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International Journal of Polymer Science
Volume 2012 (2012), Article ID 381342, 6 pages
http://dx.doi.org/10.1155/2012/381342
Research Article

Preparation and Characterization of Cellulose Nanofibril Films from Wood Fibre and Their Thermoplastic Polycarbonate Composites

Centre for Biocomposites and Biomaterials Processing, Faculty of Forestry, University of Toronto, Toronto, ON, Canada M5S 3B3

Received 4 August 2011; Accepted 29 September 2011

Academic Editor: Peng He

Copyright © 2012 S. Panthapulakkal and M. Sain. 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

The aim of this study was to develop cellulose-nanofibril-film-reinforced polycarbonate composites by compression molding. Nano fibres were prepared from wood pulp fibres by mechanical defibrillation, and diameter distribution of the fibres produced was in the range of 1–100 nm. Nanofibre films were prepared from the nanofibre suspensions and were characterized in terms of strength properties, crystallinity, and thermal properties. Strength and modulus of the nano fibre films prepared were 240 MPa and 11 GPa, respectively. Thermal properties of the sheets demonstrated the suitability of processing fibre sheets at high temperature. Tensile properties of the films subjected to composite-processing conditions demonstrated the thermal stability of the fibre films during the compression molding process. Nanocomposites of different fibre loads were prepared by press-molding nano fibre sheets with different thickness in between polycarbonate sheet at 205°C under pressure. The tensile modulus and strength of the polycarbonate increased with the incorporation of the fibres. The strength of the thermoplastic increased 24% with 10% of the fibres and is increased up to 30% with 18% of the fibres. Tensile modulus of the polycarbonate demonstrated significant enhancement (about 100%).

1. Introduction

Cellulose is the most abundant polymer in nature and is composed of linear polymer chains of β-1,4-linked glucose residues, and plant biomass is the richest resource for cellulose [13]. Utilization of the cellulose in composites is mainly to exploit its high strength and Young’s modulus originated from the crystalline nature of the cellulose molecules, which in turn results from the hydrogen bonds extended along the molecular chains [2]. Many researchers reported the generation of nanocellulose or cellulose microfibrils from various resources and their application in the composite science and engineering [327]. The exploitation of cellulosic fibres as reinforcements in the composites has started more than a decade ago [4]. The principal reasons for the utilization of cellulosic fibrils are (i) its high specific strength and modulus compared to other engineering materials [2, 4] and (ii) its reinforcing potential [5]. The main challenge associated with the preparation of nanocellulose composite is their poor dispersion in the polymer matrix due to the agglomeration of the fibrils resulting from the hydrogen bonding within the cellulose fibrils. Most of the reported works used hydrophilic polymers to improve the dispersion, and plenty of research is going on in this direction to improve the dispersion and exploit the full potential of the nanocellulose [1425]. A few attempts on the utilization of these cellulosic fibrils with hydrophobic thermoplastics were reported [4, 26, 27].

Our research target is to develop high-performance materials using the high-strength micro- and nanocellulosic fibres for industrial applications. Wood cell walls consist of aggregates of 3-4 nm wide cellulose micro/nano fibrils [3], and these fibrils are embedded as a multilayered structure in hemicellulose and lignin network. Generation of nanofibrils from this cell wall network requires chemical and/or mechanical treatment. Many methods of separation have been reported so far including chemical treatment to generate holocellulose and further mechanical shearing either through cryocrushing, homogenization using high-pressure homogenizer, microfluidizer, and/or grinder, ultrasonication, and wet milling [4, 7, 9, 1113, 28, 29]. In this paper, we are presenting the results of the wood-fibre-based cellulose microfibrils and their films in developing thermoplastic composite with polycarbonate sheets. We have used a commercial grinder with specially defined stones to generate micro- and nano fibrils. Nanosized cellulosic fibres were individualized from the pulp fibres by the shearing forces generated by the grinding stones. Commercially available wood pulp fibres used for this study were directly subjected to a grinder treatment to generate nanofibers. Composites were prepared using compression molding technique with the nano fiber films and polycarbonate sheets and were characterized.

2. Experimental

2.1. Materials

Fibres used for preparation of nanofibres and films were bleached kraft pulp fibres from Domtar, Canada. Polycarbonate film used in this study was from Mcmaster-Carr, ON, Canada.

2.2. Preparation of Nanofibre Films

The wood pulp fibres were defibrillated using a nanofibre facility at the University of Toronto to generate nanofibre suspensions. The fibers were made into a 2% suspension in water and defibrillated by passing through a commercial grinder (Masuko Corp., Japan). After defibrillation, appropriate amount of the suspension was diluted with water and vacuum-filtered using a membrane filter to produce a thin film of thickness approximately 50 microns. The films were then pressed to remove water under pressure for 15 minutes and then dried at 40°C for 48 h. The films were cut using ASTM dre Type E and then dried at 100°C for 2 h to ensure complete drying. The thickness of the samples was measured as an average of 5-point measurements in the tensile specimen.

2.3. Characterization of Fibres and Films
2.3.1. Microscopic Study and Diameter Distribution

Scanning electron microscopy (microscope model Hitachi S-2500) was used to examine the microstructure of wood fibres before processing into nanofibres. Prior to SEM examination, the samples were sputter-coated with a thin layer of gold to avoid electrostatic charge during examination. Transmission electron microscopy (TEM) was used to study the fibre diameter distribution of nanofibres generated. A drop of dilute nanofibre suspension was deposited on the carbon coated grids and allowed to dry before the analysis. Fibre diameter was measured with the help of an image processing analysis program called UTHSCA Image tool down-loaded from http://ddsdx.uthscsa.edu/dig/itdesc.html. The images from scanning electron microscopy and transmission electron microscopy were loaded into the software package and analyzed. The scale of the software was calibrated using the scale bars on each SEM and TEM images. The diameter of 200 fibres from each sample was measured and recorded to get the diameter distribution of the fibres.

2.3.2. X-Ray Diffraction and Crystallographic Study

The crystallinity of the cellulose fibre films before and after defibrillation was examined using a Bruker AXS D8 Discovery Diffraction System, and the method was explained elsewhere [11].

2.4. Preparation of Nanofibre-Polycarbonate Composite Film

Nanocellulose-polycarbonate composite films were prepared by compression molding method. The nano film was placed in between the polycarbonate sheet and pressed in between the steel plates at a temperature of 210°C under a pressure of 1 MPa for 1 minute and then under a load of 5 tons for 30 seconds. The composite was cooled to ambient temperature under pressure and left under atmospheric conditions for 24 h before testing. The nano films used for making composites were surface-treated with isocyanate-based polymers, and the composites contain about 1.5 wt% of the surface modifier.

2.5. Mechanical Properties of the Cellulose Films and Composite

Tensile properties of the nanofibre film and the nanofiber-polycarbonate composites were measured at room temperature using ASTM type E tensile specimens. A standard computerized testing machine (Instron Model 20) was used in accordance with the ASTM D-638 procedure with a load cell of 10 kN and a cross head speed of 2.5 mm/min. At least five sample specimens for each set were tested to get the average value.

3. Results and Discussion

3.1. Microscopic Studies and Diameter Distribution

A typical scanning electron micrograph and transmission electron micrograph of wood pulp fibres and nanofibres are shown in Figures 1 and 2. The mechanical grinding of the fibers resulted in defibrillation of cellulose fibrils from the cell walls as is evidenced from the diameters of the fibres. The average fibre width of wood fibres is considerably decreased after mechanical defibrillation. The fibre diameter distribution of the wood pulp fibres before and after mechanical defibrillation was calculated from the SEM and TEM images using the image processing analysis program, UTHSCSA Image tool, and is shown in Figure 3. It is clear from the figure that the size of the fibers decreases from microns to nanofibre levels after defibrillation. Diameter distribution of wood fibres shows that almost 90% of the fibres were distributed in the diameter range of 10–40 microns and is accounted for an average diameter of 22 microns with a standard deviation of 9 microns. It is evident that almost 90% of the wood nanofibres generated after shearing by the grinding action is distributed in the range of 1–100 nm with more than 60% of the fibres with a diameter in the range of 1–60 nm and lengths of several thousand nanometers.

381342.fig.001
Figure 1: Scanning electron micrograph (SEM) of wood fibre.
381342.fig.002
Figure 2: Transmission electron micrograph (TEM) of wood nanofibrils.
fig3
Figure 3: Diameter distribution of fibres before and after defibrillation.
3.2. Crystallinity of the Cellulose Films

Crystallinity of cellulose microfibrils arises from the hydrogen bonds between cellulose molecules and the resulted conformation of the cellulose molecules. It is reported that the length of crystallites in native cellulose can be 100–250 nm with cross-section of 3–10 nm. In plant cell walls it is believed that the cellulose crystallites are interconnected to each other by disordered cellulose molecules and hemicellulose and associated lignin network. The crystallinity of the cellulosic fibres highly depends on the source and the degree of degradation of the fibres during chemical and physical method used for the separation of the fibrils from the plant cell wall [30, 31].

XRD pattern of wood pulp fibre sheet and nanofibre sheet is shown in Figure 4. Cellulose I is the common variety found in the plants and is characterized by the well-defined principal peak at 22.5 (2θ) and the two overlapping secondary peaks at 14.5 and 16.3 (2θ), which are associated with crystalline planes of 1 0 1, 1 1 and 0 0 2. No rearrangement of the cellulose structure into another crystalline form was observed upon defibrillation of the pulp fibres indicating that the method of grinding affects the amorphous region more than the crystalline region. A similar study was reported in the wet-stirred media milling of wood pulp fibres [29].

381342.fig.004
Figure 4: XRD of wood fibres before and after defibrillation.

Methods for quantifying crystallinity from XRD have been proposed either by using the areas under the peaks or the heights of the maxima and minima of the curve above the base line [31, 32]. In this paper we used the method of minima and maxima for the calculation of crystallinity index and crystallinity ratio, which is the two ways of expressing crystallinity of cellulose and are calculated using the following equations: where is the height of the 22.50(2θ) peak above the base line and is the height of the 190(2θ) minimum above the base line. The crystallinity index and the crystallinity ratios calculated using the above equations are similar, and the C.I. and C.R. values of wood fibre paper are 0.86 and 0.84, while those of nanofibre are 0.90 and 0.89, respectively. The crystallinity index values of wood and nanofibres were comparable to each other indicating that crystallinity is not affected by the mechanical process for the generation of nanofibres. The high crystallinity index values of the fibre sheets show the crystalline nature of the cellulosic papers and are expected to have high strength for these cellulose papers.

3.3. Thermal Properties

The aim of this study was to process the nanofibre sheets from wood fibres with thermoplastics under temperature and pressure to make composites. In this context, thermogravimetric analysis of the wood fibre sheets was studied to understand the degradation characteristics of these sheets. The TGA curves of the wood fibre sheets and nanofibre sheets are shown in Figure 5. It is clear from the figure that the onset of degradation of both fibre sheets is well above 200°C, and the higher onset of degradation temperature indicates the improved thermal stability of the fibers compared to the lignocellulosic fibres. This enhanced stability may be due to the absence of lignin and hemicelluloses compared to the natural fibres, and this indicates the suitability of these fibers for processing with thermoplastics, even with high melting polymers. Further, in order to verify if there is any thermal degradation of the fibres occurring during processing of the composites, the nanofibre films were subjected to high temperature (185–225°C) and pressure similar to the processing conditions of composites. Tensile properties of the heat-treated samples were compared with those of the original fibre sheets. The results of the tensile strength and modulus values are shown in Figure 6. The nanofibre sheets retained its strength and modulus under the conditions of composite processing (about 200°C, 2 min) and under pressure, and it is noticed that above 225°C the strength properties decreased marginally compared to the processing conditions used for composite preparation. This indicates that the hot pressing conditions used in this study do not have any adverse effect on the strength of the films in the composites prepared.

381342.fig.005
Figure 5: TGA thermograms of wood fibres before and after defibrillation.
381342.fig.006
Figure 6: Retention of tensile properties of nanofilms subjected to different processing conditions.
3.4. Tensile Properties of the Composites

Tensile properties of the nanofiber films prepared were determined, and the average strength and modulus of the films were found to be 240 MPa ± 12 MPa and 11 GPa ± 0.6 GPa, respectively. Composites were prepared by compression molding, by placing the nano sheets in between polycarbonate sheets, under pressure and temperature. Different fibre loads of the fibres in the composites were achieved by preparing the nano sheets with different thickness. Figure 7 shows the tensile strength and modulus of the polycarbonate sheet and the wood nanofibre-polycarbonate composites with different fibre loads (varies from 10 to 32 wt%). The figure indicates that the strength and modulus of the polycarbonate sheets increased with the incorporation of the nanofibres. The tensile strength of the composites increases up to 20% of the fibre content and then remains the same at about 28% of fibre content and then showed a reverse trend. This may be due to the poor wetting of the fibres with the polycarbonate as a result of the increased surface area of the fibres. The percentage in the strength of the matrix is increased from 26% to 30% by incorporating a fibre loading of 11 wt% to 18 wt%. There is a significant increase in the modulus of the composites compared to the strength. Modulus of the polycarbonate sheets increases about 100% by using about 12 wt% of the nanofibrillated sheets. Unlike modulus, ultimate strength of the composite is influenced by the flaws present in the composite, and this could arise from different sources such as poor adhesion between the nano sheet and the polymer and nonuniformity in the thickness of the sheets. This will be investigated as a part of the further research in this direction. The results from this study indicate that reinforcing ability of the hydrophilic cellulosic fibres can be exploited for reinforcing hydrophobic thermoplastics to develop composites with improved properties.

fig7
Figure 7: (a) Tensile strength of composites, (b) tensile modulus of composites.

4. Conclusions

Cellulose nano fibrils were prepared by mechanical defibrillation of wood pulp fibres using a commercial grinder, and sheets were prepared by vacuum filtration of the dilute solutions of the fibre suspensions. The fibre films were characterized in terms of strength, crystallinity, and thermal properties. Strength and modulus of the nanofibre film were considerably high and were found to be 240 MPa and 11 GPa, respectively. Crystallinity studies showed that there is no degradation in the crystallinity of the pulp fibres during mechanical grinding process. Thermal properties of the fibre sheets showed their suitability of processing with polymers with thermoplastics, and the retention of the strength and modulus demonstrated that the processing conditions used in this study for making composites do not have an adverse effect on the properties of the sheets.

Cellulose nanocomposite processing via compression molding of nanocellulose sheets with polycarbonate was attempted. Evaluation of the strength properties of the polycarbonate and its composites showed a trend that demonstrated an improvement in the tensile strength and modulus with nanofibre reinforcement. The modulus of the PC improves about 100% by incorporating about 18% of the nanofibres, and an increase of 30% is observed in the tensile strength for the composite with the same fibre content.

The study was a preliminary attempt to develop nanofibre-reinforced thermoplastic composites with improved properties, and the results demonstrated the reinforcing ability of the cellulosic nano fibrils for reinforcing the hydrophobic thermoplastic composites. The detailed study of the composites, such as microstructural evaluation, interaction between the nano fibrils and polymer matrix, and effect of surface treatment on the wetting properties of the composites, would be the subjects of future studies.

Acknowledgment

The authors would like to acknowledge the financial support from the Natural Fibres for the Green Economy Network (NAFGEN) for this research.

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