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Journal of Nanomaterials
Volume 2011 (2011), Article ID 928659, 9 pages
Influence of Silanization Treatment on Thermomechanical Properties of Multiwalled Carbon Nanotubes: Poly(methylmethacrylate) Nanocomposites
1División de Posgrado e Investigación, Instituto Tecnológico de Querétaro, Avenue Tecnológico s/n esquina gral. Mariano Escobedo, Colonia Centro Histórico, 76000 Querétaro, QRO, Mexico
2Centro de Física Aplicada y Tecnología Avanzada, Universidad Nacional Autónoma de México, A.P. 1-1010, Santiago de Querétaro, 76000 Querétaro, QRO, Mexico
3Laboratory of Advanced Polymers & Optimized Materials (LAPOM), Department of Materials Science and Engineering, University of North Texas, Denton, TX 76203-5310, USA
Received 3 May 2011; Revised 26 July 2011; Accepted 30 July 2011
Academic Editor: Gaurav Mago
Copyright © 2011 Carlos Velasco-Santos et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.
Unfunctionalized and silanized multiwalled carbon nanotubes (MWNTs) were incorporated in poly(methylmethacrylate) matrices using in situ polymerization. Polymer-compatible functional groups on carbon nanotube (CNT) surfaces were characterized by infrared spectroscopy. These chemical moieties improve interaction at interfaces, allowing transfer of mechanical load between the matrix and the dispersed phase as reflected in the resulting improved mechanical and thermophysical properties. The composites were characterized by Raman spectroscopy to evaluate molecular level interactions and dynamical mechanical analysis. Composites with silanized CNTs have higher storage modulus (E′) than polymer reinforced with unfunctionalized nanotubes. Considering the average of the samples, only 1 wt.% of silanized nanotubes provides an increase in E′ of 165% at room temperature with respect to polymer matrix, and the increments reached are by a factor of 6.8 and 13.6 over the polymer matrix at 80∘C and 90∘C, respectively. 1 wt% of silanized CNTs increases the glass transition temperature of polymer matrix around 30∘C. Microscratch testing results of composites show that unfunctionalized CNTs cause deeper penetration of the indenter than polymer matrix at the same force; however, the composites developed with silanized CNTs present more regular behavior than polymer reinforced with unfunctionalized CNTs.
The outstanding properties of carbon nanotubes offer possibilities for developing new strong multifunctional composite materials [1–4]. Several studies have demonstrated the relevant high Young’s modulus, stiffness, flexibility, high electrical conductivity, and thermal stability that CNTs posses [5–8]. Research focus to produce polymer composites is directed to taking advantage of these features in maximum level [9–13].
Different reports provide evidence of progress in this area. Depending on the polymer and the processing method used, there are positive effects in the creation of polymeric nanocomposites based on CNTs for mechanical [11–16], electrical [13, 17–20], damping , and electroactive properties and artificial muscles [22, 23]. However, to reach the combination of different properties in one material involves diverse challenges. As discussed by Dzenis , uniform distribution of CNTs in the matrix is needed. Moreover, the attention has been paid to mechanical properties than to tribological ones. However, the analysis of tribological properties is needed because the ongoing process in several industries of replacement of metal components by polymeric ones requires polymer-based materials (PBMs) with better tribological properties . Recently studies show that the use of CNTs to improve tribology of PBMs turned out to be a two-edged sword; because, while the penetration depths decrease with increasing concentration of CNTs, the residual depths increase at the same time . Thus, clearly more work also along these lines is needed.
A way to provide uniformity on the distribution of CNTs in a polymeric matrix is functionalization [25–27]. In this paper is presented new evidence related with the efficiency of functionalization to improve compatibility and enhance dispersion and the load transfer of CNTs in polymer nanocomposites. Chemical modification applied to nanotubes is supported in the silanization process, which has been proved as successful method to produce different surface behavior in CNTs. Here we report results for functionalized as well as unfunctionalized carbon nanotube polymer composites. Poly(methyl methacrylate) (PMMA) has been chosen as the matrix because of its wide use.
Methyl methacrylate monomer (MMA) and 3-(trimethoxysilyl)-propyl methacrylate 98% (3-MAT) were supplied by Aldrich. 2,2′-azoisobutironitrile (AIBN) was donated by GIRSA Company, and arc-discharge MWNTs (ground core materials) were provided by MER Corporation. The core material has around 40 wt% MWNTs. The product is over 99% carbon and is produced without catalysts. MWNTs have 8–30 graphene layers and are 6–20 nm in diameter and 1–5 microns in length.
MWNTs previously purified and oxidized were silanized. Oxidation was achieved with KMnO4 in H2SO4 medium; this kind of purification is much recognized and produces a high yield and high purity CNTs. Nanotubes obtained by this process have been analyzed by transmission electron microscopy (TEM) and Raman spectroscopy in an earlier paper . Silanization was realized in alcoholic solution; silane was added 1 : 1 in weight with respect to the oxidized CNTs. The mix was refluxed for 3 h, maintaining the temperature around 65–70°C and under constant stirring. More details of the reactive concentrations and the procedure to oxidize and silanize CNTs were described in previous publication . Polymer samples and carbon nanotube composites were produced by in situ polymerization using AIBN as the initiator. The AIBN quantity, reaction time, and temperature were controlled in order to achieve narrow molecular weight distributions. The reaction to produce each composite was carried out in a flask using MMA and AIBN in a reflux system. In each type of the samples, unmodified CNTs (uCNTs) and previously silanized CNTs (sCNTs) were added after 30 minutes since the reaction beginning; then sample was maintained at 70°C for 2 hours under stirring. The resulting mixture was placed in a glass mold with a latex frame in order to control shrinkage. Finally, the system was controlled at 70°C in an oven for 24 hours to achieve complete polymerization. The materials obtained have the thickness of ≈1.8 mm. The samples are identified as follows: neat PMMA (PMMA), a composite with 1 wt.% of uCNTs, and a composite with 1 wt.% of sCNTs.
Two extra samples for each material (PMMA, uCNT composite, and sCNT composite) were prepared to corroborate the nanocomposites and the PMMA behaviour in dynamical mechanical analysis (DMA). The procedure to synthesize the materials was the same described previously.
Infrared analysis was performed using a Vector 33 Bruker spectrophotometer, at 100 scans, with resolution of 1 cm−1. Samples were prepared using KBr tablets.
For dynamical mechanical analysis, the samples were cut to 6 mm width and 25 mm length and tested in a Perkin-Elmer DMA-7 apparatus, using 3-point bending module at the 1.0 Hz frequency. Samples were running three times for each material developed.
Raman’s spectra of PMMA and composites were obtained in a Micro-Raman Dilor; a 632 nm laser was used, providing a spectral resolution of 3 cm−1.
Microscratch testing was performed in a machine from CSM, Neuchatel, Switzerland, with their Version 2.3 software. Scratches of 5.00 mm length were performed using a diamond tip with a 200 μm diameter. Samples were tested seven times in different parts of the composite at variable loads from 3.0 N up to 20.0 N.
3. Results and Discussion
3.1. Dispersion in Solvent
Silanization was performed using 3-mercaptopropyl-trimethoxysilane (3-MPT) and 3-(trimethoxysilyl)-propyl methacrylate (3-MAT). CNTs were then dissolved in acetone for 5 minutes using an ultrasonic bath for dispersion and left for further 1 hour without ultrasound. As expected, the dispersion is different, higher for 3-MAT than for 3-MTP. Photographs of suspensions obtained using 3-MAT are displayed in Figure 1.
In this figure, it is possible to observe that the darkest suspension corresponds to the system containing sCNTs. These CNTs stay a longer time (several hours) in suspension, while, in the other two systems, precipitation occurs sooner. Even when the acetone is evaporated and sCNTs are washed once more with hot water and acetone in order to eliminate possible remainders of unattached organosilanes, the nanotubes do not lose their dispersion in the solvent. This effect is produced due to the organosilane’s R group attached to carbon nanotube surfaces. Organosilanes can be represented as R-Si-R′3, where R is an organofunctional group. The R group can be selected to be reactive or compatible depending on the organic matrix being used. The R′ group is typically trimethoxy 3(OCH3); silicon-oxygen bonds are formed followed by an easy hydrolysis to trisilanol.
Figure 2 shows a schematic representation of silanization with 3-MAT on carbon nanotube surfaces. The dispersion of sCNTs in the suspension depends on the R group. Our 3-MAT silanization produces good dispersion of CNTs in organic solvents such as acetone or ethanol. The R moiety, in this case the methacrylate chain, changes the behavior of MWNTs when attached to the carbon nanotube surface. When 3-MPT is attached to sCNTs, the thiol group produces lower dispersion in acetone.
3.2. Infrared Spectroscopy
Figure 3 shows the infrared spectra for CNTs, oxidized carbon nanotubes (oCNTs), and sCNTs modified with 3-MAT. Spectrum 3(a) shows two bands in the zone of A2u and E1u IR phonon modes at 850 cm−1 and 1576 cm−1, which are typical signals of CNTs . In the oCNTs spectrum 3(b) new peaks are seen. Characteristic bands due to oxidation appear; the signals at 1200 cm−1 and 1346 cm−1 are due to v(C-O) and δ(O-H) in plane, respectively; small bands between 1680 cm−1 and 1740 cm−1 correspond to v(C=O) .
In the spectrum of oCNT, carboxylate groups prevail, and only few carboxyl groups are produced. This is seen in low intensities of the bands around 1740 cm−1 and 3320 cm−1 which correspond to v(C=O) and v(O-H), typical signals of carboxyl moieties. Other evidence of carboxyl group is a slight increase in 1346 cm−1 δ(O-H) and 960 cm−1 δ(O-H) related with in-plane and out-of-plane vibrations, respectively . By contrast, a higher intensity is seen in the band around 1495 cm−1, and in the peaks between 1600 cm−1 and 1680 cm−1 in comparison with the zone above 1700 cm−1, these corroborate that quinone and carboxylate groups exist in these oxidized nanotubes [30–33]. The peak at 1576 cm−1, assigned to –C=C in spectrum (a), is notably weaker than that in spectrum (b); this indicates changes in CNT surface due to oxidation ; it is known that some damage is produced in CNT walls. In Figure 3(c) we find results of successful silanization process; the bands at 794 cm−1 and 919 cm−1 are typical for v(Si-OH) and δ(OH) out of plane. These bands appear when trimethoxy groups are broken in order to form silanol groups. The silanol groups provide interactions between oxygen of carboxylates and hydroxyl moieties of the oxidized nanotubes and the organosilane. In addition spectrum 3(c) does not show bands between 815 cm−1 and 845 cm−1, characteristic signals of nonreacted SiOR groups in organosilane compound [28, 34]. Also the typical band of methoxy group, around 2850 cm−1, does not appear in this spectrum. The peaks at 1045 cm−1 and 1111 cm−1 are due to Si-O-Si and Si-O-C vibrations [30, 34] and correspond to siloxane units formed during silanization process. The high intensity band at 1740 cm−1 becomes stronger due to the ester group v(C=O) vibration which corresponds to methacrylate moiety. Additionally, in the spectrum appear the peaks at 2880 cm−1 and 2947 cm−1, v(C-H) and va(C-H), respectively , these bands are typical for aliphatic groups and correspond to the propyl chain in this case. Both methacrylate and propyl groups belong to the organosilane compound. The band at 3300 cm−1 typical of v(O-H) is strong in spectrum 3(c) and corresponds to OH vibration of silanol group. This band is often above 3700 cm−1 [28, 34]; however, the peak has been located at lower wavenumbers when silanization was performed [33, 34]. It has been suggested that this effect is due to either strong interactions between neighboring silanol groups or between silanol groups and the methacrylate ester moiety of the coupling agent via inter- or intrahydrogen bonding . In our case, the first explanation seems to apply; the strong bands at 1045 cm−1 and 1111 cm−1 shown in Figure 2 corroborate the Si-O-Si interactions. Moreover, no shifts of ester peak typical position (C=O) are observed in spectrum 3(c). Thus, we infer that Si-O-Si interactions occur during silanization.
3.3. Dynamical Mechanical Analysis Results
Figure 4 shows the close average behavior of the storage modulus () as a function of temperature. It is possible to observe in this figure the different behavior of the materials. At 30°C neat PMMA shows a value of = 1.62 GPa; PMMA with 1.0 wt.% of uCNTs shows = 2.95 GPa, while in the composite with sCNT is presented at 4.06 GPa. However, at 90°C the respective values are 3.90 MPa, 0.92 GPa, and 2.55 GPa. These results show a relevant rise in the composites with sCNTs and represent an increment in elastic modulus of 82% for the composite with untreated CNTs and 150% for the composite with sCNTs at 30°C, with respect to polymer matrix (PMMA). At 90°C, the average behavior in the composites with uCNTs and sCNTs, is higher more than 7.4- and 13.6-fold, respectively, with respect to PMMA. In addition in the sample with sCNTs, (30°C) is higher in 34% and (90°C) in 1.8-fold with respect to composite which contains unfunctionalized nanotubes.
Three different samples of PMMA and composites reinforced with functionalized and unfunctionalized nanotubes were probed. The materials were synthesized in order to corroborate the behavior of the composites. Polymers reinforced with sCNTs present the same tendency, in as much as (30°C) is superior in all composites which contain functionalized nanotubes. Also, uCNTs composites present a storage modulus (30°C) higher than PMMA. Thus, even though the storage modulus curves are not uniform in all materials, the tendency is the same and corroborates the efficiency of the functionalization in composite properties. Thus, it is verified that few loads of carbon nanotubes, and even more sCNTs, have important effect in the elastic behavior of these polymer nanocomposites. Table 1 shows storage modulus of the three materials at different temperatures. It is evident that the interaction (analyzed previously by spectroscopy) produced at the interface level by functionalization plays an important role in mechanical properties of these materials.
DMA also provide information about determination of glass transition temperatures . Figure 5 shows tan δ = as a function of temperature, where is the loss modulus. Taking the at the maximum of tan ∂ peak and PMMA as the reference, addition of untreated CNTs increases the by 10°C, while addition of sCNTs results in a 31°C increment. Since only 1 wt.% of CNTs was added, there are clear evidence of strong interactions between PMMA and sCNTs. Figure shows the tangent delta curves closer to the average behavior in all samples; further results pertaining to the thermal behavior of PMMA and composites are shown in the Table 1.
3.4. Raman Spectroscopy
Figures 6(a), 6(b) and 6(c) show Raman spectra in the region from 600 cm−1 to 1500 cm−1, 1650 cm−1 to 1800 cm−1, and from 2500 cm−1 to 3500 cm−1, for neat PMMA, and the composites which contain uCNTs and sCNTs modified with 3-MAT.
The bands situated at 2953 cm−1 va(C-H) in Figure 6(c), 1462 cm−1 δ(C-H), 1330 cm−1 δ(C-H) and 982 cm−1 v(C-C) in Figure 6(a), and the little shoulders located near of these bands [30, 36, 37] correspond to vibrations of C-C and C-H bonds in PMMA. The spectrum for the composite with sCNTs shows larger peaks, apparently due to interactions between end moieties in organosilane and the PMMA matrix. The links achieved after polymerization could be C-C and C-H interactions. It is important to indicate that the mentioned bands increase also in the composite with unfunctionalized CNTs with respect to PMMA. Thus, It is corroborated the interactions between open π bonds broken in the polymerization and C-H—π interactions. Both phenomena have been found in PMMA with unfunctionalized carbon nanotubes in a previous study by our group  and other research realized by Baskaran et al. . However, the bands are stronger when CNTs are functionalized. This shows that more interactions are achieved between carbon polymer chains with carbon nanotubes when these are functionalized.
Two bands related with C-O vibrations also are found in the IR spectra: in Figure 6(b), the peak at 1737 cm−1 v(C=O) and in the Figure 6(a) the band localized at 820 cm−1 (combination of C-H and C-O-C deformation [26, 36]). Both peaks correspond to C-O vibrations in PMMA; these signals also are stronger for sCTNs system. Thus, moieties in PMMA which contain carbon and oxygen participate in polymer-nanotube interactions, more so after functionalization.
The last suggestion is corroborated in the Figure 7; the image show a zoomed view of the Figure 6(a). Here the Raman spectra show the region between 1080 cm−1 and 1500 cm−1. Peaks at 1139 cm−1 and 1200 cm−1 which correspond to C-O-C vibrations [26, 38] are seen in PMMA and in the composite with unfunctionalized CNTs. These bands are shifted to 1128 cm−1 and 1183 cm−1, respectively in the spectrum of composite with sCNTs; this shift is not seen in the band at 1462 cm−1 used as reference in the spectra. Thus, it is inferred that PMMA’s ester groups interact with organosilane’s ester groups on the CNT surface, producing C=OOCH3 and C=OH interactions that shift the peaks position. Changes in the bands at 1330 cm−1 and 1390 cm−1 are also evident. The former appears only in the composite spectra and is stronger in the sCNT system. A small shoulder at 1390 cm−1 appears only in the PMMA spectrum. Both bands in the overlap region are attributed to C-H deformation; the first peak corresponds to δ(C-H methyne), and the second is attributed to deformation of C-H (CH3 or CH2) in the polymer. In addition, the signal at 1330 cm−1 is found in the neighborhood of the D band region which corresponds to CNTs and is related to sp3 hybridization. This suggests that C-C and C-H moieties are produced between C=C methacrylate organosilane groups and the C=C of the monomer in the polymerization. The results are changes in polymer group vibrations due to the formed links when CNTs, particularly functionalized ones, are incorporated. Also some contribution of D band could have some effect in the peak at 1330 cm−1 in the nanocomposites.
Returning to Figure 6(c), a peak appears from 2600 cm−1 to 2700 cm−1 in the sCNT system spectrum and is associated with Si-H bonds found in silanes [34, 39]. It is possible that some SiH links are created between the organosilane and aliphatic polymer groups. We recall here similarity between C and Si.
3.5. Scratching Behavior
Figure 8 shows penetration depths as a function applied force achieved in PMMA and nanocomposites. Several tests for each kind of material are shown. PMMA samples show regular behavior which is independent of the material section; inasmuch as, the seven analyses present similar penetration depth at the same loads. Thus, PMMA presents homogenous behavior that indicates similar features in any point of its surface. sCNT composite present two zones; in the region from 7.5 N to 9 N, the majority of the determinations in sCNT composite present better resistance to be penetrated with respect to PMMA; however, in the zone above 9 N, the majority of these samples show lower resistance to the penetration than PMMA. Nevertheless, the largest part of the analysis realized in sCNT composite presents better tribological properties than uCNT composite. Therefore, although a small quantity of sCNTs is incorporated in polymer; better wear resistance is presented at low load with respect to polymer matrix. Thus, neat PMMA has better scratch resistance than CNT’s reinforced materials except for the composite with sCNTs at low forces. In addition, curves show that the behavior of the composite with sCNTs is more uniform than the composite with uCNTs. The fact related with the variety of curves, relatively far apart from each other, can be explained by formation of CNT bundles for uCNT composite. Thus, also in our systems, uniform distribution of CNTs in the matrix apparently achieved for sCNTs is important. It is supposed that good distribution of silanized carbon nanotubes (sCNTs) results in efficient tribological properties only at low loads as sCNTs could support the mechanical behavior. However, it is possible that the interaction produced between sCNTs and polymer chains could produce shorter chains than those produced in uCNT composites or PMMA. Thus, shorter chains at high loads could produce easy penetration in the material. As discussed by Dzenis , CNTs can produce improvement as well as worsening of the properties of matrices. This depends on diverse factors involved in the modification and synthesis of the nanocomposites.
3.6. General Discussion
Successful silanization of carbon nanotubes is useful for changing their surface behavior and, therefore, their dispersion in organic solvents. Substituents in the organosilane, here, play an important role.
When using 3-MAT, sCNT surfaces seem to have a variety of interactions with the PMMA matrix: C-C, C=Cπ, C=OO, C=OH and SiH. The majority of these interactions begin in the polymerization.
The links produced in nanocomposites play an important role to improve thermomechanical properties in these materials, in as much as, storage modulus () at different temperatures increase notably in the composites with sCNTs with respect to the composite with uCNTs and PMMA. In addition, the glass transition temperature is increased around 31°C in the composite with sCNTs with respect to polymer matrix, in comparison with uCNT system where only increase by 10°C.
In other works moderate increments in mechanical properties have been achieved in PMMA matrix or copolymers using MMA when uCNTs have been incorporated, for instance with very low loads (0.01 wt%) of SWMTs, and MWNTs have improved tensile modulus of polymer matrix , and storage modulus has been enhanced with 1 wt% of MWNTs using dissolving processing . In addition other processing methods which involve uCNTs with other polymer matrices have reached good increments in storage modulus when uCNTs are aligned . Nevertheless when CNTs are modified by oxidation , cover by polymers , or functionalized using other molecules [25, 27], better results have been reached in mechanical and thermal properties.
Recently, silanization have been an important route to modify CNTs, and the results agree with the thermomechanical properties reported here. Important increments in tensile strength in Poly(propylene) (PP) and polyimide (PI) matrices [40, 41] and and thermal stability in epoxy matrix  have been gotten at 1 wt% of sCNTs (PP and PI) and 0.5 wt% (in the case of epoxy matrix). The silanes used in these researches were 3-methacryloxypropyltrimethoxysilane, vinyltriethoxysilane, and 3-Glycidoxypropyltrimethoxysilane, respectively. Also in recent times interesting dielectric properties have been reported in polyethylene reinforced with carbon nanofibers modified with silanes . Thus, it is corroborated that silane functionalization in CNTs is useful to improve interface and thermomechanical properties in different polymer matrices including PMMA studied in this paper.
Also, functionalization effect is reflected in tribological properties; however, other factors such as the polymer chain sizes and the low concentration of sCNTs could influence the different behavior in tribological properties at low and high force. Nevertheless, the clear differences in the tribological behavior between sCNT and uCNT composites give evidence that silanization takes part in this property; the evidence of that influence is the low quantity used as reinforcement of sCNTs and the notable effect. The curves of penetration depth and progressive force are more consistent in the composite which contains more sCNTs than that in the composite with uCNTs. This allows concluding that functionalization, furthermore, assists the dispersion of carbon nanotubes in polymer composite.
Thus, this research gives evidence that the synergic effects produced in polymer composites are reached by interactions between organosilane chemical groups of modified nanotubes and polymer matrix. The incorporation of a small quantity of sCNTs is enough to produce significant changes at polymer matrix; even uCNTs provide considerable changes in polymer, taking into account the CNT quantity that is added; as well functionalization provides to the composites extra qualities, because of not only improving storage modulus and , also uniform behavior is observed in any point of the sample when tribological properties are analyzed. These characteristics confer to this kind of nanocomposites’ additional functional properties and the possibility to be incorporated in promising uses such as transportation industry, commercial aircraft, sports industry, and textile smart polymer fibers among others possible applications. Research using different concentrations of CNTs and other organosilanes with other R group related to the features of the polymer matrices is in current study.
The authors are grateful to Dr. G. Hernández-Padron for her assistance in the IR analysis and to CINVESTAV Querétaro, particularly Dr. S. Jimenez and Mr. F. Rodríguez for their assistance in Raman measurements. Financial support has been provided by the American Chemical Society, Washington, DC, the Mexican National Academy of Sciences (AMC), Mexico City, the DGEST under project DGEST 2006 333.06, and the Consejo Nacional de Ciencia y Tecnologia (CONACyT), Mexico City under project JI-58232.
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