Mechanical properties and morphological structures of short glass fiber reinforced PP/EPDM composite
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Transcript of Mechanical properties and morphological structures of short glass fiber reinforced PP/EPDM composite
European Polymer Journal 39 (2003) 2129–2134
www.elsevier.com/locate/europolj
Mechanical properties and morphological structuresof short glass fiber reinforced PP/EPDM composite
Weizhi Wang, Longxiang Tang, Baojun Qu *
Department of Polymer Science and Engineering, University of Science and Technology of China, Hefei, 230026 Anhui, PR China
Received 20 June 2003; received in revised form 6 July 2003; accepted 14 July 2003
Abstract
The mechanical properties and crystal morphological structures of short glass fiber (SGF) reinforced dynamically
photo-irradiated polypropylene (PP)/ethylene–propylene–diene terpolymer (EPDM) composites were studied by me-
chanical tests, wide-angle X-ray diffraction (WAXD), optical microscopy, scanning electron microscopy (SEM), dif-
ferential scanning calorimetry (DSC), and thermogravimetric analyzer (TGA). The mechanical properties of PP/EPDM
composites, especially the tensile strength were greatly strengthened by dynamically photo-irradiation and the incor-
poration of SGF. The results from the WAXD, SEM, DSC, and TGA measurements reveal: (i) the formation of b-typecrystal of PP in the PP/EPDM/SGF composite; (ii) the fiber length in dynamically photo-irradiated PP/EPDM/SGF
composites are general longer than that in corresponding unirradiated samples. The size of EPDM phase in the photo-
irradiated composites reduces obviously whereas the droplet number increases; (iii) photo-irradiation improves the
interface adhesion between SGF and polymer matrix; (iv) the melting and crystallization temperatures of the photo-
irradiated composites are not affected greatly by increasing the SGF content; (v) the thermal analysis results show that
the incorporation of SGF into PP/EPDM plays an important role for increasing its thermal stability.
� 2003 Elsevier Ltd. All rights reserved.
Keywords: Glass fibers; Polypropylene; Composites; Mechanical properties; Morphological structure
1. Introduction
Polypropylene (PP) used as a thermoplastic is widely
used in many fields, such as building materials, furni-
ture, automobile and toy industries. However, the poor
impact resistance, especially at low temperature con-
siderably limits its application. Therefore, PP is usually
modified with elastomers, such as ethylene–propylene–
diene terpolymer (EPDM), to improve its impact
strength [1–4]. However, the improvement of toughness
of PP/rubber blend always follows by the decrease of
stiffness. In recent years, short glass fiber (SGF), glass
ball, calcium carbonate, talc, and montmorillonite re-
* Corresponding author. Tel.: +86-551-3606467; fax: +86-
551-3607245.
E-mail address: [email protected] (B. Qu).
0014-3057/$ - see front matter � 2003 Elsevier Ltd. All rights reserv
doi:10.1016/S0014-3057(03)00157-5
inforced composites have been widely studied and de-
veloped rapidly [5–8], which provide an alternation to
increase the stiffness of polymer composites. However,
the poor interface adhesion between fillers and matrix
will obviously lead to the reduction in tensile ductility
and impact toughness. These difficulties make the effi-
ciency for improving toughness and stiffness of PP/rub-
ber/SGF ternary composite decrease. In order to solve
this problem, many researchers focus on the glass fiber
surface modification technique or the approaches of
adding compatilizers [9–15]. Although the toughness can
be improved in some degree from these methods, the
complicated treatment and rigorous condition greatly
confine the preparation of composites in mass with low
cost.
In the present paper, we combine the dynamically
photo-crosslinking technology [16] with SGF reinforce-
ment to prepare crosslinked PP/EPDM/SGF ternary
ed.
2130 W. Wang et al. / European Polymer Journal 39 (2003) 2129–2134
composite. Their mechanical properties and crystal
morphological structures were investigated by mechan-
ical tests, wide-angle X-ray diffraction (WAXD), optical
microscopy, scanning electron microscopy (SEM), dif-
ferential scanning calorimetry (DSC), and thermo-
gravimetric analyzer (TGA).
2. Experimental
2.1. Materials
PP (F401, MFR¼ 2.7) was supplied by Yangzi Pet-
rochemical Co. Ltd., China. EPDM 4770 containing
70 wt% ethylene and 5 wt% diene was supplied by Du-
Pont Dow Elastomer Co. Ltd., USA. 2-Ethylidene-5-
norbornene was used as a diene. The short glass fiber
(diameter, 10–20 lm) was supplied by Shanghai Chem-
istry Co., China. Benzil dimethyl ketal (BDK) as a
photo-initiator and hindered amine Tinuvin 144 as a
photo-stabilizer were obtained from Ciba-Geigy Co.,
Switzerland. Triallyl isocyanurate (TAIC) used as a
crosslinking agent was obtained from Anhui Institute of
Chemical Engineering, China. All chemicals were used
as received without purification.
2.2. Sample preparation and measurements
The dynamically photo-irradiated PP/EPDM/SGF
composites were prepared as following steps: PP was
firstly mixed with EPDM (PP:EPDM¼ 8:2, wt%), a
given amount of SGF, 1 wt% BDK and 4 wt% TAIC
(based on EPDM content) for 7 min at 180 �C using a
double roller mixer. And then, a 2 kW Philips HPM 15
lamp was applied to irradiate the composite at 15 cm
distance from the lamp for 90 s while mechanically
blending. The dynamically photo-irradiated PP/EPDM/
SGF composite was continuously mixed for another
Table 1
Mechanical properties, gel content, and MFR of PP/EPDM and PP/
Sample code Component weight (g) Tensile
strength
(MPa)
Elong
(%)PP EPDM SGF
PP 100 – – 34.0 1140
PP/EPDM 80 20 – 22.5 650
PP/EPDM/
10%SGF
72 18 10 31.5 183
PP/EPDM/
30%SGF
56 14 30 34.7 118
PP/EPDMir 80 20 – 25.0 200
PP/EPDMir/
10%SGF
72 18 10 36.2 146
PP/EPDMir/
30%SGF
56 14 30 40.2 96
5 min. Finally the samples for measurements were ob-
tained by injection. The unirradiated PP/EPDM/SGF
composite as a control sample was prepared with the
above similar steps except for UV-irradiation. PP/
EPDMir and PP/EPDMir/SGF represent for the dynam-
ically photo-irradiated composites without and with the
addition of SGF, respectively. The composition of those
composites is listed in Table 1.
The tensile properties were measured with a Univer-
sal Testing Machine (DCS5000, SHIMADZU, Japan) at
25± 2 �C. The crosshead speed was 50 mm/min. The
dumb-bell shaped specimens were prepared according to
ASTM D412-87. The notched Izod impact strength was
measured by an Izod impact tester (made in Chengde,
China). The size of rectangular specimens was 80· 10· 4mm3 with a 45� V-shaped notch (tip radius 0.25 mm,
depth 2 mm). The average value from five specimens was
used for the data plot. The melt flow rate (MFR) was
measured at 230 �C under a load of 2.16 kg according to
ASTM D-1238.
The gel content of a sample was determined by
extracting the photo-irradiated sample in the basket
for 48 h with boiling xylene stabilized by 0.2 wt%
(based on the solvent content) antioxidant Tinuvin 144
and with N2 bubbling to prevent oxidation. The dy-
namically photo-irradiated sample was cut into thin
slices and put into a basket made of 200-mesh stainless
steel net. The solvent was renewed after the first 24 h
of extraction. After the extraction, the basket was
washed with acetone. After being dried in a vacuum
desiccator at about 70 �C to constant weight, the in-
soluble residue (w1) was weighed. The EPDM average
gel content (wt%) in the test was calculated as the
value of w1 � wSGF=wEPDM (wSGF and wEPDM present
the weight of SGF and EPDM in PP/EPDM/SGF
composite, respectively). Usually, five samples were
analyzed to determine the average gel content for a
given set of experimental conditions.
EPDM/SGF composites
ation Tensile
strength
(GPa)
Impact
strength
(kJ/m2, 25 �C)
Gel
content
(%)
MFR
(g/10 min)
1.30 2.3 – 3.5
0.65 8.7 – 2.5
0.88 7.8 – 1.3
1.41 5.1 – 0.8
0.69 10.8 92 1.8
0.94 9.6 90 1.0
1.48 6.2 90 0.6
W. Wang et al. / European Polymer Journal 39 (2003) 2129–2134 2131
The WAXD patterns were recorded at room tem-
perature with a D/Max-rA rotating anode X-ray dif-
fractometer (Rigaku Electrical Machine Co., Japan)
equipped with a CuKa tube and Ni filter. The diffraction
patterns were determined over a range of diffraction
angle 2h ¼ 10–40� at 40 kV and 50 mA. The fibers col-
lected after burning in a muffle furnace were observed by
a Nikon-YS2 optical microscope (Nikon, Japan). The
SEM images were obtained by a Philips-XL30 scanning
electron microscopy (Philips, Holland). The samples
were previously etched by xylene and coated with a
conductive gold layer. The DSC data were obtained in a
nitrogen atmosphere at a heating rate of 10 �C/min using
a Perkin–Elmer differential scanning calorimeter (model
DSC 2). The degree of crystallization of PP in nano-
composite was evaluated from the relative ratio of the
values of fusion heat of the blend to the fusion heat of
PP (DHPP ¼ 209 J/g) [17]. Thermal stability was deter-
mined with a Perkin–Elmer TGA-7 thermogravimetric
analyzer over a temperature range of 30–800 �C at a
heating rate of 10 �C/min.
3. Results and discussion
3.1. Mechanical properties
The tensile strength (TS), elongation at break, and
notched Izod impact strength (NIIS) of PP/EPDM
samples containing different amount of SGF before and
after photo-irradiation are summarized in Table 1. It has
been found that the TS value of 22.5 MPa for PP/EPDM
is smaller than that of 34.0 MPa for PP sample, because
of the incorporation of flexible component EPDM in PP
matrix. When blended 10% and 30% SGF into PP/
EPDM, the TS increases to 31.5 and 34.7 MPa, re-
spectively. Those results indicate that the stiffness of
composites can be improved by the addition of SGF
efficiently. After photo-irradiation, the TS further in-
creases to 36.2 and 40.2 MPa for the composites con-
taining 10% and 30% SGF, respectively, which indicates
that photo-irradiation can greatly enhance the stiffness
of composites incorporated with SGF. The elongation
data show that the rigid SGF incorporation decreases
the elongation from 650% for PP/EPDM to 183% for PP/
EPDM/10%SGF, and 118% for PP/EPDM/30%SGF.
Moreover, photo-irradiation makes the elongation at
break decreasing more obviously than the unirradiated
samples. The elongation of photo-irradiated samples
with 10 and 30 wt% SGF addition decreases from 183%
and 118% to 146% and 96%, respectively. However,
after blended EPDM rubber into PP matrix, the NIIS
increases to 8.7 kJ/m2 from 2.3 kJ/m2 of PP. On the
other hand, the NIIS of samples without SGF addition
is higher than that for corresponding samples with SGF
addition, which implies that the incorporation of SGF in
order to improve matrix stiffness is always at the expense
of tensile ductility. However, after photo-irradiation, the
NIIS increases from 7.8 and 5.1 kJ/m2 for PP/EPDM/
10%SGF and PP/EPDM/30%SGF, respectively, to 9.6
and 6.2 kJ/m2 for the corresponding photo-irradiated
samples. This result also is proved by the tensile mod-
ulus data as listed in Table 1. Gel content and melt flow
rate data present EPDM phase products crosslinked
structure after photo-irradiation. These can be suggested
that photo-irradiation significantly improves the inter-
face adhesion of different phases by photo-grafting re-
action to form grafted copolymer, such as SGF grafted
PP, SGF grafted EPDM, and PP grafted EPDM. The
interface adhesion plays a decisive role in determining
the mechanical properties of the resultant composites,
ensuring effective stress transfer from the matrix to the
SGF phase during impact or tensile deformation, which
gives rise to enhanced tensile and impact properties of
composites.
3.2. Crystal structure of PP
The WAXD spectra of unirradiated and photo-irra-
diated PP/EPDM, PP/EPDM/10%SGF, PP/EPDM/
30%SGF composites are shown in Fig. 1. It shows that
the 2h peaks of all samples at 14.1�, 16.8�, 18.5� and
21.2� due to the 110, 040, 130 and the overlapping 131,
041 and 111 planes are characteristics of a-type mono-
clinic crystal structure of PP. It proves that these sam-
ples contain a-type crystal. However, compared with PP/
EPDM curve, it can be obviously found that a new peak
at 16.2� appears for other five curves. This new peak has
been assigned to the (3 0 0) reflection of b-type hexago-
nal crystal structure of PP. Moreover, the b phase
fraction in the crystalline part of samples can be assessed
from the ratio of the height of main (3 0 0) b reflection to
the sum of the heights of four main crystalline reflec-
tions, i.e. (1 1 0), (0 4 0) and (1 3 0) from the a phase plus
(3 0 0) from the b phase, as proposed by Turner-Jones
[18]. The calculated results of b phase fraction for PP/
EPDM, PP/EPDMir, PP/EPDMir/10%SGF, PP/EPDM/
10%SGF, PP/EPDMir/30%SGF, and PP/EPDM/
30%SGF samples are 0%, 26.3%, 25.3%, 23.8%, 24.5%,
and 22.2%, respectively. It shows that the b phase
fraction in unirradiated samples is less than that in the
corresponding photo-irradiated samples, as the photo-
irradiated products act as a nucleating agent in PP
matrix. However, the incorporation of SGF decreases
the b-type crystal content in both unirradiated and
photo-irradiated samples, which leads to the reduction
of the impact strength of composites because the b-typehexagonal crystal has higher ductility and strength than
a-type monoclinic crystal with little loss of stiffness [19].
These results are also proved by the above mechanical
measurements.
12 14 16 18 20 22 24 26 28
PP/EPDM/30%SGFPP/EPDMir /30%SGF
PP/EPDM/10%SGF
PP/EPDMir /10%SGF
PP/EPDMir
PP/EPDM
16.2° (111)
(040)(131)
(130)
(040)(110)
2θ(°)
Fig. 1. WAXD spectra of unirradiated and photo-irradiated
PP/EPDM, PP/EPDM/10%SGF, PP/EPDM/30%SGF com-
posites.
2132 W. Wang et al. / European Polymer Journal 39 (2003) 2129–2134
3.3. Morphological structures
The SEM micrographs of the impact surfaces of
unirradiated and photo-irradiated PP/EPDM/30%SGF
Fig. 2. SEM images of composites: (a) and (c) for PP/EPD
samples are shown as photo (a) and photo (b) in Fig. 2,
respectively. The impact surfaces determined are per-
pendicular to the flow direction. The photo (a) shows the
clean surface of SGF, which implies that no adhesion
exists between SGF and PP/EPDM matrix. However,
the photo (b) for photo-irradiated sample shows the
SGF is packed closely by the polymer matrix and some
polymer matrix may link to the surface of SGF. The
dynamically UV irradiation not only improves the in-
terface adhesion for SGF but also makes the EPDM
crosslink. Photo (c) and photo (d) show the EPDM
component in the unirradiated and photo-irradiated
blends. It can be observed from photo (c) that the dense
black voids exist in the micrograph, which are EPDM
droplets that had been etched by xylene. After photo-
irradiation, the size and number of black voids in
photo (d) become smaller and less compared with that in
photo (c). It can be explained that the crosslinked
EPDM particles can not be etched by xylene due to the
gelled network nature. Consequently, the crosslinked
EPDM component can improve the stiffness of its
composite.
The fiber length distributions in photo-irradiated and
unirradiated PP/EPDM/30%SGF samples are shown in
Fig. 3. The blending and injection process reduce the
length of glass fiber as expected. However, it is very in-
teresting to be found that there is a difference between the
photo-irradiated and unirradiated samples. In photo-ir-
radiated sample, SGF is closely packed by the polymer
matrix as a jacket which prevents SGF from fracture.
M/30%SGF; (b) and (d) for PP/EPDMir/30%SGF.
0.0 0.2 0.4 0.6 0.8 1.00
5
10
15
20
25
30
35
uncrosslinked photocrosslinked
Num
ber f
ract
ion
(%)
Fiber length (mm)
Fig. 3. Number fraction vs fiber length distribution of unirra-
diated and photo-irradiated PP/EPDM/30%SGF composites.
0 100 200 300 400 500 600 700 800 900
0
20
40
60
80
100 PP/EPDM PP/EPDM/10%SGF PP/EPDMir /10%SGF
Wei
ght (
%)
Temperature (°C)
Fig. 4. TGA curves of PP/EPDM, PP/EPDM/10%SGF, and
PP/EPDMir/10%SGF composites.
W. Wang et al. / European Polymer Journal 39 (2003) 2129–2134 2133
Therefore, the maximum value of fiber length distribu-
tion for photo-irradiated sample located at 0.5 mm is
higher than that for unirradiated sample at 0.3 mm.
3.4. Thermal behavior
Table 2 lists the data from DSC curves for PP, dy-
namically photo-irradiated PP/EPDM and PP/EPDM/
SGF composites in the temperature range of 30–200 �C.It can be seen that the melting points slightly decrease
with the EPDM incorporation and increasing the SGF
content in the PP/EPDM/SGF samples, when compared
with that of PP. This is due to the fact that the non-
crystallizable component EPDM and solid SGF inhibit
the crystal growth of PP, which thus leads to the for-
mation of small and unperfected PP crystals. The data of
crystallinity also give another evidence for the nega-
tive effects of EPDM and SGF to the crystallinity of
composites. The crystal structure mainly provides the
stiffness of a composite. On the other hand, the crys-
tallization temperatures increase slightly with increasing
the SGF content in the composites. This result can be
explained by that SGF acts as a heterogeneous nucle-
ation agent for PP, although the total content of crystal
decreases. The above thermal analysis data are in accord
with the results obtained from WAXD.
Table 2
Melting behavior and crystallinity of PP, dynamically photo-irradiate
Sample code Heat of fusion
(DH ), J/g
Meltin
(Tm), �
PP 84.1 169.1
PP/EPDMir 70.0 168.4
PP/EPDMir/5%SGF 46.7 166.8
PP/EPDMir/10%SGF 37.7 165.4
PP/EPDMir/20%SGF 37.1 165.2
PP/EPDMir/30%SGF 36.0 165.0
Fig. 4 shows the thermogravimetric analysis curves
for PP/EPDM, PP/EPDM/10%SGF, and PP/EPDMir/
10%SGF composites in the temperature range of 20–800
�C. The curve of PP/EPDM sample shows that the initial
degradation temperature, degradation temperature, and
total weight loss are 238, 386 �C, and 98.9% respectively,
compared with 294, 446 �C, and 89.3% for PP/EPDM/
10%SGF sample. However, it was found that photo-
irradiation has a small influence on the thermal behavior
of PP/EPDMir/10%SGF. Therefore, the incorporation
of SGF into the composite plays an important role for
improving the thermal stability of a composite.
4. Conclusion
The SGF and photo-irradiation can considerably
improve the mechanical properties of PP/EPDM blends,
especially for the tensile strength and notched Izod im-
pact strength. The WAXD measurements substantiated
the formation of b-type crystal of PP, which partly en-
hances the impact strength of dynamically photo-irra-
diated PP/EPDM/SGF composites. The SEM images
demonstrated that photo-irradiation process increases
the interface adhesion of SGF and matrix, whereas de-
creases the aggregation of EPDM particles and thus in-
creases the sites for dissipation of shock or impact energy
d PP/EPDM, and PP/EPDM/SGF composites
g temperature
C
Crystallization tem-
perature (Tc), �CCrystallinity,
%
118.1 40.2
119.5 33.5
121.1 22.3
121.6 17.9
121.9 17.8
122.8 17.2
2134 W. Wang et al. / European Polymer Journal 39 (2003) 2129–2134
in photo-irradiated PP/EPDM/SGF composites. The
melting and crystallization temperatures of the photo-
irradiated composites are not affected greatly by in-
creasing the SGF content. The thermal analysis results
show that the incorporation of SGF into PP/EPDM
plays an important role for increasing its thermal sta-
bility.
Acknowledgement
Contract grant sponsor: National Natural Science
Foundation of China (no. 50073022).
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