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Effect of Coupling Agent Content and Water Absorptionon the Mechanical Properties of Coir-Agave FibersReinforced Polyethylene Hybrid Composites
Aida A. P�erez-Fonseca,1 Mart�ın Arellano,2 Denis Rodrigue,1 Rub�en Gonz�alez-N�u~nez,2
Jorge R. Robledo-Ort�ız3
1Department of Chemical Engineering and CERMA, Universit�e Laval, Quebec City, Quebec G1V 0A6,Canada
2Departamento de Ingenier�ıa Qu�ımica, Universidad de Guadalajara, Blvd. Gral. Marcelino Garc�ıa Barrag�an# 1451, Guadalajara, Jalisco 44430, M�exico
3Departamento de Madera, Celulosa y Papel, Universidad de Guadalajara, Carretera Guadalajara-Nogales km15.5, Las Agujas, Zapopan, Jalisco 45510, M�exico
In this study, high-density polyethylene/agave-coircomposites with two fiber contents (20 and 30 wt%)and different coir-agave fiber ratios (1–0, 0.8–0.2, 0.6–0.4, 0.4–0.6, 0.2–0.8, and 0–1) were produced in a two-step process using twin-screw extrusion followed byinjection molding. The effect of mixing two differentnatural fibers and the addition of coupling agent onwater absorption, mechanical properties, and morphol-ogy is reported. The rule of hybrid mixture was used topredict the properties of the composites, showing agood agreement with the experimental data. Theresults obtained showed that the combination of differ-ent fibers produces composites with unique character-istics as coir fibers absorb less water than agavefibers, while at the same time increase more tensileand flexural strengths. On the other hand, agave fiberswere found to improve the impact strength of coircomposites. Also, the effect of water absorption onthe mechanical properties was studied. Finally, the useof a coupling agent had a positive effect on mechani-cal properties, while lowering water uptake. POLYM.COMPOS., 00:000–000, 2015. VC 2015 Society of PlasticsEngineers
INTRODUCTION
Composites made from natural fibers have gained
increasing interest during the past decade. The addition of
natural fibers to polymer matrices reduces the consumption
of oil-based material and decreases density, abrasiveness,
cost, dermal, and respiratory irritation, as well as enhanc-
ing energy recovery compared to glass fiber composites
[1]. Therefore, manufacturing industries, especially pack-
aging, building construction, automotive, and furniture,
have been encouraged to use natural fibers in their applica-
tions instead of nonrenewable reinforcing materials [2].
Lignocellulosic fibers such as flax, jute, hemp, sisal, kenaf,
and bamboo have been extensively studied as replacement
for glass and carbon fibers [3]. The fact that these fibers
are obtained from natural resources makes them more
attractive in terms of sustainability and environmental
awareness [4]. However, the hydrophilic character of natu-
ral fibers results in poor interfacial bonding with most
polymer matrices limiting their applications.
Moisture absorption of composites containing natural
fibers has several adverse effects on their properties and
affects their long-term performance; i.e. increasing mois-
ture content is known to decrease mechanical strength
and change their dimensions. Numerous efforts have been
made to address this issue [1, 2, 5]. An alternative route
to overcome these disadvantages is the addition of cou-
pling agents which provides better fiber/matrix adhesion.
Chemical grafting using maleic anhydride is one of the
most popular, not only to modify the fiber surface,
exploiting the hydroxyl groups which are abundantly
available in cellulosic natural fibers, but also to entangle
with the polymer matrix achieving better interfacial bond-
ing resulting in better mechanical properties of the com-
posites [6].
In recent years, the development of composites with
reinforcing agents of more than one type and shape was
proposed to compensate their shortcomings, resulting in a
positive hybrid effect [7]. Hybridization using two types
Correspondence to: J.R. Robledo-Ort�ız; e-mail: [email protected]
DOI 10.1002/pc.23498
Published online in Wiley Online Library (wileyonlinelibrary.com).
VC 2015 Society of Plastics Engineers
POLYMER COMPOSITES—2015
of fibers having different lengths and diameters offers
some advantages over the use of each fiber alone in a
polymer matrix. Several studies on hybridization were
performed using combinations of natural fibers with glass
fibers [8, 9] to obtain materials with slightly lower
mechanical properties than using glass fibers alone, but
leading to composites with lower costs and weight.
Recently, the development of hybrid composites using
only natural fibers increased, showing that the combina-
tion of two natural fibers is a great option to get materials
with lower costs, friendlier to the environment and main-
taining good mechanical properties.
Zainudin et al. [10] prepared hybrid composites with
oil palm empty fruit bunch and coir fibers and found that
composites with 50:50 oil palm: coir fibers presented
optimum mechanical properties. Fernandes et al. [11] pre-
pared hybrid polyethylene cork/sisal composites and
found that addition of sisal in the presence of 2 wt% cou-
pling agent (based on maleic anhydride) improved the
tensile and flexural properties of the composites. P�erez-
Fonseca et al. [12] prepared polyethylene-pine/agave
composites and found that addition of agave to
polyethylene-pine composites in the presence of coupling
agent (based on maleic anhydride) increased tensile, flex-
ural, and impact strength, while the addition of pine to
polyethylene-agave composites reduced water uptake.
As a result of the advantages shown by previous stud-
ies with hybridization, hybrid composites based on high-
density polyethylene were prepared using two natural
waste fibers (agave and coir). Agave fiber is a waste of
the Tequila production process and has limited applica-
tion for this discarded fiber. On the other hand, coir
fibers are well known because of their high resistance
and low water absorption ability, but they are very abra-
sive to the processing equipment. In this sense, combina-
tion of these two fibers can produce composite materials
with unique properties at excellent costs. In particular,
the effect of water absorption and coupling agent addi-
tion on the composite mechanical properties is reported.
In particular, the effect of water absorption and coupling
agent addition on the composite mechanical properties is
reported.
EXPERIMENTAL
Materials
High-density polyethylene 60120U (PADMEX, Mexico)
with a melt flow index of 19 g/10 min (190�C/2.16 kg) and
density of 0.96 g/cm3 was used as the polymer matrix.
Coupling agent, maleated polyethylene Fusabond M603
(MAPE), was provided by Dupont Packaging and Indus-
trial Polymers (USA). Agave fibers (Agave tequilanaWeber var. Azul) were obtained from a local tequila com-
pany in Jalisco, Mexico. Coir fibers were provided by
Agrocoir S.A. de C.V., Colima, Mexico. The chemical
composition of the fibers is presented in Table 1. These
properties were determined according to TAPPI standards
T-204cm-97 (extractives), T-222-om-98 (lignin) and the
Jayme-Wise method (holocellulose).
Composites Preparation
The agave and coir fibers received a previous treat-
ment before being used. The fibers were soaked in water
for 24 hours and then passed through a Sprout-Waldron
refiner (D2A509NH) with two 30 cm diameter discs, one
fixed and the other rotating at 1,770 rpm to separate the
pith from the fibers. The fibers were then placed in a cen-
trifuge to remove excess water and finally dried outdoors.
Both fibers were milled and sieved to keep particles
between 50 and 70 mesh for agave and 100 and 140
mesh for coir. Two fiber contents (20 and 30 wt%) were
used in the formulations with different coir–agave fiber
weight ratios (1–0, 0.8–0.2, 0.6–0.4, 0.4–0.6, 0.2–0.8, and
0–1). The composites were prepared with and without
MAPE (3 wt% with respect to the total fiber content).
The materials were first processed in a twin-screw
extruder Leistritz Micro 27 GL/GG 32D with a tempera-
ture profile set to 140/150/150/160/160/160/170/170/
160�C. The extruder had three circular holes, each one
being 2 mm in diameter. The screw rotational speed was
set at 120 rpm giving a total flow rate of 4 kg/h.
The composites were cooled in a water bath and then
pelletized. The pellets were then oven-dried for 24 h at
65�C to be injection molded on a NISSEI ES 1000 with a
mold temperature of 30�C and a screw temperature pro-
file of 130/170/185/195�C. All the samples were prepared
in a rectangular mold cavity with dimensions of
8034032.5 mm3.
Morphology
Samples were submerged in liquid nitrogen and then
fractured. Micrographs of the exposed surfaces were
obtained by a scanning electron microscope HITACHI
TM-1000 to characterize the morphology; i.e. the state of
fiber adhesion/dispersion in the matrix before and after
water immersion.
TABLE 1. Characterization of agave and coir fibers.
Fiber Extractives (%) Cellulose (%) Lignin (%) Hemicellulose (%) Fiber length (mm) Fiber diameter (mm) L/D
Agave 6–7 58–65 21–24 10–13 1.49 0.18 8.27
Coir 4–6 38–46 37–41 10–15 1.10 0.12 9.16
2 POLYMER COMPOSITES—2015 DOI 10.1002/pc
Water Absorption Test
Water absorption tests were conducted according to
ASTM D570. Before testing, the weight of each specimen
was measured. Then, five specimens were submerged in
distilled water at 30 6 0.5�C for 160 days. The samples
were removed and weighted after specific time periods to
get water absorption kinetics curves. Each time, the sur-
face water was wiped off with a dry cloth and the sample
was immediately weighed before being returned in the
water bath. The amount of water absorption (Mt) was cal-
culated as
Mt5wi2w0
w0
3100 (1)
where wi is the weight of the sample after immersion and
w0 is the initial weight before water immersion.
Mechanical Properties
Impact strength of the composites was determined by a
Tinius Olsen model 104 impact tester. The specimens
were prepared according to ASTM D6110 and each value
represents the average of 10 notched (ASN automatic
sample notcher from Dynisco) samples. Flexural and ten-
sile properties were evaluated using a universal machine
Instron model 4411. Flexural tests were carried out
according to ASTM D790 and sample dimensions were
80312.732.5 mm3 with a span length of 41 mm. Six
samples per composition were tested at a crosshead speed
of 10 mm/min. Tensile tests were carried out using a load
cell capacity of 1 kN, and the specimens were tested
according to ASTM D638 (type V specimen). Testing
was performed at a crosshead speed of 5 mm/min with
seven specimens per composition. All the tests were per-
formed at room temperature (23�C), and all composites
were tested before and after water absorption to determine
the effect of water ageing.
Prediction of Properties by the Rule of Hybrid Mixture
The rule of hybrid mixture (RoHM) was used to pre-
dict the results of water absorption and mechanical prop-
erties of the hybrid composites. The base equation,
neglecting the interaction between two systems can be
written as (modified by Mirbagheri et al. [13]):
FIG. 1. SEM micrographs of HDPE-fiber composites with 30% of total fiber content. Agave: (a) 0% and
(b) 3% MAPE. Coir: (c) 0% and (d) 3% MAPE.
DOI 10.1002/pc POLYMER COMPOSITES—2015 3
rHc5rc1Xc11rc2Xc2 (2)
where rHc, rc1 and rc2 are the properties of HDPE/
coir-agave (hybrid), HDPE-agave and HDPE-coir compo-
sites respectively, while Xc1 and Xc2 are the relative fiber
mass fraction given by
Xc11Xc25Wf 1
Wf ;T1
Wf 2
Wf ;T51 (3)
where Wf,T is the total reinforcement mass fraction
(5 Wf1 1 Wf2).
RESULTS AND DISCUSSION
Morphology
The effect of coupling agent on agave and coir fibers
in the composite was observed via SEM micrographs.
Figures 1a and b present a fractured surface of HDPE-
agave composites without and with MAPE, respectively.
A clear reduction in the fiber–matrix interfacial space
because of coupling agent addition was observed (which
could be associated to better adhesion) as a result of the
reaction between the maleic anhydride groups of MAPE
and the hydroxyl groups of the fibers forming an ester
link. Furthermore, the nonpolar part (PE) of MAPE is
compatible with the HDPE matrix leading to macromo-
lecular entanglements [14]. Figures 1c and d show a frac-
tured surface of HDPE-coir composites without and with
MAPE, respectively. In these micrographs, similarly to
agave composites, it can be seen how MAPE improves
the polymer-coir fibers compatibility.
The effect of water absorption on composite morphol-
ogy is presented in Figs. 2 and 3. It can be observed that
agave composites were more affected by water uptake
than coir composites as Fig. 2b and d show higher agave
fiber damaged, with cracks on the fiber surface. This
behavior can be related to the chemical composition of
each natural fiber; i.e. the cellulose content of agave
fibers is higher than for coir fibers (see Table 1) leading
to more –OH groups available to form hydrogen bonds
with water molecules and higher water uptake. Water
absorption ageing may lead to the degradation of natural
fibers by a hydrolysis mechanism and its resulting effect
contributed to the loss of compatibilization between the
fibers and matrix. This phenomenon leads to fiber
debonding and weakening of interfacial adhesion.
FIG. 2. SEM micrographs of HDPE-agave composites with 30% of total fiber content before water uptake
with: (a) 0% and (b) 3% MAPE; and after water uptake with: (c) 0% and (d) 3% MAPE.
4 POLYMER COMPOSITES—2015 DOI 10.1002/pc
Furthermore, the degradation process occurs when swel-
ling of cellulose fibers develop stress in interfacial
regions leading to microcracks in the matrix around the
swollen fibers promoting capillarity and water transport
[15]. Since coir fibers have higher lignin content, which
is a hydrophobic compound, this leads to less fiber degra-
dation because of water uptake.
Water Absorption
Figure 4 shows the kinetics of water absorption for
hybrid composites where it can be seen that equilibrium
was reached at around 4000 hours and that composites
with higher fiber contents absorbed more water. For a
better comparison, equilibrium moisture content of the
hybrid composites was plotted in Fig. 5. It can be
observed that agave fiber composites absorbed more
water than coir fibers. When the fiber content is 30%,
HDPE-agave composites absorbed 6.7% of water, while
HDPE-coir composites absorbed only 3.8%. This behavior
is again related to the chemical composition of each fiber
as mentioned above: agave fibers have more –OH groups
which can interact with water molecules. It is known that
the macromolecular structure, and in particular the
hydroxyl groups, of polysaccharides are highly hydro-
philic which can attract water molecules via hydrogen
and van der Waals bonds. All these effects are contribut-
ing to higher water storage capacity of the composites
[16].
Moisture penetration into the composites can occur via
different mechanisms. The main process consists of water
molecules diffusion inside the microgaps between poly-
mer chains. Other common mechanisms are capillary
transport into the gaps and flaws at the interfaces between
fibers and matrix because of incomplete wettability and
impregnation, as well as transport by microcracks in the
matrix formed during compounding [17]. In this study, it
was observed that higher cellulose content in the fibers
enhanced these mechanisms. For composites with 30% of
agave fiber, the maximum amount of water absorbed was
6.7%, while the amount was reduced to 4.4% when using
MAPE. The use of coupling agents plays an important
role in this phenomenon because of the esterification
reaction between hydroxyl groups and maleic anhydride,
which causes a reduction in interfacial tension and
increases interfacial adhesion between the polymer and
fibers [18]. Also, this reaction reduced the number of
OH-group available to interact with water molecules. For
FIG. 3. SEM micrographs of HDPE-coir composites with 30% of total fiber content before water uptake
with: (a) 0% and (b) 3% MAPE; and after water uptake with: (c) 0% and (d) 3% MAPE.
DOI 10.1002/pc POLYMER COMPOSITES—2015 5
coir composites, the effect of MAPE addition was less
significant (water absorption decreased from 3.8% to
3.4%) since the fibers are less hygroscopic.
Water absorption results showed that mixing coir with
agave fibers in a polymer matrix produced hybrid compo-
sites which absorb less water than composites with agave
fibers alone. For example, hybrid composites with a fiber
content of 30% and 0.4–0.6 (coir-agave) ratio absorbed
28% less water than composites made with agave fibers
alone. A comparison of the experimental and predicted
moisture content values using the RoHM equation is also
presented in Fig. 5 where good agreement is observed.
Tensile Properties
Tensile strength results are shown in Fig. 6. It can be
seen that using agave fibers alone, tensile strength
decreases with increasing fiber content. This is related to
poor interfacial adhesion between agave fibers (highly
hydrophilic) and the polymer matrix. On the other hand,
the fact that coir fibers are less hydrophilic can explain
why tensile strength loss was lower when the fiber con-
tent increased. Hybrid composites prepared with agave
and coir fibers without MAPE showed that for 20% fiber
content, the maximum tensile strength was achieved with
higher agave contents (22 MPa), but in the case of 30%
fiber content, tensile strength was more increased with
higher coir contents because the maximum was achieved
for composites using coir fibers alone (23 MPa). For all
hybrid composites, the tensile strength was lower than the
neat HDPE (28 MPa) because fiber surfaces have waxes
FIG. 4. Water absorption kinetics for hybrid composites: 20% of total fiber content (a) without and (b)
with MAPE and 30% of total fiber content (c) without and (d) with MAPE.
FIG. 5. Equilibrium moisture content of HDPE/coir-agave composites
with different fibers contents. (M) denotes composites prepared with 3%
MAPE and the lines are predictions using Eqs. 2 and 3.
6 POLYMER COMPOSITES—2015 DOI 10.1002/pc
and other noncellulosic substances such as hemi-cellulose,
lignins and pectin, which create poor adhesion between
the matrix and the fibers. Agave fibers contain more cellu-
lose than coir fibers and it is known that fiber tensile
strength increases with cellulose content [19]. Moreover,
when fiber content increases there is more fiber agglomer-
ation leading to lower tensile strength. Table 1 shows that
agave fibers were longer than coir fibers and this increased
the probability of fiber–fiber contact, resulting in higher
agglomeration and void formation lowering interfacial
stress transfer. For both fibers, it was found that the addi-
tion of MAPE increased tensile strength: 16% (26 MPa)
and 19% (25 MPa) for composites using coir or agave
fibers, respectively. The use of coupling agents based on
maleic anhydride (MA) increases tensile strength because
of the esterification reaction between the fibers hydroxyl
groups and the anhydride part of MA leading to interfacial
tension reduction and improved interfacial adhesion
between the matrix and the fibers [11].
It was observed that water uptake decreased tensile
strength at 30% fiber content without MAPE (from 21 to
19 MPa), while at higher coir fibers content this property
was maintained. Composites with MAPE had similar ten-
sile strength before and after water uptake at 20% fiber
content (around 22 MPa), while for composites at 30%
the values decreased with the amount of agave fibers in
the composite (from 25 to 23 MPa). Azwa et al. [15]
reported that lower mechanical properties are because of
debonding at the fiber/matrix interface, as well as fiber
degradation during water ageing. Swelling of natural fill-
ers can also develop shear stress at the interface which
facilitates debonding of the fibers from the matrix leading
to tensile strength reduction [18].
The tensile modulus results (Fig. 7) were very similar
for all hybrid composites prepared with and without
MAPE (around 400 and 500 MPa for 20 and 30% fiber
content) before water uptake. But after water uptake,
composites with MAPE maintained their modulus values
while decreases were observed without MAPE: 15% in
composites with higher amount of agave fibers (510 to
431 MPa), as well as tensile strength for coir composites
for which the tensile modulus was similar (around 475
MPa). Nevertheless, all modulus values of hybrid compo-
sites before or after water uptake were higher than the
neat HDPE tensile modulus (295 MPa). It has been
FIG. 6. Tensile strength of HDPE/coir-agave composites before and
after water absorption with (a) 20% and (b) 30% of fiber content. (M)
denotes composites prepared with 3% MAPE and the lines are predic-
tions using Eqs. 2 and 3.
FIG. 7. Tensile modulus of HDPE/coir-agave composites before and
after water absorption with (a) 20% and (b) 30% of fiber content. (M)
denotes composites prepared with 3% MAPE and the line are predictions
using Eqs. 2 and 3.
DOI 10.1002/pc POLYMER COMPOSITES—2015 7
reported that decreases in tensile modulus because of
water absorption are related to the amount of water
absorbed. Tamrakal et al. [20], working on
polypropylene-wood composites, reported that tensile
modulus was not affected when the composites absorbed
around 4–5% of water, while composites absorbing more
than 8% presented important decreases in tensile modulus
because of more microcracks formation.
It was observed that the RoHM equation was able to
predict the tensile strength of hybrid composites knowing
the properties of the composites prepared with a single
type of fiber. Similar studies have shown that RoHM,
despite being a very simple model, can predict the
mechanical properties of hybrid composites compared to
more complex models [7, 13].
In the case of tensile modulus, RoHM showed differ-
ences between experimental and calculated values indicat-
ing that RoHM can have some limitations because it
neglects some factors. As fiber loading increases, more
particle–particle interaction is expected. Moreover, the
maximum packing fraction of each particle depends on
their size and shape distribution, which is not considered
in the RoHM [21].
Flexural Properties
Flexural strength results are presented in Fig. 8. Flex-
ural strength without MAPE was very similar for all
hybrid composite compositions: around 24 and 29 MPa
for 20% and 30% fiber content, respectively (higher than
22 MPa for neat HDPE). This is mainly attributed to the
reinforcing effect imparted by the fibers, which allowed a
uniform stress distribution from the continuous polymer
matrix to the dispersed fiber phase [22]. The hybrid com-
posites prepared with coupling agent showed that the
addition of MAPE increased the flexural strength of all
the composites (6–12%), the maximum being achieved
for HDPE-coir composites at 30% (32 MPa). As men-
tioned before, agave and coir fibers have different dimen-
sions and chemical composition, which explains why coir
properties were more enhanced by MAPE addition. El-
Sabbagh [6] obtained similar results with sisal, hemp, and
flax composites where he reported that sisal fibers had
the lowest improvement with maleated polypropylene
(MAPP) because of a lower number of available sites for
fiber surface–MAPP interaction because of their relatively
larger sizes.
The high agave ratio composites at 30% fiber content
were more affected by water exposure, with flexural
strength reduction from 29 to 25 MPa. Water molecules
penetrate into the composites through microcracks and
reduce interfacial adhesion between the fibers and the
matrix, causing fiber swelling creating cracks in the
matrix and eventually leading to fiber debonding [23].
The cellulose molecules are held tightly together inside
the fibrils by bonds between molecules lying closely
alongside one another. However, water can penetrate this
cellulose network and move into the capillaries and
spaces between the fibrils. In this case, water molecules
tend to force the cellulose molecules apart, reducing the
forces holding them together and lowering their rigidity
because water acts like a plasticizer and improves the
motion of cellulose molecules [1]. Consequently, cellu-
lose is softened and swelled leading to fiber dimensional
changes. Because of higher cellulose content, agave-based
composites are more susceptible to water uptake. Addi-
tion of coir to agave composites helped to prevent this
property loss after water uptake. In all cases, flexural
strength reduction (around 5%) for composites with
MAPE was the same for all hybrid combinations.
Flexural modulus is presented in Fig. 9 and the values
are very similar for all hybrid combinations, but change
with fiber content (566 MPa for neat HDPE, 900 MPa at
20% and 1100 MPa at 30%). It can be observed that fiber
content is an important parameter related to water absorp-
tion. For composites at 20% fiber content, the reduction
is less than 2%, while at 30% the reduction is 9%. The
addition of MAPE had a positive effect on flexural modu-
lus by lowering the effect of water absorption. Similarly
FIG. 8. Flexural strength of HDPE/coir-agave composites before and
after water absorption with (a) 20% and (b) 30% of fiber content. (M)
denotes composites prepared with 3% MAPE and the lines are predic-
tions using Eqs. 2 and 3.
8 POLYMER COMPOSITES—2015 DOI 10.1002/pc
to tensile properties, the RoHM was able to predict the
flexural strength and flexural modulus values before and
after water uptake.
Impact Strength
Impact strength results (Fig. 10) show that agave fiber
composites have higher impact strength compared to coir
fiber composites. HDPE-agave composites at 30% fiber
content had an impact strength of 53 J/m, HDPE-coir
composites had only 37 J/m, while neat HDPE has an
impact strength of 46 J/m. It has been reported that natu-
ral fibers can improve the impact behavior of polymers,
especially when long fibers were used [24] as it was the
case of agave fibers. Oksman et al. [25] studied the effect
of different fibers on the mechanical properties of poly-
propylene (PP) composites and found that sisal fibers
increased more significantly the impact strength of PP
composites than other fibers like flax and jute, showing
that sisal fibers were the toughest (agave tequilana is
from the same gender of sisal). Wambua et al. [26] men-
tioned that impact strength of fiber-reinforced polymers is
governed by the fiber–matrix interfacial bonding and the
individual properties of both fiber and matrix. When the
composites undergo an impact, the energy is dissipated
by the combination of fiber pullouts, fiber fracture, and
matrix deformation/cracking. For example, Alomayri
et al. [23] prepared composites of poly(lactic acid) and
reported a substantial impact strength improvement
because of the addition of cotton fibers. They concluded
that this increase was related to the higher elongation at
break of cotton fibers. High cellulose content in fibers
generally produce higher elongations at break. Since cot-
ton has a cellulose content around 88–96%, elongation at
break and impact strength were directly correlated.
In our case, it was observed that hybridization of coir
composites with agave fibers produced composites with
better impact strength. For example, a combination 40–
60% (agave-coir fibers) increased this property (compared
with coir alone) by up to 18% (from 37 to 44 J/m) with-
out MAPE and by up to 10% (45 to 49 J/m) with MAPE.
With respect to MAPE, its addition produced an impact
strength improvement only for composites at 30% fiber
content (between 5 and 7 J/m), while at 20% a negligible
effect was observed. Similar results were reported by
P�erez-Fonseca et al. [12] where a more important
FIG. 9. Flexural modulus of HDPE/coir-agave composites before and
after water absorption with (a) 20% and (b) 30% of fiber content. (M)
denotes composites prepared with 3% MAPE and the lines are predic-
tions using Eqs. 2 and 3.
FIG. 10. Impact strength of HDPE/coir-agave composites before and
after water absorption with (a) 20% and (b) 30% of fiber content. (M)
denotes composites prepared with 3% MAPE and the lines are predic-
tions using Eqs. 2 and 3.
DOI 10.1002/pc POLYMER COMPOSITES—2015 9
coupling agent effect was observed at higher fiber con-
tents (30%) increasing the impact strength of HDPE/
pine-agave hybrid composites. Also, Fig. 10 shows that
after water uptake the impact strength of hybrid compo-
sites increased substantially, the maximum obtained was
for composites at 30% of agave fiber alone and MAPE
after water immersion (73 J/m). Nevertheless, it was
found that impact strength improvement was around 20%
and 30% for all compositions regardless of fiber type.
Once the moisture penetrates inside the composite, the
fibers tend to swell. The matrix structure can also be
affected by water uptake processes such as chain reorienta-
tion and shrinkage [4]. These results are similar to those
found by Alamri and Low [2] and Karmaker [27]. Lin
et al. [17] evaluated the effect of water absorption time
and temperature on the mechanical properties of wood
composites and found that impact strength increased with
exposure time. They explained that swelling of wood fibers
made it difficult to pull the fibers out of the matrix (more
contact leading to more friction). Once again, the RoHM
equation could properly represent the experimental impact
strength values for all the hybrid composites prepared.
CONCLUSION
In this study, it was shown that a combination of coir
and agave fibers in HDPE is a good option to produce
hybrid composites with better properties than those using
coir or agave fibers alone. While agave fibers enhanced
impact strength, coir fibers enhanced flexural and tensile
strength and decreased water uptake. Composite proper-
ties with both fibers were also improved by the addition
of a coupling agent (MAPE), obtaining materials with
higher impact, tensile, and flexural strength. In general,
the tensile and flexural properties of the composites
decreased after moisture uptake because of the effect of
water molecules modifying the structure and properties
of the fibers, matrix, and mostly their interface. Addition
of MAPE also helped to decrease water uptake limiting
composite degradation when exposed to water. On the
other hand, impact strength was increased after water
absorption for all the hybrid composites because fiber
swelling made it more difficult to pull the fibers out of
the matrix. Finally, the simple rule of hybrid mixture
(RoHM) was found to predict with good precision the
effect of fiber ratio on tensile, flexural, and impact prop-
erties of hybrid composites with or without MAPE, as
well as before and after water uptake.
ACKNOWLEDGMENTS
The authors gratefully acknowledge Agrocoir S.A. de
C.V. (Colima, M�exico) for supplying coir fibers. One of the
authors (A.A.P.F.) acknowledges the financial support of
the Mexican National Council for Science and Technology
(CONACyT #266256) for a scholarship.
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10 POLYMER COMPOSITES—2015 DOI 10.1002/pc