functionalization of syndiotactic polystyrene with succinic anhydride in the presence of aluminum...
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EUROPEAN
European Polymer Journal 41 (2005) 823–829
www.elsevier.com/locate/europolj
POLYMERJOURNAL
Functionalization of syndiotactic polystyrene withsuccinic anhydride in the presence of aluminum chloride
Juan Li, Hua-Ming Li *
Department of Chemistry, Institute of Polymer Science, Xiangtan University, Xiangtan 411105, Hunan Province, PR China
Received 8 October 2004; accepted 29 October 2004
Available online 13 January 2005
Abstract
Syndiotactic polystyrene has been chemically modified with succinic anhydride by use of Friedel–Crafts acylation
reaction in the presence of anhydrous aluminum chloride in carbon disulfide. The modified syndiotactic polystyrene
containing –COCH2CH2COOH fragments in side phenyl rings, named succinoylated syndiotactic polystyrene
(s-sPS), was characterized by FTIR and 1H NMR spectroscopy. The effects of reaction conditions on the degree of suc-
cinoylation of s-sPS were investigated. In addition, the effects of incorporation of carboxyl groups into syndiotactic
polystyrene on the thermal behavior were studied by differential scanning calorimetry in comparison with pure syndio-
tactic polystyrene. It was found that the crystallization temperature, melting temperature, and degree of crystallinity of
the modified polymer decreased with increasing the degree of succinoylation, while the glass transition temperature
increased.
� 2004 Elsevier Ltd. All rights reserved.
Keywords: Syndiotactic polystyrene; Acylation; Succinic anhydride; Modification
1. Introduction
Since the first synthesis of syndiotactic polystyrene
(sPS) by Ishihara [1], this new semicrystalline polymer
has been the subject of intense investigation. Along with
high melting temperature (�270 �C), high crystallinity
and rapid crystallization rate, sPS exhibits low dielectric
constant, high modulus, and good chemical resistance,
which has been made an attractive engineering ther-
moplastic for many applications in the electronic, packag-
ing, and automotive industries. However, sPS resembles
0014-3057/$ - see front matter � 2004 Elsevier Ltd. All rights reserv
doi:10.1016/j.eurpolymj.2004.10.048
* Corresponding author. Tel.: +86 732 8293606; fax: +86 732
8293264.
E-mail address: [email protected], huamingli8@
163.com (H.-M. Li).
atactic polystyrene (aPS) polymer with poor impact
strength, inherent brittleness, and low surface energy. Re-
cently, attempts have been made to improve the physical
properties and processability of sPS through several pro-
cedures. Physical bending with other polymers or sub-
strates (e.g., engineering thermoplastics and elastomers)
may extend the commercial utility of sPS [2,3]. Except
for a few polymers such as aPS and PPO, blending with
other polymers (e.g., polyamides) usually leads to phase
separation due to lack of compatibility. Therefore, chemi-
cal modified sPS polymer with functional groups was
expected to be a very desirable material.
In previous articles dealing with the preparation of
functionalized sPS, experimental observations were
interpreted as two aspects. One involves direct polymeri-
zation of styrenic monomer or copolymerization with a
second monomer by using metallocene catalyst systems
ed.
824 J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829
to produce syndiotactic polystyrene derivatives contain-
ing functional groups [4–8]. For example, Chung devel-
oped a route to prepare functionalized sPS through the
direct copolymerization of styrene with a borane-con-
taining styrenic monomer and extended this sPS to pre-
pare functionalized sPS and sPS graft copolymers [7].
Chung also demonstrated a family of syndiotactic poly-
styrene derivatives containing primary amino groups via
stereospecific polymerization of a styrene derivative con-
taining a masking N,N-bis(trimethylsilyl)amino group
followed by acid hydrolysis leading to the complete
recovery of primary amino groups in sPS derivatives
[8]. On the other hand, functionalization of sPS can also
be achieved by introducing other types of functional
groups into the polymer or by modifying existed func-
tional groups. From a research and development point
of view, the latter one is usually more efficient and less
expensive. So far, there are only a few reports on dis-
cussing the modification of sPS-based polymer, such re-
ports including sulfonated sPS [9,10], brominated sPS
[11], acetylated sPS [12], maleated sPS [13,14], and a ser-
ies of sPS graft copolymers synthesized using ATRP
technique with brominated sPS as initiator [15]. In
addition, Liu et al. used a mixture of [Ni(p-methal-
lyl)(Br)]2and AlCl3, to graft branched oligoethene onto
the pendant aromatic groups of sPS [16].
In our previous paper, we have reported a method for
preparing acetylated syndiotactic polystyrene (AsPS) by
Friedel–Crafts reaction [12]. The outstanding virtue of
this method lies in that it is well suited for the prepara-
tion of high molecular mass of styrenic polymer based
ionomers with substituted groups situated randomly
along the polymer chain under mild conditions [12,
17,18]. In addition, all the reagents used in the reaction
are commercially available. Following our previous
work, the present work is design to introduce carboxyl
groups onto pendant aromatic groups of sPS through
Friedel–Crafts acylation reaction. There is limited infor-
mation about the preparation of sPS bearing pendant
carboxyl groups in the side phenyl rings. Pendant func-
tional groups, such as carboxyls, will be potentially
interesting for preparing amphiphilic copolymers and
ion-containing sPS. The aim of this work is to modify
sPS with succinic anhydride via Friedel–Crafts acylation
reaction. Furthermore, differential scanning calorimetry
(DSC) was used to investigate the thermal properties of
functionalized polymers in view of the crystallization
and melting behavior along with the neat sPS.
2. Experimental
2.1. Materials
The sPS used in these studies was synthesized by bulk
polymerization of styrene with a Cp*Ti (OCH2C6H5)3/
MAO catalytic system at 80 �C [19]. The resulting poly-
mer was stirred in a 10 wt.% methanol solution of HCl
for 5 h to remove the residual metal catalyst, the poly-
mer was then filtered and dried under vacuum at 70 �Cfor 72 h after which was extracted with methylethyl ke-
tone (MEK) to remove the atactic component. The puri-
fied polymer was characterized to have a very high steric
purity (>99% in syndio units) and its number average
molecular weight and polydispersity were 210,000 and
2.2, respectively. Succinic anhydride (SA) was purified
by recrystallization from chloroform before used. Car-
bon disulfide was dried overnight with anhydrous cal-
cium chloride, filtered and fractionally distilled in the
presence of phosphorus pentoxide before used. All the
other reagents and solvents were commercially available
and of analytical grade.
2.2. Modification
In a typical run, 0.50 g (5 mmol) of SA and 2.00 g
(15 mmol) of finely powdered anhydrous aluminum
chloride (AlCl3) was treated with 50 ml of carbon disul-
fide in a 150 ml three-neck round-bottom flask equipped
with condenser, dropping funnel, gas inlet/outlet, and a
magnetic stirrer. After being rapidly stirred for 2 h,
0.52 g (5 mmol based on benzene ring) of sPS (200 mesh)
was added to the mixture. The reaction was continued
under nitrogen atmosphere until the product turned to
a dark red. Then, the product was decomposed with
ice water followed by dilute hydrochloric acid, thor-
oughly washed with water to remove any residual acid,
filtered and dried overnight under vacuum at 70 �C.The modified polymer thus obtained was refined with
1,1,2-trichloroethane/methanol mixture (99/1, v/v), then
precipitated with methanol, filtered, and subsequently
dried under vacuum.
2.3. Characterization
Fourier transform infrared (FTIR) spectra were re-
corded on a Perkin–Elmer Spectrum One spectrometer.
Samples films were cast in aluminum pans from a
1.0 wt.% solution in chloroform/methanol mixture (99/
1, v/v) and dried under vacuum at 70 �C, which is suffi-
ciently high for removal of residual solvent.1H NMR spectra were obtained at 25 �C on a Bruker
AV 400 NMR spectrometer. Samples for 1H NMR spec-
troscopy were prepared by dissolving about 10 mg of
products in 5 ml of deuterated chloroform. Tetramethyl-
silane was used as an internal reference.
Quantitative analysis corresponding to the amount of
pendant carboxyl groups incorporated onto sPS was
done by a titration method as follows: 0.2 g of modified
polymer was put in 50 ml refluxing chloroform/metha-
nol mixture (99/1, v/v) for 2 h. Then the hot solution
was directly titrated without permitting it to cool to
J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829 825
a phenolphthalein end point using sodium hydroxide
(0.05 molL�1) in methanol. Results were expressed as
the degree of succinoylation, which is defined as the
mole percentage of the styrene units succinoylated. Sam-
ple without modification was also titrated, yielding the
blank value.
Thermal analysis was performed using a TA instru-
ments Q10 differential scanning calorimeter equipped
with a RCS accessory under nitrogen atmosphere. For
all samples, the standard procedure is as follows: the
samples (about 5 mg) were heated at 300 �C for 5 min
in order to eliminate the influence of thermal history
and the effect of heat treatment on the crystalline struc-
ture of the materials, then cooled down to 50 �C to
record the crystallization temperatures, and then re-
heated to 300 �C to record the melting temperatures,
all at a rate of 20 �Cmin�1. The recorded temperatures
were calibrated using Indium as standard.
3. Results and discussion
3.1. Acylation reaction
Friedel–Crafts acylation reactions are aromatic sub-
stitution reactions in which benzene (or a substituted
benzene) undergoes acylation when treated with carboxy-
lic acid derivatives (usually acyl halide or anhydride)
and a Lewis acid catalyst, such as AlCl3 [20]. These reac-
tions were widely used to modify polystyrene through
the side groups (phenyl rings) of macromolecules [21].
However, crosslinking reaction of acylated macromole-
cules usually occurs in Friedel–Crafts acylation reac-
tions, which leads to changes in the molecular mass
and the solubility of the modified polymers. In order
to overcome this problem, Hird and Eisenberg [18] re-
ported a simple method for the preparation of partial
p-carboxylation of linear polystyrene without degrada-
tion or crosslinking of the polymer. It is well established
that, in Friedel–Crafts acylation reactions, when alumi-
num chloride and acetyl chloride are allowed to react to-
gether prior to addition to the substrate, the ratio of
catalyst to acyl component remains constant throughout
the reaction, and the results are reproducible.
In this study, Friedel–Crafts acylation reaction was
used to prepare slightly succinoylated syndiotactic poly-
styrene (s-sPS) in a heterogeneous process. However,
conducting the succinoylation reaction in the solution
state proved to be difficult, since sPS only dissolves in
high-boiling chlorinated solvents, such as 1,2,4-trichlo-
robenzene and 1,1,2-trichloroethane, at elevated temper-
atures. It is well known that chlorinated solvents and
high temperatures will have opposite influences on the
acylation procedure [20]. Thus, in the first stage of the
heterogeneous sPS succinoylation experiments, a
charge–transfer complex is formed between AlCl3 and
succinic anhydride in carbon disulfide. After stirring this
complex about 30 �C for 2 h, powder sPS (200 mesh)
was added, then a formation of HCl occurred and the
polymer was functionalized (Scheme 1). The following
parameters, such as the amount of AlCl3, reaction tem-
perature and reaction time, were changed in order to
optimize the process. The work-up procedure involves
treatment with ice water followed by dilute hydro-
chloride acid to decompose the complex and dissolve
the aluminum salts. The degree of succinoylation corre-
sponding to carboxylic acid value of the polymers was
determined by chemical titration, and the data are pre-
sented in Table 1.
As shown in Table 1, a noticeable increase of the de-
gree of succinoylation can be observed initially with
increasing catalyst concentration. The results indicate
that a relatively higher equimolar catalyst concentration
which depends on the [AlCl3]/[SA] molar ratio is desired
to promote succinoylation efficiency. Data for the succi-
noylation reactions at different temperature show an in-
crease in the succinoylation efficiency with increasing
reaction temperature. On the other hand, a high reaction
temperature would lead to crosslinking of sPS. As well,
time plays an important role on the succinoylation per-
centage in the Friedel–Crafts reactions. When succinic
anhydride and AlCl3 was first added as to form a
charge–transfer complex in the reaction medium to elimi-
nate undesirable side reactions, crosslinking was still ob-
served in the presence of high levels of AlCl3, i.e.,
[AlCl3]/[SA] molar ratio above 3/1, in parallel with high
reaction temperature, i.e., above 40 �C. This is attrib-
uted to a low reactivity between succinic anhydride
and AlCl3 generated on the sPS backbone, which is be-
lieved to be responsible for the increased crosslinking.
With respect to the sPS acetylation reactions [12], it is
worth noting that the low sPS succinoylation efficiency
was achieved due to the lower reactivity of succinic
anhydride and aluminum chloride complex in compari-
son with acetyl chloride.
3.2. FTIR analysis
To aid in the structural elucidation of the succinic
anhydride-functionalization chemistries, sPS with car-
boxyl moieties along the backbone was analyzed using
FTIR spectroscopy, and assignments for the characteris-
tic groups were developed.
FTIR spectra of pure sPS and the s-sPS with a degree
of succinoylation of 3.7 mol% in the range 2000–
1500 cm�1 are given in Fig. 1a and b, respectively. Com-
pared with Fig. 1a, two new bands appeared at 1685 and
1713 cm�1 in Fig. 1b, which confirmed the presence of
carbonyl groups in the s-sPS. In the s-sPS molecule,
two different carbonyl functional groups separated by
two carbon atoms do not lie in the same plane and
can be assigned to individual keto and acid groups.
O
O
O
AlCl3
AlCl3O
O
O
H2C CH CH2 CH
O
O
O
AlCl3
H2C CH CH2 CH
H2C
H2C O
O
OH
O
O
O
AlCl3H2C CH CH2 CH
H+/H2O
m
m
n
n
m n
(1)
(2)
Scheme 1.
Table 1
Synthesis of s-sPS by Friedel–Crafts reactiona
Run [AlCl3]/[SA]
(molar ratio)
Timeb
(h)
Temperature
(�C)DSc
(mol%)
1 2 2 20 0.5
2 2 2 30 1.5
3 2 2 40 4.1
4 3 2 30 2.8
5 4 2 30 4.6
6 3 4 30 3.7
7 3 6 30 5.9
a Conditions: sPS, 0.52 g (5 mmol); SA, 0.50 g (5 mmol);
CS2, 50 ml.b The reaction time are refereed to duration of reaction
between the AlCl3–SA charge–transfer complex and sPS
polymer.c DS referred to the degree of succinoylation obtained by
titration analysis.
2000 1900 1800 1700 1600 1500
Tran
smitt
ance
Wavenumber (cm-1)
a
b
Fig. 1. FTIR spectra of pure sPS (a) and s-sPS (b) with
degree of succinoylation of 3.7 mol% in the range of 2000–
1500 cm�1.
826 J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829
Conjugation with an aromatic group leads a lower fre-
quency, the keto absorbs at 1685 cm�1, while the free
acid exhibited bands at 1713 cm�1 which attributed to
absorbance of isolated and hydrogen-bonded carbonyl
groups [22].
J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829 827
3.3. NMR analysis
Supporting evidence for the structural elucidation
was revealed by 1H NMR analysis. Fig. 2 shows the1H NMR spectra of starting sPS and the s-sPS with de-
gree of succinoylation of 3.7 mol%. The resonances at
about 1.8 and 1.3 ppm are assigned to CH and CH2
units in the sPS backbone, respectively. After succi-
noylation, two new broad peaks at about 2.8 ppm and
3.2 ppm, due to methylene (CH2) proton of –COCH2-
CH2COOH moiety, are observed. Furthermore, in the
aromatic region, a new peak due to the protons ortho
to the succinoyl group appears around 7.6 ppm [23]. A
similar chemical shift was observed for the published
acetylated sPS [12].
The degree of succinoylation of the resultant polymer
can be estimated from the ratio of the integrated area
under the peaks resulting from the aliphatic and aro-
matic protons in the 1H NMR. The signals of respective
protons in the modified polymer were assigned as a, b, c
and d as shown in Fig. 2. Aa, Ab, Ac and Ad denote inte-
grated area under the signals of respective protons maxi-
mum at d = 1.80, 1.29, 3.22 and 2.84 ppm. The degree of
succinoylation (DS) of partially succinoylated sPS was
calculated from the relative intensities of the respective
signals in 1H NMR spectra according to the following
equation:
DS ¼ f½3� ðAc þ AdÞ�=½4� ðAa þ AbÞ�g � 100%
The value obtained by a NMR quantitative analyti-
cal method through the equation (4.0 mol%) was found
to be in agreement with the titration analysis (3.7 mol%).
3.4. Thermal analysis
The random incorporation of small quantities of
noncrystallizable comonomer units into the backbone
10 9 8 7 6 5 4 3 2 1 0
H2C CH CH2 CH
H2C
H2C O
O
OH
a
c
d
b
m n
dc
b
a
B
A
ppm
Fig. 2. 1H NMR spectra pure sPS (A) and s-sPS (B) with
degree of succinoylation of 3.7 mol%.
of a semicrystalline polymer has a dramatic effect on
the thermodynamics and kinetics of crystallization. Rela-
tive to the behavior observed with homopolymer, crys-
tallizable copolymers usually exhibit low melting
temperature, low degrees of crystallinity, and a signifi-
cant decrease in the overall rate of crystallization [24].
In attempt to understand the link between succinoyl
moieties and crystallization of s-sPS, the thermal beha-
vior of s-sPS was investigated by means of DSC.
The sample subjected to the DSC experiments are
used the following protocol: equilibrium at 300 �C and
kept at this temperature for 5 min, then cooling from
300 to 50 �C, and finally reheating from 50 to 300 �C,both the heating and cooling rate are 20 �Cmin�1. Figs.
3 and 4 exhibit DSC scans of sPS (a) and related s-sPS
with different degree of succinoylation ((b) 0.5 mol%,
(c) 1.5 mol%, (d) 3.7 mol% and (e) 5.9 mol%). Table 2
lists the thermal data for each of the samples shown in
Figs. 3 and 4.
From crystallization temperature (Tc) recorded from
the cooling scans of the samples (Fig. 3), the crystalliza-
tion endotherm of pure sPS occurs at the highest tem-
perature and has the sharpest crystallization exotherm,
while crystallization temperature (Tc) and enthalpy of
cryatallization (DHc) for s-sPS samples from the melt de-
creased with increasing degree of succinoylation. Fur-
thermore, a more broadened transition temperature
range has been observed for all succinoylated samples
with increasing degree of succinoylation, which indicates
that the nonisothermal crystallization rate decreases
with increasing degree of succinoylation. This suggests
that the crystallization rate can be retarded by the pres-
ence of covalently attached carboxyl groups.
Generally, the degree of crystallinity of crystallizable
polymer materials can be estimated by measuring the
50 100 150 200 250 300Temperature (°C)
a
b
c
d
e
Endo
Fig. 3. DSC cooling scans of pure sPS (a) and s-sPS with
different degree of succinoylation, (b) 0.5 mol%, (c) 1.5 mol%,
(d) 3.7 mol% and (e) 5.9 mol%.
50 100 150 200 250 300Temperature (°C)
a
b
c
d
e
Endo
Fig. 4. DSC heating scans of pure sPS (a) and s-sPS with
different degree of succinoylation, (b) 0.5 mol%, (c) 1.5 mol%,
(d) 3.7 mol% and (e) 5.9 mol%.
828 J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829
enthalpic changes at melt. The melting enthalpy of 100%
crystalline sPS has been reported to be 53 Jg�1 [25].
Using this value, the degree of crystallinity (Xc) of the
samples was calculated. The data in Table 2 exhibits a
systematic trend of degree of crystallinity (Xc) depres-
sion with increasing degree of succinoylation. For the
sample with degree of succinoylation of 5.9 mol%, its
Xc value is 23%, much lower than that of neat sPS
(56%).
The melting point (Tm) of succinoylated polymers in
Fig. 4, as expected, exhibits a systematic trend of depres-
sion with increasing degree of succinoylation. The Tm of
neat sPS is around 270 �C, similar to the value previ-
ously obtained [26]. For the 5.9 mol% succinoylated
polymer sample, the Tm decreases to about 255 �C. Thisresult is quite different from the acetylated syndiotactic
polystyrene. For the 42.6 mol% acetylated syndiotactic
polystyrene sample, the Tm is about 265 �C [12]. This
phenomenon may be explained by comparing the size
of acyl substituents between the acylated styrene units.
It is expected that in s-sPS due to the larger size of the
Table 2
Summary of DSC results for sPS and s-sPS
Run DSa (mol%) Tgb (�C) Tm
b (�C) DHm
1 0 92.7 270.7 29.5
2 0.5 97.2 269.8 27.5
3 1.5 97.1 268.0 19.6
4 3.7 98.3 263.8 16.0
5 5.9 95.1 255.6 13.4
a DS referred to the degree of succinoylation.b The glass transition temperatures, Tgs were determined as the mi
crystallization, Tc temperatures were selected as the peak maximum orc The degree of crystallinity in the sample, Xc is determined by the
enthalpy of the sample and DH 0m is the melting enthalpy of 100% cry
substituent group, the chain mobility, which is required
for significant crystallization, would be less in s-sPS rela-
tive to the acetylated sPS. Thus, based on this chain
mobility argument, the succinoylated styrene units may
interrupt or retard crystal growth, limiting the size of
the crystallites achievable and resulting in the depression
of melting point.
The glass transition temperature (Tg) data also helps
in understanding the effects of succinoyl groups on the
movement of the polymer chains. It is clear from Table
2 that the Tg value of the modified polymer increases
with increasing the degree of succinoylation. For exam-
ple, as degree of succinoylation increases, Tg increases
from 93 �C for neat sPS to 98 �C for the 3.7 mol% s-
sPS sample. As mentioned above, the substituent groups
result in reducing the mobility of the polymer chains and
therefore raising Tg values. Furthermore, compared with
neat sPS, due to the interactions between the acid
groups, e.g., hydrogen bonding, the mobility of the poly-
mer chains is also reduced, thus raising Tgin the modi-
fied samples. This result also coincides with the results
presented in Refs. [9,12].
4. Conclusions
The succinoylated syndiotactic polystyrene was
accomplished by Friedel–Crafts reaction in a heteroge-
neous process by using carbon disulfide as dispersing
agent, succinic anhydride as succinoylating agent and
aluminum chloride as catalyst. An optimum reaction
should be carried out at 30 �C with a molar ratio of alu-
minum chloride to succinic anhydride of 3/1. The succi-
noylated syndiotactic polystyrene was confirmed by
FTIR and 1H NMR spectroscopy. Moreover, it is found
that thermal behavior of the succinoylated syndiotactic
polystyrene exhibits considerable differences in compari-
son to the neat sPS. The melting temperature (Tm), crys-
tallization temperature (Tc), and degree of crystallinity
of the succinoylated polymer samples decreases with
increasing the degree of succinoylation, while the glass
(Jg�1) Xcc (%) Tc
b (�C) DHc (Jg�1)
55.7 239.5 30.4
51.9 236.7 26.9
37.0 225.8 20.3
30.2 213.0 16.7
25.3 197.6 16.0
dpoint of the step change in the heat flow. The melting, Tm and
minimum in endothermic or exothermic transition, respectively.
equation: X c ¼ ðDHm=DH0mÞ � 100%, where DHm is the melting
stalline sPS (53 Jg�1 [25]).
J. Li, H.-M. Li / European Polymer Journal 41 (2005) 823–829 829
transition temperature increases. The functionalized sPS
offers possibility for the development of novel sPS-based
polymer blends and composites, thus extending the
application field of sPS.
Acknowledgments
The authors thank the Key Project of Scientific Re-
search Funds of Hunan Provincial Education Depart-
ment (02A011) for support of this work.
References
[1] Ishihara N, Seimiya T, Kuramoto M, Uoi M. Macro-
molecules 1986;19:2464.
[2] Li HM, Shen ZG, Zhu FM, Lin SA. Eur Polym J 2002;
38:1255.
[3] Hong BK, Jo WH. Polymer 2000;41:2069.
[4] Longo P, Oliva L, Grassi A. Macromol Chem 1990;191:
2387.
[5] Aaltonen P, Seppala J, Matilainen L, Leskela M. Macro-
molecules 1994;27:3136.
[6] Xu G, Lin SA. Macromolecules 1997;30:685.
[7] Dong JY, Manias E, Chung TC. Macromolecules 2002;35:
3439.
[8] Xu G, Chung TC. Macromolecules 2000;33:5803.
[9] Su ZH, Li X, Hsu SL. Macromolecules 1994;27:287.
[10] Orler EB, Yontz DJ, Moore RB. Macromolecules 1993;26:
5157.
[11] Jejiku T, Woolman JG. JP 10195133, 1998.
[12] Gao Y, Li HM. Polym Int 2004;53:1436.
[13] Li HM, Chen HB, Shen ZG, Lin SA. Polymer 2002;43:
5455.
[14] Lim JG, Baik JH, Zhang XQ, Son Y, Choi WM, Park OO.
Polym Bull 2002;48:397.
[15] Liu SS, Sen A. Macromolecules 2000;33:5106.
[16] Liu SS, Sen A. J Polym Sci, Polym Chem 2001;39:446.
[17] Kurbanova RA, Mirzaoglu R, Akovali G, Rzaev ZMO,
Karatas I, Okudan A. J Appl Polym Sci 1996;59:235.
[18] Hird B, Eisenberg A. J Polym Sci, Polym Chem 1993;37:
1377.
[19] Zhu FM, Lin SA, Zhou WL, Tu JJ, Chen DQ. Chem
J Chin Univ 1998;19:1844.
[20] Andrew SJ. Introduction to organic chemistry. New
York: Wiley; 1971.
[21] Sun G, Chen TY, Worely SD. Polymer 1996;37:3753.
[22] Bellamy LJ. The infrared spectra of complex molecules,
vol. 2. 2nd ed. London and New York: Chapman and
Hall; 1980.
[23] Nasrullah JM, Raja S, Vijayakumaran K, Dhamo-
dharan R. J Polym Sci, Polym Chem 2000;38:453.
[24] Orler EB, Calhoun BH, Moore RB. Macromolecules 1996;
29:5965.
[25] De Candia F, Filho AR, Vittoria V. Colloid Polym Sci
1991;269:650.
[26] Li HM, Liu JC, Zhu FM, Lin SA. Polym Int 2001;50:
421.