Cure Kinetics of Exfoliated Bio-based Epoxy/Clay Nanocomposites Developed from Acrylated Epoxidized...
Transcript of Cure Kinetics of Exfoliated Bio-based Epoxy/Clay Nanocomposites Developed from Acrylated Epoxidized...
Original Article
Cure kinetics of exfoliated bio-basedepoxy/clay nanocomposites developedfrom acrylated epoxidized castor oil anddiglycidyl ether bisphenol A networks
Nagarjuna Reddy Paluvai1,2, S. Mohanty2 and S. K. Nayak1,2
AbstractA bio-based epoxy monomer was synthesized by acrylation of epoxidized castor oil (ECO). Subsequently, acrylated ECO(AECO)-toughened diglycidyl ether of bisphenol A (DGEBA) nanocomposites were prepared via sol–gel process with theaddition of organically treated montmorillonite nanoclays. In this study, the curing kinetics of anhydride-cured DGEBA/AECOmonomer with and without clays was studied by non-isothermal differential scanning calorimetry analysis. The apparent acti-vation energy obtainedbyFlynn–Wall–Ozawa method was reduced from 63 to59kJ mol�1 and 69 to61kJ mol�1, respectively,with the addition of 1 wt% clay to the DGEBA/10 wt% AECO and DGEBA/20 wt% AECO systems, respectively. The two-parameter Sestak–Berggren autocatalytic model was used to obtain the reaction orders m and n, respectively. The curvesobtained by the Malek method show good agreement with the experimental data for bio-based epoxy systems.
KeywordsAcrylated epoxidized castor oil, cure kinetics, diglycidyl ether of bisphenol A, montmorillonite clays
Introduction
Petroleum-based polymers have been attracting interest
because of their potential applications, which range from
commodity to aerospace industry. In recent years, renew-
able-based polymer products have become increasingly
important due to environmental concerns, sustainability,
and rapid depletion of petroleum-based polymers.1–4 Bio-
based polymers are derived from plants, such as cellulose,
fatty acids, starch, and sugars, which can replace the
petroleum-based polymers.5 Monomers derived from unsa-
turated fatty acid compounds such as vegetable oils are cur-
rently being given significant attention in industrial
applications due their abundance, low cost, and the pres-
ence of more functional groups.6,7 These oils are converted
into polymers through various polymerization techniques
that have been reported in earlier studies.8–14
Epoxy resins are one of the most important thermo-
setting polymers that are widely used in many industrial
applications due to their superior mechanical, thermal,
dielectric, insulating, and optical properties. The molecular
structure of the epoxy monomer can be easily modified due
to its versatile properties.4,15,16 The major disadvantage of
cured monomers is low toughness due to the presence of
aromatic groups on their backbone. To address this, the
toughness of brittle epoxy resin is increased by adding elas-
tomers and thermosetting and thermoplastic polymers to
it.4,17 However, the use of elastomers and other polymers
reduces some of the macroscopic and microscopic proper-
ties of the epoxy resin.16–20 In this regard, several attempts
have been made to develop bio-based polymers, modify
and then to improve the physical and chemical performance
of epoxy monomers, and to protect the environment from
carbon emissions.3 Herein, castor oil (CO)-based polymers
have been synthesized and used to modify the epoxy
1 Advanced Research School for Technology & Product Simulation
(ARSTPS), Central Institute of Plastics Engineering and Technology
(CIPET), Chennai, Tamil Nadu, India2 Laboratory for Advanced Research in Polymeric Materials (LARPM),
Central Institute of Plastics Engineering and Technology (CIPET),
Bhubaneswar, Odisha, India
Corresponding author:
Nagarjuna Reddy Paluvai, Advanced Research School for Technology &
Product Simulation (ARSTPS), Central Institute of Plastics Engineering
and Technology (CIPET), Chennai, Tamil Nadu, India.
Email: [email protected]
High Performance Polymers2015, Vol. 27(8) 918–929ª The Author(s) 2015Reprints and permission:sagepub.co.uk/journalsPermissions.navDOI: 10.1177/0954008314566052hip.sagepub.com
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monomers due to their low-cost preparation, easy process-
ing, and ability to make partially or fully sustainable mate-
rials. CO is one of the most abundant vegetable oils, also
renewable, biodegradable, biocompatible, and is of low
cost. It contains unsaturated fatty acid compounds (i.e, rici-
noleic acid (12-hydroxy-cis-9-octadecenoic acid)) that
have been used to develop eco-friendly polymers via in situ
polymerization processes.21–23 However, one of the main
disadvantages of bio-based polymers obtained from CO is
the poor mechanical properties they exhibit. Thus, the
novel bio-based acrylated epoxidized CO (AECO) resins
have been obtained by the acrylation of ECO resin to
improve their thermomechanical properties and water resis-
tance due to the presence of pendant acrylic double bonds,
which readily participate in the free radical reaction.24,25
AECO has been considered as a partial replacement of digly-
cidyl ether of bisphenol A (DGEBA) epoxy monomer in
developing industrial components. For example, several
studies have reported on the acrylated epoxidized soybean
oil (AESO) system for making greener composites.26–28
Further, the AECO-toughened DGEBA epoxy systems
are reinforced with nanoparticles to enhance their mechan-
ical and thermal properties. Nanocomposites are formed by
mixing different organic or inorganic fillers such as silica
particles, aluminum nitride nanoparticles, organoclay, tita-
nium dioxide, and mesoscopic into the polymer matrix to
improve their properties.29–33 Herein, organically treated
montmorillonite (OMMT) clays were used to prepare the
acrylated epoxy nanocomposites to enhance their polymer
properties. Kardar et al.34 used nano-alumina particles to
improve the physical–mechanical properties of epoxy acry-
late composites. Thielemans et al.35 have prepared AESO
nanocomposites and observed a 30% enhancement in their
mechanical properties. It is well known that the properties
of cured epoxy monomers depend on the curing conditions
such as the temperature and the time.36 Differential scan-
ning calorimetry (DSC) technique was used to study the
kinetics of cure reaction under non-isothermal modes.37–41
A variety of kinetic models had been proposed to inves-
tigate kinetic parameters, such as Kissinger,42,43 Flynn–
Wall–Ozawa,44 Kamal,45 autocatalytic,46 and Borchardt
Daniels47 methods. Sestak–Berggren model applied to a
two-parameter autocatalytic model to give emphasis to the
cure kinetics of epoxy systems by non-isothermal DSC.48,49
The objective of this study is to understand the effect of
OMMT clays on the cure mechanism and kinetics of AECO-
toughened DGEBA epoxy systems. The chemical structures
and functional groups of CO, ECO, and AECO systems were
examined by Fourier transform infrared (FTIR) and nuclear
magnetic resonance (NMR) spectroscopies. DSC technique
was used to investigate non-isothermal cure kinetics of bio-
based systems. The cure kinetic parameters were obtained by
applying iso-conversional Kissinger and Flynn–Wall–Ozawa
methods and a two-parameter Sestak–Berggren autocatalytic
model.
Experimental
Materials
Anhydrous sodium sulfate, acrylic acid, diethyl ether, glacial
acetic acid, hydrogen peroxide (30 wt.%), hydroquinone,
sodium carbonate, sulfuric acid (98%), triethylamine, and
other analytical grade products used were procured from
Fisher Scientific Company (Hyderabad, Telangana, India).
CO was procured from SD Fine-Chem Limited (Mumbai,
Maharashtra, India). DGEBA epoxy resin (viscosity: 9–
12 Pa s and epoxide equivalent: 182–192 g eq�1) was sup-
plied by M/s Allied agencies Ltd., Hyderabad, Telangana,
India. OMMT Cloisite 30B contains bis(2-hydroxyethyl)
methyl tallow ammonium ions from Southern Clay Products
(Gonzales, Texas, USA) and were used as filler. Methylhex-
ahydrophthalic anhydride (MHHPA), benzyltriethylammo-
nium chloride (TEBAC), and 3-aminopropyltriethoxy
silane were purchased from Sigma-Aldrich (Bangalore, Kar-
nataka, India).
Synthesis of ECO
Typically, ECO was synthesized by the following procedure:
100 g of CO, 26 g of glacial acetic acid, and 29 g of H2SO4
were charged to a three-necked round flask. The mixture was
rapidly stirred for 30–40 min at 55�C. The epoxidation reac-
tion was carried out using 80 g of H2O2 (30 wt%) slowly
added dropwise using a funnel to the mixture for 3 h at
55–60�C. After the addition of all reagents, the obtained
mixture was further stirred at 55�C for 7 h. The reacted mix-
ture was then extracted using diethyl ether in a separating
funnel and followed by washing two times with 10 wt% of
sodium carbonate (Na2CO3) solution. The distilled water was
used to remove the free acids. The collected organic phase
was kept in a vacuum oven at 70�C overnight to remove
diethyl ether and to obtain a light reddish viscous liquid
of ECO (yield: 97 g, average epoxy equivalent weight ¼278 g eq�1, oxirane oxygen of about 6.19%).3,8,50,51
Synthesis of AECO
A mixture of ECO (50 g) and acrylic acid (12 g) containing
0.5 wt% hydroquinone was charged into a 250-ml round-
bottomed flask and stirred at 70�C for 30 min. Then,
triethylamine (2 g) was added to the mixture and stirred for
another 1 h at 45–60�C. An additional amount of acrylic
acid (8 g) was added to the mixture and then kept at
60�C for another 1 h. The mixture was brought to room
temperature and then the unreacted acrylic acid was
removed by dissolving the product in diethyl ether and
washed several times with 10% sodium carbonate solution.
The product was washed with saturated sodium chloride
solution and dried over magnesium sulfate. The collected
organic phase of AECO was kept in a vacuum oven at
70�C for 4 h to remove diethyl ether.9,28,29
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Sample preparation
Bio-based epoxy nanocomposites were prepared by adding
1 wt% clay to the DGEBA/AECO systems. Prior to the addi-
tion of clays, the different weight ratios of 10, 20, 30, and 40
wt% AECO-toughened DGEBA epoxy systems were pre-
pared by mechanical mixing for 2 h followed by sonication
for 30 min. OMMT clays were dried in an oven at 120�C for
4 h. High-pressure mixing method was chosen to disperse
the clays into DGEBA/AECO systems.52 OMMT clays were
dispersed in acetone and mixed at 1400 r min�1 for 20–30
min until a wet slurry was obtained. The slurry was com-
bined with a mixture of DGEBA/AECO at room tempera-
ture with a mechanical stirring for about 4 h to obtain a
homogeneous liquid. Then the mixture was sonicated for
about 2 h with pulse mode (15 s on/15 s off) to achieve a tem-
perature of 70�C to remove the acetone. After that, a stoi-
chiometric ratio of MHHPA and TEBAC were added to
the sonicated mixture and continuously stirred for 10 min
at room temperature using a mechanical stirrer. The opti-
mum weight of the uncured sample was placed in the DSC
pan and dynamically cured from room temperature to
200�C at various heating rates to obtain the characteristics
of the exothermic peak. The prepared samples for this inves-
tigation were named as E1–E4 (DGEBA/10–40% AECO)
and EC1–EC4 (DGEBA/10–40% AECO/1% OMMT).
Characterizations
FTIR spectra of CO, ECO, and AECO systems were
recorded using a Perkin-Elmer 1720X (Norwalk, California,
USA) spectrometer. Each sample was placed between two
potassium bromide disks, and the spectrum was obtained
by co-adding 64 consecutive scans with a resolution of 4
cm�1 within the range of 400–4000 cm�1 using a DTGS
detector.
The proton NMR (1H NMR) spectra of CO, ECO, and
AECO were recorded on a Bruker Avance III 500 MHz
(AV 500) NMR Spectrometer (Billerica, Massachusetts,
USA) operating at 400 MHz. Tetramethylsilane was used
as the internal standard and deuterated chloroform (CDCl3)
as the solvent.
Dynamic DSC analysis of samples was carried out using
a differential scanning calorimeter (Q 50, TA Instruments,
New Castle, Delaware, USA) as per ASTM E 1868, sam-
ples of �10 mg were secured from 0�C to 200�C at differ-
ent heating rates (5, 10, 15, and 20�C min�1) under nitrogen
atmosphere.
Kinetic models
The cure kinetics has been studied using DSC analysis.
The basic assumption in DSC analysis of cure kinetics is
that the area under the exothermic curve is proportional
to the conversion or degree of the cure (�) and can be
expressed as53:
�ðtÞ ¼ HðtÞ�HT
ð1Þ
where �HT is the total heat of cure reaction and H(t) is the
partial heat of cure reaction at time t. The rate of conversion
(d�/dt) at a given temperature (T) is usually obtained by54:
d�
dt¼ q
d�
dt¼ dHðtÞ
�HTdtð2Þ
where q ¼ dT/dt is the heating rate and dH(t)/dt is the
instantaneous heat flow. The cure reaction is carried out
at a constant heating rate and then the �rate of the kinetic
process can be expressed as55:
d�
dt¼ KðTÞ � f ð�Þ ð3Þ
where K(T) is the temperature-dependent reaction rate con-
stant, T is the absolute temperature, and f(�) is a dependent
kinetic model function. The reaction rate constant is usu-
ally assumed to be of Arrhenius form56:
KðTÞ ¼ A exp�Ea
RT
� �ð4Þ
where the parameters A is the pre-exponential factor, R
is the gas constant (8.31 J mol�1 K�1), and Ea is the app-
arent activation energy. It is calculated using various
iso-conversional methods such as Kissinger and Flynn–
Wall–Ozawa method. According to the Kissinger analysis,
the equation (5) is expressed as:
� lnq
T2max
� �¼ Ea
RTmax
� lnAR
Ea
� �ð5Þ
where, Tmax is the peak temperature and A is the pre-
exponential factor. The activation energy could be calculated
from the plot of an approximately linear relationship of�ln(q/
Tmax2) versus 1/Tmax with the correlation of experimental
data. The Flynn–Wall–Ozawa model was also used to calcu-
late the Ea throughout the entire reaction. According to the
Flynn–Wall–Ozawa analysis, equation (6) is expressed as:
log q ¼ logAEa
g �ð ÞR� 2:315� 0:4567Ea
RTmax
� �ð6Þ
where g(�) is a conversion-dependent function, and other
parameters are the same as described earlier. To determine
the corresponding activation energy at each degree of cure,
a plot of log q versus 1000/Tmax was drawn. The resulting
slope obtained from linear fitting plot indicates the activa-
tion energy. For non-isothermal DSC analysis of thermo-
setting resin cure, f(�) can be obtained using
autocatalytic models. Sestak–Berggren proposed that two
independent reaction orders can be considered: m and n
as shown in equation (7).48
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d�
dt¼ A exp
�Ea
RT
� �ð1� �Þn�m ð7Þ
On the other hand, Malek proposed two special func-
tions, y(�) and z(�), and can be expressed as57:
yð�Þ ¼ d�
dtexpðxÞ ð8Þ
zð�Þ ¼ �ðxÞ d�dt
T
qð9Þ
where x is reduced activation energy (Ea/RT) and �(x) is
the expression related to the temperature integral, which
can be approximated using the equation of Senum and
Yang58:
� xð Þ ¼ x3 þ 18x2 þ 88xþ 96
x4 þ 20x3 þ 120x2 þ 240xþ 120ð10Þ
The values of both y(�) and z(�) functions normalized
within the interval from 0 to 1. The kinetic parameters such
as n, m, and A can be obtained from the curves of normal-
ized y(�) and z(�) versus the degree of cure (�). The curves
of y(�) and z(�) exhibit maxima at �M and �1p , respec-
tively. The mean of �M is used to calculate the kinetic para-
meters. The ratio of reaction order, p ¼ m/n as pointed out
by Malek, can be replaced by:
p ¼ m
n¼ �Mm
1� �Mm
ð11Þ
where �Mm is the mean of �M.
Results and discussions1H NMR spectroscopy
The synthesis reactions of CO, ECO, and AECO systems
are shown in Figure 1. 1H NMR spectroscopy analysis was
performed to confirm the chemical structures in CO, ECO,
and AECO, depicted in Figure 2. The characteristic signals
appeared at 5.3 to 5.7 ppm of CO associated with C¼C
bonds which got converted into an oxirane ring at 2.8 to
3.2 ppm in case of ECO.31–34 The peaks obtained in AECO
from 5.7 to 6.2 ppm indicate the presence of C¼C of the
acrylate ester.24,51,52
FTIR spectroscopy
Figure 3 shows the infrared spectra of the CO, ECO, and
AECO systems. The spectrum of ECO shows OH stretching
at 3400 cm�1, CH2-asymmetric stretching at 2927 cm�1, sym-
metric stretching at 2852 cm�1, asymmetric C¼O ester at 1744
cm�1, epoxy group at 1244 and 844 cm�1, asymmetric C–O–C
Figure 1. The possible synthesis mechanism of ECO and AECO systems. ECO: epoxidized castor oil; AECO: acrylated epoxidizedcastor oil.
Figure 2. 1H NMR spectra of the CO, ECO, and AECO sys-tems. 1H NMR: proton nuclear magnetic resonance; CO: castoroil; ECO: epoxidized castor oil; AECO: acrylated epoxidizedcastor oil.
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ester at 1165 cm�1, respectively. The acrylation of ECO was
further confirmed by the appearance of FTIR peaks at 1639,
1462, and 1400 cm�1 corresponding to acrylate groups.59–62
DSC analysis
To identify the curing process of E1–E4 and EC1–EC4 sys-
tems, DSC analysis (with 10�C min�1 heating rate) was
undertaken and the corresponding thermograms are shown
in Figures 4 and 5. The data presented in Table 1 indicate
the heat of reaction, which decreased with the increasing
AECO content within the DGEBA resin. This phenomenon
is primarily due to the decrease of rate of reaction with the
addition of AECO to the DGEBA resin, which decreases in
the cross-linking density. As shown in Figure 4, the cure
reaction of exothermic peaks of E1–E4 increased with the
addition of AECO to the tune of 10 to 40 wt% to the
DGEBA system. It is evident that Tend decreased from
159 to 175�C, which indicated the fact that the rigid aro-
matic groups of DGEBA were replaced by the flexible
groups of AECO resin. Then plasticization increased with
the lack of chemical interactions between the DGEBA and
higher concentrations of AECO resin. As shown in Table 1,
the heat of reaction (�H) obtained for the E1, E2, E3, and
E4 were 524, 440, 412, and 324 J g�1, respectively. These
values suggest that the mixing of AECO into DGEBA
needs more heat for the curing process. Figures 4 and 5
show that the curing reaction of EC1–EC4 had lower
exothermic (low �H) values than that of E1–E4 sys-
tems.63,64 The enthalpies of the DGEBA/AECO/OMMT
samples were decreased which is attributed to the catalytic
Figure 3. FTIR spectra of the CO, ECO and AECO systems. FTIR:Fourier transform infrared; CO: castor oil; ECO: epoxidized castoroil; AECO: acrylated epoxidized castor oil.
Figure 4. DSC thermograms of DGEBA/AECO blends. DSC:differential scanning calorimetry; DGEBA: diglycidyl ether ofbisphenol A; AECO: acrylated epoxidized castor oil.
Figure 5. DSC thermograms of DGEBA/AECO/OMMTnanocomposites. DSC: differential scanning calorimetry; DGEBA:diglycidyl ether of bisphenol A; AECO: acrylated epoxidizedcastor oil; OMMT: organically modified montmorillonite.
Table 1. Data obtained from DSC curves.
Samples Tmax (�C) Tend (�C) �H (J g�1)
E1 95 159 524E2 89 160 440E3 93 170 412E4 100 175 324EC1 93 190 437EC2 80 170 340EC3 88 145 310EC4 87 130 220
DSC: differential scanning calorimetry; Tmax: maximum peak temperature;�H: enthalpy.
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effect and dispersion of OMMT silicate layers of clay in the
DGEBA/AECO systems. This behavior can be further
explained by the fact that the presence of alkyl ammonium
ions in the OMMT clay acted as a catalyst for the DGEBA/
AECO system, thus contributing to an increase in the rate
of reaction with faster curing at lower temperatures. This
resulted in a shift of the exothermic peaks to the lower tem-
perature as manifested in our findings. However, when
compared with unfilled DGEBA/AECO systems, the max-
imum peak temperature (Tmax) was slightly decreased with
the addition of 1% OMMT to the DGEBA/AECO samples.
This behavior is possibly attributed to the increase in the
cross-linking density, which results in strong interactions
due to formation of covalent bond between the clay and
DGEBA/AECO system. As observed from Table 1, the
E2 system shows improved performance with regards to
decrease in the curing temperature in presence of 1%OMMT nanoclay from 89�C to 80�C in EC2. Camille
et al.65 reported that the montmorillonite is responsible for
the decrease of Tmax and heat of reaction of the nanocom-
posite as compared to the DGEBA system. Similar facts
have been substantiated in our findings. Further, the �H
values decreased with the addition of 30% and 40% AECO
to the DGEBA due to the plasticizing effect.
The cure kinetics of E1, E2, EC1, and EC2 systems were
studied using non-isothermal differential scanning (DSC)
calorimeter at various heating rates (q) at 5, 10, 15, and
20�C min�1 (Table 2). The curing of bio-based systems
exhibited only one exothermic peak during the non-
isothermal DSC analysis. The maximum peak temperature
(Tmax) even increased with the increase of heating rates
(Figures 6 to 9, Table 2), which is due to the addition of
AECO. The obtained peak63–65 curing temperature of
EC2 (70�C) was much lower than that of E2 (79�C) at a
heating rate 5�C min�1, which indicates that the reactivity
of EC2 was higher than that of E2.66 The activation energy
of the curing reaction was determined by both Kissinger
and Flynn–Wall–Ozawa methods using equations (5) and
(6). The activation energy for cure kinetics can be calcu-
lated from the slope of the plot from Figure 10 and values
obtained for E1, E2, EC1, and EC2 were 59, 66, 53, and 57
kJ mol�1, respectively. Figure 11 shows that the resulting
slope obtained from linear fitting plot indicates the
activation energy. The activation energy for cure kinetics
was 63, 69, 59, and 61 kJ mol�1 obtained for E1, E2,
EC1, and EC2 systems, respectively. An increase in the
AECO content to DGEBA resulted in increased activation
energy due to the decrease of the viscosity and increase of
the number of epoxy groups. The activation energy of the
E2 system was higher than that of the E1 system. This is
due to the presence of more flexible (aliphatic) groups of
AECO added to the aromatic groups of DGEBA epoxy sys-
tem, which greatly decreases the reactivity of the system
during the curing process. Higher activation energy was
obtained for the lower reactivity systems. The reactivity
of the DGEBA/AECO/OMMT system was higher than that
of the DGEBA/AECO systems, due to the strong bonds
Table 2. Data obtained from non-isothermal DSC curves atheating rates of 5, 10, 15, and 20�C min�1.
Heating rate (�C min�1) Ea (kJ mol�1)
Samples 5 Tp 10 Tp 15 Tp 20 Tp Ea,Kissnger Ea,Ozawa
E1 84 95 102 108 59 63E2 79 89 95 100 66 69EC1 81 93 101 106 53 59EC2 69 80 87 92 57 61
DSC: differential scanning calorimetry; Ea: activation energy.
Figure 6. DSC thermograms of 90% DGEBA/10% AECO atdifferent heating rates. DSC: differential scanning calorimetry;DGEBA: diglycidyl ether of bisphenol A; AECO: acrylatedepoxidized castor oil.
Figure 7. DSC thermograms of 80% DGEBA/20% AECO atdifferent heating rates. DSC: differential scanning calorimetry;DGEBA: diglycidyl ether of bisphenol A; AECO: acrylatedepoxidized castor oil.
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formed between DGEBA/AECO and OMMT clay. The
results revealed that the presence of organoclay has lowered
the curing temperature to a greater extent, significantly low-
ering the activation energy and increasing the reactivity of the
bio-based epoxy system.67 The activation energies obtained
for all bio-based systems from the Flynn–Wall–Ozawa model
were found to be higher than that of the kissinger Model. Sim-
ilar results have been reported by several authors.68,69
The degree of cure or conversion for 10 and 20 wt%AECO toughened DGEBA epoxy nanocomposites have
been calculated46,70 using equation (1). The degree of cure
versus temperature curves of both EC1 and EC2 systems
shows an ‘S’ shape; which indicates that the cure reaction
was autocatalytic (Figures 12 and 13).69
The estimated Ea values from Flynn–Wall–Ozawa model
were used to calculate the y(�) and z(�) functions using
equations (8) and (9), respectively. Figures 14 and 15 and
16 and 17 represent the variation of y(�) and z(�) values with
the degree of cure for 10 and 20 wt% of AECO-toughened
DGEBA nanocomposites, respectively. As noted, the y(�)
curve exhibits maximum value at�M, and that of z(�) exhibits
maximum value at�1P , as shown in Table 3. The results are in
good agreement with those reported by several authors36,71
that the values of �1P lower than 0.632 indicate that the stud-
ied cure reaction can be described using the two-parameter
autocatalytic kinetic model Sestak–Berggren. Using equation
(7), the value of the kinetic exponent n can be obtained from
the slope of linear dependence In½qeX d�dt� versus ln[�P(1 –
�)]. The estimated n value was used to calculate the kinetic
parameter m from equation (11). The kinetic parameters n,
m, and ln A at different heating rates are listed in Table 4.
Figure 11. Plots to determine activation energies by the Flynn–Wall–Ozawa model DGEBA/AECO and its nanocomposites.DGEBA: diglycidyl ether of bisphenol A; AECO: acrylated epoxi-dized castor oil.
Figure 9. DSC thermograms of 80% DGEBA/20% AECO/1%OMMT at different heating rates. DSC: differential scanningcalorimetry; DGEBA: diglycidyl ether of bisphenol A; AECO:acrylated epoxidized castor oil; OMMT: organically modifiedmontmorillonite.
Figure 8. DSC thermograms of 90% DGEBA/10% AECO/1%OMMT at different heating rates. DSC: differential scanningcalorimetry; DGEBA: diglycidyl ether of bisphenol A; AECO:acrylated epoxidized castor oil; OMMT: organically modifiedmontmorillonite.
Figure 10. Plots to determine activation energies by the Kissingermodel for DGEBA/AECO and its nanocomposites. DGEBA: digly-cidyl ether of bisphenol A; AECO: acrylated epoxidized castor oil.
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The accuracy of the kinetic model proposed by the
Malek method was verified by plotting d�/dt versus the
temperature with the calculated data in Table 4 and experi-
mental data. Figures. 18 and 19, show that the calculated
data (solid lines) coincide with the experimental values
(symbols) at different heating rates, which indicate that the
two-parameter Sestak–Berggren model deduced by the
Malek method could be used to study the entire curing reac-
tion process of 10 and 20 wt% of AECO-toughened
DGEBA epoxy nanocomposites.
Conclusions
The cure kinetics of AECO-toughened DGEBA epoxy sys-
tems were investigated by non-isothermal DSC analysis
with and without OMMT clay. The epoxy groups of ECO
Figure 15. Normalized function curve of y(�) for DGEBA/20%AECO/1% OMMT system. DGEBA: diglycidyl ether of bisphenolA; AECO: acrylated epoxidized castor oil; OMMT: organicallymodified montmorillonite.
Figure 16. Normalized function curve of z(�) for DGEBA/10%AECO/1% OMMT system. DGEBA: diglycidyl ether of bisphenolA; AECO: acrylated epoxidized castor oil; OMMT: organicallymodified montmorillonite.
Figure 14. Normalized function curve of y(�) for DGEBA/10%AECO/1% OMMT system. DGEBA: diglycidyl ether of bisphenolA; AECO: acrylated epoxidized castor oil; OMMT: organicallymodified montmorillonite.
Figure 13. Conversion rate versus temperature of 80% DGEBA/20% AECO/1% OMMT system. DGEBA: diglycidyl ether ofbisphenol A; AECO: acrylated epoxidized castor oil; OMMT:organically modified montmorillonite.
Figure 12. Conversion rate versus temperature of 90% DGEBA/10% AECO/1% OMMT system. DGEBA: diglycidyl ether ofbisphenol A; AECO: acrylated epoxidized castor oil; OMMT:organically modified montmorillonite.
Paluvai et al. 925
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were confirmed by 1H NMR spectra at 2.8 to 3.2 ppm
and by FTIR spectra at 1244 and 844 cm�1, respectively.
Further, the acrylation of ECO was confirmed through the
appearance of peaks in the FTIR spectra at 1639, 1462, and
1400 cm�1, respectively. The heat of reaction decreased for
EC1–EC4 due to the addition of the catalytic effect of
OMMT on DGEBA/AECO system. With the addition of 1
wt% OMMT clay to the DGEBA/10% AECO and
DGEBA/20% AECO systems, the Ea values obtained by the
Flynn–Wall–Ozawa method were reduced from 63 to 59 kJ
mol�1 and 69 to 61 kJ mol�1, respectively. The two-
parameter autocatalytic Sestak–Berggren model was used
to describe the curing process of the studied systems. The
model parameters were calculated by the Malek method.
The calculated kinetic parameter data show good agreement
with the experimental data of bio-based systems. This sys-
tem represents the DGEBA resin replaced by AECO/OMMT
and indicates a sustainable material for industrial use.
Table 4. Estimated kinetic parameters m, n, and ln A for Sestak–Berggren model.
Sample Heating rates (�C min�1) m n ln A (min�1)
EC1 5 0.96 1.56 15.7110 1.00 1.58 15.9415 1.01 1.55 16.0920 1.05 1.58 16.37
Mean 1.00 1.57 16.02EC2 5 0.88 1.36 15.37
10 0.89 1.34 15.6115 0.88 1.29 15.8020 0.92 1.29 15.97
Mean 0.89 1.32 15.68
Figure 18. Comparison of experimental (symbols) and calculated(lines) DSC curves for DGEBA/10% AECO/1% OMMT system.DSC: differential scanning calorimetry; DGEBA: diglycidyl ether ofbisphenol A; AECO: acrylated epoxidized castor oil; OMMT:organically modified montmorillonite.
Figure 19. Comparison of experimental (symbols) and calculated(lines) DSC curves for DGEBA/10% AECO/1% OMMT system.DSC: differential scanning calorimetry; DGEBA: diglycidyl ether ofbisphenol A; AECO: acrylated epoxidized castor oil; OMMT:organically modified montmorillonite.
Figure 17. Normalized function curve of z(�) for DGEBA/20%AECO/1% OMMT system. DGEBA: diglycidyl ether of bisphenolA; AECO: acrylated epoxidized castor oil; OMMT: organicallymodified montmorillonite.
Table 3. Characteristic peak conversions �M and �P1.
Sample Heating rates (oC min�1) �M �P1
EC1 5 0.38 0.6110 0.39 0.6115 0.39 0.6320 0.40 0.62
Mean 0.39 0.62EC2 5 0.39 0.63
10 0.39 0.5815 0.41 0.5920 0.41 0.62
Mean 0.40 0.60
926 High Performance Polymers 27(8)
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Declaration of Conflicting Interests
The author(s) declared no potential conflicts of interest with
respect to the research, authorship, and/or publication of this
article.
Funding
The author(s) disclosed receipt of the following financial support
for the research, authorship, and/or publication of this article: The
authors are thankful to the Center of Excellence (CoE) under the
GREET project sponsored by the Department of Chemicals and
Petrochemicals, Govt of India.
References
1. Chen GQ and Patel MK. Plastics derived from biological
sources: present and future: a technical and environmental
review. Chem Rev 2012; 112: 2082–2097.
2. Reddy PN, Mohanty S and Nayak SK. Synthesis and modifi-
cations of epoxy resins and their composites: a review. Polym
Plast Technol Eng 2014; 53: 1723–1758.
3. Park SJ, Fan-Long J and Lee JR. Effect of biodegradable epox-
idized castor oil on physicochemical and mechanical properties
of epoxy resins. Macromol Chem Phy 2004; 205: 2048–2054.
4. Joshua MS, Anh-Phuong TN, Faye RT, et al. Isosorbide-
methacrylate as a bio-based low viscosity resin for high per-
formance thermosetting applications. J Mater Chem A 2013;
1: 12579–12586.
5. Galia M, de Espinosa LM, Ronda JC, et al. Vegetable oil-
based thermosetting polymers. Euro J Lipid Sci Technol
2009; 111: 1–10.
6. Khot SN, Lascala JJ, Can E, et al. Development and applica-
tion of triglyceride-based polymers and composites. J Appl
Polym Sci 2001; 82: 703–723.
7. Auvergne R, Caillol S, David G, et al. Biobased thermoset-
ting epoxy: present and future. Chem Rev 2014; 114:
1082–1115.
8. Srikanta D, Anand VP, Vaibhav VG, et al. Epoxidation of
cottonseed oil by aqueous hydrogen peroxide catalysed by
liquid inorganic acids. Bioreso Technol 2008; 99: 3737–3744.
9. Gaston F, Francisco C and Nathan WM. Cure kinetics of an
acrylated epoxidized hemp oil-based bioresin system. J Appl
Polym Sci 2013; 128: 2030–2037.
10. Gunter W, Arunjunai RM, Muller U, et al. Photocrosslinking
of an acrylated epoxidized linseed oil: kinetics and its appli-
cation for optimized wood coatings. J Polym Environ 2012;
20: 1063–1074.
11. Ravindra D, Priya SD, Sujay UM, et al. Epoxidation of
mustard oil and ring opening with 2-ethylhexanol for biolu-
bricants with enhanced thermo-oxidative and cold flow char-
acteristics. Ind Crop Prod 2013; 49: 586–592.
12. Esmat M, Mohamed KA and Nik MNS. Improved yield of
solvent free enzymatic methanolysis of palm and jatropha oils
blended with castor oil. Appl Ener 2013; 104: 905–909.
13. Oliver K, Tommy T and Michael ARM. Copolymers derived
from rapeseed derivatives via ADMET and thiol-ene addi-
tion. Euro Polym J 2011; 47: 1804–1816.
14. Altuna FI, Esposito LH, Ruseckaite RA, et al. Thermal and
mechanical properties of anhydride-cured epoxy resins with
different contents of biobased epoxidized soybean oil. J Appl
Polym Sci 2011; 120: 789–798.
15. Mohan P. A critical review: the modification, properties, and
applications of epoxy resins. Polym Plast Technol Eng 2012;
52: 107–125.
16. Mathew VS, Sinturel C, George SC, et al. Epoxy resin/liquid
natural rubber system: secondary phase separation and its
impact on mechanical properties. J Mater Sci 2010; 45:
1769–1781.
17. Guijun Y and Peiyi W. Effect of chemically modified gra-
phene oxide on the phase separation behaviour and properties
of an epoxy/polyetherimide binary system. Polym Chem
2014; 5: 96–104.
18. Srivastava AK and Mohan P. Synthesis, reactions, and prop-
erties of modified epoxy resins. J Macromol Sci Part C.
Polym Rev 1997; 4: 687–716.
19. Chinnakkannu KC, Alagar M, Rajkumar JS, et al. Thermo
mechanical behaviour of unsaturated polyester toughened
epoxy–clay hybrid nanocomposites. J Polym Res 2007; 14:
319–328.
20. Sung S and Dae SK. UV-curing and mechanical properties
of polyester–acrylate nanocomposites films with silane-
modified antimony doped tin oxide nanoparticles. J Appl
Polym Sci 2013; 129: 1340–1344.
21. Ogunniyi DS. Castor oil: a vital industrial raw material. Bior-
eso Technol 2006; 97: 1086–1091.
22. Mutlu H and Meier MAR. Castor oil as a renewable resource
for the chemical industry. Euro J Lipid Sci Technol 2010;
112: 10–30.
23. Xiao P, Partha S and Dean CW. Novel biobased epoxy com-
pounds: epoxidized sucrose esters of fatty acids. Green Chem
2011; 13: 965–975.
24. Behera D and Banthia AK. Synthesis, characterization,
and kinetics study of thermal decomposition of epoxidized
soybean oil acrylate. J Appl Polym Sci 2008; 109:
2583–2590.
25. Akesson D, Skrifvars M and Walkenstrom P. Preparation
of thermoset composites from natural fibres and acrylate
modified soybean oil resins. J Appl Polym Sci 2009; 114:
2502–2508.
26. John LS and Richard PW. Property analysis of triglyceride-
based thermosets. Polym 2005; 46: 61–69.
27. Jue L and Richard PW. Sheet molding compound resins from
soybean oil: thickening behavior and mechanical properties.
Polym Eng Sci 2007; 47: 1469.
28. Thielemans W and Richard PW. Kraft lignin as fiber treat-
ment for natural fiber reinforced composites. Polym Compos
2005; 26: 695–705.
29. Chenlu B, Yuqiang G, Lei S, et al. In situ preparation of func-
tionalized graphene oxide/epoxy nanocomposites with effec-
tive reinforcements. J Mater Chem 2011; 21: 13290–13298.
30. Biqiong C and Julian RGE. Impact strength of polymer-clay
nanocomposites. Soft Mat 2009; 5: 3572–3584.
Paluvai et al. 927
at Hanyang University Central Library on December 9, 2015hip.sagepub.comDownloaded from
31. Nathan WM, Francisco C, Thiru A, et al. Cure kinetics of an
epoxidized hemp oil based bioresin system. J Appl Polym Sci
2011; 122: 444–451.
32. Bibekananda D, Gupta K, Mandal M, et al. Biodegradable
hyperbranched epoxy from castor oil-based hyperbranched
polyester polyol. ACS Sustaniable Chem Eng 2014; 2:
445–453.
33. Poornima VP, Debora P, Jose MK, et al. Effect of organically
modified nanoclay on the miscibility, rheology, morphology
and properties of epoxy/carboxyl-terminated (butadiene-co-
acrylonitrile) blend. Soft Mat 2013; 9: 2899–2911.
34. Kardar P, Ebrahimi M and Bastani S. Study the effect of
nano-alumina particles on physical–mechanical properties
of UV cured epoxy acrylate via nano-indentation. Prog Org
Coat 2008; 62: 321–325.
35. Thielemans W, Ian MM, Valerie B, et al. Impure carbon
nanotubes as reinforcements for acrylated epoxidized soy oil
composites. J Appl Polym Sci 2005; 98: 1325–1338.
36. Rosu D, Cascaval CN and Mustata F. Cure kinetics epoxy
resins of studied by non-isothermal DSC data. Thermochi
Acta 2002; 383: 119–127.
37. Ricky H, Julie LPJ, Frank EP, et al. Cure kinetics character-
ization and monitoring of an epoxy resin using DSC, Raman
spectroscopy, and DEA. Compos A 2013; 49: 100–108.
38. Honghua W, Bo L, Xiaoqing L, et al. Synthesis of biobased
epoxy and curing agents using rosin and the study of cure
reactions. Green Chem 2008; 10: 1190–1196.
39. Fang Z, Wang J, Gu A, et al. Curing behavior and kinetic
analysis of epoxy resin/multi-walled carbon nanotubes com-
posites. Front Mater Sci China 2007; 1(4): 415–422.
40. Zengping Z, Guozheng L, Penggang R, et al. Curing behavior
of epoxy/POSS/DDS hybrid systems. Polym Compos 2008;
29: 77–83.
41. Rucigaj A, Alic B, Krajnc M, et al. Investigation of cure
kinetics in a system with reactant evaporation: Epoxidized
soybean oil and maleic anhydride case study. Euro Polym J
2014; 52: 105–116.
42. Geeta D, Parveen K and Narula AK. Studies on curing
kinetics and thermal behavior of phosphorylated epoxy resin
in the presence of aromatic amide-amines. J Appl Polym Sci
2010; 118: 3612–3618.
43. Ghaemy M and Bazzar M. effect of nanosilica on the kinetics
of cure reaction and thermal degradation of epoxy resin. Chi-
nese J Polym Sci 2011; 29: 141–148.
44. Mousa G, Bazzar M and Farshad RB. Curing of DGEBA/ZnO
nanocomposite with new fluorinated curing agents: study
of kinetics, water absorption, thermal and photophysical
properties. High Perfor Polym 2012; 24(7): 632–645.
45. Qing G, Yan H, Yu-Ying Z, et al. Curing behavior of epoxy
resins with a series of novel curing agents containing 4,40-
biphenyl and varying methylene units. J Therm Anal Calorim
2010; 102: 915–922.
46. Gamal RS, Enas EAE and Said AE. Dynamic cure kinetics and
thermal degradation of brominated epoxy resin–organoclay
based nanocomposites. Thermochi Acta 2011; 524: 186–193.
47. Rosu D, Mustata F and Cascaval CN. Investigation of the cur-
ing reactions of some multifunctional epoxy resins using dif-
ferential scanning calorimetry. Thermochi Acta 2001; 370:
105–110.
48. Sestak J and Berggren G. Study of the kinetics of mechanism
of solid state reactions at increasing temperatures. Thermochi
Acta 1971; 3: 1–12.
49. Jin Z, Hongxing D, Lili T, et al. Investigation of curing
kinetics of sodium carboxymethyl cellulose/epoxy resin sys-
tem by differential scanning calorimetry. Thermochi Acta
2012; 549: 63–68.
50. Zhi-Qiang Y, Shu-Li Y and Horst B. Effect of organosilane
coupling agents on microstructure and properties of nano-
silica/epoxy composites. Polym Compos 2012; 33:
1516–1524.
51. Weiping L, Hoa SV and Pugh M. Water uptake of epoxy–clay
nanocomposites: experiments and model validation. Compos
Sci Technol 2008; 68: 2066–2072.
52. Samuel BS, Vinicius P, Sandro CA, et al. Investigation of
cure kinetics in epoxy/multiwalled carbon nanotube nano-
composites. J Appl Polym Sci 2014; 131: 39857.
53. Margit H, Jozsef KK and Marco H. Influence of fillers and
additives on the cure kinetics of an epoxy/anhydride resin.
Euro Polym J 2007; 43: 1168–1178.
54. Malek J. The kinetic analysis of non-isothermal data. Ther-
mochi Acta 1992; 200: 257–269.
55. Montserrat S and Malek J. A kinetic analysis of the curing
reaction of an epoxy resin. Thermochi Acta 1993; 228: 47–60.
56. Wang F, Xiao J, Wang JW, et al. Study on curing kinetics of a
diglycidyl ether of bisphenol A epoxy resin/microencapsu-
lated curing agent system. High Perfor Polym 2012; 24(8):
730–737.
57. Malek J. Kinetic analysis of crystallization processes in amor-
phous materials. Thermochi Acta 2000; 239: 239–253.
58. Senum GI and Yang RT. Rational approximations of the inte-
gral of the Arrhenius function. J Thermal Anal 1977; 11:
445–447.
59. Liyu F, Liting Y, Chunlan D, et al. Thermal and mechanical
properties of acrylated expoxidized-soybean oil-based ther-
mosets. J Appl Polym Sci 2010; 117: 2220–2225.
60. Sharif A, Nijas PK and Ufana R. Effect of microwave pro-
cessing on the spectral, mechanical, thermal, and morpholo-
gical characteristics of sustainable resource based castor oil
epoxy/pva blends. Adv Polym Tech 2011; 30: 96–109.
61. Denize MB, Maria ADL and Sydnei M. Organic–inorganic
coatings based on epoxidized castor oil with APTES/TIP and
TEOS/TIP. Prog Org Coat 2013; 76: 736–742.
62. Sung HR, Sin JH and Shanmugharaj AM. Study on the effect
of hexamethylene diamine functionalized graphene oxide on
the curing kinetics of epoxy nanocomposites. Euro Polym J
2014; 52: 88–97.
63. Mustata F, Tudorachi N and Rosu D. Curing and thermal
behavior of resin matrix for composites based on epoxidized
soybean oil/diglycidyl ether of bisphenol A. Compos Part B
2011; 42: 1803–1812.
928 High Performance Polymers 27(8)
at Hanyang University Central Library on December 9, 2015hip.sagepub.comDownloaded from
64. Marta W. Thermal and dynamic mechanical properties of
IPNS formed from unsaturated polyester resin and epoxy
polyester. J Mater Sci 2009; 44: 4069–4077.
65. Camille A, Alice M, Luc V, et al. Effects of incorporation of
organically modified montmorillonite on the reaction
mechanism of epoxy/amine cure. J Phy Chem B 2012; 116:
5786�5794.
66. Honghua W, Bo L, Xiaoqing L, et al. Synthesis of biobased
epoxy and curing agents using rosin and the study of cure
reactions. Green Chem 2008; 10: 1190–1196.
67. Pei-Yu K, Sain M and Ning Y. Synthesis and characterization
of an extractive-based bio-epoxy resin from beetle infested
Pinus contorta bark. Green Chem 2014; 16: 3483–3493.
68. Nayef El T, Tizazu M, Paolo M, et al. Nonisothermal DSC
study of epoxy resins cured with hydrolyzed specified risk
material. Ind Eng Chem Res 2013; 52: 8189�8199.
69. Kun H, Pei Z, Jinwen Z, et al. Preparation of biobased epoxies
using tung oil fatty acid-derived C21 diacid and C22 triacid
and study of epoxy properties. Green Chem 2013; 15:
2466–2475.
70. Ton-Thati MT, Ngo TD, Ding P, et al. Epoxy nanocompo-
sites: analysis and kinetics of cure. Polym Eng Sci 2004;
44: 1132–1141.
71. Gamal RS, Enas EAE and Said AE. Dynamic cure kinetics and
thermal degradation of brominated epoxy resin–organoclay
based nanocomposites. Thermochi Acta 2011; 524: 186–193.
Paluvai et al. 929
at Hanyang University Central Library on December 9, 2015hip.sagepub.comDownloaded from