Modification of Functional Properties of Whey Protein Isolate Nanocomposite Films and Coatings with Nanoclays

Müller, Kerstin; Jesdinszki, Marius; Schmid, Markus

doi:https://doi.org/10.1155/2017/6039192

Journal of Nanomaterials

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Abstract Introduction Methods Results and Discussion Conclusions Conflicts of Interest Acknowledgments References Copyright Related Articles

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Nanomaterials from Natural Products for Industrial Applications

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Research Article | Open Access

Volume 2017 | Article ID 6039192 | https://doi.org/10.1155/2017/6039192

Modification of Functional Properties of Whey Protein Isolate Nanocomposite Films and Coatings with Nanoclays

Kerstin Müller,¹Marius Jesdinszki,¹and Markus Schmid^1,2

Academic Editor: Vijay K. Thakur

Received25 Feb 2017

Accepted04 May 2017

Published31 May 2017

Abstract

Whey protein based films have received considerable attention to be used for environment friendly packaging applications. However, such biopolymers are prevented for use in commercial packaging due to their limited mechanical and barrier performance. The addition of nanofillers is a common method to overcome those drawbacks of biopolymers. Whey protein isolate (WPI) based nanocomposite cast films and coatings were produced using montmorillonite and vermiculite clay as nanofiller in different concentrations. Uniform distribution of filler within the polymeric matrix was confirmed by scanning electron microscopy. Mechanical properties such as tensile strength as well as Young’s modulus were increased after increasing the filler content, while elongation at break values decreased. All samples showed weak barrier potential against water vapor. Nanoclay incorporation, however, reduced water vapor transmission rates by approximately 50%. The oxygen barrier performance was improved for all nanocomposites. Results also indicated proportionality with the filler ratio according to applied models. The highest barrier improvement factors (BIF) were greater than five for the cast films and even greater than sixteen for the coatings. Developed WPI-based composites depicted nanoenhanced material properties representing a promising alternative to fossil-based packaging films.

1. Introduction

The ability of globular proteins such as whey proteins to form self-supporting films showed great potential for edible coatings or numerous packaging applications and have been widely studied [1–6]. However, applications are limited since without any modification, whey protein films only display a low moisture barrier as well as relatively poor mechanical properties compared to commercial and mainly fossil-based packaging materials [7–10]. Recently, polymer nanocomposites have received considerable attention in research and development [11–13] and are already widely used in areas such as automotive or packaging [12, 14]. Just like conventional microcomposites such as glass fiber enforced polymers, material stiffness can be increased by filler addition [15]. However, the nanosize scale brings several advantages such as a reinforcement in all directions, a less filler content needed (wt%), and a better surface finish [13]. In terms of barrier performance, the introduction of nanoclays or particles significantly influences the permeation behavior of gases by extending diffusion path and time [13]. This effect can be specifically ascribed to exfoliated clay morphologies [16] based on the good platelets distribution within the matrix. Compared to conventional microcomposites, meaning composites with filler particles of approximately 60% vol in a microscale range, nanocomposites already show enhanced properties at low filler loads (<2% vol) [16]. In terms of nanocoatings, even super gas barrier coatings that match performance of metallized films have been developed [17]. Thus, the usage of nanometre-sized filler particles is also becoming a promising option to overcome the limited mechanical and barrier properties of biopolymer based films and coatings [7, 18]. Likewise, whey protein based nanocomposites have been a field of interest in the last decade [7, 11, 19–26] confirming this topic is of scientific and industrial relevance. In case of whey protein based films, present oxygen barrier properties could even potentially be further improved with nanoparticles. The main goal of this study was the development of exfoliated clay–whey protein nanocomposites with enhanced barrier and mechanical properties to maximize material suitability for packaging applications in industrial applications. The related scientific issue was the effect of the nanofillers on the processability and functional properties of nanomodified whey protein isolate based cast films and coatings with emphasis on packaging related properties.

2. Material and Methods

2.1. Materials

Whey protein isolate (WPI) was obtained from Davisco Foods International Inc, USA. Glycerol was purchased by Chemsolute, Th. Geyer GmbH & Co KG, Germany. Deionized water was supplied by Fraunhofer IVV. The aqueous montmorillonite nanodispersions were provided by ITENE, Spain using Cloisite Na⁺ and Nanofil 116 (both BYK Additives & Instruments, Wesel, Germany) with a clay concentration of 5% (w/w) for both dispersions. The Sunbar Vermiculite SX009 aqueous nanodispersion with a clay concentration of 7.6% (w/w) was obtained from SunChemical Ltd., UK. The chemically treated polyethylene terephthalate (PET) substrate Sarafil Polyplex Polyester Film with a thickness of 23 μm was supplied by Polyplex, Thailand.

2.2. Preparation of Film Forming Suspensions

Following the standard method by McHugh et al. [27] and Schmid et al. [4] a whey protein standard solution (WPSS) was produced. Therefore, 10% WPI (w/w) and deionized water are homogenized at room temperature in an electric stirrer (Thermomix 31-1, Vorwerk Deutschland Stiftung & Co. KG, Wuppertal, Germany) for 30 minutes at 200 rpm. Afterwards the solution is heated for 30 minutes at 90°C with continuous stirring (200 rpm). Thus, denaturation of the proteins was fully completed [28]. For cooling and degassing the solution is placed in an ultrasonic bath for 15 min (DT 514H, Ultrasonic peak output: 860 W, Bandelin electronic GmbH & Co. KG, Berlin, Germany) at 23°C and 37 kHz·s. After cooling down, glycerol (Glycerol, Merck KGaA, Darmstadt, Germany) is added to solution and stirred for further 30 minutes with the Thermomix at 200 rpm. Finally, the solution is placed in an ultrasonic bath again for degassing for further 15 minutes.

For the nanosuspensions, WPSS and the aqueous nanodispersions were mixed using a magnetic stirrer (Ikamag RCT, IKA-Labortechnik, Staufen, Germany) at 1200 rpm for at least one hour in different ratios to achieve the desired nanofiller ratios of 1%, 3%, 6%, and 9% (w/w) with reference to the protein content. To prevent agglomeration, it is highly important to gradually add the nanodispersion under continuous stirring. Additionally, the nanodispersions were redispersed for 30 minutes at 500 rpm electric stirrer (Thermomix 31-1, Vorwerk Deutschland Stiftung & Co. KG, Wuppertal, Germany) at room temperature and ultrasound treated with a sonotrode (Labsonic 1510, B. Braun, Melsungen, Germany) at 400 W for 45 minutes before mixing with WPSS.

2.3. Preparation of WPI/Clay Composite Cast Films and Coatings

All suspensions were coated on a chemically treated 23 μm PET film A4 sheets using the coating unit CUF 5 (Sumet Messtechnik, Denklingen, Germany) with 40 mm/s speed of application, a drying temperature of 105°C and a drying time of 5.5 minutes. For the target dry film thickness of 10 μm, a wired rod with 100 μm wet film thickness was used. Dried coatings were stored at ambient conditions of 23°C and 50% RH. Nanocomposite cast films were produced by solvent casting. Film forming suspensions were casted into square shaped Petri dishes with a target film thickness of 200 μm. Cast films were dried at ambient conditions of 23°C and 50% RH until they reach constant mass (approx. 8 days). All samples were stored at least 3 weeks prior to characterization in order to allow potential postcrosslinking to be completed [29].

2.4. Composite Film and Coating Characterization

2.4.1. Film Thickness

Thickness measurements were performed with a precision thickness gauge FT3 with 0.1 μm resolution (Rhopoint Instruments, Beyhill on Sea, United Kingdom) at five random positions around the film testing area and averaged for determination. For barrier and mechanical measurements, thicknesses were determined for each sample.

2.4.2. Mechanical Properties

Young’s modulus (), tensile strength (TS), and elongation at break (EB) of the cast films were tested using a tensile testing machine Z005 (Allround Line) of the Zwick GmbH & Co.KG, Ulm, Germany, at 23°C and 50% RH according to the DIN EN ISO 527-1. Tensile tests were performed with five strips of 15 mm width with a clamping length of 50 mm. The test speed was 50 mm/min with a load shut-off at 95% and a preload of 0.3 N.

2.4.3. Barrier Properties

Water Vapor Transmission Rate. The water vapor transmission rate was measured with a gravimetric method according to DIN 53122-1. The initial weight was measured by an analytical balance Mettler H315 of the Mettler-Toledo GmbH and the cups were then stored in a climate chamber of the Binder GmbH at 23°C and 85% RH. The samples were weighed four times in 48 hours until the weight gain stagnated. For each specimen, four replicates were tested. The water vapor transmission rate was calculated using the following formula [30]:where is time between two weight measurements of which is calculated [h], is weight difference of two successive weight measurements [g], and is sample area [cm²].

Oxygen Permeability. The oxygen permeability (OP) was measured with the oxygen-specific carrier gas method according to DIN 53380-3. The measurements were performed with a Mocon Ox-Tran Twin Oxygen Permeation Measuring Machine at a temperature of 23°C and 50% RH. The measurement stopped when a value was constant for at least ten hours. Two replicates of all coating and cast film specimens were determined.

For a better comparison of different polymers the permeability can be standardized to the –value relating to a thickness of 100 μm [31]:To adapt permeability properties of a packaging material, multilayers can be used instead of raising the thickness of a monolayer. The total permeation of a multilayer system can be calculated as follows:

2.4.4. Scanning Electron Microscopy (SEM)

The scanning electron microscopy was performed with an ISI scanning electron microscope ABT 55 (ISI Akashi Beam Technology Corporation, Tokyo, Japan). Images were taken at 10 kV at different magnification and evaluated with a digital image scanning system DISS 5 by Point electronic GmbH, Halle (Saale), Germany. The measurements were performed in a high vacuum environment of bar at room temperature. For sample preparation, cryofractures of selected samples were performed. The cross sections of the samples were fixed to the specimen holder with carbon tape and sputtered with a metal coating for improved conductivity.

2.5. Statistical Analysis

Statistical evaluations were performed using the computer programme Visual-XSel 12.0 Multivar (CRGRAPH, Munich, Germany). All measured data were tested on normal distribution. Depending on sample size, Kolmogorov-Smirnov test (sample size 3 or 4) or Anderson-Darling normality test (sample size ≥ 5) was used with a significance value α at 0.05. The Hampel test for outliers was used to detect and eliminate outliers of nonnormal distributed data with a significance value α at 0.05. Condition for elimination is that all other values are part of the same population, proved by normality tests. Comparison of sample sets was conducted with a multi--test using a significance value of 0.05.

2.6. Descriptive Statistics

2.6.1. Curve Fitting of the Modulus

According to literature, the models widely applied to describe the Young’s moduli of composites filled with various types of filler are the Halpin-Tsai model and modified equations from it [12, 32]. According to this model, longitudinal elastic modulus can be expressed as follows:where is Young’s modulus of the composite [MPa], is Young’s modulus of the matrix [MPa], and is volume fraction of the filler with the constants and given bywhere is Young’s modulus of the filler [MPa] and is Young’s modulus of the matrix [MPa]where is the aspect ratio α of the reinforcing filler [12].

Since this model overestimated the experimental data, a Modulus Correction Factor (MCF) was introduced, adapting an approach by Wu and others [33]. Equation (7) describes the modified model used for calculations. The parameter MCF was determined for each type of used clay by minimizing the residual sum of squares RSS with Excel Solver (Microsoft Office Professional Plus, Version 14.0.7166.5000).

2.6.2. Predicting Barrier Properties

Table 1 shows different models that have been suggested to predict barrier properties of nanocomposites. The used models differ according to the particle geometry and calculations are based on aspect ratio α and the filler degree . Since only single particles are considered, those models assume fully exfoliated clays.

Considering the relatively simple model by Nielsen and making realistic assumptions with an aspect ratio of and a volume fraction of for nanocomposites, a barrier improvement of a factor of 20 is generally possible and was also already achieved in lab-scale experiments [39].

However, interactions between filler and matrix, state of exfoliation, and particle orientation also have to be taken into account. Therefore further important factors for the diffusion path extension are the state of dispersion, eventual aggregation or flocculation, and the orientation within the matrix [40]. The highest possible aspect ratio can be achieved by individual nanolayers requiring complete exfoliation [12]. Although best enhancement of barrier properties can be achieved with aligned platelets, the processing of exfoliated nanoclays mainly shows misaligned structures as well as nonexfoliated areas within the composites [12]. For those reasons, practical permeability data given by suppliers provide much lower barrier improvements compared to the theoretical values, normally with a factor of two [41].

3. Results and Discussion

3.1. Microstructure

The cross-sectional SEM images of selected WPI nanocomposite cast films and coatings can be seen in Figure 1. Nanoparticles are given in lighter color, while dark spots display small holes which are the traces of nanoparticles that remained on the opposite side of the cast films during hand fractioning. All composites show a homogeneous distribution of the nanofiller with maintaining WPI matrix structure. Even at the high nanoparticles concentrations only little agglomeration could be detected. The uniform distribution and dispersion of Cloisite Na⁺ in the WPI matrix contributed to the mechanical and barrier improvement of the nanocomposites. The poor improvements detected at the Nanofil composites could be due to the occurrence of comparably bigger agglomerates marked exemplary in Figure 1(b). Depending on the sample spot chosen for determination, distribution can of course differ.

(a)

(b)

(c)

(d)

3.2. Mechanical Properties

Measured data for mechanical properties of all casted nanocomposites can be seen in Table 2. All nanofillers used showed significant enhancement of Young’s modulus and tensile strength at high nanoparticles concentrations. The increase of material stiffness and strength by the incorporation of nanofillers into whey protein based matrices was also confirmed by several studies [7, 21, 24–26]. Similar to the modulus, the material reinforcement and therewith higher strength levels depend on composite morphology, since better exfoliation leads to higher improvements. However, tensile strength as well as elongation at break are nonlinear mechanical properties and decrease beyond a critical filler ratio [12]. Here, the transfer of load between filler and matrix is decisive and depends on their compatibility. Results indicate efficient interfacial interaction between matrix and filler at all nanoclays used. In terms of tensile strength, measured improvements are comparable to other studies using nanoclay in whey protein based matrices [21, 24–26]. Furthermore, the continuous increase in tensile strength values is another evidence for a good distribution of the nanofiller at all concentrations as well as good interface adhesion.

Since the addition of filler into a polymeric matrix decreases material ductility, elongation levels of nanocomposites are typically lower than those of the polymer itself [13]. As discussed before, the incorporation of nanofiller contributes to a reinforcement of the cast films and reduces their flexibility at the same time [42], which explains a general decrease of elongation at break with increasing nanofiller ratio at the measured samples. Except for the highest concentration, elongations at break of the Nanofil composites were not statistically different to pure WPSS cast films () and also did not contribute to mechanical strength as good as the other fillers used. The diverse results of the different clays used can be attributed to different matrix-filler interactions, inhomogeneous spots at the measured samples, or the differences in sample thicknesses. Comparable studies using nanofillers in protein based matrices also showed diverse results. Wakai and others also incorporated 5% ((w/w), relative to the protein content) MMT clay into WPI matrix leading to a comparable decrease in elongation at break by 34% [43], while Sothornvit and others reported no significant differences at 5% Nanofiller (Cloisite Na⁺) in MMT/WPI cast films [20] which was explained by the assumption of incomplete nanoclay dispersion.

As expected by composite theory, the modulus was increased when a filler was incorporated into the polymeric matrix. Young’s modulus is a linear mechanical property which is measured at low strains and reflects material stiffness [44]. In the case of polymer nanocomposites, stiffness generally increases with the volume fraction of the nanofiller, as long as sufficient dispersion and exfoliation are ensured [12].

To be able to predict the Young’s modulus of such nanocomposites, the data was also fitted to the described modified Halpin-Tsai model. Therefore, the Young’s modulus of the Cloisite Na⁺ and Nanofil 116 fillers was assumed to be at 178 GPa, following an estimation by Fornes and Paul for MMT clay [45]. There was no explicit modulus data found for vermiculite clays. Since the range for Young’s moduli of layered silica lies between 178 and 265 GPa [45–47], a realistic assumption of 200 GPa was made for the Sunbar vermiculite filler. The modification of the Halpin-Tsai model was needed due to overestimation of the experimental data. This is because the Halpin-Tsai model is based on assumptions that are only partly fulfilled by the examined nanocomposites. The model presumes linear elastic and isotropic matrix and filler as well as completely oriented particles of similar size and shape. Additionally, the properties of matrix and filler do not change in the presence of each other [48]. Also, occurring agglomeration and the state of exfoliation are not considered. The MCF takes deviations into account and gives a better model fit. Table 3 shows the used and calculated constants and parameters for the curve fitting.

The determined Young’s modulus values ranged from approximately 60 to 180 MPa. Therefore, the RSS values also lie in a three-digit range. As described before, Sunbar and Cloisite Na⁺ samples showed proportionality between filler ratio and Young’s modulus according to the Halpin-Tsai model. RSS as well as indicates a good model fit; therefore it is possible to describe this proportionality with the adapted Halpin-Tsai model. The correction factors of Cloisite Na⁺ and Sunbar filler lie in the same range. As can be seen in Figure 2, for the Nanofil filler, the initial Halpin-Tsai theory highly overestimated Young’s modulus leading to a lower MCF. This is also in line with the varying results at other tested mechanical properties indicating a heterogeneous filler distribution and occurring agglomeration. Furthermore, inherent moisture of the Nanofil clay is lower compared to the Cloisite clay, resulting in an actual lower net volume of the silicate filler. Therefore also lower and higher RSS values were determined.

3.3. Barrier Properties Oxygen Permeability

3.3.1. Coatings

To evaluate oxygen barrier properties of the coatings, permeabilities for the coated monolayer without the PET substrate were calculated by converting (3) with the values measured for the bilayer-system and the pure substrate. Coating thicknesses varied from approximately 7 to 9 μm; therefore resulting values were additionally normalized to 100 μm thickness following formula (2). Cloisite Na⁺ as well as the Sunbar filler both showed decreases at each concentration step, indicating proportionality between filler ratio and permeability (see Figure 3). The lowest permeability of 2.097 [(cm³ 100 μm)/(m² d bar)] was determined for a monolayer with 9% ((w/w), relative to protein) Sunbar filler. The corresponding BIF, defined as the ratio of the permeability through the pure whey protein film and the permeability through the respective composite, was higher than 16. Weizman et al. [49] also used MMT clay for whey protein isolate based coatings with comparable OP for the zero sample. However, compared to Cloisite Na⁺, barrier improvements at measured 1% and 5% clay were lower (appr. 30 and 25 (cm³ 100 μm)/(m² d bar), resp.) compared to this study.

3.3.2. Cast Films

To get comparable results and since cast film thicknesses of the samples varied, measured values were normalized to 100 μm thickness (2).

All samples showed improved barrier performance with the addition of nanofiller, which can be seen in Figure 4. The WPSS sample gave an OP of approx.. 80 cm³/(m² d bar) for 100 μm film thickness. By adding Closite Na⁺, oxygen permeabilities were reduced up to a factor two at the highest filler ratio of 9% (w/w). The Sunbar Vermiculite filler gave even better results with barrier improvements of 20, 50, 75, and even 80% for the respective ratios compared to the zero sample. Measured values for the Nanofil sample set varied widely and showed no expected decrease of OP with increasing filler ratio. Explanation could be given by filler agglomeration at the measured sample spots generating no tortuous pathway for the permeating oxygen molecules. Furthermore, Nanofil 116 clays depict higher inherent moisture (8–13%) compared to the similar MMT clay Cloisite Na⁺ (4–9%). Therefore, the net volume of silicate layers in the composite is lower which could explain lower effects that also were observed at mechanical measurements. In terms of barrier properties and especially oxygen permeability, inherent moisture of the Nanofil clay could have had a negative effect on the barrier performance, since oxygen permeability of whey protein based films is a moisture-related property with decreasing barrier performance at increasing moisture [50]. Similar observations were also made for water vapor measurements, confirming this declaration.

Since both the Cloisite Na⁺ and the Sunbar Vermiculite sample sets showed expected decreases with increasing filler content, measured data was compared to the usual applied models for predicting the barrier performance of polymer nanocomposites. The following figure shows the measured data and the corresponding theoretical values for four different models. The aspect ratio for Cloisite Na⁺ of 70 was already applied in a former study [43], for both other fillers realistic values were assumed with 70 for Nanofil 116 (also MMT clay) and 100 for Sunbar Vermiculite based on found results, since there was no information available.

For the Cloisite Na⁺ filler, the model by Fredrickson and Bicerano seemed most appropriate to predict barrier properties based on visual assessment (see Figure 5). Unlike Nielsen or Cussler, Fredrickson and Bicerano assumed disk-shaped platelets that are aligned, but positionally disordered [37], which is presumed to be present in here produced nanocomposites. Sunbar Vermiculite showed higher decreases and lowest deviations to the simple model by Nielsen. Due to a higher basal spacing and inherent water compared to MMT, exfoliation processes are favoured in vermiculite clay. Additionally, due to different densities, the net volume ratio of platelets is higher with vermiculite clay. In terms of oxygen permeability, especially a higher state of exfoliation could have caused higher decreases and an approximation to the simple expression by Nielsen. All other models showed higher variations and mainly overestimated the measured data and are therefore not applicable for the used matrix-filler combination. However, for a suitable prediction of oxygen barrier properties for such WPI-based nanocomposites, the type of clay as well as the state of exfoliation and dispersion should be considered. Therefore, further parameters should be included to modify existing models if a barrier performance prediction is desired.

3.4. Water Vapor Permeability

Figure 6 shows water vapor transmission rates of all denatured specimen (cast films). All samples only showed weak barrier potential against water vapor. However, using Cloisite Na⁺ and Sunbar Vermiculite as filler, WVTR could be significantly reduced () by approximately 30 and 50% at the highest filler ratio.

The slight increase in WVTR when adding nanofillers (Nanofil and Sunbar) to the cast films could be explained by a decreased post-cross-linking of the WPI matrix due to the presence of the nanoplatelets/clays. At higher concentrations, the influence of an extended tortuous pathway for water vapor molecules takes more account and WVTR is decreased with increasing filler ratio at both the Cloisite and Sunbar filler. Nanofil specimen did not contribute to water vapor barrier capacities of WPI cast films. Possible reasons could be agglomeration of the nanofiller, so that no tortuous pathway was generated. Additionally, sample swelling could have caused free volume and easy water vapor solubility within the matrix so that even higher transmission rates were detected. Permeation tests performed at large relative humidity steps unluckily lead to swelling of WPI films. Theoretical constant diffusivity and constant thickness cannot not be assumed anymore, resulting in inaccurate measurement values [22]. Compared to a study by Sothornvit et al. [20] also using Cloisite Na⁺ clay (5% w/w relative to protein) in whey protein isolate/clay nanocomposites, measured WVTR values were much higher. However, the improvement by clay incorporation is of the same order of magnitude. Similar to the OP data, WVTR values were compared to common models for barrier predictions (see Figure 7).

Cloisite Na⁺ and Sunbar Vermiculite filler showed good model adjustment for barrier prediction. At WVTR measurements, the Fredrickson and Bicerano gave the best model fit by visual assessment for both sample sets. All other models displayed high differences between measured data and theoretic calculated values.

Compared to the oxygen permeation values, much lower barrier improvements were achieved with the same nanocomposite system. On the one hand, these results can clearly be attributed to the sample swelling which appeared at water vapor transmission measurements. On the other hand, however, other studies using nanoclay fillers in nonswelling PET matrix also revealed oxygen barrier improvements but no significant improvements concerning the water vapor transmission [51]. This different behavior of oxygen and water vapor transmission within the same system can be ascribed to occurring interactions between the permeating molecules with each other, the polymer matrix or the filler. Water vapor molecules generally have a greater tendency to those interactions by forming hydrogen bonds, making barrier improvements rather a function of hydrophobicity of the filler surface [12]. Since the used nanofillers rather display hydrophilic properties, stronger interactions between water vapor molecules and the filler platelets can occur resulting in lower barrier performances compared to oxygen. Existing models do not take interaction between filler and matrix into account. Thus, at least for water vapor permeability in protein based nanocomposites, interaction parameters should be established and used to adapt models for barrier predictions.

4. Conclusions

The homogeneous distribution proved by microscopy techniques indicated good compatibility and strong interactions between filler and matrix and confirmed a suitable method for the described processing of WPI-based nanocomposites. This was also reflected by the results of the mechanical and barrier properties characterizations. The incorporation of nanofillers gave improved stiffness and strength to the composite materials. Since no decline was visible at elongation and tensile strength measurements, the limit for nonlinear mechanical properties, meaning a critical filler ratio, is not reached yet; therefore further material reinforcement can be expected with higher filler ratios. Just like other protein based films, samples only showed weak barrier potential against water vapor. However, a significant WVTR reduction of approximately 50% was achieved using 9% (w/w) Sunbar Vermiculite as filler in cast films. For all prepared nanocomposites, oxygen barrier improvements were achieved. The highest BIF above 16 was achieved for the 9% (w/w) Sunbar Vermiculite nanocomposite coating with a permeability comparable to conventionally used oxygen barrier materials. Therefore, the development of WPI-based nanocomposites could expand the potential of whey proteins coating to be used in sustainable and biodegradable packaging solutions. Due to shown mechanical and barrier improvements, such nanocomposites could present an alternative to fossil-based packaging materials.

Conflicts of Interest

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

Acknowledgments

Part of the research presented in this study received funding from the European Union’s Horizon 2020 research and innovation programme under Grant Agreement no. 686116. For more information, refer to http://www.optinanopro.eu/. The works on the Sunbar-formulations have been funded by internal means of Fraunhofer IVV. The authors wish to acknowledge their respective colleague M. Pummer for his assistance with material processing and process optimization. Thanks are also extended to Z. Scheuerer and all colleagues responsible for the material characterization. Furthermore the authors want to thank Mr. Safraz Khan for the outstanding support with the Sunbar-formulation and the material supply as well as ITENE for providing the Cloisite and Nanofil dispersions. The authors thank E. Bugnicourt for the revision of the manuscript. This work was supported by the German Research Foundation (DFG) and the Technische Universität München within the funding programme Open Access Publishing.

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Copyright © 2017 Kerstin Müller 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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