) 0 2
Compression time (s) 5 13
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orientation, that is, a core layer in the middle and two
skin and two shell layers on both sides, exists in ICM
parts. This is schematically shown in Fig. 3. This result is
quite different from that in CIM parts reported in Refs.
10 and 11, characterized by most fibers orienting parallel
to the flow direction near the cavity wall but perpendicu-
lar to the flow direction in the core. The simulated fiber
orientation across the through thickness of position A in
CIM part is presented in Fig. 4. The Moldflow Plastic
Insight 6.1 was used to conduct the simulation. The same
mold cavity geometry and molding conditions as in
experiment were utilized in the simulation. The first prin-
cipal values of fiber orientation tensor are used to show
the probability of fiber alignment in the flow direction. A
value close to 1 in the result indicates a high probability
of fiber alignment in the flow direction, whereas a value
close to 0 indicates a low probability. From Fig. 4, one
can see the difference of fiber orientation states across the
thickness in CIM parts when compared with that in ICM
parts described earlier.
The different fiber orientation patterns in parts molded
by ICM and CIM can be explained by the way in which
the mold cavity is filled. In the ICM process, the molten
polymer is injected into the slightly opened mold cavity,
and after the filling stage is completed, the compression
process is activated to apply uniform pressure to the
entire cavity until the gate solidifies. This process influen-
ces the orientation of the fibers in the part to a certain
extent. Specifically, in the injection stage of ICM process,
the molten polymer is pushed into the cavity by a piston
having a constant velocity. The mold cavity in this study
has a constant cross-section area, thus based on the
assumptions that the polymer is incompressible and no
slip takes place on the mold cavity, the parabolic gap-
wised flow velocity distribution will move constantly
along the flow direction. In this stage, the molten polymer
next to the mold cavity experiences the highest shear rate.
At the same time, the cooling rate is also high next to the
mold cavity due to the thermal conduction between mol-
ten polymer and mold cavity. After the delay time, the
compression stage begins, in which the already injected
melt is pushed further by the movable mold platen. Dur-
ing this stage, the flow mass must be balanced. As a
result, the compressed melt in the core region near posi-
tion A must flow towards the end of the cavity. The main
characteristic of the compression stage is relatively low-
shear rate of the flow when comparing with the injection
stage. In a word, in ICM parts the fiber state in the skin
region is the result of high-shear rate and immediate cool-
ing rate once the melt contacts the cold mold cavity. The
fiber orientation parallel to the flow direction in the shell
region at position A is caused by the strong shear effect
induced by the injection flow, whereas that at position B is
caused by the compression flow with relatively low-shear
FIG. 2. Typical SEM micrographs of (a) position A and (b) position B
in ICM parts (compression force, 3 t; compression time, 13 s; compres-
sion distance, 1 mm; compression speed, 1 mm/s; and delay time, 2 s).
[Color figure can be viewed in the online issue, which is available at
wileyonlinelibrary.com.]
FIG. 1. Part dimensions and the locations for SEM observation (unit:
mm). [Color figure can be viewed in the online issue, which is available
at wileyonlinelibrary.com.]
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effect. The low-shear rate in the core region leads to a ran-
dom fiber orientation in both positions.
Effects of Processing Parameters on Fiber Orientation
Figure 5 shows the influence of compression force on
the fiber orientation at positions A and B in ICM parts. It
can be seen that a thicker shell region is formed at both
positions in ICM part molded under a higher compression
force. For example, the thickness of the shell region at
position A increases from 0.39 to 0.58 mm as the com-
pression force increases from 1 to 3 t. Recall that study
carried out by Shokri and Bhatnagar [5] showed that
when applying packing pressure to the melt in CIM, the
degree of fiber alignment along the flow direction reduces
significantly compared with the case without packing
pressure. The part geometry in their investigation is very
similar to that used in this study. However, this work
showed that the compression force in ICM exhibits a con-
trary effect on the fiber orientation. This phenomenon can
be explained by clarifying the difference between the
packing phase in the CIM and the compression phase in
the ICM. As shown in Fig. 6a, in the packing phase of
CIM process, the packing pressure is transferred from the
gate to the end of the cavity, which forms a radialized
pressure distribution from the gate. To simplify the analy-
sis, only two forces (denoted as F1 and F2 in Fig. 6a)
resulted from packing pressure are assumed to be applied
to a single SGF, which already aligned in the flow direc-
tion. Because of different pressure drop paths, the force
F1 is larger than the force F2, which results in a torque-
moment that can make the fiber rotate in a direction
inclined or even perpendicular to the flow direction (from
directions p1 to p2 as shown in Fig. 6a). Therefore,
increasing the packing pressure in the CIM process
decreases the degree of fiber orientation along the flow
direction. Unlike the packing pressure distribution in the
CIM, the compression force in the ICM is uniformly
applied on the melt through the movable mold platen.
Therefore, no torque-moment is caused by forces F1 and
F2 (as shown in Fig. 6b). Instead of making the aligned
fibers rotate, the uniform compression force encourages
the arrangement of fibers along the flow direction.
Bay et al. [12] investigated the short-fiber orientation
in the CIM part with simple strip geometry. They found
that in general there is no in-plane stretching that occurs
during radial flow; the orientation of fibers in the core
layer is a result from the flow in the gate and is carried
down the cavity with little change. In this work, the part
has dimensions of 150 3 20 3 2 mm3 and hence can
also be considered as a strip. Unlike Bay et al.’s result,
there are more fibers orienting in a random state
(including the skin and the core regions) at position B
than position A under the same compression force, as
shown in Fig. 5. This may be attributed to the fact that
the ICM process involves a compression stage following
the injection stage. In the injection stage, the fibers in the
core region near position A orient randomly due to
the low-shear rate. In the compression stage, most of the
polymer melt containing randomly oriented fibers in the
core region near position A is pushed to fill the remaining
cavity. Because of the weak flow-induced shear rate in
the compression stage, the state of fiber orientation at
position B changes slightly. That is to say, at position B,
most fibers maintain the random state, similar to the core
region at position A.
Figure 7 shows the fiber orientation patterns at posi-
tions A through D in ICM parts molded under compres-
sion distances of 1 and 2.5 mm. As can be seen from
Fig. 7(1), more fibers orient orderly along the flow
direction under 2.5 mm compression distance than 1 mm
compression distance at position A. This can be
explained as follows. As compression distance increases,
the melt filling length in the injection stage becomes
shorter, providing a longer channel to be filled in the
FIG. 4. Simulated fiber orientation across the through thickness of posi-
tion A in CIM part. (melt temperature, 2108C; mold temperature, 508C;injection time, 1.5 s; injection pressure, 30 MPa; and cooling time,
30 s). [Color figure can be viewed in the online issue, which is available
at wileyonlinelibrary.com.]
FIG. 3. Schematic representation of fiber states in ICM parts.
[Color figure can be viewed in the online issue, which is available at
wileyonlinelibrary.com.]
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compression stage. As a result, more melt in the core
region near position A, where most fibers randomly ori-
ent, is pushed forward to fill the void cavity. Meanwhile,
after compression stage the melt remaining near position
A contains more fibers that are already oriented along
the flow direction in the injection stage. Figure 7(2 and 3)
demonstrates that the changes of fiber orientation versus
compression distance at positions D and B are very sim-
ilar, with more fibers orienting randomly in the core
region under a larger compression distance. This is
because that as mentioned earlier, the melt at positions
D and B come from the core region near position A in
compression stage, meaning that the final fiber orienta-
tion at positions D and B is to a large extent determined
by the injection stage, in which most fibers in core
region near position A orient randomly. From Fig. 7(4),
it can be seen that at position C, most fibers across the
whole thickness orient parallel to the flow direction
except that a few fibers in the skin region have a tend-
ency to arrange normal to the flow direction. This is
also valid for the fibers in the core region that have a
weak dependence on the compression distance. This high
degree of fiber orientation along the flow direction may
FIG. 5. SEM micrographs of positions (1) A and (2) B in ICM parts molded under compression forces of (a) 1
and (b) 3 t. (compression time, 13 s; compression distance, 1 mm; compression speed, 1 mm/s; and delay time,
2 s). [Color figure can be viewed in the online issue, which is available at wileyonlinelibrary.com.]
FIG. 6. Comparison of pressure distributions between (a) packing phase
in CIM and (b) compression phase in ICM. [Color figure can be viewed
in the online issue, which is available at wileyonlinelibrary.com.]
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result from high-shear rate due to the special location of
position C. The closeness of position C to the mold cav-
ity wall causes the velocity profiles of the flow with low
velocity in the thickness and width directions to overlap,
resulting in high-shear rate across the whole section near
position C.
FIG. 7. SEM micrographs of positions (1) A, (2) D, (3) B, and (4) C in ICM parts molded under compres-
sion distances of (a) 1 and (b) 2.5 mm. (compression force, 1 t; compression time, 13 s; compression speed,
1 mm/s; and delay time, 2 s).
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Figure 8 shows the influence of compression speed on
the fiber orientation at positions A through D in ICM
parts. As can be seen, less fiber in the core region
arranges randomly as the compression speed increases,
especially at positions A and D. Stronger shear caused by
increased compression speed may account for this result.
FIG. 8. SEM micrographs of positions (1) A, (2) D, (3) B, and (4) C in ICM parts molded under compres-
sion speeds of (a) 1 and (b) 5 mm/s. (compression force, 1 t; compression time, 13 s; compression distance,
1 mm; and delay time, 2 s).
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FIG. 9. Average flow velocity distribution along the flow direction in compression stage of the ICM
process. (compression force, 1 t; compression time, 13 s; compression distance, 1 mm; compression
speed, 1 mm/s; and delay time, 2 s). [Color figure can be viewed in the online issue, which is available at
wileyonlinelibrary.com.]
FIG. 10. SEM micrographs of positions (1) A and (2) B in ICM parts molded under delay times of (a) 0
and (b) 2 s. (compression force, 1 t; compression time, 13 s; compression distance, 1 mm; and compression
speed, 1 mm/s).
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In this study, the cross-section area of the mold cavity
keeps constant along the flow direction. Thus for CIM,
except around the gate area, the flow velocity keeps con-
stant as the melt front flows forward from the gate provid-
ing that a constant velocity control of the machine is used
for the injection stage. Whereas in the compression stage
of the ICM, the longer the melt front advances from the
gate, the higher the average flow velocity is. This can be
proved by the numerically simulated average flow veloc-
ity along the flow direction in the ICM using Moldflow
Plastic Insight 6.1, as shown in Fig. 9. Therefore, with
increased compression speed, it is easy to understand that
less randomly oriented fibers exist in the core region at
position D than position A. On the other hand, because of
the strong shear effect resulted from the strip geometry of
the molded part, the fibers across the whole surface at
position C have a perfect orientation along the flow direc-
tion regardless of the compression speed [see Fig. 8(4)].
In general, high orientation of polymer molecules results
in a significant anisotropy of the part properties, whereas
random orientation of polymer molecules gives more uni-
form properties in various directions. Hence, the ICM
parts may possess different properties across the thick-
ness. This deduction was also confirmed by the work of
Kang et al. [13]. They experimentally examined the bire-
fringence distribution in thickness direction of an ICM
optical part and found that the birefringence has a local
minimum value in the center and two local maximum val-
ues next to the core on both sides. They contributed the
increase of birefringence near the center to the thermal
stress caused by quenching. However, this study suggests
that the molecular orientation distribution developed in
the ICM process also accounts partially for that birefrin-
gence pattern.
As can be seen in Fig. 10(1), the fiber orientation
states are very similar at position A in ICM parts
molded under different delay times. This is because
most of the melt near position A is that close to the
mold cavity wall developed in injection stage. The
processing conditions in the injection stage are
the same in all the experiments, which results in the
same fiber orientation along the flow direction near
position A. Differently, all the melt at position B
comes from the core layer at position A developed in
injection stage, where the fibers orient randomly. In
compression stage, the melt temperature decreases as
the delay time increases. The increased viscosity caused
by decreased melt temperature in the core layer induces
stronger shear effect, leading to more fibers arranging
randomly to orient along the flow direction, as shown
in Fig. 10(2). Consequently, it can be concluded that
the variation of delay time has an obvious effect on
the fiber orientation at positions far from the gate, but
has little influence on the fiber orientation near the
gate.
Figure 11 illustrates the changes of the fiber orientation
at position B with different compression times. It can be
seen that the compression time has little effect on the
fiber orientation. The reason may be that the effective
time when the compression force is acted on the polymer
melt is much shorter than the set compression time. This
indicates that once the gate is solidified, further increasing
the compression time does not affect the fiber arrange-
ment. This observation agrees with the conclusion of
Huang et al.’s research [14] in which the shrinkage distri-
bution of ICM PP parts does not change with continually
increased the compression time.
CONCLUSIONS
In this work, experiments were carried out to investi-
gate the effects of processing parameters on fiber orienta-
FIG. 11. SEM micrographs of position B in ICM parts molded under compression times of (a) 5 and (b) 13 s.
(compression force, 1 t; compression distance, 1 mm; compression speed, 1 mm/s; and delay time, 2 s).
DOI 10.1002/pc POLYMER COMPOSITES—-2010 1907
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tion states in ICM short-fiber-reinforced PP parts. Differ-
ent from the skin-core structure of fiber orientation in
CIM parts, a five-layer structure of fiber orientation is
found across the thickness under most conditions in ICM
parts. The fibers orient orderly along the flow direction in
the shell region, whereas most fibers arrange randomly in
the skin and the core regions. In addition, the fiber orien-
tation changes greatly in the width direction, with most
fibers orienting along the flow direction at positions close
to mold cavity wall. The results also show that the com-
pression force, compression distance, and compression
speed are important parameters influencing the fiber orien-
tation. Larger compression force or compression speed
leads to that more fibers orient along the flow direction in
the shell region. Moreover, the delay time has an obvious
effect on the fiber orientation at positions far from the
gate, and compression time is found to have a weak influ-
ence on the fiber orientation in ICM parts.
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