Preparation of Novel Coumarin Cyclic Polymer/Montmorillonite Based Nanocomposites

Article abstract of DOI:10.1134/S1070427217120199

In present study, the synthesis, characterization, and thermal properties of novel coumarin cyclic polymer poly(3-benzoyl coumarin-7-yl-methacrylate) polymer/montmorillonite based nanocomposites were performed. At the characterizations of nanomaterials FT

Full text of DOI:10.1134/S1070427217120199

ISSN 1070-4272, Russian Journal of Applied Chemistry, 2017, Vol. 90, No. 12, pp. 2019−2027. © Pleiades Publishing, Ltd., 2017.
VARIOUS TECHNOLOGICAL
PROCESSES
Preparation of Novel Coumarin
Cyclic Polymer/Montmorillonite Based Nanocomposites1
A. Kurt* and O. K. Topsoy
Adiyaman University, Adiyaman, 02040 Turkey
*
e-mail: adnkurt@gmail.com
Received December 21, 2017
Abstract—In present study, the synthesis, characterization, and thermal properties of novel coumarin cyclic
polymer poly(3-benzoyl coumarin-7-yl-methacrylate) polymer/montmorillonite based nanocomposites were
performed. At the characterizations of nanomaterials FTIR, XRD, DSC and TGA techniques were used. It was
determined from XRD measurements that the morphologies of nanocomposites were shifted from exfoliated type
to intercalated type when the clay ratio in the coumarin polymer matrix was increased from 1 to 5% level. From
DSC analysis, a partial increasing at the glass transition temperatures of nanocomposites was observed related
to clay ratios. On the other hand, a positive correlation was observed between the clay ratio and thermal stabil-
ity of nanomaterials from TGA analysis. Also, the increasing of decomposition temperatures of nanocomposites
according to homopolymer was recorded to be 9–17°C.
DOI: 10.1134/S1070427217120199
As a result of the dispersing of different additives into
polymers, some changes are observed at the properties
of these materials. In particular, when the nano-sized
additive elements are distributed to the polymer matrix,
significant developments have been performed in the
properties of those nanomaterials [1]. One of the most
important of these nanomaterials is clay-reinforced
nanocomposites. So, polymer-clay nanocomposites
are widely preferred and used due to many advantages
such as easy preparing, achieving high success in the
targeted properties, easy availability, etc. [2]. When
the polymer clay nanocomposites are compared to neat
polymers, they exhibit advanced physical, mechanical
and chemical properties such as mechanical strength,
electrical resistance, dielectric property, thermal behavior,
rheological, gas barrier, and flame retardant [3–13]. These
properties generally change according to the distribution
pattern of clay in the polymer matrix [4].
used in specific applications because of not only their
macromolecular properties but also their functional
properties [14]. In the class of these polymers, the
coumarin-derived polymers belonging to the group of
polyphenolic compounds are one of the leading members
of reactive functional polymers. As is known, coumarins
belong to the family of lactones in the class of oxygen
heterocyclic compounds [15]. They are also known as
2
H-chromen-2-one or 1-benzopyran-2-one consist of
fused pyrone and benzene rings with the pyrone carbonyl
group at second position [16]. These compounds are
widely occurring in the nature and isolated from plants
as well as the synthesis may be well performed in the
laboratory by various processes [15]. Coumarins have
also intensive π-conjugated bonds in their structures
and this property makes them very popular for versatile
applications in various fields of science and technology
[
17]. Therefore, coumarins and derivatives exhibit
significant photophysical and spectroscopic properties
16] and they have been extensively investigated for
On the other hand, a large number of polymers with
different reactive functional groups have successfully
synthesized and tested todays. These polymers are
[
electronic and photonic applications such as electro-
optical materials, organic-inorganic hybrid materials,
1
The text was submitted by the authors in English.
2
019

2020
KURT, TOPSOY
Scheme 1. Synthesis of 3-benzoyl-7-hydroxy coumarin.
liquid crystal materials, light storage/energy transfer
materials [18–22]. Therewithal, these compounds are
naturally found, they have also attracted scientific interest
due to their important biochemical properties such as
antibacterial, antibiotic, antimitotic, antiviral, antitumor,
antifungal and antioxidant properties [23–29].
analysis was conducted on a Seiko SII 7300 TG/DTA
under nitrogen flow from 25°C to 500°C at the heating
rate of 10°C/min. A Perkin Elmer DSC 8000 was used
to examine the glass transition temperature of the
nanocomposites. Samples were heated from 25 to 200°C
at a rate of 20°C/min under nitrogen atmosphere.
Nanomer® I.28E (25–30 wt % trimethyl stearyl am-
monium) was purchased from Sigma–Aldrich, which
used as organomodified clay (OMMT). The reagents
of 2,4-dihydroxybenzaldehyde, ethyl benzoyl acetate,
piperidine, triethylamine, methacryloyl chloride and the
solvents of chloroform, acetone, methanol, ethanol, tetra-
hydrofuran (THF), N,N-dimethylformamide (DMF) were
purchased from Sigma-Aldrich. Azobisisobutyronitrile
Although some papers been performed to synthesize
and examine various properties of small or monomeric
coumarin derivatives [30,31], very little attention has been
paid to coumarin polymers [32]. In recent years, several
works have been reported on the investigation of various
properties of coumarin derived polymers [16,33,34].
Within our literature knowledge, however, none of
the papers on these polymers are about the coumarin
containing polymer/organoclay nanocomposites except
of our previous study [35]. With this view, the synthesis
of novel coumarin derived polymer/clay nanocomposites
based poly(3-benzoyl coumarin-7-yl-methacrylate)
polymer reinforced with various contents of organoclay
is under taken in current work. The prepared coumarin
monomer and polymer are spectrally characterized by
FTIR, H NMR and C NMR techniques while, at the
characterization of clay nanocomposites, FTIR and XRD
measurements are used. The influence of organoclay
on the thermal behaviors of present polymer is studied
by means of thermogravimetric analysis (TGA). The
obtained results showed a positive relation between the
amount of added organoclay phase and thermal stability
of nanocomposites.
(AIBN) was obtained from Merck, and it was purified by
dissolving in chloroform and recrystallizing from ethanol
just before polymerization.
Synthesis of 3-benzoyl-7-hydroxy coumarin was
performed as following: 2,4-dihydroxybenzaldehyde
(2.762 g), ethyl benzoyl acetate (3.844 g), three drops
of piperidine and 50 mL of acetone were dissolved in a
three neck flask. The mixture was stirred on a magnetic
stirrer for 2 hours. After this, the organic crude product
was precipitated in excess methanol, filtered and dried,
respectively. The result compound 3-benzoyl-7-hydroxy
coumarin was purified by crystallization from ethanol.
The synthesis scheme was shown in Scheme 1. FTIR
1
13
–
1
(
cm : the most characteristic bands): 3171 (–OH
stretching), 3062–2930 (aromatic C–H stretching),
900–2825 (aliphatic C–H stretching), 1682 (lactone
C=O stretching), 1650 (lactone aliphatic C=C stretching),
2
EXPERIMENTAL
1
609 (aromatic C=C stretching).
1H NMR (DMSO, δ, ppm): 10.98 (–OH proton),
.35 (lactone =CH–proton), 7.88–6.79 (aromatic =CH–
protons).
13C NMR (DMSO, δ, ppm): 191.95 (benzoyl ketone
carbonyl carbon), 163.28 (lactone carbonyl carbon),
158.37, 156.60, and 146.80 (ipso carbons next to hydroxyl
group, lactone oxygen and benzoyl carbonyl carbon,
A Perkin Elmer Spectrum 100 was used to obtain the
infrared spectra of the nanocomposites. NMR spectra
8
1
13
(
H NMR, C NMR) were recorded on a Bruker 300
MHZ NMR spectrometer. XRD patterns were recorded
at room temperature using Rigaku RadB-DMAX II
X-Ray Diffractometer equipped with a CuK radiation
α
(
λ = 0.15418 nm) and Ni filter. Thermogravimetric
RUSSIAN JOURNAL OF APPLIED CHEMISTRY Vol. 90 No. 12 2017

PREPARATION OF NOVEL COUMARIN CYCLIC POLYMER/MONTMORILLONITE
2021
Scheme 2. Synthesis of 3-benzoyl coumarin-7-yl-methacrylate (BCMA) monomer.
respectively), 136.73–102.04 (aromatic and aliphatic
C=C carbons).
154.28 and 145.08 (ipso carbons next to lactone oxygen,
methacrylate ester carbonyl and benzoyl carbonyl carbon,
respectively), 136.06–110.19 (aromatic and aliphatic
To synthesize 3-benzoyl coumarin-7-yl-methacrylate
monomer (BCMA), 3-benzoyl-7-hydroxy coumarin
C=C carbons), 17.95 (–CH carbon next to vinyl group).
3
(
1.76 g, 8.70 mmol), TEA (1.20 g, 8.70 mmol) and THF
Then, a free radical polymerization method was
applied to polymerize the 3-benzoyl coumarin-7-yl-
methacrylate monomer (BCMA). For this purpose,
monomer (2.0 g), DMF solvent (10 mL) and AIBN
initiator (0.12 g, 6 wt % of the monomer) were added
into a polymerization tube and degassed with argon for
10 minutes. After that, polymerization was carried out
60°C for 48 h. The polymer was precipitated in ethanol,
filtrated and dried overnight in a vacuum oven at 40°C.
Synthesis of poly(3-benzoyl coumarin-7-yl-methacrylate)
was illustrated in Scheme 3.
(75 mL) were added into a reaction flask. Methacryloyl
chloride (0.91 g, 8.70 mmol) was dropwised to this
mixture and stirred on the magnetic stirrer for 12 h at
room temperature. After the reaction was completed,
the mixture was filtered and the THF was removed in
vacuum. The organic phase was taken up in chloroform
and extracted several times with diluted NaOH solution
of 3%. The chloroform phase was dried over anhydrous
MgSO overnight. The mixture was filtered and the
4
solvent was removed in vacuum. The reaction mechanism
of 3-benzoyl coumarin-7-yl-methacrylate monomer was
shown in Scheme 2.
–1
FTIR (cm : the most characteristic bands): 3164–
3
038 (aromatic C–H stretching), 2995–2888 (aliphatic
–
1
FTIR (cm : the most characteristic bands): 3122–
034 (aromatic C–H stretching), 2982–2846 (aliphatic
C–H stretching), 1737 (methacrylate C=O stretching),
1731 (coumarin benzoyl C=O stretching), 1696 (lactone
C=O stretching), 1662 (lactone aliphatic C=C stretching),
1613 (aromatic C=C stretching).
3
C–H stretching), 1737 (methacrylate C=O stretching),
710 (coumarin benzoyl C=O stretching), 1682 (lactone
C=O stretching), 1656 (lactone aliphatic C=C stretching),
1
1H NMR (DMSO, δ, ppm): 8.19 (lactone =CH–
1
638 (vinylic C=C stretching).
1H NMR (DMSO, δ, ppm): 8.45 (lactone =CH–
proton), 7.78–7.22 (aromatic =CH– protons), 1.69 and
1.45 (methylene and methyl protons on the polymer main
chain, respectively).
proton), 7.97–7.28 (aromatic =CH– protons), 6.35 and
5
.97 (vinyl =CH protons), 2.03 (CH protons next to
2 3
Finally, the novel nanocomposites of coumarin derived
polymer reinforced with various ratios of organoclay
(poly(BCMA)/OMMT) were prepared using the solution
casting method. For this process, the necessary amounts
of organoclay (1%, 3% and 5%) were separately taken
vinyl group).
13C NMR (DMSO, δ, ppm):191.60 (benzoyl ketone
carbonyl carbon), 164.71 (methacrylate ester carbonyl
carbon), 157.81 lactone carbonyl carbon), 154.83,
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KURT, TOPSOY
Scheme 3. Synthesis of poly(3-benzoyl coumarin-7-yl-methacrylate) [poly(BCMA)].
into three balloons (50 mL) and dispersed in 3 mL of
DMF, and stirred by magnetic stirrers at room temperature
for 48 h. During this period, three separate poly(BCMA)
polymer samples (weights of 0.5 g) were also separately
dissolved in 3 mL of DMF at room temperature in
the other three balloons. Then, these poly(BCMA)
polymer/DMF solutions were gradually added into
each organoclay/DMF suspensions. The mixtures were
stirred for another 48 h with magnetic stirrers at room
temperature.After that, the polymer/organoclay mixtures
were precipitated in the excess ethanol to isolate from
DMF solvent. Then, the prepared nanocomposites were
dried in the air atmosphere for 24 h and finally, they were
powdered by passing from a sieve with 21 micron mesh.
(a)
RESULTS AND DISCUSSION
We have spectral characterized the coumarin
derived polymer, poly(3-benzoyl coumarin-7-yl-
methacrylate). One of the used spectral techniques is FTIR
technique. Figure 1a shows FTIR spectrum of polymer
in which the most important evidence of performing
the polymerization is the disappearing of the absorption
4
000
3200 2400
1800
1400
1000
500
(b)
–1
attributed to vinylic C=C stretching at 1638 cm with the
polymerization. In addition to this important changing,
the other absorption bands characterizing the coumarin
–1
polymer are observed at 3164–3038 cm (aromatic C–H
–
1
stretching), 2995–2888 cm (aliphatic C–H stretching),
–
1
–1
1
(
737 cm (methacrylate C=O stretching), 1731 cm
–
1
coumarin benzoyl C=O stretching), 1696 cm (lactone
C=O stretching), 1662 cm (lactone aliphatic C=C
stretching), 1613 cm (aromatic C=C stretching).
Also, another spectral technique, H NMR spectrum of
–
1
–
1
1
2
10
8
6
ppm
4
2
0
1
1
poly(BCMA) is shown in Fig. 1b. The resonances at 6.35
Fig. 1. (a) FTIR and (b) H NMR spectra of poly(BCMA)
polymer.
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PREPARATION OF NOVEL COUMARIN CYCLIC POLYMER/MONTMORILLONITE
2023
and 5.97 ppm attributed to the aliphatic =CH protons
2
which are characteristic for the monomer vinyl group are
not observed. This indicates that the vinylic C=C double
bonds in the monomer opened during polymerization
and thus, the polymerization has been achieved. Besides,
the other signals are also observed at 8.19 ppm (lactone
a
=CH– proton), 7.78–7.22 ppm (aromatic =CH– protons),
1.69 and 1.45 ppm (methylene and methyl protons on the
polymer main chain, respectively).
The organomodified clay (OMMT) is characterized
with FTIR technique and its spectrum is illustrated in
Fig. 2a. Especially, two different signal groups have
been seen in this spectrum. One of them characterizes the
pristine clay (Na–MMT) units. The most characteristic
b
c
–
1
absorptions of that are for 3620 cm OH stretching,
–
1
–1
1
7
001 cm Si–O stretching, 913 cm Al–OH deformation,
97 cm–1 silica Si–O stretching, 621 cm out of
–1
–
1
plane Al–O and Si–O stretching, 520 cm Al–O–Si
deformation. Another signal groups are recorded for the
intercalating agent units where the most characteristic
–
1
bands are 2922–2850 cm aliphatic C–H stretching and
d
e
–
1
1
469 cm aliphatic C–H shear vibrations. This spectrum
containing both of mentioned two signal groups indicates
that the organic modification of pristine montmorillonit
clay (Na–MMT) with intercalating agent is well
performed [36]. For comparison, we have discussed
here only the FTIR spectrum of the poly(BCMA)/
OMMT: 5% nanocomposite because of its similarity to
the FTIR spectra of all other nanocomposites illustrated
in Figs. 2b–2d. Also, the FTIR spectrum of neat polymer
poly(BCMA) polymer is re-illustrated as Fig. 2e to make
comparison easier. The characteristic absorptions for both
polymeric and organosilicate units are also available
in Fig. 2d. The most characteristic bands observed for
4
000
3200
2400
1800
1400
1000
Wavenumber, cm–1
–1
poly(BCMA) units are seen in 3096–2888 cm (aromatic
Fig. 2. FTIR spectra of (a) organoclay (OMMT),
b) poly(BCMA)/OMMT 1%, (c) poly(BCMA)/OMMT 3%,
(d) poly(BCMA)/OMMT 5%, (e) neat poly(BCMA).
–1
and aliphatic C–H stretching vibrations), 1735 cm (ester
(
–1
carbonyl stretching), 1664 cm (lactone C=C stretching),
–1
1
612 cm (aromatic C=C stretching). On the other hand,
especially, the absorption band characteristic for clay and
–
1
attributed to Si–O stretching shifts 1043 cm frequency.
Compared to other nanocomposites, a clear increasing at
the peak intensity of this absorption has been seen depend
on the rate of loading clay. Also, at this spectrum, the
units and coumarin polymer units appears in the same
spectrum. From these results, it can be said that the
organomodified clay presents in polymer matrix as is
reported by Krishna and Pugazhenthi [37].
–
1
absorptions of 919, 627, and 522 cm are recorded for
Al–OH deformation, Al–O/Si–O out of plane vibration
and Al–O–Si deformation, respectively. In the FTIR
spectra recorded for all polymer–clay nanocomposites,
the adsorptions attributed to both organomodified clay
The structure of clay dispersion in the polymer matrix
was determined by XRD analysis depend the d-spacing of
clay galleries. Especially, two general structures of layered
clay dispersion which are intercalated and exfoliated
types are seen in the polymer/clay nanocomposites
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KURT, TOPSOY
Thermal behaviors of poly(BCMA)/OMMT nanocomposites
Weight
loss, %
Weight
loss, %
(400°C)
Weight
loss, %
(500°C)
Nanocomposite
Poly(BCMA)
T, °Ca
T, °Cb
T, °Cc
(350°C)
179
321.37
330.36
402.79
406.39
11.91
46.65
41.06
87.02
83.02
Poly(BCMA)/OMMT 1%
Poly(BCMA)/OMMT 3%
Poly(BCMA)/OMMT 5%
179.2
8.43
2.53
6.71
179.6
180.5
338.71
337.72
407.75
405.76
38.48
41.91
76.16
72.88
a
Glass transition temperature. b,c Temperatures at 5% and 50% weight losses, respectively.
[
38]. When d-spacing (d001) of galleries are larger than
the diffraction peaks are shifted to 3.68° and 3.74° and
also, the basal spaces of them are 2.40 nm and 2.36 nm,
respectively. The interlayer spaces of both these two
nanocomposites have partially increased according to
organomodified clay galleries. However, these diffraction
peaks have not completely disappeared in the testing
range although it has seen a splayed in the peak shapes.
As positively associated with high clay contents, the
poly(BCMA) polymer chains with bulky coumarin side
groups are partially placed between the clay galleries by
reducing the present interlayer seconder forces. Since
all the interlayer forces have not been removed between
the galleries, the clay layers are not separated from each
other. Thus, the clays are intercalated in the poly(BCMA)
polymer matrix at the ratios of 3 and 5% OMMT. This
observation also agrees with the previous observations
in the literatures that clays can be intercalated in polymer
matrix [4,37].
the pure clay, the intercalated structure is seen for the
morphology of nanocomposites, whereas no peak is
seen in the XRD curve, in this case, the structure of clay
dispersion becomes exfoliated type [37]. The d-spacing
of clay galleries is calculated using the Bragg’s law: nλ =
2
d sin θ, where λ is the X-ray wave length (1.5418 Å),
d is the interlayer distance and θ is the angle of incident
radiation.
The wide angel X-ray diffraction curves of novel
prepared coumarin derived polymer/clay nanocomposites
reinforced with the different clay ratios (1, 3, and 5%)
are illustrated in Figs. 3a–3d). The XRD curve recorded
for organomodified clay (Fig. 3a), the diffraction angel
of clay layers are at 3.9° that corresponds to the basal
gallery spacing of 2.27 nm. On the other hand, the
d-spacing of pristine clay is at higher diffraction angels
about ≈9° and also lower basal distances in literature
[39, 40]. As is seen in Fig. 3a, the basal spacing of the
Figures 4a–4d shows DSC curves of the pure
poly(BCMA) homopolymer and its nanocomposites
reinforced with clay in various percentages. The glass
organomodified clay is significantly expanded with the
long alkyl chains and with the volume of the substituent
of the intercalating agent [36]. In the XRD curve of the
poly(BCMA)/OMMT : 1% nanocomposite containing
transition temperatures (T ) of nanocomposites were
g
given in the table. The pure poly(BCMA) showed a
transition at 179°C due to the large coumarin side group
and the restriction of polymer chain movement.
1
% organoclay content (Fig. 3b), the diffraction angle
of 3.9° recorded for the organoclay (OMMT) has
been completely disappeared and no diffraction peaks
characteristic of OMMT clay have observed in the 2θ–10θ
testing range. These result shows that the clay layers in
the poly(BCMA)/OMMT : 1% nanocomposite reinforced
This value is agreement with the T values recorded
g
for the coumarin-derived polymers in the literature. In a
study, Fomine and coworkers reported that the T values
g
1
% organoclay exhibits the exfoliation behavior in which
of some coumarin polymers were shifted in the range
of 100–230°C [41]. Venkatesan et al. [32] reported that
the copolymer of 7-methacryloyloxy-4-methylcoumarin
with butoxyethyl methacrylate (feed composition 80 : 20)
the clay layers are completely separated from each other
and dispersed in the polymer matrix randomly [37]. On
the other hand, in the XRD patterns of poly(BCMA)/
clay nanocomposites containing 3% and 5% OMMT,
showed the T at 138°C. In our previous study [35],
g
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PREPARATION OF NOVEL COUMARIN CYCLIC POLYMER/MONTMORILLONITE
2025
a
3.9°C
a
b
c
b
c
3
.68°C
d
3
.74°C
4
d
2
6
8
10
2
5
75
125
175
225
2
θ, deg
Temperature, °C
Fig. 3. XRD patterns of (a) organoclay (OMMT),
Fig. 4. DSC curves of (a) poly(BCMA), (b) poly(BCMA)/
OMMT 1%, (c) poly(BCMA)/OMMT 3%, (d) poly(BCMA)/
OMMT 5%.
(b) poly(BCMA)/OMMT 1%, (c) poly(BCMA)/OMMT 3%,
d) poly(BCMA)/OMMT 5%.
(
we determined the glass transition temperature of a
coumarin derived polymer poly(3-acetylcoumarin-7-yl-
methacrylate) to be 176°C.
OMMT loading 2% to 10%. They interpreted the reason
of that caused by the strong interaction between OMMT
and polystyrene which limited the cooperative motions
of the polymer chains. In another study, Wang et al. [43]
reported the glass transition temperatures of polystyrene–
clay (1–5 wt %) nanocomposites were 2.4–6.2°C higher
than that of neat polystyrene, which was reasoned by the
preventing of segmental motions of the intercalated poly-
mer chains within the clay galleries. In a similar work,
Krishna and Pugazhenthi [37] observed that the glass
transition temperature of PS/OMMT nanocomposites
prepared via solvent blending method at various ratios of
organoclay (3–20 wt %) were approximately 7.1–8.6°C
higher than that of neat polymer.
As can be seen in Figs. 4a–4d, when the organomodi-
fied clay ratio in the coumarin derivative poly(BCMA)
matrix increased to 5% level, the glass transition tem-
perature also partially increased from 179 to 180.5°C.
It was observed that the glass transition temperature of
nanocomposites was approximately 1.5°C higher than
that of pure poly(BCMA). This partial increasing may
be because the movement of poly(BCMA) homopolymer
chains are prevented by the sheets of the clay. Thus, the
segmental motions of the polymer chains are restricted at
the polymer–clay interface due to polymer–clay interac-
tion and thus, the transition temperatures of polymeric
nanomaterials increase as described in literature [35–37].
Thermal behaviors of novel nanocomposites based
coumarin derived poly(BCMA) filled with the organoclay
in different ratios are determined by TGAtechnique, and
their thermograms are shown in Figs. 5a–5d compared
with each other. Also, their results are given in the table
which clearly demonstrates that the thermal decomposi-
tion temperatures of poly(BCMA)/clay nanocomposites
are higher than that of pure poly(BCMA) homopolymer.
However, the increasing at the T of nanocomposites
g
is not at very high levels. As a result, the glass transi-
tion temperature values of the poly(BCMA)/OMMT
nanocomposite samples have not significantly changed
with the clay reinforcements, and show the transitions
near that of the pure polymer (179°C). On the other
hand, we think that one of the reasons why the glass
transition temperature is not sufficiently increased may
be that the clay dispersion is not well dispersed in the
polymer matrix. In this perspective, similar results on
the glass transition temperatures of polymer/organoclay
nanocomposites have been seen in the literature. In one
study of them reported by Zidelkheir and coworkers [42],
–
1
When the 5% weight loss at the 10°C min heating rate
have been chosen for comparison, the thermal decom-
position temperature of poly(BCMA) homopolymer and
its nanocomposites reinforced with organoclay at the
ratios of 1, 3, and 5% are determined as 321.37, 330.36,
338.71, and 337.72°C, respectively. As can be seen from
these results, thermal stabilities of nanocomposites are
increased by about 9–17°C by loading clay into the cou-
marin derived polymer matrix. These results also agree
with the previous observations in the literatures that the
they expressed that the T of intercalated polystyrene/
g
OMMT nanocomposite prepared by melt intercalative
compounding technique was increased 3.3–4°C by the
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KURT, TOPSOY
ACKNOWLEDGMENTS
1
00
We wish to thank the Adıyaman University Scientific
Research Projects Unit (ADYÜBAP/FFYL2015-0001)
for financially supporting this study.
8
6
4
2
0
0
0
0
0
a
b
c
d
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