Thermomechanical Properties of Jute/Bamboo Cellulose Composite and Its Hybrid Composites: The Effects of Treatment and Fiber Loading

Author

Advances in Materials Science and Engineering
Volume 2017 (2017), Article ID 8630749, 10 pages
https://doi.org/10.1155/2017/8630749

Author

Fui Kiew Liew,1,2 Sinin Hamdan,1 Md. Rezaur Rahman,1 and Mohamad Rusop3

1Faculty of Engineering, Universiti Malaysia Sarawak, 94300 Kota Samarahan, Sarawak, Malaysia
2Faculty of Applied Science, Universiti Teknologi MARA, 94300 Kota Samarahan, Sarawak, Malaysia
3NANO-SciTech Centre (NST), Institute of Science, Universiti Teknologi MARA, Shah Alam, Selangor, Malaysia

Correspondence should be addressed to Fui Kiew Liew

Received 16 January 2017; Revised 27 March 2017; Accepted 27 April 2017; Published 23 May 2017

Academic Editor: Peter Chang

Copyright © 2017 Fui Kiew Liew 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

Jute cellulose composite (JCC), bamboo cellulose composite (BCC), untreated hybrid jute-bamboo fiber composite (UJBC), and jute-bamboo cellulose hybrid biocomposite (JBCC) were fabricated. All cellulose hybrid composites were fabricated with chemical treated jute-bamboo cellulose fiber at 1 : 1 weight ratio and low-density polyethylene (LDPE). The effect of chemical treatment and fiber loading on the thermal, mechanical, and morphological properties of composites was investigated. Treated jute and bamboo cellulose were characterized by Fourier transform infrared spectroscopy (FTIR) to confirm the effectiveness of treatment. All composites were characterized by tensile testing, thermogravimetric analysis (TGA), and differential scanning calorimetry (DSC). Additionally, surface morphology and water absorption test was reported. The FTIR results revealed that jute and bamboo cellulose prepared are identical to commercial cellulose. The tensile strength and Young’s modulus of composites are optimum at 10 weight percentage (wt%) fibers loading. All cellulose composites showed high onset decomposition temperature. At 10 wt% fiber loading, JBCC shows highest activation energy followed by BCC and JCC. Significant reduction in crystallinity index was shown by BCC which reduced by 14%. JBCC shows the lowest water absorption up to 43 times lower compared to UJBC. The significant improved mechanical and morphological properties of treated cellulose hybrid composites are further supported by SEM images.

1. Introduction

Cellulose is the world’s most abundant natural raw material with renewable sources for composite fabrication. Natural cellulose fibers have attracted global researchers owing to their unique properties such as biodegradability, low weight, easy availability, easy processing, being environmental friendly, flexibility, high strength, and stiffness [1–3].

Jute is commonly grown in India, China, and Bangladesh. Jute fibers contain mainly cellulose (58~63%), hemicellulose (20~24%), and lignin (12~15%) [4]. It has been used as packaging material, geotextiles, household textiles, and carpet backing. Bamboo is a fast-growing species and a high-yield renewable resource. Bamboo fiber consists of cellulose (73.8%), hemicellulose (12.5%), lignin (10.1%), pectin (0.4%), and aqueous extract (3.2%) [5]. Bamboo fibers have been widely used in the household, transport, and composite manufacturing industries [6]. However, all cellulose fibers have similar drawbacks which include being polar, hydrophilic in natural, low thermal stability and poor compatibility with polymer matrix. Those limitations contributed to weak fiber-matrix interfacial bonding, leading to decrease in mechanical properties [7].

To improve the interfacial bonding, researchers have attempted various surface treatments, such as alkali treatment [8–10], silane treatment [11, 12], acetylation [13], and different coupling agents. Among various treatments, alkali treatment has been found to be most effective method [14, 15]. The surface treatments of cellulose fibers provide advantages which include increased hydrophobicity, increased surface roughness, reduced water uptake, and increased reactivity towards polymeric matrices [16, 17]. Alkaline treatment or mercerization led to break down of fiber bundle into smaller fibers. Mercerization also modifies the lignin content by rupturing the ester bonds that form cross-links involving xylan and lignin, thus increasing the porosity of the lignocelluloses [18]. This treatment can effectively remove lignin and hemicellulose which indirectly increase cellulose contained in treated fiber. Mercerization increases the number of possible reactive sites and allows better fiber wetting [16]. As a result, mercerization had long-lasting effect on the mechanical properties of fibers, mainly on fiber strength and stiffness [19].

Hybrid cellulose composites are materials made from combining two or more different celluloses in a common matrix. Hybrid cellulose composites made up of two different cellulosic fibers are less common but they are potentially useful materials with respect to environmental concerns [20]. Hybrid cellulose composites fabrication by cellulosic fibers is economical and provides another dimension to the versatility of cellulosic fiber reinforced composites. The constituent fibers in a hybrid composite can be altered in many ways, leading to good mechanical properties [21]. Hybrid composites are one of the emerging fields that draw attention for application in various sectors ranging from automobile to the building industry. Previous research showed that cellulose composites have best mechanical performance at about 10–15 wt% fiber loading [22, 23].

Pöllänen et al. (2013) studied the influence of the viscose fibers and the microcrystalline cellulose on the morphological, mechanical, and thermal expansion properties of high density polyethylene (HDPE) composite. The filler content of 5, 10, 20, and 40 wt% was used. The interaction between the fillers and the matrix was improved with maleic anhydride grafted polyethylene. Both fillers increased Young’s modulus and tensile strength of polyethylene with the highest values achieved by 40 wt% viscose fibers [24]. Both fillers show decreased coefficients of the linear thermal expansion of the HDPE matrix in the flow direction. Cellulose composites containing up to 10 wt% cellulose pulp fibers with low-density polyethylene (LDPE) were fabricated by Sdrobiş et al. (2012). Unbleached and bleached Kraft cellulose pulp fibers modified with oleic acid in cold plasma conditions have been used. It was found that thermal stability of cellulose pulp fibers composites is higher than that of pure LDPE [25]. Bleached cellulose pulp fibers are more efficient in enhancement of composites properties.

In the present work, the jute and bamboo cellulose had been extracted and treated with peracetic acid solution and then followed by mercerization. The effects of chemical treatment and cellulose fiber and hybrid cellulose fiber loading on thermal, mechanical, morphological, and water absorption properties of cellulose composites were investigated and reported. The outcome of investigation is expected to determine the suitability of composite for nonstructural and outdoor applications such as door trim panels, parts of automobile, and playground facilities.

2. Materials and Methods

Jute (Corchorus olitorius) and bamboo (Dendrocalamus asper) fibers were obtained from Bangladesh Jute Research Institute (BJRI), Dhaka, Bangladesh, and Forest Research Institute, Sarawak, Malaysia, respectively. Low-density polyethylene (LDPE) granula was obtained from the Siam Polyethylene Co., Ltd., Prakanong, Bangkok, Thailand. The density and the melting point were 0.935 g·cm−3 and between 105 and 125°C, respectively. The chemicals used were toluene (Sigma Aldrich, St. Louis, MO, USA), commercial cellulose (Sigma Aldrich, St. Louis, MO, USA), ethanol (Sigma Aldrich, St. Louis, MO, USA), hydrogen peroxide (Qeric), acetic acid glacial (JT Baker, Center Valley, PA, USA), titanium (IV) oxide (JT Baker, Center Valley, PA, USA), and sodium hydroxide (Merck KgaA, Darmstadt, Germany). All chemicals were of analytical grade.

2.1. Natural Fiber Preparation

The jute fibers were cleaned and air-dried for 48 h under direct sunlight. The middle portion of the jute fiber was removed and chopped into approximately 10-mm long and then oven-dried at 105°C for 24 h. Finally, the sections were ground and sieved using a 100-μm sieve. The length of the bamboo culm trim, excluding the bamboo internode, was 1 m in length. It was cut using a planner machine to produce chips and then ground to powdered form. The chips and powder mixture were dried in an oven at 70°C for 72 h. The oven-dried samples were grinded and sieved, using a 100-μm sieve, to obtain bamboo fibers with a mesh size of 100 μm.

2.2. Chemical Treatment of Jute and Bamboo Fiber

Jute and bamboo fiber were chemically treated to obtain treated cellulose. Initially, fibers were dewaxed. Then, cellulose fiber was obtained by oxidative delignification using a water solution containing acetic acid, hydrogen peroxide with titanium (IV) oxide, and TiO2 catalysts adopted Kuznetsov method [26]. Cellulose fiber is alkaline treated to obtain mercerized cellulose fiber. The details of chemical treatments flow are shown in Figure 1 and steps are explained below.

Figure 1: Flow diagram of cellulose preparation.

Dewaxing of Fiber. The dewaxing was done by applying the Leavitt-Danzer method. In this process, two types of chemical were used, namely, toluene (C6H5CH3) and ethanol (C2H6O) with ratios of 2 : 1 (v/v). The extraction process was done using the extraction column (Soxhlet extractor, round bottom flask, Liebig condenser, heater, membrane, and thermometer). Then, the jute/bamboo fibers were immersed in the extraction column. This process was continued for 2 hours at 250°C. The collected fibers were later placed in the forced air convention oven for 24 hours at 75°C for drying overnight and were kept for delignification processes.

Delignification of Fiber. The delignification was done using peracetic acid solution which consists of 99.8 wt% acetic acid (CH3COOH) and 35 wt% hydrogen peroxide (H2O2) in the present of titanium (IV) oxide (TiO2) catalyst in a round bottom vector vessel. The reaction scheme is shown in Figure 2.

Figure 2: Peracetic acid solution reaction scheme.

Then, the dewaxed jute/bamboo fibers were placed in the round bottom vessel. This process was continued for 2 hours at 130°C. After this, the collected fibers were carefully washed and placed in the forced air convention oven for 24 hours at 70°C.

Mercerization. Delignified fiber was immersed into alkaline solution to dissolve the pectin and hemicelluloses. 6 wt% sodium hydroxide was used to treat the cellulose fiber in a flask. The mixture was stirred using autoshaker at 150 rpm, heated to 80°C for 2 hours, and stopped after 8 hours of stirring. The mixture was rinsed with deionized (DI) water. The treated product was then filtered using Buchner flask and rinsed with DI water until the pH level reaches 7 and was freeze-dried at −85°C for 48 hours. The treated fiber was then ground using a shear grinder for 10 min to obtain fine mercerized cellulose fiber. The detail of reaction is shown in Figure 3.

Figure 3: Mercerization reaction scheme.

2.3. Composite Preparation

Both mercerized jute and bamboo cellulose were kept in a convection oven at 100°C for 24 hours prior to composite fabrication. Desired weight fraction of hybrid cellulose fibers was equally distributed using sieve on correct weight fraction of LDPE laminate sheet to produce hybrid cellulose fibers composite. The LDPE laminate sheet was put in an aluminum mold using sandwich method and then placed in an electric hot press set at 180°C with 3.45 MPa (500 psi) for 45 min. Aluminum mold was cooled down under pressure for 1 hour and the prepared specimens were taken out to label. Specimens were cut into composite samples by tensile cutter. Table 1 shows the details of hybrid composites by weight percentages. Flow of hybrid composite preparation was shown in Figure 4.

Table 1: Hybrid composite by weight percentage.

Figure 4: Flow of hybrid composite preparation.

3. Characterization Methods

3.1. Fourier Transform Infrared Spectroscopy (FTIR)

The FTIR spectra were obtained using a spectrometer (spectrum 100, Perkin Elmer, Waltham, MA). The obtained spectra are described in the Results and Discussion. The transmittance range of the scan was 4000 to 650 cm−1.

3.2. Tensile Test

Tensile testing was conducted according to the ASTM D 638-10 (2010) [27] testing standard using a universal testing machine (MSC-5/500, Shimadzu Company Ltd., Japan) at a crosshead speed of 5 mm·min−1. The dimensions of the specimens were 115 mm  × 6.5 mm  × 3.1 mm . Five rectangular specimens were tested and the average value was reported for each series.

3.3. Thermogravimetric Analysis (TGA)

Thermogravimetric measurements were performed using a Perkin Elmer Pyris 1 TGA system. All measurements were obtained under a nitrogen flow rate of 20 mL·min−1 over a temperature range of 50 to 600°C. Then, an oxygen flow rate of 20 mL·min−1 and a temperature range of 600 to 700°C was applied, while maintaining a constant heating rate of 20°C·min−1. Three specimens were tested and the average value was reported.

3.4. Differential Scanning Calorimetry (DSC)

The DSC tests were conducted using a differential scanning calorimeter (DSC; 8000, Perkin Elmer). Temperature programs for dynamic tests were run from 50 to 180°C at the heating rate of 20°C·min−1 under a 20 mL·min−1 nitrogen atmosphere. The degree of crystallinity was calculated according to the following formula.where  is enthalpy of fusion,  is the weight fraction of polymeric matrix in the composite, and  = 290 J/g (heat of fusion for 100% crystalline LDPE).

3.5. Scanning Electron Microscopy (SEM) Analysis

The surface morphology was examined using a scanning electron microscope (TM 3030 pitch emission, Hitachi, Tokyo, Japan). The SEM specimens were sputter-coated with gold using auto-fine coater (JFC-1600, Joel Ltd.). The micrographs with a 500-time resolution were presented in the Results and Discussion.

3.6. Water Absorption Test

In order to measure the water absorption characteristics of the composites, rectangular specimens were prepared. The water absorption test was conducted according to ASTM D570-99 [28]. The test specimens were immersed in a beaker containing 100 mL of deionized water at room temperature (27°C) for 22 days. The initial weights of the samples were determined. After 24-hour interval, samples were taken out from the beaker, wiped and dried, and weighed immediately. The percentages of water absorbed by the samples were calculated using the following formula. Three replicates were tested for each set and average data was recorded.

4. Results and Discussions

4.1. Fourier Transform Infrared Spectroscopy (FTIR)

FTIR composition of bamboo fiber, jute fiber, commercial cellulose, jute cellulose, and bamboo cellulose was shown in Figure 5.

Figure 5: Wavelengths in FTIR of (A) jute fiber, (B) bamboo fiber, (C) commercial cellulose, (D) jute cellulose, and (E) bamboo cellulose.

Figure 5 showed bamboo fiber and jute fiber were having similar peak intensity. Both bamboo and jute fiber consist of cellulose, hemicellulose, and lignin; therefore peak intensities are identical. However, there were still differences among bamboo fiber and jute fiber peak. Only jute fiber showed peak at 1324 cm−1, which is attributed to the CH2 bending. Both jute and bamboo fibers show peak at 1738 cm−1 represented either the acetyl and uronic ester groups or the ester linkage of carboxylic group of the ferulic and p-coumeric acids of hemicelluloses [29, 30]. The absence of this peak is observed in jute and bamboo cellulose, indicating the removal of most of the hemicellulose. The peak at 1242.4 cm−1 region is due to the stretching of phenolic hydroxyl groups in lignin [31]. Total disappear of this peak in jute and bamboo cellulose samples revealed that lignin is removed. On the other hand, all cellulose samples show peak at 1166–1160 cm−1 region assigned as C–O–C stretching attributed to the β-(1→4)-glycosidic linkage in cellulose [32].

Figure 5 also shows all cellulose with broad peak intensity band at 3343–3331 cm−1 attributed to O–H stretching vibration. The peaks at 2923–2900 cm−1 and 1324–1312 cm−1 regions are characteristics of C–H stretching and –CH2 bending, respectively. The peak at 1651–1646 cm−1 is attributed to the H–O–H stretching vibration of absorbed water in carbohydrate. The peak at 903–898 cm−1 region is related to glycosidic –C1–H deformation, a ring vibration, and –O–H bending. These characters imply the β-glycosidic linkages between the anhydroglucose units in cellulose. The rise of intensity peak at 1026–1020 cm−1 region confirms that the cellulose content increases due to chemical treatment [33]. Both jute and bamboo cellulose show identical peaks compared to commercial cellulose. This further confirms that hemicelluloses and lignin in both jute and bamboo fiber were well removed during the chemical treatment.

4.2. Tensile Properties

The tensile strength and Young’s modulus of UJBC, JCC, BCC, and JBCC hybrid composite by weight percentages are shown in Figures 6(a) and 6(b), respectively. The results indicated that all treated cellulose composites have significant high tensile strength and Young’s modulus compared to untreated hybrid composite (UJBC). Hybrid cellulose composite with 10 wt% fiber loading shows highest tensile strength and Young’s modulus among the sample series tested. The tensile strength gradually decreases when fiber loading is greater than 10 wt%.

Figure 6: (a) Tensile strength of composite at different fiber loading. (b) Young’s modulus of composite at different fiber loading.

Among the cellulose hybrid composites, it is obviously shown that JBCC at 10 wt% was the optimized hybrid composite which increases tensile strength and Young’s modulus by 157% and 195%, respectively. The significant increase of tensile properties in JBCC is contributed by great improvements of interfacial adhesion between the treated hybrid cellulose fibers and LDPE matrix. The removal of hemicelluloses in hybrid cellulose fibers further enhances fiber rearrangement in composite which led to effective loads transfer [34]. JCC and BCC show similar tensile strengths which increase by 130% and 126.5%, respectively. On the other hand, Young’s modulus of BCC increased by 144% is much higher than JCC which only increases by 64.3%. High resistance of elastic deformation on BCC attributed to high stiffness of bamboo cellulose in composite. Smaller cross-section of bamboo cellulose enhanced the stiffness of the composites [35]. The strong interface bonding between bamboo cellulose and LDPE enables effective stresses distribution on composite and contributed to high Young’s modulus.

It is worth noting that all UJBC series show decreasing trend of mechanical properties with increased hybrid fibers loading. The incompatibility of hydrophilic fibers with hydrophobic polymer matrix causes relative weak fibers-matrix interfacial adhesion. Untreated hybrid fibers also exhibit poor resistance to moisture and led to high water absorption and subsequently contributed to poor mechanical properties of UJBC composites.

The stress-strain graph of UJBC, JCC, BCC, and JBCC composite at 10 wt% fiber loading is shown in Figure 7. The results revealed that all treated cellulose composites have high stress with greater strain compared with UJBC. The removal of hemicellulose and lignin in fiber provides strong adhesion between fiber and matrix. It contributed to enhancing strain by greater elongation of composites.

Figure 7: Stress-strain graph of hybrid composite at 10 wt% fiber loading.

4.3. Thermogravimetric Analysis (TGA)

The thermogravimetric analysis of UJBC, JCC, BCC, and JBCC hybrid composites at 10 wt% fiber loading was summarized in Table 2. Previous studies have found that there is no degradation of jute-bamboo hybrid composite up to 300°C [36]. Above this temperature, the decomposition takes place and thermal stability decreased.

Table 2: Comparison of activation energy among hybrid composites at 10 wt% fiber loading.

UJBC sample showed that low onset decomposition started at 304.9°C. Low onset decomposition of UJBC was mainly contributed by decomposition of hemicellulose [37]. On the other hand, all treated cellulose hybrid composites showed significant high onset decomposition temperature ranging from 346 to 415°C. Relative high onset decomposition was due to high thermal resistance of treated cellulose fibers in hybrid composite. The high onset decomposition also confirms that hemicellulose was well removed in cellulose composites. There is no significant difference between untreated hybrid composite and treated cellulose hybrid composite related to major decomposition. The major decomposition of hybrid composite occurs between 511°C and 529°C involving -cellulose and LDPE resin [38]. At above 545°C, final decomposition takes place. The final decomposition of F10JCC, F10BCC, and F10JBCC showed remaining weight of 5.1%, 3.2%, and 3.5%, respectively. The final remaining weight was mainly due to char formation.

The activation energy  was calculated from TGA graphs using Broido equation [39] as given below:where  is the fraction of undecomposed nonvolatilized material,  is the absolute temperature (in Kelvin), and  is the gas constant (8.314 J mol−1 K−1). The values of  have been taken from the TGA data. The values of  were plotted on -axis, while the temperatures as  (in Kelvin scale) were plotted on -axis. Finally, from the slope of the trend line, the activation energy of the composite was calculated.

Table 2 shows that all treated cellulose composites obtain higher activation energy compared to F10UJBC. Among those composites, F10JBCC shows 2.5 times higher activation energy followed by F10BCC and F10JCC which are 2.0 and 1.1 times, respectively. The higher value of activation energy indicates the higher thermal stability of composite [40]. Higher activation energy in treated cellulose hybrid composite was attributed to rough surface and pores on the cellulose fibers become more prominent, which give better adhesion with the matrix [41].

4.4. Differential Scanning Calorimetry (DSC)

The melting characteristic of 10 wt% cellulose composite is showed in Table 3. From Table 3, all cellulose and its hybrid composites show higher initial melting temperature compared to F10UJBC.

Table 3: Melting characteristics of neat LDPE, UJBC, JCC, BCC, and JBCC at 10 wt% cellulose fiber loading.

The crystallinity index was reduced from 55.9% for neat LDPE to 41.9%–50.3% for treated cellulose hybrid composites. Shortening of composite solidification time due to presence of cellulose fiber and the surface energy of fibers becoming closer to the surface energy of the matrix are reasons of reduced crystallinity index [42]. Significant reduction in crystallinity index was shown by F10BCC which reduced by 14%. The result revealed that F10BCC has better fiber-matrix interfacial bonding which further supports high Young’s modulus results. On the other hand, F10UJBC, F10JBCC, and F10JCC show a marginal reduction in crystallinity index of 9.9%, 9.6%, and 5.6%, respectively. It is worth noting that all DSC results for F10JBCC show a value between F10JCC and F10BCC. Those results indicated that F10JBCC hybrid composite shows average melting characteristic combination of F10JCC and F10BCC which is following rule of mixtures for hybrid composite [43].

4.5. Scanning Electron Microscopy (SEM) Analysis

Figure 8 shows SEM images of the cross-section surface of UJBC, JCC, BCC, and JBCC at 10 wt% fiber loading after tensile test. Figure 8(a) shows the delamination of F10UJBC. There were some microcracks because of the relatively weak interfacial bonding among the fibers and the matrix. Poor adhesion between the untreated hybrid fibers and the matrix creates further voids spaces around fibers in the hybrid composite [44].

Figure 8: SEM images of the cross-section surface of (a) UJBC, (b) JCC, (c) BCC, and (d) JBCC at 10 wt% fiber loading.

Figure 8(b) shows the well-bonded jute cellulose composite. The good interfacial bonding between jute cellulose and LDPE matrix contributed to high tensile strength and modulus. Strong interfacial bonding was observed in F10JCC. Micrographs revealed that the jute cellulose fibers smoothly distributed in of LDPE resin.

Figure 8(c) shows a well-bonded interface between the bamboo cellulose fiber and LDPE matrix with some minor voids observed. This strong interfacial bond among cellulose fiber-LDPE matrix contributed to a higher tensile strength and modulus. This was mainly attributed to an elimination of the hydroxyl groups from chemical surface modified cellulose fibers.

Figure 8(d) shows strong bonding between the jute-bamboo cellulose fiber and LDPE matrix. The hydrophobic characteristics of treated hybrid cellulose fibers and well bonding of LDPE both strengthen the fibers-matrix interfacial adhesion. Relative minor microvoids appear between fiber and matrix interfacial.

4.6. Water Absorption Test

Figure 9 showed that water absorption of UJBC, BCC, JBCC, and JCC of 10 wt% cellulose fibers loading for 22 days. The untreated hybrid fiber composite (UJBC) showed highest water absorption rate up to 30.2% in this duration. Water absorption rate of UJBC starts to saturate after 11 days. High water absorption was results of poor wettability and adhesion between hydrophilic fibers-LDPE [45]. Untreated fibers are hydrophilic with many hydroxyl group (–OH). The high percentage of –OH group in fibers tend to show low moisture resistance. This leads to dimensional variation of UJBC and poor interfacial bonding between the fiber and matrix. This also caused microcracks and voids formation in UJBC which trap and absorb greater percentage of water. As the microcracks propagated, capillarity and transport of water molecules via microcracks become active [46].

Figure 9: Water absorption percentage of UJBC, BCC, JBCC, and JCC for 22 days for 10 wt% fiber loading.

Among treated hybrid composites, F10JBCC shows the lowest water absorption rate of 0.7%. F10JBCC water absorption saturated after 10 days. The mercerization treatment reduced the polar groups in fiber by replacing the hydroxyl groups on the surfaces of fibers [47]. The low water absorption rate in F10JBCC is contributed by good adhesion among treated hybrid fibers-matrix composite. Good interfacial adhesion bonding among treated cellulose fiber-matrix reacts to retard water entering cellulose fiber. F10JCC attained a saturation level after 6 days with water absorption of 1.9%. It is worth noting that F10BCC shows highest water absorption rate among treated cellulose hybrid composites. The water absorption is 5.9% and absorption rate reduced only after 10 days. This is mostly due to high surface porosity of bamboo cellulose combined with microvoid among treated cellulose and matrix interfaces. Overall, water absorption was significantly low for all treated cellulose hybrid composites compared with untreated hybrid fiber composite.

5. Conclusions

The present study reveals that both treated jute and bamboo cellulose were successfully used as reinforcement fiber in hybrid composites. The FTIR results show that jute and bamboo cellulose obtained are identical to commercial cellulose. The tensile strength and Young’s modulus of hybrid cellulose composite are optimized at 10 wt% hybrid fibers loading. JBCC at 10 wt% reveals high tensile strength and Young’s modulus increased by 157% and 195%, respectively. All treated cellulose hybrid composites showed high onset decomposition temperature ranging from 346 to 415°C due to elimination of hemicellulose. F10JBCC shows 2.5 times higher activation energy followed by F10BCC and F10JCC at 2.0 times and 1.1 times, respectively. Water absorption was significantly low for all treated cellulose hybrid composites compared with untreated hybrid fiber composite. F10JBCC shows lowest water absorption up to 43 times lower compared to F10UJBC. The significant improved mechanical and morphological properties of treated cellulose hybrid composites are further supported by SEM images that show better matrix-fiber interaction compared to untreated hybrid fiber composite. The outcome of the composite shows cellulose hybrid composite suitable for outdoor application such as street light enclosure, automobile signal light cover, and playground slides.

Conflicts of Interest

The authors declare that there are no conflicts of interest regarding the publication of this paper.

Acknowledgments

The authors would like to acknowledge the Center of Excellence and Renewable Energy (CoERE), UNIMAS for their financial support, Grant no. CoERE/Grant/2013/06 and Ph.D. seed fund F02(DPP30)/1245/2015(05). The authors would like to thank Forestry Department Sarawak for their technical support on tensile testing.

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