Advances in Materials Science and Engineering

Volume 2012 (2012), Article ID 518392, 5 pages

doi:10.1155/2012/518392

Research Article

The Influence of Hydroxylated Carbon Nanotubes on Epoxy Resin Composites

Jiaoxia Zhang,¹ Yaping Zheng,² Haijun Zhou,¹ Jing Zhang,¹ and Jun Zou¹

¹School of Materials Science and Engineering, Jiangsu University of Science and Technology, Zhenjiang 212003, China

²Department of Applied Chemstry, School of Natural and Applied Science, Northwestern Polytechnical University, Xi’an 710129, China

Received 23 July 2012; Accepted 7 November 2012

Academic Editor: Manish U. Chhowalla

Copyright © 2012 Jiaoxia Zhang 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.

Abstract.

Hydroxylated multiwall carbon nanotubes (MWNTs)/epoxy resin nanocomposites were prepared with ultrasonic dispersion and casting molding. The effect of hydroxylated MWNTs content on reactive activity of composites is discussed. Then the flexural and electrical properties were studied. Transmission electron microscope was employed to characterize the microstructure of nanocomposites. As a result, the reactive activity of nanocomposites obtained increases with the increasing content of MWNTs. When MWNTs content of the composites is 1 wt%, as compared to neat resin, the flexural strength increases from 143 Mpa to 156 MPa, the modulus increases from 3563 Mpa to 3691 MPa, and the volume and surface resistance of nanocomposites decrease by two orders of magnitude, respectively.

1. Introduction

Carbon nanotubes (CNTs), since their discovery in 1991 [1], have generated huge activity in many areas of science and engineering due to their unprecedented physical and chemical properties [2–4]. The theoretical analysis and experimental investigation indicate that their extraordinary mechanical properties, the high chemistry stability, thermal stability, the good electric conductivity, unique nanometer effect, and so on make CNTs ideal for a wide range of applications such as nanoelectronics, nanomechanical system, electronic field launch, and sensor [5, 6]. Especially CNTs are used to improve the mechanical and electrical properties of polymer because of the similar segmer structure between C–C covalent bond of CNTs and polymer matrix. Due to the nonreactive surface of MWNTs, it is difficult to achieve efficient dispersion in a polymeric matrix. The realization of MWNTs reinforced polymer requires a homogeneous dispersion and strong interfacial interaction between MWNTs and the polymer. To address this problem, current work is in progress on noncovalent surfactant or polymer-wrapping modifications of MWNTs and on covalent functionalized utilizing open-end and sidewall chemistry. In the recent years, researchers have made efforts on the surface modification to increase the properties of the polymer matrix composites [7–10].

Epoxy resin is a thermosetting epoxy polymer, which is used in a variety of applications because of its properties, such as thermal stability, mechanical response, and electrical resistance. In general, epoxy resins are known for their excellent adhesion, chemical and heat resistance, excellent mechanical properties, and electrical insulating properties [11, 12], but the curried epoxy resin by mixing with a catalyzing agent is brittle and the impact strength is lower. So it is necessary to toughen epoxy resin in order to extend its application [13].

In the present work, the hydroxylated MWNTs (MWNTSOH) were added to the epoxy resin and sonicated to prepare MWNTSOH/epoxy resin nanocomposites. The gel time and curing dynamics of nanocomposites were studied, and their mechanical and electrical properties were also tested.

2. Experimental Method

2.1. Material

The hydroxylated MWNTs (MWNTSOH) used in this study were synthesized by chemical vapor deposition (CVD) and were provided by Chengdu organic chemicals CO., LTD. The average diameter of MWNTSOH (hydroxylated content: 3.06 wt%) was about 20–30 nm, the length was several micrometers, and the purity was >95 wt%. The MWNTSOH was used in our experiment without further purification. Epoxy resin 830 (epoxy number of 0.56–0.61 eq/100 g) was produced by Wuxi Di’aisheng epoxy resin CO., LTD. Aromatic hardener (JHB-590) with an acid value of 660–685 mgKOH/g was produced by Dalian-Jinshi Chemical Industry. The formula is 75 parts of hardener by 100 parts of epoxy resin.

2.2. Fabrication of MWNTSOH/Epoxy Nanocomposites

The MWNTSOH was added to the epoxy resin at 80°C in order to lower the viscosity of the epoxy resin. Filler weight fractions ranging from 0 wt% to 5 wt% were dispersed in the epoxy resin and were sonicated (1200 W ultrasonic cell disruptor) for 1 hour. After cooling to room temperature, the hardener was added to the homogenous mixture and was compounded for another 30 min. The resulting mixture was then taken into a preheated steel mold coated with the mold release agent. The mold enclosed resulting mixture was degassed at 80°C under vacuum for 30 min to remove bubbles. The mixture was cured at 80°C for 1 hour, followed by 3 h at 120°C and another 3 hours at 140°C to complete the crosslink reaction.

2.3. Measurements

MWNTSOH dispersion in the epoxy matrix was observed through transmission electron microscope (TEM Hitachi (Tokyo, Japan) H-800). The film samples with a thickness of 1 μm of the MWNTSOH/epoxy nanocompsites were prepared by ultramicrotome cutting.

Differential scanning calorimetry (DSC) traces were collected using Q1000 TA instruments at a heating rate of 10°C/min.

The gel time was carried out by plate-spinning method. The mixtures were put into the plate at specified temperature to obtain the interval of time required for a colloidal solution to become a semisolid jelly or gel.

The flexural properties were measured using a universal testing machine under the three-point loading scheme (GB/T2571-1995) and the sample size is 80 mm × 15 mm × 4 mm. Ten specimens of each nanocomposite were tested and the mean values and standard deviations were computed.

The volume and surface resistance were measured by Ultrahigh resistance (10¹⁷) and microcurrent () testing instrument (ZC36), and sample size was 100 mm × 100 mm × 4 mm.

3. Results and Discussion

3.1. The Influence of MWNTSOH on the Gel Time of Nanocomposites

The gel time reflects effect of temperature-dependent activity of system. In this process, the influence of MWNTSOH contents on the gel time of the epoxy resin according to different temperatures was tested (shown in Figure 1). It showed that the gel time of MWNTSOH/epoxy resin nanocomposites decreased with the increase of the MWNTSOH content. In addition, the gel time tends to be consistent at higher temperature and is the shortest when the MWNTS content being 5%. It indicated that MWNTSOH accelerated the curing reaction and enhanced the reactivity of epoxy resin at low temperature. That may relate to the hydroxylated group on the surface of MWNTSOH which participates in the curing reaction of epoxy resin system.

Figure 1: Gel time of MWNTSOH/epoxy resin nanocomposites versus temperature.

3.2. The Influence of MWNTSOH on the Thermal Behavior of Nanocomposites

DSC was used to characterize the thermal properties of MWNTSOH/epoxy resin nanocomposites. The reaction enthalpy () was obtained by the area integration between DSC curve and baseline with as unit. Figure 2 and Table 1 show the process of curing reaction of MWNTSOH/epoxy resin nanocomposites with different contents of MWNTSOH. It was shown that the peak temperature () decreased, but the increased. It further explained that the reactive activity increased, so the curing reaction is easy to occur at lower temperature. It was clear that the self-catalyzed reaction of epoxy resin is evoked by hydroxy. The hydroxylated groups on the surface of MWNTSOH participate in the reaction of epoxy resin to decrease the temperature of reaction and increase the cross linking reaction leading to an increase in the .

Table 1: The influence of MWNTSOH on the thermal properties of nanocomposites.

MWNTSOH content/(%)
/(°C)
/(°C)
/(°C)
H/(J/g)

0
118.70
190.63
151.78
268.6

0.5
117.37
188.94
150.68
297.1

1
116.46
187.07
149.98
301.0

2
114.01
186.13
149.55
311.0

5
110.52
183.13
148.09
331.2

Figure 2: The influence of MWNTSOH on the thermal properties of nanocomposites.

3.3. The Influence of MWNTSOH on the Flexural Properties of Nanocomposites

The flexural strength and flexural modulus of epoxy nanocomposites with various addition ratios of MWNTSOH were described in Figure 3. It showed that when the content of MWNTSOH is 1%, its flexural strength increased from 143 MPa to 156 MPa and their flexural modulus can be improved from 3563 MPa to the maximal value of 3691 MPa, as compared to neat resin. The group of –OH on the surface of MWNTSOH participates in the curing reaction and forms fine interfacial bonding between matrix and MWNTSOH. In addition, a microforce of mutual locking is produced, the unsaturated dangling bonds on the outer wall leading to the formation of chemical bonds, and Van der Waals force between the MWNTs and substrate can play an important role to evenly disperse MWNTs and enhance the bending property [14].

(a)

(b)

Figure 3: The influence of MWNTSOH on flexural properties of nanocomposites ((a) bending strength, (b) bending modulus).

When the content of MWNTSOH increased further, flexural properties of nanocomposites decreased. The less efficient improvement at higher contents is attributed to an increasing amount of observed agglomerates that cannot effectively transfer outside force. The locale agglomerate formed stress point leads to the generation of fracture source, which decrease the mechanical properties [15]. Furthermore, the MWNTSOH is cut and the length of MWNTSOH becomes short due to the strong ultrasonic power that damages the properties of MWNTs, so the effect of improvement of mechanical properties is reduced (see Figure 5).

3.4. The Influence of MWNTSOH on the Electrical Properties of Nanocomposites

The application of conductive nanoparticles in the polymer matrix is supposed to decrease the electrical resistance. The experimental results of the nanocomposites are shown in Figure 4. The volume and surface resistivity decrease with the increase of MWNTSOH contents. When the content is 2%, the value of volume and surface resistivity drop by two orders of magnitude. The formation of good conductive circuit of MWNTSOH in polymer matrix improves the electrical properties of composites. The charge carrier MWNT moving in the material leads to conduct in the nanocomposites. However, because the length of MWNT became shorter in the ultrasonic process, the volume and surface resistivity decrease lower than the previous reports [16]. That is consistent with the result of Feng et al. [17] that the aspect ratio has influence on the electric conductivity.

Figure 4: The influence of MWNTSOH on the electrical properties of nanocomposites.

(a)

(b)

Figure 5: The TEM images of MWNTSOH/epoxy resin nanocomposites.

3.5. The Microstructure of MWNTSOH in Epoxy Matrix

Figure 5 is the TEM image of MWNTSOH (1%) in epoxy matrix, and the black line is the dispersed MWNTSOH. There is not agglomeration phenomenon in the polymer matrix because the hydroxyl groups on the surface MWNTSOH have good compatibility with epoxy resin. The shorter high aspect ratio shown in Figure 5 with about 30 nm diameter and 100 nm length also improves the dispersion but damages the mechanical and electrical properties that further lead to the improvement of properties of nanocomposites being decreased.

4. Conclusion

The MWNTSOH/epoxy resin nanocomposites were prepared by melt mixing. There is a homogeneous dispersion in polymer matrix of MWNTSOH through ultrasonic treatment. So MWNTSOH improves the reactive activity and increases the flexural and electrical properties of composites, whereas the shorter high aspect ratio damages the flexural and electrical properties of MWNTSOH which make the improved affectivity of composite’s properties reduced to a certain extent.

Acknowledgments

The authors greatly acknowledge a project funded by the Priority Academic Program Development of Jiangsu Higher Education Institution, the Key Laboratory Funded by Jiangsu advanced welding technology, the Starting Research Fund (635061201) from the Jiangsu University of Science and Technology, and Jiangsu Provincial Natural Science Foundation of China (Grant no. BK2012279).

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