thermostable polycyanurate-polyhedral oligomeric silsesquioxane hybrid networks: synthesis, dynamics...
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Macromol. Symp. 2012, 316, 90–96 DOI: 10.1002/masy.20125061290
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Thermostable Polycyanurate-Polyhedral Oligomeric
Silsesquioxane Hybrid Networks: Synthesis,
Dynamics and Thermal Behavior
Olga Starostenko,1 Vladimir Bershtein,*2 Alexander Fainleib,1 Larisa Egorova,2
Olga Grigoryeva,1 Alfred Sinani,2 Pavel Yakushev2
Summary: A series of hybrid polycyanurate - epoxy cyclohexyl-functionalized poly-
hedral oligomeric silsesquioxane (PCN/ECH-POSS) nanocomposite networks with
ECH-POSS content varying from 0.025 to 10 wt. % were synthesized and characterized
using FTIR, DSC, DMA and CRS techniques. It was revealed that already as low as
0.025 wt. % POSS cardinally changed PCN glass transition characteristics including
the strong shift of the transition onset to higher temperatures and manifesting a
second, higher-temperature glass transition characterizing interfacial dynamics;
additionally, enhancing creep resistance and thermal stability at the earlier stage
of degradation were observed.
Keywords: glass transition; nanocomposites; polycyanurates; POSS
Introduction
Densely cross-linked polycyanurates (PCN)
synthesized from cyanate ester resins have
attracted much interest in recent years
because of their excellent thermal and good
mechanical properties, which commend
them for use in high performance technology
(e.g., as matrices for composites for high-
speed electronic circuitry and transpor-
tation).[1,2] Additionally, cyanate/epoxy
composites provide superior performance
through the co-reaction between cyanate
and epoxy groups of blend components; as a
result, fine properties of the final composite
are reached.[3] Further enhancing PCN and/
or overcoming their drawbacks could be
attained in PCN hybrids and nanocompo-
sites.[4]
Last years the great attention has been
paid to preparing and characterization of
hybrid polymer/inorganic nanocomposites
stitute of Macromolecular Chemistry, NAS, 02160
yiv, Ukraine
ffe Physical-Technical Institute, RAS, 194021
.-Petersburg, Russia
mail: [email protected]
yright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
containing 3D molecules (particles) of poly-
hedral oligomeric silsesquioxane (POSS) of
about 1 nm in size.[5] POSS compounds have
the cage structureswith the common formula
(RSiO1.5)8, 10, or 12, which are called as T8, T10
and T12 cages, respectively. Typically, an
each cage silicone atom in POSS is bonded
to three oxygen atoms and to a single R
substituent. The functional groups of POSS
may react, via grafting, copolymerization or
other reaction, with monomer or polymer,
and hence POSS cages can be covalently
incorporated into a polymer matrix. Thus,
POSS offers a chance to prepare hybrid
nanocomposites with molecularly dispersed
inorganic structural units where POSS
cages may be considered, to a certain
extent, as�1 nm silica inclusions or clusters
chemically bound with a polymer matrix.
Just the ability of POSS to be dispersed as
unassociated units covalently bound to a
matrix is the key to impact POSS on
polymer dynamics and properties. The
numerous studies (see, e.g.,[5–9]) showed
that different polymer-POSS nanocompo-
sites can exhibit dramatic improvements in
polymer matrix properties such as thermal
stability, oxidation resistance, mechanical
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Macromol. Symp. 2012, 316, 90–96 91
behavior, surface hardness as well as
reduction in flammability and so on.
Recently, amine- or cyan-, or hydroxyl-
functionalized POSS molecules were intro-
duced into cyanate ester resin in the
amounts from 1 to 15wt. %.[10,11] Thus,
octaaminophenyl-POSS additive provided
formation of the hybrid PCN/POSS nano-
composites with the substantially changed
properties, in particular Tg shift to both
higher and lower temperatures.
In the present study, the nanocomposites
based on PCN with different doping levels
by epoxy cyclohexyl-POSS, starting from
0.025wt. %, were studied. The chemical
structure and final properties of the nano-
composites were investigated by means of
Fourier-transform infra-red spectroscopy
(FTIR), differential scanning calorimetry
(DSC), dynamic mechanical analysis (DMA)
and laser-interferometric creep rate spec-
troscopy (CRS).
Experimental Part
1,1’-bis(4-cyanatophenyl) ethane (dicya-
nate ester of bisphenol E, DCBE), under
the trade name PRIMASET1 LECy L-10
(from Lonza Group Ltd., Switzerland), and
epoxy cyclohexyl POSS1 Cage Mixture
(ECH-POSS, from Hybrid Plastics Inc.,
Hattiesburg, MS, USA) were used as
received. The formulas for this monomer
and ECH-POSS (T8 cage) are shown
below. The polymer nanocomposites
from DCBE and ECH-POSS with ECH-
POSS content c¼ 0.025, 0.05, 0.1, 0.5, 1.0,
2.0, 5.0, and 10.0wt. % were synthesized.
The initial mixtures were first stirred
at 1708C during 2 hrs for pre-polymeriza-
tion of DCBE and chemical grafting of
ECH-
Copyright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
POSS to the growing PCN network
through the reaction between cyanate and
epoxy groups. Then the filled pre-polymer
was step-by-step cured and sequentially
post-cured at 170-3008C for 6 hrs.
At monitoring the curing process, FTIR
spectra were recorded between 4000 and
600 cm�1 using a Bruker Tensor 37 spectro-
meter. For each spectrum, 32 consecutive
scans with a resolution of 4 cm�1 were
averaged. The IR band at 2968 cm�1 was
used as an internal standard. The dynamics,
thermal behavior and elastic properties
of the PCN/ECH-POSS hybrids were
characterized using the combined DSC
(Perkin-Elmer DSC-2 apparatus), DMA
(DMS 6100 Seiko Instruments, 1Hz), and
CRS[12] approach.
Results and discussion
Figure 1 shows how decreasing the inten-
sities of the absorption bands at 2237 and
2266 cm�1 characterizing cyanate groups is
accompanied with appearing the bands at
1369 and 1564 cm�1 of the cyanurate ring
vibration in the spectra during the poly-
merization of initial DCBE/POSS mixture,
as a consequence of the basic process
of polycyclotrimerization of cyanate
groups with formation of triazine cycles.
Meantime, the slight absorption band at
1738 cm�1 appears also in the nanocompo-
site spectra which confirms the presence of
oxazolidinone rings formed owing to co-
reaction between cyanate groups of DCBE
and epoxy groups of ECH-POSS.[3] This
provides the evidence of chemical hybridi-
zation between both constituents in these
systems. A simplified scheme of molecular
structure of the hybrid network formed is
presented in Fig. 2.
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Figure 1.
FTIR spectra of model initial PCN/ECH-POSS reactive blend (a), and heated at 1708C for 2 hrs (b) or 3 hrs (c). The
composition of the blend was cyanate/epoxy groups¼ 1:1.
Macromol. Symp. 2012, 316, 90–9692
It was revealed that POSS additives
substantially changed PCN glass transition
characteristics, as estimated by DSC
(Figs. 3 and 4). Unlike a single glass
transition (Tg¼ 2448C) in neat PCN, DSC
Figure 2.
A scheme of PCN/ECH-POSS molecular structure fragme
Copyright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
curves of the hybrids exhibit two transi-
tions, the main one with Tg1 varying,
depending on a composition, from 243 to
2758C, and the weaker transition with Tg2 �3758C followed by the hybrid degradation.
nt.
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Figure 4.
Main glass transition temperatures of the PCN/ECH-
POSS nanocomposites as a function of POSS content.
Figure 3.
DSC curves of neat PCN and three PCN/ECH-POSS
nanocomposites at heating up to 4008C with the
rate 208Cmin�1 (scans I and II, cooling rate
3208Cmin�1).
Macromol. Symp. 2012, 316, 90–96 93
The latter transition may be assigned to
dynamics in the interfacial layers (a strong
‘‘constrained dynamics’’ effect [12,13]).
TGA control showed that thermal
degradation with mass loss started from
� 4208C for neat PCN and low-POSS
content composites, however, degradation
of interfacial bonds started, obviously,
already at T � 4008C since the second glass
transition disappeared in the DSC curves
obtained at scan II (Fig. 3). The largest, by
�300, increasing Tg1 was recorded for the
hybrids with c¼ 0.025 or 0.1% only;
essentially, the temperature of glass transi-
tion onset, Tg1’, increased from 209 to
Copyright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
2618C, and main glass transition became
more narrow in these hybrids (from 540 for
neat PCN to 20-258C for the hybrids,
Fig. 4). The opposite tendency of decreas-
ing Tg1, especially Tg1’, and broadening
glass transition was observed at high POSS
contents, obviously, due to decreasing
locally PCN cross-linking because of DCBE
expense for co-reaction with ECH-POSS.
Enhancing thermal stability of PCN-
POSS hybrids compared with neat PCN at
the earlier stage of degradation was
revealed also by DSC: after scanning to
4008C in nitrogen atmosphere, the tem-
peratures of the transition onset Tg1’ at
scanning II equaled 1878C for neat PCN,
1618C for the hybrid with c¼ 10% but
2498C for the hybrid with c¼ 0.025%.
Similarly, unlike DMA peak with
Tmax¼ 2488C in neat PCN, the main peak
with Tmax varying from 246 to 2658C(the latter at c¼ 0.025%), as well as the
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Macromol. Symp. 2012, 316, 90–9694
overlapping peaks at �370–390 and 4308C,associated with the interfacial dynamics
and degradation process respectively, were
observed for the hybrids. Dynamic modulus
E’ over the 20–2008C range increased for
the hybrids regarding neat PCN, maximum
by 30–40% at c¼ 0.5% (Fig. 5).
At last, the discrete creep rate spectra,
including a few overlapping peaks and
demonstrating the pronounced dynamic
heterogeneity aroundmain Tg, were obtained
(Fig. 6). The constrained dynamics effect
manifests itself here in the displacement of
the spectra by 10-208C to higher tempera-
tures regarding the PCN spectrum, enhan-
cing creep resistance and increasing the
temperature of the sharp creep acceleration
and fracture of the nanocomposites regard-
Figure 5.
DMA data (above - Tand, below – dynamic modulus E’ vs
ECH-POSS hybrids.
Copyright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
ing neat PCN, e.g., from 270 to 3308C at
c¼ 0.1wt.%.
Thus, the most remarkable result in this
study is the strong impact on polymer
dynamics of very low 3D nanofiller content,
viz., as low as 0.025wt. %. Really, for linear
polymer matrix with 3D nanofiller additive,
a totally nanoscopically-confined state of a
matrix is usually suggested in case an
average inter-particle distance, L, is close
to or less than the unperturbed dimensions
of macromolecular random coil, as esti-
mated by radius of gyration Rg, typically of
an order of 10 nm in size for many
polymers.[12,13] Therefore, a few percent
loading was typically required for attaining
the substantial constraining dynamics by
3D particles of 10-20 nm size. Meantime, in
. temperature plots) obtained for PCN and three PCN/
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Figure 6.
Creep rate spectra obtained at tensile stress 0.5MPa for neat PCN and two hybrids.
Macromol. Symp. 2012, 316, 90–96 95
the case of semi-interpenetrating networks
such effect was strongly pronounced at
0.25wt. % nanodiamonds only when L >>
Rg; this was explained by the double
covalent bonding (hybridization) between
the matrix components and of the matrix
with nanofiller.[14]
The unusually large impact of 0.025%
POSS on PCN glass transition dynamics
may be explained, obviously, by the
combined action of a few factors. First,
separated (unassociated) 1-nm size ECH-
POSS molecules of cage structure play the
role of nanofiller particles (silica nano-
blocks) with extraordinarily high specific
surface area of a few thousands m2g�1; that
provides the enormous surface of inter-
facial boundaries in the hybrid nanocom-
posites under study and �10 nm average
inter-particle distances at c¼ 0.025wt. %
POSS. Secondly, strong interfacial interac-
tions due to covalent bonding of POSS with
the polymer matrix are of importance.
Meantime, however, the amounts of 1-
10wt. % POSS have earlier been used
typically as the blocks at preparing poly-
mer-inorganic hybrids.[5] Therefore, we
suppose that unusually strong influence of
Copyright � 2012 WILEY-VCH Verlag GmbH & Co. KGaA
low POSS loading on dynamics may be
treated also as a consequence of more long-
range impact of rigid 3D nanoparticles
within the densely cross-linked PCNmatrix
than in linear or loosely cross-linked
matrices.
Thus, under the optimal conditions the
nanocomposites studied behave, to a cer-
tain extent, as ‘‘interphase controlled
materials’’ containing mainly the nanodo-
mains with exclusively strongly (directly at
interfaces, glass transition at �370–3908C)and substantially suppressed dynamics
(main glass transition at � 260–2808C).
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