Glycerine Treated Nanofibrillated Cellulose Composites

Erbas Kiziltas, Esra; Kiziltas, Alper; Nazari, Behzad; Gardner, Douglas J.; Bousfield, Douglas W.

doi:https://doi.org/10.1155/2016/7851308

Journal of Nanomaterials

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Abstract Introduction Experimental Results and Discussion Conclusions Disclosure Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2016 | Article ID 7851308 | https://doi.org/10.1155/2016/7851308

Glycerine Treated Nanofibrillated Cellulose Composites

Esra Erbas Kiziltas,^1,2Alper Kiziltas,^1,3Behzad Nazari,⁴Douglas J. Gardner,¹and Douglas W. Bousfield⁴

Academic Editor: Wanshuang Liu

Received20 Jan 2016

Revised14 Mar 2016

Accepted28 Mar 2016

Published19 Apr 2016

Abstract

Glycerine treated nanofibrillated cellulose (GNFC) was prepared by mixing aqueous nanofibrillated cellulose (NFC) suspensions with glycerine. Styrene maleic anhydride (SMA) copolymer composites with different loadings of GNFC were prepared by melt compounding followed by injection molding. The incorporation of GNFC increased tensile and flexural modulus of elasticity of the composites. Thermogravimetric analysis showed that as GNFC loading increased, the thermal stability of the composites decreased marginally. The incorporation of GNFC into the SMA copolymer matrix resulted in higher elastic modulus () and shear viscosities than the neat SMA copolymer, especially at low frequencies. The orientation of rigid GNFC particles in the composites induced a strong shear thinning behavior with an increase in GNFC loading. The decrease in the slope of elastic modulus with increasing GNFC loading suggested that the microstructural changes of the polymer matrix can be attributed to the incorporation of GNFC. Scanning electron microscopy (SEM) images of fracture surfaces show areas of GNFC agglomerates in the SMA matrix.

1. Introduction

In the past twenty years, much attention has been devoted to the study and development of polymer nanocomposites using various nanofillers including clay, silica, carbon nanotubes, and cellulose nanofibers [1, 2]. Recent years, in particular, have seen a large global interest regarding cellulose nanocomposites. National and international meetings of the Organization for Economic Cooperation and Development, Society of Wood Science Technology, Forest Products Society, American Chemical Society, and Technical Association of the Pulp and Paper Industry have covered the subject of cellulose nanocomposites. Interest throughout the last decade in the subject has also led to an increase in the number of publications on the preparation of cellulose nanofiber reinforced composites (including nanofibrillated cellulose (NFC), microfibrillated cellulose (MFC), cellulose nanocrystals (CNC), bacterial cellulose (BC), and electrospun cellulose nanofibers (ECN)). Interest is also reflected through the increasing number of review papers which provide detailed information on the production of cellulose nanofibers, processing, and characterization of cellulose nanocomposites and new developments, with particular emphasis on their applications [3–12].

Because of its unique properties, NFC has received considerable attention for the preparation of green nanocomposites with polymer matrices. Such properties include high strength, high stiffness, low density when compared to glass fibers, ease of chemical modification attributable to a natural advantage of an abundance of hydroxyl groups on the surface of NFC, and biodegradability [3, 13–16]. The potential benefits associated with NFC have been confirmed; however, uniform dispersion of NFC remains a challenge in exploiting the exceptional properties of NFC [17]. To improve the compatibility at the fiber-matrix interface and dispersion of NFC, various methods have been adopted, including the use of surfactants, functionalization of NFC, and the use of carrier systems in NFC-polymer nanocomposites [15, 16, 18–25]. One of the main challenges to address is the stability of NFCs in suspension, which is a difficult impediment to overcome because of NFCs’ high surface energy and the large number of hydrogen bonds that can be formed among NFCs [3, 16]. NFCs can agglomerate leading to gel formation which negatively impacts the mixing properties of such suspensions in polymer matrices. The desulfonation of CNC with glycerol has been reported by Dorris and Gray [26], but, to the best of our knowledge, formation of a stable NFC suspension in glycerine by mixing aqueous suspensions of NFC with glycerine has not yet been reported in literature.

Styrene-malic anhydride (SMA), which has higher glass transition temperature () and heat deflection temperature (HDT) than most commodity plastics, is an engineering thermoplastic copolymer and both unfilled and glass-filled SMA are used extensively in the automobile industry for both injection molding and thermoforming of interior parts [27–29]. Because of its simplicity, applicability for industrial composite production, and reactive functional groups, SMA copolymers are also used as compatibilizing agents, which reduce the initial interphase incompatibility, in carbon nanotube reinforced polyamide 12 (PA12) and polyvinyl chloride (PVC) nanocomposites [30–32]. To the best of our knowledge, we are the first to examine the properties of NFC dispersed in a SMA copolymer matrix prepared by melt compounding followed by injection molding. The maleic anhydride group on the polymer backbone reacts with hydroxyl groups on the NFC. The modified NFC surfaces and SMA copolymer composites will be characterized in detail by elemental analysis, contact angle measurements, inverse gas chromatography, X-ray photoelectron, and infrared spectroscopy in our next publications. The reaction is depicted schematically in Figure 1.

Despite the technological interest in SMA copolymers, only a few studies of filled-SMA copolymer composites have been reported [27, 28, 33–36]. Simonsen et al. showed that the mechanical properties of recycled newsprint-filled SMA copolymer were higher than those of unfilled plastics but lower than those of wood fiber-filled SMA copolymers [27]. Chrysostomou and Hashemi investigated the dependence of mechanical and fracture properties of SMA copolymer on volume fraction of glass fibers. Their results indicated that the addition of glass fibers enhances tensile and flexural strengths of the SMA matrix [33]. Moreover, Michalik and coworkers claimed a novel method for making foamed cellulosic fiber-SMA copolymer thermoplastic composites. They reported that foamed cellulosic fiber-SMA copolymer thermoplastic composites showed superior tensile and thermal properties to wood fiber and/or wood flour-filled polyolefins composites [36]. Earlier SMA studies were concerned with mechanical and morphological properties and there is lack of information related to rheological properties of SMA copolymer composites in the literature. In this paper, the rheological properties of SMA copolymer composites with different glycerine treated NFC loadings are also systematically studied to investigate the effect of glycerine treated NFC on the rheological properties of the SMA copolymer matrix.

It is hypothesized that the incorporation of glycerine treated NFC (GNFC) into SMA copolymer should lead to an enhancement of composite mechanical properties. However, the interactions of hydrophilic NFC with hydrophilic polymer chains and glycerine are likely to be complex. Glycerine can act as a plasticizer which can reduce the mechanical properties of the composite materials and the addition of glycerine can also decrease the thermal stability of NFC, limiting its reinforcing efficiency in SMA copolymer composites with high processing temperatures. In this paper, the properties and structure of SMA copolymer composites containing GNFC relative to neat SMA are examined.

2. Experimental

2.1. Materials and Gel Preparation or Treatment of NFC

NOVA chemical company (Pittsburgh, PA) kindly supplied SMA copolymer, Dylark 232 (SMA-7), which contained 7% maleic anhydride. The lubricant (Struktol TPW 113), processing aid, was kindly supplied by Struktol Company with a specific gravity of 1.005 and dropping point of 67–77°C. NFC with diameters 20–50 nm and lengths over a micron was produced mechanically from a bleached softwood kraft pulp fiber using refining or homogenization at a 3.5 wt.% solids content. The G5150 glycerine (99% purity) was purchased from Sigma Aldrich Co., USA, and used as received. Gels or glycerine treated cellulose (GNFC) was prepared by mixing aqueous NFC suspensions with glycerine. The premixture containing NFC and glycerine (10/1 by wt. ratio) was stirred vigorously with a high speed rotor stator mixer (Kady Mill) for 30 min to achieve suspension homogeneity. Prior to freeze drying, GNFC suspensions (about 100 mL) were frozen in vials at a temperature of −80°C for 24 h.

2.2. Processing of Composite Materials

The SMA-GNFC compounding was conducted using a Brabender Prep-Mixer® and the temperature was set to 240°C and rotor speed at 60 rpm. NFC was added to the mixer when the polymer melt appeared visually well mixed. The processing temperature and NFC residence times, approximately three minutes, were recognized as a relatively safe temperature range to prevent thermal degradation. The mixing process was completed in 10 min until torque of the mixture stabilized. All materials were injection-molded using a barrel temperature of 240°C, mold temperature of 240°C, and injection pressure of 17 MPa. The details of sample preparation and processing of composite materials can be found in Kiziltas et al. 2014 [37]. The compositions of the SMA-GNFC composites are shown in Table 1.

2.3. Characterization

2.3.1. Mechanical Testing

Tension and flexure tests were conducted according to the American Society of Testing and Materials (ASTM) standard D 638-03 and ASTM D 790-03, Test Method 1, and Procedure A, respectively. The details of these testing methods can be found in Aydemir et al. [38].

2.3.2. Thermogravimetric Analysis (TGA)

TGA measurements were performed using a Mettler Toledo analyzer. Each 10 mg sample was scanned from room temperature to 600°C at a heating rate of 10°C/min under nitrogen flow (20 mL/min) to prevent sample oxidation. Five random samples were chosen for the TGA measurements from the ground test specimens. To eliminate the buoyancy effect, experiments were repeated with an empty sample pan and a baseline was thus obtained.

2.3.3. Rheological Measurements

Rheological properties of the SMA copolymer and GNFC composites were measured on a stress-controlled Bohlin Gemini rheometer (Malvern Instruments, UK) at a temperature of 240°C. Small-amplitude oscillatory shear measurements were performed using a parallel plate geometry with a plate diameter of 25 mm and a plate gap of 1.0 mm to acquire the elastic moduli (), the loss moduli (), and the loss factor (). Steady rate sweep tests were also performed at a low shear rate range to obtain the apparent viscosities () of the SMA copolymer and GNFC composites. To maintain the rheological measurements in the linear viscoelastic region, strain sweeps were performed in advance for each sample, and consequently, a strain of 1% was selected for all frequencies (0.01–100 Hz). The melt flow behavior of the composites was also studied using a conventional melt flow index (MFI) tester at a temperature of 240°C and the details of MFI testing can be found in Aydemir et al. [39].

2.3.4. Scanning Electron Microscopy

Scanning electron microscopy (SEM) was used to observe the dispersion of the GNFC in the SMA copolymer matrix and the quality of the interfaces between the GNFC and SMA copolymer matrix. More detailed information about SEM analysis can be found in Ozen et al. [40].

2.4. Statistical Analysis

The tensile and flexural properties and MFI values were evaluated using a one-way analysis of variance followed by Tukey-Kramer Honestly Significant Differences (HSD) test using a JMP statistical analysis program (JMP) [41].

3. Results and Discussion

3.1. Mechanical Properties

The mechanical properties of the composites are presented in Table 2. It was observed that the neat SMA copolymer exhibits nonlinear elastic behavior with a tensile strength of 45.7 MPa and an elongation at break of 2.3%. The GNFC reinforced composite displayed significantly lower tensile strength (10 wt.% GNFC content, decreased 10.3%) in comparison with the neat SMA copolymer. Two potential explanations are offered for this finding: (1) poor interfacial bonding between GNFC and the SMA copolymer and (2) the existence of the cellulose nanofibrils, as an obstruction, separating the molecular chains of the SMA copolymer, which makes the distance among the molecules larger and the force among the molecular chains of SMA copolymer weaker [42, 43]. Glycerol can decrease mechanical properties by lowering the strength of the composites because of its plasticizing effect [43]. In Table 2, elongation at break of the composites was lower (decreasing values from 2.3 to 1.2% with the addition of 10 wt.% GNFC). The tensile modulus of elasticity (TMOE) of GNFC composites increased noticeably with increased GNFC loading (attaining values from 3.1 to 3.6 GPa with the addition of 10 wt.% GNFC) attributable to the high modulus of GNFC.

In Table 2, the average values of flexural strength of the neat SMA copolymer and GNFC composites are shown. The flexural strength of neat SMA copolymer is 85.5 MPa and incorporation of GNFC significantly reduced flexural strength (10 wt.% GNFC content, decreased 18.9%). The decrease in flexural strength can be explained by the same explanations presented for the observed reduced tensile strength of the composites. As can be seen in Table 2, the flexural modulus of elasticity of composites was higher than that of the neat SMA copolymer. Similar to TMOE, the flexural modulus of elasticity (FMOE) also increased with increasing GNFC loading (reaching values from 3.0 to 3.4 GPa with the addition of 10 wt.% GNFC). It can be concluded that FMOE and TMOE of GNFC-filled composites are affected by GNFC loading and GNFC orientation and less by the SMA copolymer-GNFC interaction [44].

3.2. Thermogravimetric Analysis (TGA)

The TGA and derivative TGA (DTGA) curves for the SMA copolymer and GNFC composites are presented in Figure 2. The SMA copolymer and 2.5 and 5% GNFC composites undergo a single-stage degradation with a peak around 410°C, whereas the 10% GNFC composites show two degradation peaks in the range of 355 to 406°C. The temperature at 5% weight loss () and the temperature at 50% weight loss () for the SMA copolymer and GNFC composites are shown in Figure 3. Both and values for the composites decreased monotonically from the SMA copolymer to 10 wt.% GNFC addition. The results also show that the thermal stability of the composites decreased slightly as the GNFC content increased because of the lower thermal stability of GNFC compared to the SMA copolymer. The SMA copolymer shows slightly better thermal stability in comparison with lubricant modified SMA copolymer. In this study, lubricant was used to improve extrusion processing. It is also known that glycerine starts to evaporate at 200°C and fully evaporates at 300°C [45]. Therefore, the addition of glycerine may decrease thermal decomposition of NFC and this lower thermal stability of GNFC can limit the processing temperature of GNFC in SMA copolymer. The higher processing temperature of SMA resulted in lower mechanical properties that could also be explained by the thermal decomposition of GNFC. A summary of DTGA peak temperature, weight loss (WL) at DTGA peak temperature, and residual weight after 600°C of the composites is given in Table 3.

3.3. Rheological Properties

The decomposition temperature of SMA copolymer and GNFC composites was higher than 250°C as determined by TGA in Figure 2. Hence, the melt rheological measurements for SMA copolymer and GNFC composites were carried out at 240°C. The elastic modulus () for SMA copolymer and GNFC reinforced composites as function of frequency () are shown in Figure 4. It is clear that GNFC has a distinct effect on of the SMA copolymer matrix, even at small loading level (2.5 wt.%). The values of of GNFC reinforced SMA copolymer composites were significantly increased with GNFC content at lower frequencies because of the intrinsic rigidity of GNFC; the elastic modulus of composites is higher than the neat matrix, especially for the highest GNFC loading level, indicating that stress transfers from the matrix to the treated NFC [46].

In Figure 4, the slope of the elastic modulus’ curves decreased with increasing amounts of GNFC and the decrease in the slope can be explained by the microstructural changes with incorporation of GNFC. The GNFC-GNFC, which increase with increasing GNFC content in the polymer matrix, cause the formation of the interconnected or network-like structures of GNFC in the polymer composites. Because elastic modulus data serve as a measure of molecular rigidity, it can be concluded that, with the addition of the GNFC, the samples become more rigid: for comparison, at and 1 Hz, the elastic modulus of SMA copolymer-10% GNFC is up to 55 and 2 times higher than that of the neat SMA copolymer, respectively. It is also evident from Figure 4 that SMA copolymer composites undergo a transition from liquid-like to solid-like viscoelasticity with an increase in GNFC loading in the low frequency region. In contrast, the effect of the nanofibers on the rheological behavior is relatively weak at high frequencies, as shown in Figure 4, suggesting that GNFC has a substantial influence on large-scale polymer chain relaxations but has little effect on short-range motion of polymer chains [47, 48]. Figure 4 also shows the variation of tan_delta (loss modulus/elastic modulus) with frequency for the SMA copolymer composites and the tan_delta decreases with increasing the GFNC loading. This reduction is more noticeable at low (less than 1 Hz) and can be explained by improved elastic properties by introducing GNFC into SMA copolymer matrix and the changes in the microstructure and the formation of network structure in the composites [48, 49]. Figure 5 depicts the variation of melt viscosity as a function of shear rate at 240°C for the SMA copolymer and GNFC composites. It was found that the SMA composites behave as pseudoplastic fluids. The higher the GNFC content of the composite, the higher the shear viscosity and this behavior is attributed to the hindering of the movement of the macromolecular chains of the matrix by the GNFC [50]. The importance of the pseudoplastic behavior is greater as the GFNC content in the composite increases. Thus, the higher the amount of GNFC, the poorer the dispersion of the GNFC in the melt and the higher the viscosity of the filled polymer [46, 50]. For the composite samples with 5 and 10 wt.% GNFC, the plateau at high shear rates was not observed in the applied shear rate range which may indicate that the shear rate is not high enough for the microstructure in these samples to break down. Figure 5 also shows that there are rapid drops on viscosity values at high shear rates. There is lack of information about rheological properties of SMA copolymer matrix in the literature. Further investigation is needed to fully understand rheological properties of GNFC reinforced SMA copolymer composites.

Table 2 also shows the MFI values for the SMA copolymer and GNFC treated composites. The incorporation of treated NFC reduced the flowability of SMA copolymer, which can increase the elastic modulus of a composite or the viscosity of a fluid suspension [51]. The MFI also decreased with increasing treated GNFC loading because of the incorporation of rigid GNFC weight to the SMA copolymer matrices restricting the composites free mobility and increasing the material viscosity [51]. The MFI value of the neat SMA copolymer was 5.1 g/10 min and decreased to 0.3 g/10 min (10 wt.% GNFC content, decreased 95.1%). Similar results were also reported by Teng et al. for multiwalled carbon nanotube/polypropylene composites [52]. SMA copolymer-GNFC formulations did not present significant problems during the injection molding process; however, some small adjustments of the processing conditions may be necessary to make products with a GNFC content of more than 20 wt.%, especially increasing the injection pressure [53]. Adding lubricant to the matrix made a slight decrease in elastic modulus at all frequencies reflecting that the stiffness of the polymer decreased by adding a low molecular weight material. Similarly, the addition of lubricant decreased melt viscosity of composites at all shear rates and increased flowability of the SMA copolymer. In this study, lubricant was used only as an additive to improve processing conditions. The results of TMOE and FMOE are in accordance with the rheological data. Because of the intrinsic rigidity of GNFC, the TMOE and FMOE are higher than SMA copolymer, especially for the highest GNFC content (10 wt.%). Increasing the modulus of elasticity of composites compared with the matrix polymer can also be associated with the restrictions of macromolecules mobility and deformability imposed by the presence of GNFC. The presence of GNFC perturbs normal polymer flow and restricts the mobility of chain segments. Thus, the higher the amount of GNFC, the lower the MFI or the higher the viscosity of the filled polymer [46].

3.4. Morphological Properties

SEM micrographs of the fractured surfaces of the SMA copolymer and GNFC composites are shown in Figure 6. The aim was to investigate if any GNFC aggregates were visible on the impact fracture surfaces.

(a)

(b)

(c)

(d)

As expected, because of the presence of polar groups, it is likely that SMA copolymer chains adhere to GNFC via esterification reactions between NFC and maleic anhydride on the SMA and the attraction between GNFC and SMA copolymer may also make dispersion of the GNFC within the matrix more effective. However, the image shows areas which are attributed to fiber bundles in all samples (Figures 6(b)–6(d)) indicating that mixing was not complete at the level of individual fibers. It appears that all the images showed evidence of aggregation of GNFC fibers and generally poor adhesion between the GNFC surface and the SMA copolymer matrix. In other words, glycerine was not efficient to disperse the NFC within the SMA copolymer matrix. Similar results were also reported by Simonsen et al. for wood fiber-reinforced SMA copolymer composites [28]. To gain a better understanding of interface between SMA copolymer and GNFC as well as the need for addition of coupling agents or surface modification of NFC surface to improve properties, techniques such as nanoindentation and microbond testing methods could be employed [54].

4. Conclusions

Mechanical properties, thermal stability, melt rheology, and morphological behavior of SMA copolymer and composites with various GNFC loadings were studied in this work. The SMA composites reinforced with GNFC displayed higher tensile and flexural modulus of elasticity; however, the tensile and flexural strength and elongation at break of the composites decreased compared to the neat SMA copolymer matrix. The thermal stability of the composites decreased slightly as GNFC content increased because of the lower thermal stability of GNFC compared to the SMA copolymer. The decreased noticeably with increasing the GFNC loading at lower frequencies. It was found that the incorporation of GNFC in a SMA copolymer matrix results in higher elastic modulus and shear viscosities compared to those of neat SMA copolymer, especially in the low frequency region. With an increase in GNFC loading, the composites experienced a transition from liquid-like to solid-like viscoelasticity and strong shear thinning behavior was observed in the composites. SEM micrographs showed that glycerine was not efficient to disperse the NFC within the SMA copolymer matrix. The results of TMOE and FMOE are in accordance with the rheological data for SMA/GNFC composites.

Disclosure

This is the 3468th paper of the Maine Agricultural and Forest Experiment Station.

Competing Interests

The authors declare that they have no competing interests regarding the publication of this paper.

Acknowledgments

The authors would like to acknowledge the contributions of Alex Nash and Chris West whose hard work made this paper possible. The authors would also like to thank Maine Agricultural and Forest Experiment Station Project ME09615-08MS and the Wood Utilization Research Hatch 2007-2008 Project.

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Copyright © 2016 Esra Erbas Kiziltas 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.

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