On the Correlation of Lignocellulosic Filler Composition with the Performance Properties of Poly(ε-Caprolactone) Based Biocomposites

In this work, three types of agricultural waste: olive stones (OS), date seed (DS) and wheat bran (WB) were applied as potential lignocellulosic fillers in poly(ε-caprolactone) (PCL) based biocomposites. Differences in composites’ performance were related to the higher content of proteins, noted for WB comparing to other fillers applied, which enhanced plasticization of PCL matrix. The mechanical properties of biocomposites were significantly affected by the agricultural waste fillers. Use of WB caused an obvious, even 25% decrease of tensile strength and hardness, which could be explained on account of glass transition temperature depletion and weaker matrix–filler interfacial interactions. Such phenomenon also increased water uptake of PCL/WB composites by more than 100%, while for PCL/OS and PCL/DS systems only for about 50%. Thermogravimetric analysis revealed that all investigated composites can be effectively processed without thermal decomposition. Generally, the outcome of this work demonstrated that OS, DS, and WB could be applied as promising lignocellulosic fillers used in manufacturing of high-performance polymer biocomposites.


Introduction
Wood polymer composites (WPCs) are a special group of polymer-based composites, showing specific properties, such as relatively low density, enhanced stiffness and biodegradability, which properties can be designed by proper choice of lignocellulosic filler [1]. Moreover, lignocellulosic fillers incorporated into polymer matrices can reduce the materials' costs. For instance, the application of by-products resulting from the processing of various renewable raw materials, e.g. wood, crops or fruits is a promising approach in this field.

3
Materials, which can be considered as a very interesting sources of low-cost lignocellulosic fillers for WPCs are olive stones (OS) and date seeds (DS). OS are a by-product generated during manufacturing of olive oil. Its global production is estimated at ~ 3 million tonnes annually, 80% of which is produced in EU countries (mainly: Spain, Greece and Italy) [2]. The amount of OS generated by olive oil production depends on the applied processing method [3]. Generally, OS stand for 13-23 wt% of olive mass and are considered as by-product [4]. Their industrial applications have been already investigated to some extent and comprehensively discussed by Rodriguez et al. [5]. Among them energy production, production of activated carbon, cosmetics industry, biosorbents production or animal feeding, are especially worth mentioning. OS have been also incorporated into manufacturing of WPCs, however mainly polyolefins and poly(vinyl chloride) were used as a matrices for such applications [6][7][8].
Date palm is a very important crop in North Africa and Middle East, cultivated for its edible fruits [9]. Global production of date fruits exceeds 7.2 million tonnes a year. The largest producer is Egypt with annual production of over 1.5 million tonnes [10]. DSs stand for 8-15 wt% of total date fruit mass [11]. However, they have not generally received much attention due to their lack of popularity and commercial application [12]. In their traditional origin, in Arab world, they have been used to make drinks, which could be classified as non-caffeinated coffee [13]. Several attempts have been made to use DS in polymer composites [14][15][16][17]. Alsewailem and Binkhder [18] noted that incorporation of DS into HDPE and PS matrix resulted in the reduction of mechanical properties, due to the weak compatibility between matrix and filler phase. Ghazanfari et al. [19] also analyzed the properties of HDPE/DS composites. It was found that the application of DS resulted in a decrease of melt flow index (MFI), as well as an increase of thermal conductivity of studied composites. In other work, a decrease of the PP/DS composites' crystallinity was noted with an increasing filler content [20]. Nevertheless, almost all works related to polymer/DS composites were focused on polyolefins or epoxy resins, only few reports were associated with biodegradable polymers, such as polylactide (PLA) and poly(butylene adipate-co-terephtalate) (PBAT) [21,22].
In our previous works, we aimed to examine the application of brewers' spent grain [23][24][25] and wheat bran (WB) [26] in polymer composites. We established that these lignocellulosic fillers can be successfully applied as a low-cost alternative for "conventional" fillers in WPCs. Therefore, in presented research work we aimed to investigate the potential of OS, WB and DS as fillers for a development of biocomposites based on poly(ε-caprolactone) (PCL). We examined the effect of filler type and content (from 10 to 50 parts by weight) on the processing (MFI), chemical structure (FTIR analysis), thermal properties (TGA), dynamic mechanical properties (DMA), static mechanical properties (tensile strength, elongation at break, hardness) and water uptake of prepared PCL-based biocomposites.

Materials
Poly(ε-caprolactone) Capa™ FB100 with M w = 100,000 g/ mol and melting point 58-60 °C was acquired from Perstorp Holding AB (Sweden). OS were obtained from oil mill at Tripoli, Libya. DSs were collected from local manufactories of date pastes and juices in Zlitan city at the coastal region of Libya. WB was acquired from Młyn Gospodarczy Sp. J. (Poland) and used in its original state. OS and DSs were collected and put into plastic bags and immediately transported to the laboratory. Then, the material was washed completely with boiling water and soap using mixing at speed of 180 rpm for 2 h. Washing was repeated three times to remove oil, impurities and other undesirable materials. Next, the fillers were chemically treated by KOH solution for 4 h. Then, they were washed several times with distilled water and dried to constant weight. All used fillers were mechanically grinded to obtained similar size distribution of filler particles, since the size of filler has a significant influence on the incorporation of filler in polymer matrix.

Biocomposites Preparation
Biocomposites were prepared using GMF 106/2 Brabender batch mixer. Temperature of mixing chamber was 70 °C and the rotational speed of rotors was 100 rpm, in order to provide an efficient dispersion of filler, due to high shear forces acting inside the mixer. At the beginning, PCL granules were mixed for 2 min in order to plasticize the polymer. Then, previously grinded fillers were added to the PCL and mixed for another 5 min to provide proper dispersion of modifiers. Filler content in biocomposites was from 10 to 50 pbw. Then, obtained biocomposites, without cooling and grinding, were compression molded into 2-mm thick samples at 150 °C (what guaranteed an efficient flow of material) and 4.9 MPa for 1 min. After that, samples were kept in other press, with non-heated plates, until cooled down to room temperature. Poly(ε-caprolactone), after processing in the same conditions, was used as a reference sample. Samples of composites were coded as PCL/OS X, PCL/DS X or PCL/ WB X , where X standed for the amount of filler used in parts by weight.

Measurements
Particle size distribution of lignocellulosic fillers was determined by sieve analysis, according to our laboratory internal standard. Approximately 100 g of filler was manually sieved in a constant time (30 min), using woven cloth sieves with size of 1.02, 0.75, 0.50, 0.25 and 0.12 mm, respectively.
Macro-and microelements content in lignocellulosic fillers was determined by the wavelength dispersive X-ray fluorescence spectrometry (WD-XRF) using S8 Tiger 1 kW spectrometer from Bruker.
Elemental analysis (C, H, N) of lignocellulosic fillers was carried out using a Flash 2000 CHNSO Analyser from Thermo Scientific.
The chemical structure of fillers and biocomposites was determined using Fourier transform infrared spectroscopy (FTIR) analysis performed by Thermo Scientific IR200 Nicolet Spectrometer with a diamond crystal ATR attachment. Measurements were performed in a 1 cm −1 resolution in the range from 4000 to 400 cm −1 .
MFI of biocomposites was investigated using Zwick mFlow plastometer according to ISO 1133 at 200 °C, with load of 5 kg.
The tensile strength and elongation at break were estimated in accordance with ASTM D638. Tensile tests were performed on the Zwick Z020 apparatus with elongation head and extensometers at a constant speed of 50 mm/min. For the calculation of tensile modulus, the speed of 1 mm/ min was applied. Five dumbbell samples, type IV according to ASTM D638 standard, were used for each specimen. Shore hardness type D was estimated using Zwick 3131 durometer in accordance with ISO 868.
Dynamic mechanical analysis was performed using DMA Q800 TA Instruments apparatus. Samples cut to the dimensions of 40 × 10 × 2 mm were loaded with a variable sinusoidal deformation force in the single cantilever bending mode at the frequency of 1 Hz under the temperature rising rate of 4 °C/min within the temperature range between − 100 and 100 °C.
The results of static and dynamic mechanical analyses were used to calculate the brittleness of investigated composites, in accordance with the following formula presented by Brostow et al. [27] (Eq. 1): where B is the brittleness, 10 10 %·Pa; ε b the elongation at break, %; E′ is the storage modulus at 25 °C, MPa.
Moreover, for better understanding of interactions between matrix and filler, the volume fraction of polymer chains immobilized by filler particles (C v ), as well as the adhesion factor (A) determining the strength of interfacial interactions, were calculated from the results of dynamic mechanical analysis. Detailed procedures and mathematical formulas used for these calculations were presented in our previous works [25,26]. Thermogravimetric analysis (TGA) was performed on a Netzsch TG 209 apparatus using 5-mg samples in the temperature range 25-600 °C and under nitrogen atmosphere, at a heating rate of 20 °C/min.
The water uptake and the degradation of the materials were studied over a period of 2 weeks. Biocomposites (0.2 g samples) were conditioned in room temperature and then put into distilled water in order to determine their degradation behavior. Samples were taken out and weighted after 48, 120, 144, 168, 312 and 336 h. Water uptake was determined according to the following Formula (2): where m t is the mass of the sample after immersion, g; m 0 is the initial mass of sample, g.

Characteristics of Waste Lignocellulosic Fillers
Particle size distribution of applied lignocellulosic fillers is presented in the Fig. 1. OS particles were characterized by the smallest dimensions, with ~ 40 wt% of particles below 0.12 mm. For DS filler, more than 80 wt% of particles were smaller than 0.50 mm, while for WB it was over 83 wt%. Nevertheless, only ~ 31.5 wt% of WB particles was characterized by a size lower than 0.26 mm, while for DS it was almost 61 wt%. Such phenomenon was related to the shape of WB particles, which can be seen in the Fig. 2. The size and shape of filler particles has a great impact on their dispersion in the polymer matrix, hence on the properties of a composite material. Differences in size of applied filler particles resulted in variation in composites' porosity, which also affected the mechanical performance of materials. Some differences in the composition of analyzed fillers, presented in Table 1, were observed. The highest carbon content was noted for OS, which can be associated with the highest amount of lignin contained in this filler (see Table 2). In comparison to cellulose, lignin contains more carbon in its structure-61.7%, versus 44.4% (determined by elemental analysis) [28,29]. The highest nitrogen content was observed for WB, which is related to the high content of proteins, mainly gluten [30], comparing to OS and DS filler. Moreover, analysis of applied lignocellulosic fillers with WD-XRF revealed higher content of potassium, phosphorous, magnesium and other elements in WB comparing to other fillers. Higher content of macro-and micro-elements in lignocellulose filler could support further biodegradation of studied composites, therefore, in future studies, their impact on efficiency of this process should be evaluated. Generally, presented results of OS and DSs composition analysis correspond with literature data [31,32].
In the Fig. 3, the FTIR spectra of applied lignocellulosic fillers are presented. All analyzed fillers contained hydroxyl groups, present in polysaccharides (cellulose, hemicellulose), which was expressed by the presence of   Table 2 Chemical composition of used waste lignocellulosic fillers a According to [5] b According to [33] c According to [34] d According to [35] e According to [36] f According to [ characteristic signal (a) in the range of 3300-3350 cm −1 , responsible for their stretching vibrations. Peaks (b) in the range of 2840-2940 cm −1 were related to the symmetric and asymmetric stretching vibrations of C-H bonds in CH 2 and CH 3 groups present in structure of applied fillers, more precisely in the hydrocarbon chains of polysaccharides [37]. Absorption bands present around 1740 and 1640 cm −1 (signals c and d), were attributed to the stretching vibrations of unconjugated C=O and C=C bonds in polysaccharides [38]. Group of peaks (e) in the range of 1370-1460 cm −1 is related with CH 2 and HOC in-plane bending vibrations, characteristic for carbohydrates, e.g. lignin [39,40], while signal (f) at 1235 cm −1 is associated with the stretching of C-O and C=O bonds [41]. The most intensive signal (g) was observed around 1010-1030 cm −1 , which is typical for FTIR analysis of lignocellulosic fillers [42] and can be associated with the stretching vibrations of C-O bonds [43].

FTIR Analysis of Biocomposites
In the Fig. 4 the FTIR spectra of pure PCL and biocomposites containing 50 pbw of applied cellulosic fillers are shown. Signals (a) observed in the range of 2860-2940 cm −1 were attributed to the symmetric and asymmetric stretching vibrations of C-H bonds in CH 2 and CH 3 groups present in the structure of PCL matrix. Peak (b) at 1724 cm −1 can be ascribed to the stretching vibrations of carbonyl bonds [44]. Multiple absorption bands (c) observed at 1360-1480 cm −1 were related to the deformation vibrations of C-H bonds. Signal (d) at 1294 cm −1 was associated with the stretching vibrations of C-O and C-C bonds in the crystalline phase of poly(ε-caprolactone). Slight decrease of this signal's intensity with the incorporation of lignocellulosic fillers may suggest a disturbance of crystalline structure of PCL matrix due to the presence of solid particles [45]. Peak (e) at 1240 cm −1 was attributed to the asymmetric stretching of COC groups. Multiplet band (f) at 1160-1190 cm −1 shows complex structure and is associated with the symmetric COC stretching, as well as stretching vibrations of C-O and C-C bonds in the amorphous phase of poly(ε-caprolactone) [46]. Signals (g) in the range of 1044-1106 cm −1 were attributed to the stretching of C-O bonds. Peaks (h and i) observed from 730 to 955 cm −1 were related to the skeletal vibrations of C-C bonds in poly(ε-caprolactone) chains. It can be seen that, from the qualitative point of view, hardly any difference can be observed between analyzed materials. Moreover, negligible differences between spectra for pure poly(ε-caprolactone) and biocomposites indicating physical interactions at the interphase between matrix and filler.

Melt Flow Index of Biocomposites
The effects of lignocellulosic filler type and content on the MFI of studied composites were measured and plotted in Fig. 5. Both factors have noticeable influence on the flowability of biocomposites, which is obviously related to the incorporation of solid particles into poly(ε-caprolactone), disturbing flow of polymer matrix [47]. It can be seen that the level of MFI decrease is related to the particle size distribution of applied fillers. The most significant decrease was observed for PCL/OS composites, which is related to the smallest size of OS particles comparing to other studied fillers. In this case, physical interactions between poly(ε-caprolactone) matrix and filler particles were stronger, due to the larger specific surface area of applied cellulosic filler, therefore the highest melt viscosity was observed [22,48].

Morphology of Biocomposites
In the Fig. 6 the SEM microscopic images of investigated composites are presented. Prior to analysis, samples were cooled in liquid nitrogen in order to obtain brittle fracture area in images. It can be seen that the noticeably biggest filler particles are observed for PCL/WB composites, which confirms the results of sieve analysis. Moreover, for this group of materials the lowest compatibility can be observed, due to high porosity and lack of strong interfacial interactions, which can be also associated with the particle size of fillers [26]. Differences in morphology can be also related to the chemical composition of applied fillers, e.g. higher content of proteins and lipids, for WB and DS respectively, which can act as plasticizers [49].

Static Mechanical Properties of Biocomposites
In the Figs. 7 and 8 the impact of filler type and content on the tensile strength and elongation at break of investigated Fig. 6 SEM images of prepared biocomposites biocomposites, is shown. As could be expected, noticeable drop of these parameters was observed. It was related to the high tensile properties of poly(ε-caprolactone) matrix and insufficient interfacial interactions between matrix and filler phase, which was also observed in our previous work [25]. Mittal et al. [22] have made similar observations in case of PBAT/DS and PLA/DS biocomposites. They attributed the decrease of tensile strength with poor polymer-filler interactions and with too big particle size of filler, which led to the stress concentration. Generally, in case of lower loadings, some differences between particular fillers were observed. Incorporation of WB resulted in higher decrease of tensile strength comparing to OS and DS. It can be associated with lower content of polysaccharides, such as cellulose, hemicellulose, lignin or starch, which enhances interfacial interactions with matrix, due to the high number of polar groups, e.g. hydroxyl groups [50]. Moreover, WB has higher content of proteins, which could act as plasticizers of PCL matrix [49]. This also explains the highest elongation at break for PCL/WB composites.
For the highest loadings, tensile properties were hardly dependent on filler type. In that case, the deterioration of mechanical performance was rather related to the disturbance of matrix integrity and limitation of PCL chains mobility [51].
In the Fig. 9 elastic modulus of investigated composites, determined during tensile tests are presented. As could be expected, incorporation of lignocellulosic fillers resulted in the stiffening of the material, expressed by the increase of modulus. Such phenomenon was associated with the PCL chains' mobility limited by filler particles and potential interactions between carbonyl group of PCL and polar groups present on the surface of applied fillers [7,51]. Presented results fully confirm previous work related to polymer biocomposites containing DS filler [22].
The hardness values of biocomposites are shown in the Fig. 10. As expected, incorporation of analyzed fillers into poly(ε-caprolactone) matrix resulted in the increase of hardness, which confirms the results of previous works [20,25]. The most significant rise of hardness was observed for PCL/ OS composites, from 50.2 for pure PCL to 52.8, 54.7 and 56.7 °Sh D, respectively, for 10, 30 and 50 pbw of filler. This confirms enhanced physical interactions between matrix and filler phases, due to a larger specific surface area (the smallest particle size) of OS among used lignocellulosic fillers. The lowest values of hardness were observed for materials containing WB, ~ 5% lower than for PCL/OS composites,

Dynamic Mechanical Properties of Biocomposites
In the Figs. 11 and 12 and in Table 3 the the results of dynamic mechanical analysis of prepared composites are presented. In the Fig. 11 the plots of composites' storage modulus (E′) as a function of temperature are shown. Presented plots confirm the results obtained during tensile tests, which indicated enhancement of materials' modulus and increase of hardness by addition of lignocellulose fillers. The strongest effect of stiffening was observed for PCL/DS composites, which is also in line with the results of static mechanical tests. For all samples, two phase transitions can be observed, which is related to the rapid drop of modulus. First one, the glass transition, occurs in the range of − 60 to − 30 °C, while the second one, noted around 70 °C is associated with melting of PCL matrix. In Table 3 the glass transition temperatures (T g ) values determined as the maximum value of the loss tangent (tan δ) curve versus temperature, are presented. It can be seen that composites containing lignocellulosic fillers showed noticeably higher values of T g (almost 6 °C difference for PCL/OS 50 sample), comparing to pure poly(ε-caprolactone). According to Mousa et al. [7], who also investigated incorporation of olive-based fillers into polymer matrix, it was due to the addition of rigid and stiff particles, which are restricting chain mobility, e.g. due to polar-polar interactions, as well, as hydrogen bonding between polar groups present on the surface of fillers and poly(ε-caprolactone). Some differences in T g between composites with various fillers were observed. The lowest values of glass transition temperature were noted for PCL/WB materials, which is related to the presence of amino acids, which enhance PCL's ability to flow under stress [52].
Moreover, in the Fig. 12 it can be seen that incorporation of waste lignocellulosic fillers not only affected the temperature position of tan δ peak, but also its magnitude. Similar  observations, related to the lowering of tan δ peak, were observed by other researchers [53,54].
As mentioned before, we applied methodology described in our previous works [25,26] for interpretation of DMA results. We used the magnitude of tan δ peak to calculate the constrained chains volume (C v ). Results of these calculations are presented in Table 3. C v parameter is associated with the limiting of polymer chains' mobility by incorporation of solid filler particles. Such limitation occurs through polar-polar interactions and hydrogen bonding between matrix and filler phases. Lowering of tan δ peak, as well, as its broadening, indicates reduction in the amount of mobile polymer chains.
For all composites, volume of constrained chains is increasing with the addition of filler, which confirms the stiffening of the material. Such phenomenon is associated with an increase of interfacial area and enhancement of matrix-filler interactions, due to the presence of various polar groups on the surface of applied lignocellulosic fillers. Moreover, C v value is related to the particle size distribution of used fillers. For lower particle size, the specific surface area is higher, therefore interfacial interactions between matrix and filler are enhanced. The lowest values of C v were observed for PCL/WB composites, which could be related to the highest particle size of WB filler and the highest content of proteins. Plasticizing PCL matrix by proteins might reduce stiffness of biocomposites.
We also used DMA results, more precisely values of tan δ in the temperature range of 15-35 °C, to calculate the adhesion factor (A) describing the strength of interfacial interactions. Results of calculations are presented in Table 3. During calculations we assumed that due to the relatively high rigidity, tan δ of filler can be neglected. Moreover, in case of composites characterized with very strong interfacial interactions between matrix and filler, the mobility of polymer chains in the vicinity of filler surface is significantly reduced, simultaneously reducing tan δ of interphase. As a result, for high degree of matrix-filler interactions, value of adhesion factor is low. Calculated A values are in line with the presented values of Cv, which suggest matrix-filler adhesion for PCL/OS and PCL/DS composites is higher than for PCL/WB samples. As a result of stronger interactions at the interphase, mechanical properties of these materials were superior to those containing WB. Stronger interphase enabled better transfer of stress inside the material, which led to higher tensile strength, stiffness or hardness. In case of composites containing 10 pbw of fillers, negative values of adhesion factor can be observed. Such phenomenon can be associated to the simplification of proposed model and A factor calculations, when filler anisotropy and development of the interphase region were neglected, which can have impact on the matrix mobility around filler particles [55].
In Table 3 there are also presented values of materials' brittleness calculated using the results of elongation at break and storage modulus. Brittleness can be opposed to toughness, which is determined as an integrated stress-strain curve, so higher elongation at break is related to higher toughness. Storage modulus is responsible for high ability to withstand repetitive fatigue. Therefore, materials characterized with high ε b and high E′ are considered as materials with low brittleness [56]. It can be seen that B of composites is increasing with the share of lignocellulosic filler. Such phenomenon is associated with the weakening of interfacial interactions and drastic decrease of elongation at break. Therefore, despite the stiffening of the material, its toughness is reduced. The lowest brittleness was noted for PCL/ WB composites, which confirms the plasticization of PCL matrix due to the presence of proteins in WB.

Water Uptake of Biocomposites
In the Fig. 13 the plot of water uptake of PCL/WB composites as a function of immersion time is presented. It can be seen that with the increasing content of filler in composite its water absorption also increases, which was observed for all applied fillers, confirming results of other research [7]. Such phenomenon may be related to the increased porosity, related to the incorporation of solid particles into polymer matrix, but mainly to the fact that all fillers consist mainly of cellulose, hemicellulose, lignin and other polysaccharides (see Table 2). These components show relatively high values of water binding capacity and swelling capacity, which is due to the hydrogen bonding between polar groups present in their structure and water molecules [57][58][59]. Increased water uptake, hence the biodegradation ability, can be considered as a very positive feature from the potential application point of view. In case of composite materials, water uptake is strictly related to their porosity. Incorporation of natural fillers into polymer matrix is often related to the increase of porosity, caused by inclusion during processing, insufficient wettability of fillers and poor interfacial interactions [60]. It is also the reason of the increasing ability of biocomposites to absorb water, comparing to neat polymers. Similar effect was observed in case of investigated materials. In the Fig. 14 the influence of filler type on the water uptake of prepared biocomposites is shown. The highest ability to absorb water was observed for PCL/WB composites, which is related to the porosity of material, observed on SEM images, as well as to the chemical structure of material, especially to the presence of starch in WB, which show high water uptake [61]. Moreover, also proteins show relatively high water absorption, which resulted in the higher water uptake of PCL/DS and PCL/WB comparing to PCL/OS composites (see Table 2) [62].

Thermogravimetric Analysis of Biocomposites
The results of the TGA of PCL biocomposites are presented in Table 4. Data indicate a significant deterioration of the thermal stability with the addition of applied fillers, which is associated with their relatively poor thermal stability. The highest stability was observed for PCL/OS composites, which is related to the lowest content of proteins and lipids, moreover OS filler showed the highest content of lignin, which according to literature decomposes around 400 °C [37]. The peak T max1 on differential thermogravimetric curves is related to the degradation of applied fillers, e.g. their significant constituent-hemicellulose, which shows a decomposition stage in the range of 244-310 °C [22,37,63]. Second peak, T max2 is related to the decomposition of PCL matrix. Its highest values were observed for composites containing 10 pbw of fillers. This can be related to the reduced mobility of polymer matrix, what enhancing its thermal stability. These results are in line with the results of DMA analysis, e.g. constrained chains' volume. Nevertheless, the most important insight from TGA analysis is that thermal stability of composites containing 50 pbw significantly exceeds 180 °C. This is very important from technological point of view, because most of polyolefin-based WPC are processed near to this temperature. In Table 4 the values of weight residue of investigated biocomposites at 590 °C (wtr 590 ) are also shown. The highest values of residue were noted for PCL/ WB composites, which can be related to the highest ash content of this filler (see Table 2).

Conclusions
This manuscript presents the possibility of incorporation of OS, WB and DS into polymer biocomposites during manufacturing. PCL/OS and PCL/DS composites showed properties similar or even superior to those containing WB, which has been already examined as a filler for WPCs based on biodegradable polymer matrix. Differences between composites containing WB and other fillers were related to the more than two times higher content of proteins in WB, causing plasticization of polymer matrix. Such phenomenon noticeably affected mechanical properties of analyzed biocomposites, such as tensile strengtheven 34% increase. It was strongly associated with the higher content of polymer chains immobilized by OS and DS particles (over 7 and 28% increase), as determined by dynamic mechanical analysis, which was also related to the particle size of applied fillers. Composites containing WB were characterized by over 50% higher water uptake comparing to PCL/OS and PCL/DS materials. These dependences can be used in the future to design materials characterized by a desired water uptake, which strongly affects the course and rate of biocomposites' degradation.
Presented results indicate that prepared OS, DS or WB filled biocomposites could be applied in many industrial applications.
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