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versão impressa ISSN 0104-1428versão On-line ISSN 1678-5169

Polímeros vol.27 no.2 São Carlos abr./jun. 2017  Epub 29-Jun-2017 

Original Article

Influence of microcrystalline cellulose in thermoplastic starch/polyester blown films

Mônica Oliveira Reis1  * 

Juliana Bonametti Olivato1 

Juliano Zanela1 

Fábio Yamashita1 

Maria Victoria Eiras Grossmann1 

1Departamento de Ciência e Tecnologia de Alimentos, Centro de Ciências Agrárias, Universidade Estadual de Londrina – UEL, Londrina, PR, Brazil


This work investigated the influence of microcrystalline cellulose (MCC) in thermoplastic starch/poly (butylene adipate-co-terephthalate) films produced by blown extrusion, using different MCC contents (4, 7 and 10 g.100 g-1). The films were characterised for their mechanical, structural and barrier properties. Increasing fibres concentration reduced the tensile strength (6.9 to 4.6 MPa), the elongation at break (568 to 147%) and weight loss in water (12.8 to 11.1%) of the films. The rigidity of the films increased from 19.8 MPa (without MCC) to 79.2 MPa in the samples with 10 g.100 g-1 of MCC. SEM images showed the occurrence of some agglomerates in this sample. The water vapour permeability of the films was not affected by the presence of MCC. The production of starch/PBAT/MCC films by blown extrusion was successful; however some adjustments are necessary to improve the dispersion of the particles at the polymeric matrix.

Keywords:  extrusion; cellulosic fibres; biodegradable films; polyester

1. Introduction

In the last years, there was an increase in the researches focused in the development of biodegradable materials, due the growing accumulation of the conventional plastic materials, which are hard to be decomposed. Biodegradable polymeric packaging derived from cellulose, proteins and starch[1-4] have gained a great impulse because they allow the reduction of the use of materials derived from petroleum.

The starch is the most used agro-resource to produce biodegradable films due their biodegradability, low cost and wide availability[5]. According to Teixeira et al.[6] and Tang and Alavi[7], the native starch is not a real thermoplastic, but however, in the presence of a plasticiser, high temperatures and shear, it melts and flows, forming a material called thermoplastic starch (TPS).

The TPS, however, when used as a single polymer to produce biodegradable materials presents some restrictions that limit their use, including their hydrophilic character with high water vapour permeability and deficient mechanical properties, which are dependent of the relative humidity of the environment[7,8]. To overcome these drawbacks, TPS is frequently blended with biodegradable synthetic polymers[9-12], as poly (butylene adipate-co-terephthalate) (PBAT), an aliphatic-aromatic copolyester that combines desirable performance properties with biodegradability[13,14].

The inclusion of cellulosic fibres in biodegradable matrices has been the focus of numerous studies, with the aim to improve the mechanical and barrier properties of the materials[4,15-19]. Müller et al.[16] studied the effect of cellulose fibres (0.10, 0.30 and 0.50 g fibres/g starch) in the mechanical and physicochemical properties of starch-based films produced by casting. Their results showed that more resistant (8.39 MPa) and rigid (Young’s modulus of 217 MPa) films were produced with the addition of the fibres, but with a lower elongation at break (22%), when compared to the material containing no fibres (1.59 MPa, 21 MPa and 83%, respectively).

Microcrystalline cellulose (MCC) presents as an alternative to the vegetal fibres used in biodegradable films. The MCC is a purified and insoluble cellulose produced by partial acid hydrolysis of the wood cellulose. The hydrolysis occurs in the amorphous areas of the polymeric chain, followed by the separation of the released microcrystals, which corresponds to a highly crystalline cellulose[20-22]. The use of MCC in different biodegradable polymeric materials has been studied[18,23-25].

Sun et al.[18] developed poly (vinyl alcohol) (PVA)/MCC composites by injection moulding. The Young’s modulus of the plasticised PVA increased from 204.8 MPa to 731.2 MPa, with the addition of 20% of MCC. The tensile strength increased from 37.8 MPa (PVA/MCC-0) to 46.5 MPa (PVA/MCC-20), which confirmed the strong interfacial interaction and good dispersion between MCC and PVA.

While the injection moulding and the production of films by casting are less exigent process in relation to the structuration of the polymeric matrix and their interaction with the fillers, this does not occur with the blown film production. In this case, the requirements concerning the compatibility, dispersion, fibre/matrix adherence and the capacity of the fibres to transmit the tension along the material are greater, and the content of the added fibres has an important effect. To the best of our knowledge, our previous work[24] is the only study about blown films with MCC in blends of thermoplastic starch/polyester. The aim of this work was to produce biodegradable films based on thermoplastic starch/PBAT/MCC by blown extrusion and evaluate the influence of higher concentrations of MCC in their properties.

2. Materials and Methods

2.1 Materials

The blown films were produced with native cassava starch (17% wt amylose, 13 g.100 g-1 moisture), (Indemil, Guaíra, Brazil), poly (butylene adipate-co-terephthalate) (PBAT), supplied by BASF (Ludwigshafen, Germany) under the commercial name Ecoflex®, microcrystalline cellulose (MCC) M 101 Avicel®, supplied by Hexus Food Ingredients (Portão, Brazil), with a particle size of 10-15 µm and aspect ratio around 1, and glycerol, supplied by Dinâmica (Diadema, Brazil).

2.2 Methods

2.2.1 Blown films production

The materials were processing using a laboratory co-rotating twin-screw extruder (BGM, model D20, Taboão da Serra, Brazil) with screw diameter (D) of 20 mm and length/diameter (L/D) ratio of 34. The TPS/MCC/PBAT pellets were produced in two steps. In the first step, TPS/MCC pellets were produced by dispersing the MCC in distilled water for 3 min with the aid of an Ultra Turrax homogeniser (MARCONI, model MA 102, Piracicaba, Brazil), which was then added to the starch and glycerol and manually mixed before extrusion. The mixture was pelletised using a temperature profile of 90/120/120/120/120 °C, screw speed of 100 rpm, and a matrix with five 2-mm holes. The venting ports were maintained closed to avoid water evaporation. In the second step, the produced TPS/MCC pellets were processed with the PBAT with the same process conditions to produce TPS/MCC/PBAT pellets.

To obtain the blown films, TPS/MCC/PBAT pellets were fed to a single-screw extruder (BGM, model EL-25, Taboão da Serra, Brazil) composed of a 25-mm diameter screw with an L/D ratio of 30. The barrel temperature profile used was 90/120/120/130 °C for the four zones and 130 °C for the 50-mm film-blowing die and screw speed of 40 rpm. The process conditions (screw speed and temperature profiles) were defined according to Reis et al.[24]. The pellets and the blown films were produced in duplicate.

The proportion of the components in each sample is presented in Table 1. The control sample (MCC0), without MCC, contained 56 g.100 g-1 of TPS (27 g glycerol/100 g starch) and 44 g.100 g-1 of PBAT. The concentrations of MCC (expressed as % w/w, TPS/PBAT basis) were selected in preliminary tests. The inclusion of water (2.4 mL/g MCC) was necessary to improve the dispersion of MCC and the used content was the minimum required to promote this dispersion. Before the mixture with starch and glycerol, none free water was visible being the MCC hydrated and swollen.

Table 1 Concentration of the components in the formulations. 

Samples Components
(g.100 g-1)
(g.100 g-1)
(g.100 g-1 TPS/PBAT)
MCC0 56 44 0.0 0.0
MCC4 56 44 4.0 9.6
MCC7 56 44 7.0 16.8
MCC10 56 44 10.0 24.0

aContaining 27g glycerol/100g starch;

bCalculated as 2.4 mL/g MCC;

The numbers in the codes of the samples represent the level of added MCC.

The film thickness was controlled by the roll speed and the air-flow rate. The average thickness of the films was of 164 ± 17 to 195 ± 6 µm.

2.2.2 Mechanical properties

A texture analyser model TA.XT2i (Stable Micro Systems, Goldaming, England) fitted with a 50 kg load cell was used to conduct the tensile tests of the films. Tensile tests were based on ASTM method D-882-02[26]. Ten samples from each formulation were cut along the longitudinal direction (50 mm in length and 20 mm in width) and fit in the tensile grips. The crosshead speed was set at 50 mm.min-1 and the initial distance between the grips was 30 mm. Before testing, the samples were conditioned at 23 ± 2 °C and 53 ± 2% relative humidity (RH) (saturated solution of Mg(NO3)2) for 48 h. The tensile strength (MPa), elongation at break (%) and Young’s modulus (MPa) were determined.

2.2.3 Density

To determine the films density, three samples from each formulation with 20 mm × 20 mm were kept in a desiccator with anhydrous calcium chloride (CaCl2/0% RH) for 2 weeks and then, were weighed according to the procedure described by Müller et al.[27].

2.2.4 Water Vapour Permeability (WVP)

The tests were conducted using the American Society for Testing and Materials ASTM E-96-00[28] standard, with some modifications. Before the analysis, the samples were stored at 25 °C and 53% RH for 48 h. Each film sample was fixed in the circular opening of a permeation cell with a 60 mm internal diameter, and silicone grease was applied to ensure that humidity migration occurred only through the film. The interior of the cell was filled with a magnesium chloride solution (MgCl2/32.8% RH) and the device was stored at 25 °C in a desiccator to maintain a 42% RH gradient across the film. A saturated sodium chloride solution (NaCl) was used in the desiccator to provide 75.3% RH. The samples were weighed every 3 h during the 72 h of testing time. Changes in the weight of the cell or mass gain (m) were plotted as a function of time (t). The slope of the line was calculated by linear regression (R2> 0.98), and the water vapour permeation ratio (WVPR) was obtained with Equation 1:

WVPR=(mt). (1A) (1)

where m/t is the angular coefficient of the curve and A is the sample permeation area.

The WVP (g.s-1.m-1.Pa-1) was calculated using Equation 2: (2)

where st is the mean sample thickness (m), sp is the water vapour saturation pressure at the assay temperature (Pa), RH1 is the relative humidity of the desiccator and RH2 is the relative humidity in the interior of the permeation cell. These tests were conducted in duplicate.

2.2.5 Weight Loss in Water (WLW)

The weight loss in water was determined according to Olivato et al.[29]. Samples were previously dried for three days in a desiccator containing anhydrous CaCl2 (0% RH). After weighing, the films were immersed in distilled water, maintaining a proportion of 30:1 (water/sample), for 48 h at 25 °C. The samples were then removed and dried at 105 °C for 4 h, and the weight of the conditioned specimen after treatment was used to determine the % weight loss in water. These tests were conducted in triplicate.

2.2.6 Scanning Electron Microscopy (SEM)

A scanning electron microscope FEI, model Quanta 200 (Hillsboro, USA) was used to observe the fractured surface of the blown film samples. The samples were submerged in liquid nitrogen and then broken (cryogenic fracture). Before coating with a gold layer, the samples were stored at 25 °C in a desiccator with silica gel (≈0% RH) for 3 days. The coating was produced with a Sputter Coater (BAL-TEC SCD 050). Images were taken of the fractured surface and surface of films at a magnification of 1600x and 800x, respectively.

2.2.7 Statistical analysis

The data were analysed using STATISTICA 8.0 software (Statsoft, Oklahoma), with analysis of variance (ANOVA) and Tukey’s test at a 5% significance level.

3. Results and Discussions

3.1 Mechanical properties and density

The mechanical properties and density of the films are expressed at Table 2. With a separate behaviour, the sample with greater proportions of MCC (MCC10) presented the lower tensile strength (4.6 ± 0.1 MPa) and elongation at break (147 ± 34%) and higher Young’s modulus (79.2 ± 13.6 MPa). Comparing the samples without MCC (MCC0) and MCC4, no significant differences between these samples were observed, for all the analysed parameters.

Table 2 Mechanical properties and density of the films. 

Formulations* Properties
Tensile strength
Elongation at break
Young’s modulus
MCC0 6.9 ± 0.3a 568 ± 53a 19.8 ± 0.6b 1.03 ± 0.01ª
MCC4 6.5 ± 0.1a 579 ± 27a 23.3 ± 0.9b 1.04 ± 0.02ª
MCC7 5.7 ± 0.6b 448 ± 86b 25.3 ± 1.4b 0.96 ± 0.06ª
MCC10 4.6 ± 0.1c 147 ± 34c 79.2 ± 13.6a 0.98 ± 0.05a

*Numbers in the formulation codes are concerning MCC content (g.100g-1 TPS/PBAT);

Results express in (mean ± standard deviation); Different letters in the same column indicate significant differences (p≤0.05) according to the Tukey’s test.

The increase of MCC content from 4 to 10% wt reduces the tensile strength and elongation at break of the films, from 6.5 ± 0.1 to 4.6 ± 0.1 MPa and from 579 ± 27 to 147 ± 34%, respectively. This fact occurred as a result of the formation of cellulose agglomerates when higher concentration of this component was used, which reduced the reinforcing efficiency. The SEM images (Figure 1) confirm these results.

Figure 1 SEM images of the fractures (1) (1600x magnification) and surfaces (2) (800x magnification) of the samples: (a) MCC0; (b) MCC4; (c) MCC7; (d) MCC10. 

The rigidity of the material, represented for the Young’s modulus, increased from 19.8 MPa (MCC0) for 79.2 MPa (MCC10). This effect can be related to the formation of a network structure above the percolation threshold produced by the cellulose fibres by means of hydrogen bond interactions[18,30].

According to Ibrahim et al.[31], the Young’s modulus of the polymers may increase by the reinforcement effect of the cellulose fibres while the tensile strength may not be improved, or even be reduced, due the flocculation of the cellulose fibres, which is in accordance with the results of the present work.

Similar effects were reported by Ma et al.[32] for thermoplastic pea starch composites containing 12% wt of MCC. Mathew et al.[21] analysed the effect of MCC in poly (lactic acid) (PLA) matrix and observed that greater concentrations of MCC in the samples (from 10 to 25% wt) reduced the tensile strength and elongation at break and increased the Young’s modulus.

Considering the density of the films, no significant differences were recorded between the formulations. Despite the lower density of the fibres, the concentrations used in this work ranged from 4-10% wt and were not sufficient to affect the density of the materials. A possible cause of this is related to the absence of compaction of the polymeric chains with the inclusion of MCC (as can be observed in the Figure 1).

3.2 Water Vapour Permeability and Weight Loss in Water

Opposite to the effects of MCC in the mechanical properties, the addition of these fibres did not influence the water vapour permeability (WVP) of the films, even at highest concentrations, as showed at Figure 2.

Figure 2 Water Vapour Permeability (WVP) and Weight Loss in Water (WLW) of the films. 

The presence of high concentrations of the fibres probably introduces a tortuous path, which makes more difficult the water diffusion through the polymeric matrix[33]. According to Dogan and McHugh[34], with the incorporation of cellulose fibres a reduction of the coefficient of water diffusion is expected since that the diffusion process into the matrix depends on the available pathways for the water molecules. However, a slight reduction on the diffusion coefficient was not sufficient to change the water vapour permeability of the films, as evidenced in the results of the present work.

On the other hand, Kunanopparat et al.[35] reported that the addition of hemp and wood fibres in wheat gluten/glycerol composites reduced the water sensibility of the materials. Also Ma et al.[32] found similar results for thermoplastic pea starch composites containing MCC. The various processing techniques (extrusion, compression moulding, and casting), polymeric matrices, type and concentrations of the fibres can explain the different effects of the cellulose fibres in the water vapour permeability of the composites.

The Figure 2 presents the % of weight loss in water (WLW) of the samples. All the samples presented significant distinct results. While the formulation MCC0, without microcrystalline cellulose, exhibited a weight loss in water of 12.75 ± 0.09%, the inclusion of MCC in concentrations of 7 and 10% wt reduced the WLW of the films. This reduction was dependent of the concentration of the MCC at the formulations, with greatest values for WLW observed for the MCC10 (containing 10% wt of MCC). This behaviour could be associated to the less hydrophilic character of the cellulose, when compared to the starch[36,37]. The molecules of cellulose, due their linear structure, are able to perform intra and intermolecular hydrogen bonds, resulting in the formation of a crystalline structure which is totally insoluble in water[22,38]. In the samples containing greater proportions of MCC, the concentration of starch is lower, i.e., there are a substitution of a more soluble molecule (starch) for a less soluble one (cellulose), which results in a reduction of WLW of the samples.

On the other hand, the MCC4 sample showed an opposite behaviour, i.e., the weight loss in water (13.18 ± 0.15%) was greater than the sample MCC0. A possible reason for this could be related to the easier removal of the MCC from the matrix structure, due to the starch solubilisation. Thus, even being insoluble, MCC stayed dispersed at the water. This explanation is valid only for low MCC contents (≤ 5%), as reported by Reis et al.[24].

3.3 Scanning Electron Microscopy (SEM)

The fracture and surface SEM images are presented at Figure 1, with magnification of 1600x and 800x, respectively. Under high temperature, shear and in the presence of a plasticiser, the starch granules were completely disrupted and no residual granules could be observed at SEM images. It is possible to notice a uniform dispersion of MCC in the starch/PBAT polymeric matrix, in the films with lower MCC concentration (Figure 1 b.2 and c.2), however, the inclusion of MCC changed the films structure.

Greater concentrations of MCC added to the films led to the occurrence of micropores, as evidenced at SEM images (Figure 1 c.1 and d.1). This effect was more pronounced in the films containing 7 and 10% wt of MCC (MCC7 and MCC10). Oriented beams were observed at surface images (Figure 1 a.2, b.2 and c.2), corresponding to the MCC0, MCC4 and MCC7, respectively. In a different way, the beams disappeared at surface image of the sample MCC10 (Figure 1 d.2), which, on the other hand, presented some aggregates.

In the Figure 1 c.1 and d.1 images, some empty spaces were identified in the starch/PBAT matrix, which indicates weak or none interfacial adhesion between the matrix and MCC, when it was added in higher concentrations. A similar result was demonstrated by Mathew et al.[21], studying PLA/MCC films, indicating no interfacial adhesion of MCC in the PLA matrix. Santos and Tavares[39] also developed PLA/MCC films and found in the SEM images that the dispersion of the MCC is relatively poor, due the self-aggregation of their molecules and the hydrophobic nature of the polymeric matrix. In the present work, the polymeric matrix contains thermoplastic starch (hydrophilic) and also PBAT, with hydrophobic character, which contributed to a low interfacial adhesion of the MCC in this matrix.

4. Conclusion

The addition of MCC in starch/PBAT films was successful, considering the low thickness characteristic of the materials produced by blown extrusion, which makes more difficult the processability of the films, since the MCC particles represents more fragile points in the matrix structure.

Using greater proportions of MCC, a significant increase of the rigidity of starch/PBAT blown films was observed, but nevertheless, no contribution can be noticed in the tensile strength.

The occurrence of micropores, identified at SEM images, mostly at the samples with higher MCC content, did not affect the water vapour permeability of the films. The SEM images also showed that MCC tended to form some agglomerates when used at higher concentrations (10% wt).

The blown extrusion process could have influenced the results of the films, considering that most of the materials studied and produced with MCC frequently use other techniques, as casting or compression moulding, to obtain biodegradable sheets. So, to make viable the use of MCC in the blown films, some adjustments in the process must be focused in future studies, such as a treatment in the MCC particles to improve their dispersion/compatibility when used at content higher than 5% wt and, consequently, improve the tensile strength and water vapour permeability of the biodegradable films.

5. Acknowledgements

The authors thank CAPES, CNPq and Fundação Araucária for financial and fellowship support.

6. References

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Received: August 14, 2015; Revised: May 31, 2016; Accepted: June 29, 2016

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