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Preparation and Characterization of Graphene/RTV Silicone Rubber
Composites
Jian Dong a*, Penghui Wang b, Daobao Sun c, Yuliang Xu d and Kepeng Li e
School of Chemical Engineering, Taishan Medical University, Taian, Shandong, 271016, China
Keywords: graphene; RTV silicone rubber; composites; morphology; mechanical properties
Abstract. In this article we report the preparation of a graphene/room temperature vulcanized (RTV)
silicone rubber composite. Both the morphology and the properties of the composite were
investigated in detail. SEM study shows that the composite has a microphase-separated structure.
PDMS is the continuous phase, and the randomly distributed graphene nanosheets and a few
aggregates are the dispersed phase. However, DSC curves of the composites have only one glass
transition temperature (Tg). With the increases of the graphene content, Tg increases and Tm decreases.
Mechanical properties tests show that the addition of graphene has a significant reinforcement effect
on silicone rubber. The tensile strength is 0.37MPa with graphene mass fraction at 1.0%, which
increases 76% compared with that of pure silicone rubber parallel sample.
Introduction
Graphene is an atomically thick, two-dimensional sheet composed of sp2 carbon atoms arranged in a
honeycomb structure. Since its discovery by K. S. Novoselov and A. K. Geim in 2004 [1]
, it has
attracted tremendous attention from researchers in recent years owing to its large specific surface area
and unique electrical, mechanical and thermal properties. With the development of wide-scale
applicability including facile synthesis and high yield, this exciting material is ready for its practical
application in the preparation of polymer nanocomposites [2]
. In past studies, different polymer
matrixes have been employed, such as polystyrene (PS), polyurethane (PU), poly(methyl
methacrylate) (PMMA) and poly(vinyl alcohol) (PVA), etal. Electrical and thermal conductivity and
mechanical properties have been improved significantly when a suitable amount of graphene was
dispersed into the different polymer hosts [3-5]
. Thus far, little has been done to explore the composite
based on graphene nanosheets and silicone rubber [6]
.
The present contribution reports on the preparation, morphology, and properties of the
graphene/room temperature vulcanized (RTV) silicone rubber composites. The obtained composites
exhibited a significant enhancement of mechanical property at a low loading of graphene.
Experimental
Materials. Graphite oxide (GO) was synthesized by oxidizing graphite using a modified
Hummer’s method [7]
. Hydrazine hydrate was supplied by Tianjin BASF Chemical Industry. PDMS
(weight-average molecular weight 50,000) were supplied by Jinan Guobang Chemical Company.
PDMS was kept at 80℃ under vacuum for 24h to eliminate the cyclic compounds and oligomers.
Toluene and tetraethyl orthosilicate (TEOS) were supplied by Sinopharm Chemical Reagent
Company. Dibutyl tin dilaurate was supplied by Tianjin Reagent Company.
Preparation of graphene. The GO was suspended in water and exfoliated through ultrasonication
for 1h. The exfoliated GO was reduced to graphaene nanoplatelets by refluxing the GO solution with
hydrazine hydrate at 100℃ for 24h. The final products were then centrifuged, washed, and finally
vacuum-dried.
Advanced Materials Research Vols. 652-654 (2013) pp 11-14Online available since 2013/Jan/25 at www.scientific.net© (2013) Trans Tech Publications, Switzerlanddoi:10.4028/www.scientific.net/AMR.652-654.11
All rights reserved. No part of contents of this paper may be reproduced or transmitted in any form or by any means without the written permission of TTP,www.ttp.net. (ID: 130.207.50.37, Georgia Tech Library, Atlanta, USA-13/11/14,20:39:10)
Preparation of Graphene/RTV Silicone Rubber Composite. Graphene suspension was
obtained by dispersing graphene powder in toluene with the aid of sonication at room temperature.
The suspension was then combined with a solution of PDMS in toluene. Ultrasonication was then
applied to the mixture for 1h. After removing the solvent under vacuum, 5wt%TEOS was added to the
graphene-PDMS system and the mixture was stirred vigorously for 5 min. 1.0 wt% Dibutyl tin
dilaurate was then added as catalyst. After stirring for another 2 min, the resulting mixture was
transferred into a polytetrafluoroethylene mold. The cross-linking reaction was allowed to proceed at
room temperature for 7 days. The composite was then removed and stored at room temperature under
vacuum for at least 24h prior to investigation.
Characterization. Transmission Electron Microscopy (TEM) was performed on graphene by
using a JEM-2100 transmission electron microscope (JEOL Ltd., Japan). TEM samples were
prepared by dispersing graphene in absolute ethanol with the aid of sonication to form a homogeneous
suspension. Then, the suspension was dropped on a TEM copper grid and the solvent was evaporated
overnight at room temperature. Dimensions of graphene on a freshly cleaved mica substrate were
estimated with contact-mode atomic force microscopy (Agilent 5500 model, USA). Scanning
electron microscope (SEM) images of graphene/RTV silicone rubber composites were acquired using
a S-4800 scanning electron microscope (Hitachi, Japan). The surfaces and fracture section of the
sample were coated with gold just before examination. Differential scanning calorimeter (DSC)
measurements were conducted in a Q10 DSC apparatus (TA Instruments, USA) at a heating rate of
20℃/min. The tensile strength and elongation at break of all the composites were measured using a
AGS-H tensile testing machine (Shimadzu, Japan). The experiments were carried out at room
temperature at a crosshead speed of 100mm/min.
Results and discussion
Graphene Characterization. The obtained graphene nanosheets were fully analyzed by TEM and
AFM observations. Fig.1 shows a TEM image of graphene nanosheets. Large graphene nanosheets (a
few hundred square nanometers) were observed to be situated on the top of the copper grid, where
they resemble crumpled silk veil waves. Graphene nanosheets were rippled and entangled with each
other. They are transparent and exhibit a very stable nature under the electron beam. The most
transparent and featureless regions in Fig.1 are likely to be monolayer graphene nanosheet. Fig.2
shows an AFM image of graphene nanosheets, which reveals that the typical lateral size of graphene
is on the order of micrometers. Ripples and folds of the graphene nanosheets also can be seen in the
AFM image. The measured height of the flat graphene nanosheets is between 1-3 nm. While the
pristine graphene sheet is flat with a well-known van der Waals thickness of ~0.34nm, the as-prepared
graphene sheets are expected to be 1-9 graphene layers thick. Furthermore, the vertical distance
between the crest and the trough in the wrinkled sheets may contribute to the higher apparent
thickness.
Fig.1. TEM image of graphene. Fig.2. AFM image of graphene.
Composite Morphology. Fig.3 shows the SEM images of graphene/RTV silicone rubber
composite with a loading of 1.0 wt % graphene nanosheets. Fig.3 (a, b) show its surfaces, which are in
contact with air and with the polytetrafluoroethylene mold, respectively. Both surfaces exhibit a
12 Advances in Materials and Materials Processing
corrugated morphology, which is due to (1) the material shrinkage occurring during the crosslinking
or (2) the corrugation and scrolling of graphene sheets in the PDMS matrix. Fig.3 (c) shows the
fracture section of the composite. The image demonstrates that the graphene nanosheets randomly
disperse in the PDMS matrix and some graphene nanosheets protrude from the fracture surface. It
indicates that the graphene nanosheets can achieve relatively good dispersion in RTV silicone rubber
by solution-blending method. The image also reveals that there are a few graphene aggregates in the
PDMS matrix, which due to the inherent curl, folding function of graphene sheet [8]
, and the weak
interaction between graphene and PDMS matrix.
(a) (b) (c)
Fig.3. SEM images of graphene/RTV Silicone Rubber Composite.
DSC analysis. The transition behaviors of the composites were investigated by DSC. The observed
thermograms are illustrated in Fig.4. Glass transition and melting temperatures are given in Table 1.
As can be seen from Fig.4, the two composites have a crystalline melting point (Tm) around -44.7℃
and-45.2℃, respectively. This observation shows that even the presence of rigid domains of graphene
in the RTV silicone rubber does not prevent the formation of an organized structure of PDMS chains
in the network. Apart from the melting peak, both composites exhibit one glass transition temperature
(Tg). With the increases of the content of graphene, Tg increases. The reason may be attributed to the
reducing of the molecular chain flexibility of PDMS, which due to the interactions between graphene
and PDMS.
Fig.4. DSC thermograms of the composites.
Table 1 DSC analysis of the composites with different graphene mass fractions
Graphene mass fraction
[%]
Tg
[℃]
Tm
[℃]
0.1 -126.3 -44.7
1.0 -123.4 -45.2
Advanced Materials Research Vols. 652-654 13
Mechanical properties. Table 2 shows the mechanical properties of the composites with different
graphene mass fration. It is obvious that the addition of graphene has a significant reinforcement
effect on silicone rubber. Upon the graphene nanosheets loading, the tensile strength of the
composites apparently exhibits an enhancing trend. The tensile strength of the composite containing
1.0 wt % graphene is up to 0.37 MPa, while that of the pure silicone rubber parallel sample is 0.21
MPa; i.e. the tensile strength increased by 76%. The trend of the elongation at break with the graphene
mass fraction is similar to that of the tensile strength. The elongation at break of the composite
containing 1.0 wt % graphene is 224%, which increases 62% compared with that of pristine silicone
rubber.
Table 2 Mechanical properties of the composites with different graphene mass fractions
Sample
code
Graphene mass fraction
[%]
Tensile strength
[MPa]
Elongation at break
[%]
1 0 0.21 138
2 0.1 0.25 165
3 0.5 0.34 201
4 1.0 0.37 224
Conclusion
In this paper, the graphene/RTV silicone rubber composites were prepared by incorporating
graphene nanosheets into PDMS matrix by solution blending and ultrasonic dispersion method. The
composites thus formed exhibit superior mechanical properties with respect to the pristine RTV
silicone rubber parallel sample. However, more work should be continued. Further improvement of
mechanical properties via enhancing the interfacial interaction between the graphene nanosheets and
the PDMS matrix is the key challenge.
Acknowledgements
This work was supported by the Research Award Fund for Outstanding middle-aged and young
scientists of Shandong Province, China (Grant No. BS2010CL045) and the Science and Technology
Innovation Action Plan for College Students of Taian City (Grant No. 2011D1029).
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14 Advances in Materials and Materials Processing
Advances in Materials and Materials Processing 10.4028/www.scientific.net/AMR.652-654 Preparation and Characterization of Graphene/RTV Silicone Rubber Composites 10.4028/www.scientific.net/AMR.652-654.11