polyurethane networks nanoreinforced by polyhedral oligomeric silsesquioxane
TRANSCRIPT
Polyurethane Networks Nanoreinforced by Polyhedral
Oligomeric Silsesquioxane
Hongzhi Liu, Sixun Zheng*
Department of Polymer Science and Engineering, Shanghai Jiao Tong University, Shanghai 200240, P. R. ChinaFax: 86-21-54741297; E-mail: [email protected]
Received: October 11, 2004; Revised: November 16, 2004; Accepted: December 1, 2004; DOI: 10.1002/marc.200400465
Keywords: nanocomposites; polyhedral oligomeric silsesquioxane; polyurethanes
Introduction
Incorporating inorganic or organometallic segments into
polymers to afford improved properties continues to be a
driving force for the development of new materials.[1,2]
Polyhedral oligomeric silsesquioxane (POSS) reagents,
monomers and polymers are emerging as a new chemical
technology for nano-reinforced organic-inorganic hybrids.
Polymers incorporating POSS are becoming the focus of
many studies due to the simplicity of processing and the
excellent comprehensive properties of this class of hybrid
materials.[3–12]
Most previous studies have been concerned with thermo-
plastics or thermosets and the modification of elastomeric
polymers with POSS was relatively less common.[13–15]
Polyurethanes (PU) are an important class of elastomeric
materials and their extensive applications motivated us
to prepare materials with improved properties. Hsiao
et al.[15,16] investigated the structure and properties of
linear POSS-containing polyurethane. In their work, a
3-(allybisphenol-A) propyldimethysiloxane POSS was
used as a chain extender and the POSS was grafted onto
the macromolecular backbone through one corner group.
More recently, Devaus et al.[17] reported that the incorpora-
tion of POSS into polyurethane gave materials with
improved flame retardance. To the best of our knowledge,
there are no reports on studies of polyurethane networks
containing POSS.
In this communication, we have reported the synthesis
and characterization of polyurethane networks incorporat-
ing POSS. An octaaminophenyl polyhedral oligomeric
silsesquioxane (OapPOSS) was used to replace part of the
Summary: Octaaminophenyl polyhedral oligomeric silses-quioxane (OapPOSS) was used as a crosslinking agent to-gether with 4,4
0-methylenebis-(2-chloroaniline) to prepare
polyurethane networks containing POSS. Fourier transforminfrared spectroscopy (FT-IR), dynamic mechanical analysis(DMA) and thermogravimetric analysis (TGA) were em-ployed to characterize the POSS-reinforced polyurethane.The POSS-containing PU networks displayed enhanced glasstransition temperatures (Tgs) and the storage moduli of thenetworks of the glassy state and rubber plateaus were alsoobserved to be significantly higher than that of the controlpolyurethane although only a small amount of POSS wasincorporated into the systems. The results can be ascribed tothe significant nanoscale reinforcement effect of POSS cageson the polyurethane matrix. TGA results showed the thermalstability was also improved with incorporation of POSS intothe system.
Dynamic mechanical spectra of PU and PU nanocompositescontaining POSS.
Macromol. Rapid Commun. 2005, 26, 196–200 DOI: 10.1002/marc.200400465 � 2005 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
196 Communication
aromatic amine crosslinking agent [viz. 4,40-methylenebis-
(2-chloroaniline), MOCA] and thus the POSS cages act as
nanostructured crosslinking sites. The nanoscale reinforce-
ment effect of POSS on the polyurethane networks and the
thermal stability of the hybrid polyurethanes were address-
ed on the basis of dynamic mechanical analysis (DMA) and
thermogravimetric analysis (TGA).
Experimental Part
Materials and Preparation of Samples
The POSS monomer used in this work was an octaaminophenylpolyhedral oligomeric silsesquioxane (denoted OapPOSS),as shown in Scheme 1, which was synthesized by followingliterature methods[18,19] with slight modification.[20] Toluene-2,4-diisocyanate (TDI) was of a chemically pure grade and wasobtained from Shanghai Reagent Co., Shanghai, China. Poly-(propylene oxide) glycol was kindly supplied by PolyurethaneDivision, Gaoqiao Petrochemical Co. Shanghai, China underthe trade name of GE-210 and had a quoted molecular weightof Mn ¼ 1 000. 4,4
0-Methylenebis-(2-chloroaniline) (MOCA)
was used as the crosslinking agent and was kindly supplied byChangshan Chemical Factory, Zhejiang Province, China. Allthe solvents used in this work were obtained from commercialsource and purified in general ways before use.
Synthesis of PU Networks Containing POSS
25.68 g (25.68 mmol) of polyether glycol and 7.15 g(41.09 mmol) of TDI were charged into a 250 ml three-neckedround bottomed flask, equipped with a mechanical stirrer. Thereaction was performed under a nitrogen atmosphere at 80 8Cfor 2 h to afford the polyurethane prepolymer, which was usedfor the next reaction. 0.21 g (0.18 mmol) of OapPOSS wasdissolved in 10 ml of N,N-dimethylformamide (DMF) and thesolution was added to the above PU prepolymer at 80 8C withvigorous stirring for 2 h and the small amount of DMF wasdistilled out under reduced pressure and the POSS-containingocta-armed star-like polyurethane prepolymer was obtained.An equal molar amount of MOCAwas added to the system withrespect to the remnant number of –NCO groups in the POSS-containing polyurethane prepolymers. This was vigorouslystirred and the mixtures were then cast into a pre-heatedstainless steel mold. The samples were sealed in the molds andcured at 100 8C for 2 h and at 120 8C for 3 h. The wholepreparation procedure for the POSS-PU is depicted inScheme 1.
Measurement and Techniques
Fourier Transform Infrared Spectroscopy (FT-IR)
The infrared measurements were conducted on a Perkin-ElmerParagon 1000 Fourier transform spectrometer at room
Scheme 1. Synthesis of polyurethane networks containing POSS.
Polyurethane Networks Nanoreinforced by Polyhedral Oligomeric Silsesquioxane 197
Macromol. Rapid Commun. 2005, 26, 196–200 www.mrc-journal.de � 2005 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
temperature (25 8C). The attenuated total reflection (ATR)accessories were used to measure the FT-IR spectra of all thespecimens at fresh surfaces. In all cases, 64 scans at a resolutionof 2 cm�1 were used to record the spectra.
Dynamic Mechanical Analysis (DMA)
The dynamic mechanical tests were carried out on a DynamicMechanical Thermal Analyzer (DMTA) (MKIII, RheometricScientific Ltd, UK) using a temperature range from �80 to100 8C. The frequency used was 1.0 Hz at a heating rate of3.0 8C min�1. The experiments were carried out until thesample became too soft to be tested.
Thermogravimetric Analysis (TGA)
A Perkin-Elmer thermal gravimetric analyzer (TGA-7) wasused to investigate the thermal stability of the hybrids. Thesamples (about 10 mg) were heated under a nitrogen atmos-phere from ambient temperature up to 600 8C at a heating rateof 20 8C �min�1 in all cases.
Results and Discussion
In order to prepare the POSS-modified polyurethane elasto-
mer, the molar ratio of isocyanate to polyether glycol was
set at 1.6:1 and the rest of the isocyanate groups were
allowed to react with the equal molar amount of amine
groups from octaaminophenyl POSS and MOCA. The
fraction of POSS amine groups was controlled to be 0, 5, 10
and 15 mol-% with respect to the total amine groups, which
corresponded to POSS weight fractions of 0, 0.53, 1.12 and
1.68 wt.-% in the total hybrid, respectively. We report here
the synthesis of PU-POSS hybrids via the three-step
continuous reaction as shown in Scheme 1.
Figure 1 shows the FT-IR spectra of the control PU and
PU hybrids containing POSS. For the control PU, the stret-
ching vibrations of the N-H groups occur at 3 300 cm�1,
which together with the carbonyl bands at 1 726 cm�1 are
indicative of the presence of urethane moieties. For
OapPOSS, the double bands at 3 462 and 3 366 cm�1 are
typical of the stretching vibration of the primary aromatic
amine in OapPOSS whereas the band at 1 116 cm�1 is
ascribed to the stretching vibration of Si-O-Si groups in the
silsesquioxane cages. For the PU-POSS hybrids, this band
unfortunately overlapped with that of the aliphatic ether. It
is worth pointing out that the disappearance of the bands at
2 250–2 275 cm�1 which are characteristic of isocyanate
indicates the completion of the crosslinking reaction be-
tween the aromatic amine and the PU prepolymers in the
control PU and PU hybrids containing POSS.
Dynamic Mechanical Properties
Shown in Figure 2 are the dynamic mechanical spectra of
the control PU and the PU hybrids containing 0, 5, 10 and
15 mol-% of OapPOSS with respect to the total amine
groups. It is interesting to note that in the glass state
((�75)–(�25) 8C) the dynamic storage moduli of all
the POSS-containing hybrids are significantly higher than
that of the control PU. The introduction of a small amount of
POSS cages (<2 wt.-%) gave rise to a significant increase in
dynamic storage modulus. It is also worth noticing that the
storage moduli of the rubbery plateau for the POSS-
containing hybrids were close to or higher than that of the
control PU. Only at the higher concentration of POSS (viz.
�15 mol-%) was the storage modulus of the hybrid lower
than that of the control PU. There are several competitive
factors which affect the moduli of the POSS-containing PU
Figure 1. FT-IR spectra of PU and PU hybrids containing POSS.A) OapPOSS; B) 5 mol-% of amine groups of POSS; C) 10 mol-%of amine groups of POSS; D) 15 mol-% of amine groups of POSS.
Figure 2. Dynamic mechanical spectra of the control PU and thePU nanocomposites containing POSS.
198 H. Liu, S. Zheng
Macromol. Rapid Commun. 2005, 26, 196–200 www.mrc-journal.de � 2005 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
networks. On the one hand, the nanoreinforcement of the
POSS cages on the polymer matrices will give rise to an
increase in modulus, as seen in glassy state and the rubbery
materials with the lower POSS contents, i.e. the PU matri-
ces could be reinforced on the nanoscale by the POSS cages
which were covalently bonded onto the PU networks. On
the other hand, the inclusion of POSS in the system could
give rise to a decrease in the densities of the materials,
which will result in a decrease in the moduli of the nano-
composites. The decreased densities could be ascribed to an
increase in the porosity of the nanocomposites.[21,22] The
porosity of POSS-containing nanocomposites is composed
of two portions. One portion comes from the external poro-
sity as a result of the inclusion of POSS cages, which can be
interpreted as the increase in free volume of the nanocom-
posites caused by the interactions of POSS cages and
polymer segments.[21,22] The second portion of porosity can
be attributed to the nanoporosity of the POSS core with a
diameter of 0.54 nm in a POSS cage. The crosslinking
densities per unit volume will decrease with increasing
concentration of POSS in the hybrids. Nonetheless, it can be
seen that the storage moduli of the nanocomposites con-
taining POSS with less than 10 mol-% of amine groups with
respect to the amine groups in all the crosslinking agents are
significantly higher than or close to that of the plain PU.
This implies significant nanoreinforcement by the POSS
cages, which counteracts the effect of decreased densities
on the storage moduli of the rubber plateau for the networks.
Only at higher POSS contents could the effect of the re-
duced degree of crosslinking dominate the nanoreinforce-
ment. In fact, we indeed observed this result when the
concentration of OapPOSS was 15 mol-% with respect to
the amine in all the crosslinking agents (see Figure 2).
Figure 2 also shows plots of tan d as a function of
temperature for the control polyurethane and its hybrids
with POSS. The control polyurethane network exhibits a
well-defined relaxation peak centered at �7.2 8C, which is
ascribed to the glass transition of the crosslinked poly-
urethane. The PU hybrids containing 5 and 10 mol-% of
OapPOSS also clearly display single a transitions on the
internal friction (tan d) versus temperature curves, which
correspond to the glass transition of the materials. It can be
seen that the temperature values of the tan d peaks increase
with increasing POSS concentration. For the nanocompo-
sites containing 15 mol-% of POSS, a ramp peak appeared
at ca. 50 8C, suggesting the formation of a structure with a
higher glass transition temperature, i.e. the POSS-contain-
ing PU hybrids could possess structural inhomogeneities.
This observation is ascribed to the nanoreinforcement effect
of the POSS cages on polyurethane networks. The massive
and bulky POSS cages could restrict the motion of the
macromolecular chains and thus higher temperatures are
required to provide the requisite thermal energy for the
occurrence of a glass transition in hybrid materials.[24] In
addition to the enhancement of glass transition temper-
atures, it was noted that the tan d peaks were significantly
broadened when the content of POSS cages was increased.
The width of the tan d peaks could reflect the structural
homogeneity of the crosslinked networks. The broadening
of the glass transition region could result from the incorpo-
ration of the nanosized massive and bulky POSS cages,
which could restrict the segmental motion of molecular
chains and network junctions, i.e. the topological con-
straints provided by the presence of POSS reinforcements
could slow the motion of the network junctions. Therefore,
a higher temperature is needed to reach structural equili-
brium.[24,25] It has been proposed that the broadening of the
loss peaks could prefigure superior mechanical properties,
such as damping properties.[23]
Thermal Stability
Shown in Figure 3 are the TGA curves of the control PU and
its nanocomposites with POSS. Within the experimental
temperature range, the TGA curves of all the samples dis-
played similar degradation profiles, suggesting that the
existence of the POSS did not significantly alter the degra-
dation mechanism of the matrix polymers. The incorpora-
tion of OapPOSS into the PU networks showed a significant
effect in improving the thermal stability, resulting in a
retarded weight loss rate and an enhanced char yield in the
higher temperature region.[26–29] This effect was observed
to be increasingly significant with increasing the concen-
tration of POSS cages. The improvement in weight reten-
tion was ascribed to the POSS constituent, which
participated in the formation of a homogeneous hybrid
network. The higher char yields for PU nanocomposites
implied that there were fewer volatiles being released from
the nanocomposites during heating. The decreased rate of
Figure 3. TGA curves of PU hybrids containing POSS.
Polyurethane Networks Nanoreinforced by Polyhedral Oligomeric Silsesquioxane 199
Macromol. Rapid Commun. 2005, 26, 196–200 www.mrc-journal.de � 2005 WILEY-VCH Verlag GmbH & Co. KGaA, Weinheim
volatile release from the materials suggested the improved
flame retardance. It is proposed that the inorganic compo-
nent provides additional heat capacity, thereby stabilizing
the bulk materials against thermal decomposition, except at
surfaces where initial decomposition would begin.[30]
Conclusion
Octaaminophenyl polyhedral oligomeric silsesquioxane
was used as a crosslinking agent to prepare polyurethane
hybrid networks. The POSS-containing PU networks
displayed enhanced glass transition temperatures (Tgs).
The storage moduli of the networks at the glassy and rubber
plateaus were observed to be significantly higher than that
of the control polyurethane. The TGA results indicated
that the thermal stabilities of the nanocomposites were
improved, as evidenced by the rate of volatile release from
the materials and the enhanced char yields together with
ceramic yields. The above results could be ascribed to the
significant nanoscale reinforcement effect of the POSS
cages on the polyurethane matrix and the formation of the
specific structure of the POSS-containing PU networks.
Acknowledgements: The financial support from ShanghaiScience and Technology Commission, China under a key project(Number 02DJ14048) is acknowledged. We thank the NaturalScience Foundation of China (Grant Number 20474038,50390090) for partial support of this work.
[1] G. M. Whitesides, J. P. Mathias, C. T. Seto, Science 1991,254, 1312.
[2] J. J. Schwaband, J. D. Lichtenhan, Appl. Organomet. Chem.1998, 12, 707.
[3] F. J. Feher, K. D. Wyndham, R. K. Baldwin, D. Soulivong,J. D. Lichtenhan, J. W. Ziller, Chem. Commun. 1999, 1289.
[4] F. J. Feher, K. D. Wyndham, D. Soulivong, F. Nguyen,J. Chem. Soc., Dalton Trans. 1999, 1491.
[5] J. D. Lichtenhan, N. Q. Vu, J. A. Carter, J. W. Gilman,F. J. Feher, Macromolecules 1993, 26, 2141.
[6] J. D. Lichtenhan, Y. A. Otonari, M. J. Carr, Macromolecules1995, 28, 8435.
[7] T. S. Haddad, J. D. Lichtenhan, J. Inorg. Organomet. Polym.1995, 5, 237.
[8] R. A. Mantz, P. F. Jones, K. P. Chaffee, J. D. Lichtenhan, J. W.Gilman, I. M. K. Ismail, M. J. Burmeister, Chem. Mater.1996, 8, 1250.
[9] T. S. Haddad, J. D. Lichtenhan, Macromolecules 1996, 29,7302.
[10] J. W. Gilman, D. S. Schlitzer, J. D. Lichtenhan, J. Appl.Polym. Sci. 1996, 60, 591.
[11] A. Romo-Uribe, P. T. Mather, T. S. Haddad, J. D. Lichtenhan,J. Polym. Sci., Part B: Polym. Phys. 1998, 36, 1857.
[12] C. Zhang, R. M. Laine, J. Organomet. Chem. 1996, 521, 199.[13] J. D. Lichtenhan, Comments Inorg. Chem. 1995, 17, 115.[14] G. Z. Li, L. C. Wang, H. L. Ni, C. U. Pittman, J. Inor &
Organometallic Polym. 2001, 11, 123.[15] B. X. Fu, B. S. Hsiao, S. Pagola, P. Stephens, H. White, M.
Rafailovich, J. Sokolov, P. T. Mather, H. G. Jeon, S. Phillips,J. D. Lichtenhan, J. J. Schwab, Polymer 2001, 42, 599.
[16] B. S. Hsiao, H. White, M. Rafailovich, P. T. Mather, H. G.Jeon, S. Phillips, J. D. Lichtenhan, J. J. Schwab, Polym. Int.2000, 49, 437.
[17] E. Devaux, M. Rochery, S. Bourbigot, Fire Mater. 2002, 26,149.
[18] J. F. Brown, L. H. Vogt, P. I. Prescott, J. Am.Chem. Soc.1964,86, 1120.
[19] R. Tamaki, Y. Tanaka, M. Z. Asuncion, J. Choi, R. M. Laine,J. Am. Chem. Soc. 2001, 123, 12416.
[20] Y. Ni, S. Zheng, Chem. Mater. 2004, 16, 5141.[21] C.-M. Leu, M. Reddy, K.-H. Wei, C.-F. Shu, Chem. Mater.
2004, 15, 2261.[22] C.-M. Leu, Y.-T. Chang, K.-H. Wei, Chem. Mater. 2004, 15,
3271.[23] D. M. Crawford, J. A. Escarsega, Thermochimica Acta 2000,
357&358, 161.[24] A. Lee, J. D. Lichtenhan, Macromolecules 1998, 31, 4970.[25] A. Lee, J. D. Lichtenhan, W. A. Reinerth, Polym. Mater. Sci.
Eng. 2000, 82, 235.[26] H. Zhang, R. J. Farris, P. R. Westmoreland, Macromolecules
2003, 36, 3944.[27] C.-S. Wu, Y.-L. Liu, K.-Y. Hsu, Polymer 2003, 44, 565.[28] S.-Y. Lu, I. Hamerton, Prog. Polym. Sci. 2002, 27, 1661.[29] J. Choi, J. Harcup, A. F. Yee, J. Am. Chem. Soc. 2001, 123,
11420.[30] M. Zuo, T. T. Chi, Polymer 1999, 40, 5153.
200 H. Liu, S. Zheng
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