Upgrading Recycled Polypropylene from Textile Wastes in Wood Plastic Composites with Short Hemp Fiber

This research reports the manufacturing and characterization of green composites made from recycled polypropylene obtained from the remnants of polypropylene non-woven fabrics used in the textile industry and further reinforced with short hemp fibers (SHFs). To improve the interaction of the reinforcing fibers with the recycled polymeric matrix, two types of compatibilizing agents (maleic anhydride grafted, PP-g-MA, and maleinized linseed oil, MLO) were added during melt-processing, the percentage of which had to remain constant concerning the amount of fiber loading to ensure complete reactivity. Standardized test specimens were obtained by injection molding. The composites were characterized by mechanical (tensile, impact, and hardness), thermal (DSC, TGA), thermomechanical, FTIR, and FESEM microscopy tests. In addition, color and water uptake properties were also analyzed. The results show that the addition of PP-g-MA to rPP was satisfactory, thus improving the fiber-matrix interaction, resulting in a marked reinforcing effect of the hemp fibers in the recycled PP matrix, which can be reflected in the increased stiffness of the samples. In parallel to the compatibilizing effect, a plasticizing effect was obtained by incorporating MLO, causing a decrease in the glass transition temperature of the composites by approximately 6 °C and an increase in ductility compared to the unfilled recycled polypropylene samples.


Introduction
New materials research over the last 40 years has led to an increase in the number of wood plastic composites (WPCs). Currently, they can be used in many applications such as decking (indoor or garden furniture), packaging, or consumer goods [1,2]. The automotive industry is one of the areas where these composites have a great incursion due to their excellent weight-strength ratio. The use of natural fibers in polymeric matrices could reduce about 20% of the overall weight and 30% of the cost. Weight reduction in cars leads to fuel saving and as a result a reduction in greenhouse gases [3]. Natural fibers, such as hemp, flax, and jute, among others, are used as a reinforcement in thermoplastics due to their good mechanical properties and their ease of acquisition. This factor facilitates the replacement of synthetic fibers such as aramid, carbon, and glass currently used because the production of synthetic fibers is more expensive, and they have a negative effect on the environment [4,5]. Moreover, the use of bio-based materials with the aim to reduce the the water absorption of rPP/kenaf fiber due to the PP-g-MA addition [29]. Srebrenkoska et al. prepared PP reinforced with kenaf fiber composites compatibilized with PP-g-MA and further simulated the recycling process by reprocessing the composites; they observed that recycled composites showed some improvement on the interfacial adhesion [30]. Kord et al. reinforced virgin PP with 50 wt% of hemp fibers (100 mm in length) compatibilized with PP-g-MA and compared it with rPP-based composites obtaining the rPP from the waste spindle during the processing of virgin PP. The rPP-based composites showed a higher swelling effect than virgin PP-based composites due to the high hydrophilicity of hemp fiber and required a fourth component such as a clay (montmorillonite) to reduce the hydrophilicity of the composites [31]. On the other hand, some authors reported that the introduction of maleinized linseed oil (MLO) enhanced the compatibility of different WPCs by the formation of bonds between the carboxylic ester of MLO and the hydroxyls groups of cellulose [32,33]. Nevertheless, MLO compatibilized SHFs as the reinforcing phase for PP and/or rPP has not been studied yet.
With the main objective of mitigating the environmental problems associated with polypropylene textile wastes, in this work, the reuse of polypropylene fiber industrial wastes in the manufacture of wood plastic composites was evaluated. The rPP was obtained from non-woven polypropylene fabrics, and composites were prepared by an injection molding process to simulate the most typical WPC industrial processing conditions. The influence of short hemp fibers (SHFs), another textile waste, as reinforcement fiber for rPP, was studied by loading rPP with 30 wt% of SHFs (with length less than 3 mm). Since the main drawback of natural fibers is the high hydrophilicity which leads to low compatibility with PP matrix, two types of compatibilizing agents were used, polypropylene grafting maleic copolymer (PP-g-MA) and maleinized linseed oil (MLO), to improve the interaction between the reinforcement fibers and the polymeric matrix. The wood plastic composites were evaluated in terms of mechanical, thermal, and thermo-mechanical properties. The interaction between the matrix and the reinforcing fiber was analyzed by FTIR and FESEM. Finally, since these composites are intended for industrial applications where the hydrophobicity represents a handicap (i.e., automotive, construction materials, outdoor applications, etc.), the effect of the addition of compatibilized short hemp fibers in different percentages (10,20, and 30 wt%) on the water absorption properties of the rPP-based composites was studied. Finally, the composites' appearance was evaluated, and the color properties were assayed to get insights regarding the industrial applicability of the PP textile wastes recyclability as WPC materials.

Materials
A recycled polypropylene (rPP) was used as a matrix of the manufacture of the compounds, this material was obtained from the unused pieces of the ends of the nonwoven polypropylene fabrics supplied by AITEX (Alcoy, Spain). A short hemp fiber (SHF) type F 517 supplied by Schwarzwälder Textil-Werke Heinrich Kautzmann GmbH (Schenkenzell, Germany) was used as a fiber filler; it has an approximate fiber coarseness of 50-80 µm as can be seen in Figure 1, and it has a specific gravity of 1.48-1.50 g cm −3 . It also presents an approximate tensile strength of ≈1100 N mm −2 . Two types of compatibilizers were used to improve the interaction between the matrix and the reinforcing fibers, a commercial maleic anhydride grafted, metallocene-catalyzed polypropylene wax grade Licocene PP MA 6452 granules from Clariant Plastics & Coatings (Frankfurt, Germany) (PP-g-MA), and a maleinized linseed oil (MLO) from VEOMER LIN by Vandeputte (Mouscron, Belgium) with a viscosity of 10 dPa s (20 • C).

Manufacturing of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
To avoid later defects in the samples caused by moisture, the materials were subjected to a drying stage at 60 • C overnight before processing. All formulations were mixed in the first stage by manual methods in a ziplock bag to obtain uniform mixtures. Table 1 shows the coding and formulations of the compounds manufactured. The formulations are designed so that the amount of compatibilizer remains constant with increasing load. For instance, for every 10% load, 2.5 phr is added; they were extruded in a twin-screw corotating extruder from Dupra S.L. (Alicante, Spain). The temperature profile was selected considering the melting peak temperature of a conventional polypropylene (PP), starting at the feed hopper with 155 • C and ending at the nozzle with 175 • C, and the rotating speed was set at 20 rpm. Once the strands were obtained, they were cooled down to room temperature in air, and then pelletized in an air knife unit. To obtain standard specimens, the pellets from all formulations were then injection-molded in an injection molding machine model Meteor 207/75 from Mateur & Solé (Barcelona, Spain). The temperature profile was 155 • C in the feed hopper and increased by 5 degrees at each stage, up to the injection nozzle with 170 • C; the injection and cooling times were set at 1 and 10 s, respectively.

Mechanical Properties
Tensile test of recycled polypropylene sample and the rPP/ hemp fiber composites was carried out on a universal testing machine ELIB 30 from Ibertest (Madrid, Spain); test parameters and dog-bone shape specimen were according to ISO 527 standard. The machine was equipped with a 5 kN load cell with a crosshead rate of 10 mm min −1 . Through this test, the tensile modulus, E t , tensile strength, σ b , and elongation at break, ε b , were obtained. The impact strength of the samples was determined on a Charpy pendulum from Metrotec S.A. (San Sebastian, Spain); this was done on unnotched samples using a 1 J pendulum according to ISO 179 standard. Five specimens of each formulation were tested to obtain reliable data. In addition, the Shore D hardness was measured using a durometer model 637-D from J. Bot S.A. (Barcelona, Spain), following the guidelines of ISO 868 standard, with a stabilization time of 15 s. Measured at five different points and averaged, this process was repeated for all formulations.

Morphological Characterization
The morphological study of the fractured surfaces of the samples subjected to impact tests was carried out by field-emission scanning electron microscopy (FESEM). A Zeiss Ultra 55 FESEM microscope supplied by Oxford Instruments (Abingdon, UK) was used. An electron acceleration voltage of 1.5 kV was established. Prior to the study, the sample surfaces were subjected to a sputtering coating process using an ultrathin gold-palladium layer in a high vacuum sputter coater model EM MED20 supplied by Leica Microsystem (Milton Keynes, UK).

Thermal Properties
The determination of the main thermal transitions of recycled polypropylene sample and the rPP/hemp fiber composites' compounds was carried out by differential scanning calorimetry (DSC) using an 821 DSC calorimeter supplied by Mettler-Toledo Inc. (Schwerzenbach, Switzerland). This test was performed with samples weighing approximately 5 mg, which were subjected to a three-stage thermal cycle. The first stage consists of a heating process from room temperature to 180 • C in order to erase the thermal history caused to the previous processing stages, followed by a cooling stage down to −30 • C. Finally, a second heating cycle from −30 • C to 200 • C. Both the heating stages (first and second cycle) and the cooling cycle were programmed at a constant heating and cooling rate of 10 • C min −1 , respectively. Tests were conducted under an inert atmosphere to prevent unwanted oxidation, and thus a constant flow of nitrogen (66 mL min −1 ) was maintained throughout the test. The crystallization temperature (T c ), melting enthalpy (∆H m ), and the peak melting temperature (T m ) could be obtained from the cooling and the second heating cycle, respectively. The maximum crystallinity, χ c _ max , of the different compounds can be obtained by Equation (1).
where ∆H 0 m correspond to the theoretical melting enthalpy of fully crystalline polypropylene, which according to the literature, is 138 J g −1 [34,35], and w is the filler mass fraction.
The thermal stability and thermal degradation of recycled polypropylene sample, the short hemp fibers, and the rPP/hemp fiber composites were studied by thermogravimetric analysis (TGA) using a thermobalance model TGA1000 from Linseis (Selb, Germany). The average weight of the samples was between 10 and 20 mg. These were placed in standard alumina crucibles (70 mL) to obtain comparable data; the weight of the samples was kept constant. All samples were exposed to a dynamic heating cycle from 30 up to 700 • C at a constant heating rate of 10 • C min −1 under inert atmosphere, and thus a constant flow of nitrogen of 66 mL min −1 was used during the tests. Thermal parameters such as the onset degradation temperature, which is assumed to occur when the sample loses 5% of its mass, T 5% , and maximum degradation rate temperature, T deg , could be obtained from this test.

Thermomechanical Properties
Dynamic mechanical behavior of the recycled polypropylene sample and the rPP/hemp fiber composites was analyzed by a dynamic mechanical thermal analysis (DMTA) in a DMA1 dynamic analyzer from Mettler-Toledo (Schwerzenbach, Switzerland); the equipment operates in single cantilever/flexural conditions. Solid samples with dimensions of 20 × 7 × 1 mm were used and subjected to a temperature sweep from −100 to 120 • C at a constant heating rate of 2 • C min −1 , with a frequency of 1 Hz and maximum flexural deformation (%γ) of 0.1%. The test allowed us to observe the evolution of the storage modulus, E', and the dynamic damping factor, tan δ, as a function of the temperature, allowing the determination of thermal transition such as the glass transition temperature, T g .

Color Measurements
The influence of short hemp fiber addition on the color of rPP/hemp fiber compounds was studied in a colorimeter KONICA CM-3600d Colorflex-DIFF2 from Hunter Associates Laboratory (Reston, VA, USA). The CIELab color scale was used to determine the L*, a*, and b* coordinates, where L* represents the luminance, a* shows the change between the red and green color, and b* shows the change between the yellow and blue color. The equipment was calibrated taking into account the standard white tile and a mirror device for the black. The total color difference, ∆E * ab , was obtained following Equation (2).
where ∆L * , ∆a * , and ∆b * are the differences between the color of the samples and the reference color.

Water Absorption Analysis
Water absorption of the recycled polypropylene sample and the rPP/hemp fiber composites was performed following the guidelines of ISO 62:2008 standard. The test consists of immersing samples (80 × 10 × 4 mm) of the different formulations in distilled water at room temperature for a period of 15 weeks. The samples were removed from the water, dried, and then weighed on an analytical balance AG245 from Mettler-Toledo (Schwerzenbach, Switzerland) with an accuracy of ±0.001 g, then finally immersed again in the water. This process was carried out once a week during the experimental period to ensure the veracity of the results, and all measurements were made in triplicate. The percentage of water absorption was calculated with the following Equation (3).
where W t is the weight of the dry sample in a time t and W 0 is the weight of the initial dry sample.

Chemical Structure and Infrared Spectroscopy
A chemical analysis of the rPP/SHF green composites was carried out by attenuated total reflection-Fourier-transform infrared (ATR-FTIR) spectroscopy. Spectra were recorded using a Bruker S.A Vector 22 (Madrid, Spain) coupled to a PIKE MIRacleTM single reflection diamond ATR accessory (Madison, Wisconsin, USA). Data were collected as the average of 15 scans between 4000 and 650 cm −1 with a spectral resolution of 4 cm −1 .

Mechanical Properties of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
The results obtained by the mechanical characterization process are shown in Table 2 (tensile test, hardness, and impact Charpy) of rPP sample and rPP/SHF composites. The incorporation of short hemp fibers leads to an improvement of the elastic modulus. The addition of 10 wt% SHF results in an increase in stiffness to 1617 MPa from 933 MPa (compared with neat rPP). The elastic modulus shifted up to 2977 MPa for the 30 wt% compatibilized with PP-g-MA, which means about 320% more than the neat rPP. The effect of the compatibilizer (PP-g-MA) is clearly observed in the rPP-H30 and the rPP-H30-C samples, improving the interaction between the thermoplastic matrix and the lignocellulosic fiber, the elastic modulus increased from 2339 MPa to 2977 MPa (27.2% more), and similar results were reported by Sullins et al. [36]. The use of MLO results in a different effect on the rPP/hemp composites. In fact, the elastic modulus of rPP-H30-M decreased. Table 2. Summary of the mechanical properties of the rPP-SHF composites, elastic modulus (E t ), tensile strength (σ max ), elongation at break (ε b ), Shore D hardness, and impact strength.
The use of MLO with a lignocellulosic filler could produce different phenomena like the plasticization effect at the same time as the compatibilization effect due to an interaction of hydroxyl groups in cellulose (SHF) and the polar groups of MLO [37,38]. The samples compatibilized with PP-g-MA showed an increasing tensile strength by the addition of hemp fibers, reaching values of 28.9 MPa for the rPP-H30-C samples approximately 32% more than neat rPP (21.8 MPa). The absence of compatibilizer produced that the rPP-H30 had a tensile strength of 22.4 MPa, only 5.6% more than neat rPP. This is due to the low interaction of the fibers with the matrix, causing voids between the matrix and the fiber that act as stress concentrators [39]. rPP-30-M samples registered a tensile strength of 17.7 MPa, 16.5% less than neat rPP, as Liminana et al. [38], suggesting that MLO reduced the resistant properties in PBS/ASF composites. The elongation at break (εb) is highly affected by the introduction of short fiber in the polymeric matrix; the neat rPP obtained an elongation at break of 100%, and the addition of 10% of SFH led to a reduction of 93.3%. Higher contents of hemp slightly changed the elongation at break of the compatibilized composites. As was mention above, the addition of MLO provided a plasticizing effect, which results in an improvement of the elongation at break compared with the H30-C samples.
The incorporation of microfibers also has an effect on the hardness of the different composites. This effect could be seen in greater depth for rPP-H30-C, which obtained values of 76 on the Shore D hardness scale, 8.1% more than neat rPP. According to Ivorra-Martinez et al. [40], hardness follows a trend similar to that of stiffness in composite materials. It can be observed that the use of MLO results in materials with a lower hardness, being even lower than that of rPP. The improvement of impact strength properties by introducing fibers into polymeric matrices has been reported by many authors previously. This effect can be attributed to the ability of the materials to dissipate energy by pulling the fibers away from the thermoplastic matrix [10,11]. In fact, the improvement of the impact strength properties could be seen by adding 20 wt% SFH content, with an improvement of 9.1% compared to neat rPP. The dissipation of energy during the debonding of the fibers is highly affected by the interaction between the fiber and the matrix, for this reason, rPP-H30 values were 15.6% lower than the one compatibilized with PP-g-MA [41,42]. Moreover, the use of MLO provided an extra improvement by the plasticization. Quiles et al. [43] reported similar results when they introduced AESO (acrylate epoxidized soybean oil) into PLA.

Morphological Characterization of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
To assess the quality of the rPP polymeric matrix/fiber interface, the morphology of the fracture surfaces of the injection-molded samples after the impact tests was observed by FESEM, and the images are shown in Figure 2. The fracture surface of the rPP sample ( Figure 2a) shows roughness, and this phenomenon is related to the plastic deformation of the thermoplastic. One feature of this rPP is the presence of some particles inside the polymer matrix, and this phenomenon was attributed to the recycling process wherein these particles have been mixed. The incorporation of SHF does not show a significant effect on fracture roughness, but a somewhat reduced roughness can be detected. On the other hand, the addition of MLO increased the roughness due to the plasticization of the rPP matrix that promoted the ability of plastic deformation (Figure 2f). As proposed in the mechanical characterization, a debonding phenomenon of the fibers was produced when the composites were subjected to the impact test. Some holes produced by the fibers that were pulled out during the breakage are remarked with red arrows [44,45]. Additionally, the effect of the compatibilizer could be seen in the noncompatibilized rPP (Figure 2d). The green arrows show the gaps between the SHF and rPP matrix confirming the poor phase adhesion produced by the lack of compatibility between the fiber and the polymeric matrix. The incorporation of the different compatibilizers helped to reduce this effect as the gaps between rPP and compatibilized hemp fibers mainly disappeared (Figure 2e,f). The morphologies observed, corroborate the mechanical properties obtained in terms of the compatibilizer employed. The absence of the compatibilizer promoted a deterioration of the resulting values as a result of the gap formation between the thermoplastic and the hemp [40]. Meanwhile, the compatibilization of SHF with both PP-g-MA and MLO promotes a more effective fiber/polymeric matrix adhesion as can be clearly seen in Figure 2e,f, respectively.

Thermal Properties of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
The main thermal transitions of recycled polypropylene sample and the rPP/hemp fiber composites were obtained by the DSC analysis. Figure 3 displayed the comparative thermograms of the compounds. Figure 3a shows the cooling cycle; from this cycle, it was possible to record the crystallization temperature (T c ). The rPP has a crystallization peak at around 118.34 • C. Luyt et al. [46] showed very similar results for virgin polypropylene, with a value of 115 • C. The melting point (T m ) and the melting enthalpy (∆H m ) were extracted from the second heating cycle (Figure 3b). Table 3 gathers the main parameters extracted from the thermograms.  Regarding the melting point (T m ), it is observed that the recycled polypropylene unfilled presents a value of 163.7 • C, which is a value similar to that of virgin polypropylene [34] as well as recycled polypropylene [47], according to the literature. When a low amount of hemp fiber (i.e., 10% and 20%) is incorporated with PP-g-MA compatibilizer, no noticeable variation in melting temperature is observed; an increase of about 2 • C can be seen with the addition of 30% hemp fiber. It should be noted that the addition of both compatibilizers (PP-g-MA or MLO) to the structure does not influence the melting temperature of the composite materials, maintaining a temperature similar to that of unfilled recycled polypropylene (163 • C). The peak of the crystallization temperature decreases slightly with the incorporation of 10%, 20%, and 30% hemp fiber with PP-g-MA. This refers to the good interaction of the reinforcing fibers with the matrix due to the strong bonding generated by reacting the maleic anhydride groups of PP-g-MA with the hydroxyl groups of the hemp fibers; good bonding with the PP chains also occurs, resulting in grafted maleic anhydride copolymers [48]. It is worth noting that the use of MLO as a compatibilizer when incorporating 30% of hemp fiber results in a decrease in T c reaching values of 115.7 • C. This reduction may be due to the fact that the MLO in addition to the compatibilizing effect causes a plasticizing effect in the rPP matrix, and this leads to greater mobility of the polymeric chains, and consequently, the interaction between them somewhat decreases [49,50]. This could also lead to a decrease in the contact between the reinforcement fibers and the matrix, causing the nucleating effect of these compatibilized fibers on the rPP matrix tent to decrease [51]. Concerning crystallinity, the recycled polypropylene without reinforcement fibers presents a percentage close to 68.3%. These results are similar to the ones presented by Garcia-Garcia et al. [52] and correspond to virgin polypropylene. It is observed that the addition of 20% of hemp fiber considerably increases the crystallinity, being 8.8% higher than that of recycled polypropylene without reinforcement. This is because hemp fibers are lignocellulosic fillers, and lignocellulosic fibers have a nucleating effect on the PP matrix, which is more noticeable with the use of PP-g-MA as compatibilizer [53,54].
The addition of 30% of short hemp fiber without any compatibilizers results in a decrease of the crystallinity, and this may be because the fiber-matrix interaction is not good enough, inhibiting the nucleating effect typical of these fibers. As mentioned above, the use of MLO as a compatibilizing agent also has a plasticizing effect, causing the free volume between the matrix chains to increase, thus decreasing the contact of the fibers with the matrix and decreasing the nucleating effect of the fibers in the matrix, which is reflected in the decrease in crystallinity [55].
The thermal stability at high temperatures of the recycled polypropylene, the rPP/short hemp fiber composites, and short hemp fiber was determined by thermogravimetric tests. The thermogravimetric graphs of the different composites and short hemp fiber are shown in Figure 4. Table 4 summarizes the main parameters extracted from the thermogravimetric curves, i.e., onset degradation temperature (T 5% ) and the maximum degradation temperature (T deg_max ).  It is observed that thermal degradation of short hemp fiber occurs in three main steps. The first weight loss occurs below 110 • C where the mass loss is about 3% due to the moisture content of the fibers. By increasing the temperature to~220 • C, it is possible to observe the next degradation step, which ends at 385 • C; this corresponds to the thermal depolymerization of hemicellulose, and a mass loss of 36% was observed [56]. The last step occurs in the range between 385-600 • C, where the degradation of cellulose and lignin begins, which corresponds to the typical degradation of lignocellulosic fillers [57,58]. Moreover, it is observed that the residual mass is around 25%, consistent with the literature on typical hemp fibers [59,60]. In the case of recycled polypropylene, degradation occurs in a single stage, starting at about 350 • C and ending at 550 • C, and this behavior is typical of virgin polypropylene, as suggested by Aurrekoetxea J et al. [61]. The effect of reprocessing (recycling) on polypropylene is noticeable after the fifth reprocessing. The maximum degradation occurs at 448 • C, which corresponds to the degradation of saturated and unsaturated carbon atoms [34]. It can be noted that the incorporation of hemp fiber has a direct effect on the thermal stability of the composite materials. As the loading percentage increases, the thermal stability tends to decrease, as evidenced by the decrease in T 5% and maximum degradation temperature (T deg_max ), compared to the unreinforced rPP. This effect can be attributed to both the chemical structure of the hemp fiber and the action of the compatibilizing agent. Figure 4 shows that as the amount of fiber loading increases, the thermogravimetric curves of the composites have a fiber-like behavior. This is because the compatibilizing agent increases the interaction between the fiber and the matrix as the hemp fiber, having a relatively low percentage of lignin (3.7-5.7%) in its constitution, does not provide the typical thermal stability generally obtained when using lignocellulosic fillers [62], which is more noticeable at low percentages of fillers. It is important to note that by incorporating a higher percentage of fiber (i.e., 30%), the degradation of the compounds occurs in three steps. The first step is due to moisture and occurs below 115 • C. The second step occurs between 280 and 400 • C, where both the hemicellulose and cellulose parts are degraded. Between 400 and 500 • C, the polypropylene matrix and the lignin corresponding to the hemp fiber are mainly decomposed. Nevertheless, it should be underlined that all rPP/SHF-based formulations present the onset degradation temperature well above than selected processing conditions (maximum processing temperature 175 • C) and are enough thermally stable for the intended application (i.e., automotive parts, indoor or garden furniture, where the service temperature is well below the onset degradation temperature). Regarding the residual mass obtained at 700 • C, Table 4 shows that rPP has a residual mass of 6.8%. Other authors like Yuan et al. [63] reported a residual mass for PP about 0.5%; this difference can be attributed to the presence of residues inside the recycled polymer matrix and observed by FESEM ( Figure 2) and have already been commented on during the microscopy analysis. Hemp degradation as commented before occurs in three steps as could be observed in Figure 4; at 700 • C, the residual mass was 25%, and similar results were obtained by Oza et al. [64]. As expected, the incorporation of the fibers inside the polymer matrix provided a progressive increment of the residual mass up to 11.3% for the rPP-H30-M. Figure 5 shows the comparative curves corresponding to the thermomechanical properties of the rPP sample and the rPP/hemp fiber composites. Figure 5b shows the evolution of the storage modulus (E') with respect to temperature, which in general relates to the stiffness of the samples concerning the elastic energy they store. Figure 5b shows the damping factor (tan δ) with respect to temperature. In general, the curve presents two relaxations that are typical of polypropylene, which is observed around 14 • C, corresponding to the relaxation (β), being related to the glass-rubber transition of the amorphous part of the materials, which can be related to the glass transition (T g ). The second relaxation occurs at around 80 • C and corresponds to relaxation (α), which belongs to the mechanism of lamellar sliding and rotation of the crystalline part [65]. Some of these important values are listed in Table 5. The addition of the short hemp fiber in the recycled polypropylene matrix results in a noticeable increase in stiffness, as reflected in the increase in storage modulus values compared to the unfilled rPP sample. In addition, an increasing trend can be seen with increasing load, being more noticeable at low temperatures, these data are in agreement with those presented by Sullins et al. [36] and Etaati et al. [66]. The increase in stiffness caused by the incorporation of the hemp fiber is due to the reinforcing effect obtained with the addition of the lignocellulosic fillers, as mentioned above. This is because, with increasing fiber load, the energy absorption capacity increases, and the high interaction of the matrix with the fiber prevents energy dissipation [66].

Thermomechanical Properties of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
It is worth noting a particular case of decreased stiffness that occurs with the addition of 10% hemp fiber, which is more noticeable at low temperatures. In spite of this, the reinforcing effect provided by the hemp fibers can be noticed when passing the relaxation α, reaching values slightly higher than the rPP unfilled sample. This behavior is due to the fact that the lamellar motion of the crystalline part of the polypropylene that generally occurs at this temperature is reduced by the presence of the fibers, giving a reinforcing effect to the material, which results in an increase in stiffness as suggested by John and Anadjiwala [67].
Analyzing the evolution of the damping factor as a function of temperature, it is observed that the recycled polypropylene presents a relaxation (relaxation β), marked by the glass transition temperature (peak), with a value of 13.5 • C, in addition to the relaxation α at a temperature of 78 • C, as mentioned above. In general, rPP/hemp composites show a slight increase in glass transition temperature; this is due to the incorporation of compatibilizing agents such as PP-g-MA, making the interaction between the matrix and the fiber good enough. In addition to this, the incorporation of fibers produces a slight decrease in the intensity of the peak damping factor; this is because the fibers restrict the mobility of the chains, causing the degree of molecular movement to decrease, thus decreasing the intensity of the damping factor [67].
The use of MLO as a compatibilizing agent results in a considerable decrease in the glass transition temperature compared to its counterpart PP-g-MA. This is due to the fact that in addition to the compatibilizing effect of the MLO, it has a plasticizing effect which generates a less dense matrix that increases the mobility of the polymeric chains and, as a consequence, decreases their T g [68]; this is in agreement with the results found in the literature [69]. Table 5. Thermomechanical parameters of rPP pieces and the rPP/hemp fiber composites with different compatibilizers in terms of storage modulus (E') and glass transition temperature (T g ).

Water Uptake Properties of the Recycled Polypropylene Sample and the rPP/Hemp Fiber Composites
As it was already commented, the major drawback of the use of natural fibers as reinforcing fillers is their high hydrophilicity which can lead to a final hydrophilic material with poor interfacial adhesion and a tendency to decrease the overall thermomechanical performance with time. Thus, the water uptake behavior was studied. Figure 6 shows the evolution of water absorption of rPP samples and rPP/hemp fiber composites concerning soaking time (15 weeks). rPP absorbed the least amount (less than 0.2%) of water throughout the period of 15 weeks, in good agreement with the literature [70] showing the hydrophobic nature of rPP. It is observed that the addition of short hemp fiber as reinforcement has a direct impact on the water absorption capacity of composite materials. As the amount of fiber in the structure increases, the ability of the composites to absorb water tends to increase as well, mainly due to the hydrophilic nature of natural fibers as a result of the large amount of -OH groups present in hemicellulose and cellulose that tend to interact with water molecules easily [71,72]. The incorporation of PP-g-MA in the structure of the composites is noteworthy since this agent has an inhibiting effect on the water absorption capacity. Samples containing PP-g-MA and loaded with 10% fiber absorbed approximately the same amount of water as rPP samples (0.5 wt%), while samples loaded with 30% fiber absorbed only 2 wt% after 15 weeks of immersion. The optimum PP-g-MA treatment and loading made the rPP-H30-C WPC more compact by improving the interfacial adhesion between the short hemp fibers and the rPP matrix, as can be clearly seen in the FESEM image (Figure 2e). This is mainly because the maleic anhydride groups of PP-g-MA reacted with a large amount of the available -OH groups of the hemp fibers as was proposed in Scheme 1, causing the reduction of the free -OH groups in the fibers so that they are not available to react with water as suggested by Garcia-Garcia et al. [52]. This effect is clearly evident in the rPP-H30 samples which have an absorption percentage of approximately 5.5 wt%. Moreover, it is known that the roughness also has an effect on the transport properties of the porous matrix, where the equilibrium time in a single tortuous capillary with roughened surfaces increases with decreasing relative roughness [73]. As can be seen from the FESEM analysis (Figure 2), the roughness of WPCs decreased with respect to rPP. In addition, a large number of porous tubular structures existing in fiber speed up the penetration of water by the so-called capillary action [74]. Thus, with the high uncompatibilized fiber content in the rPP-H30 sample, there are highly available -OH groups which leads to highly absorbed water.
The results obtained here by compatibilizing the rPP with PP-g-MA showed better results than other compatibilizing strategies. For instance, Rachini et al. reinforced virgin PP with 30 wt% of short hemp fibers using two silane-based agents, vinyltrimethoxysilane (VTMS) and a coupling system based on VTMO and 3-(triethoxysilyl)propylsuccinic anhydride (SiAn), as compatibilizers. They observed that the water uptake of PP-SHF was increased when using VTMS as compatibilizer, and it was reduced by 43% with (VTMO + SiAn) reaching values of about 1.25% after one month of immersion in water (without reaching the steady state) [26]. Meanwhile, the rPP-H30-C developed here showed a reduction of 60% from 2.5 wt% in rPP-H30 to 1.0 wt% in rPP-H30-C after one month of immersion in water. Reference [75] studied virgin PP reinforced with 30 wt% of short hemp fibers hybridized with 10 wt% of glass fibers and observed that although the water absorption properties of the hemp fiber composites were somewhat improved by hybridization with glass fibers, the water absorption value was around 7% when the materials reach the steady state (in around five months). Meanwhile, the rPP-H30-C developed here showed a reduction of 63% (from 5.5 wt% in rPP-H30 to 2.0 wt% in rPP-H30-C) after 15 weeks of immersion in water which is the time required to reach the steady state. On the other hand, the rPP-H30-M sample presents the highest percentage of water absorption, reaching values of 7.6 wt%. This can be attributed to the plasticizing effect resulting from the use of MLO, which increases the free volume between the matrix chains, helping the diffusion of water in the composite, thus increasing the water absorption capacity [33].

Colorimetry Properties of rPP/Hemp Fiber Composites
One important parameter when WPCs were analyzed was the colorimetry changes when the short fiber was introduced. CIELEAB color space (L*, a*, b*) results are summarized in Table 6. The most remarkable difference between the colors appeared when 10% SHFs were introduced to rPP with a color difference (∆E * ab ) of 23.7. The lightness (L*) of the resulting composites was reduced as a function of the SHF amount employed (87.5 for rPP and 55.0 for rPP-H30). In general, the a* values trend to red colors while the b* values trend to yellow colors in function of the amount of fiber.  Figure 7a shows the obtained materials, and it is evident that the visual aspect significantly changed acquiring wood aspect. As can be seen in Figure 7b, the incorporation of SHF modified the color coordinates so that they acquired the appearance of woods like teak or eucalyptus [72,[76][77][78]. In this instance, rPP-H30-M took an appearance very similar to oak wood. Thus, the obtained WPCs are interesting for industrial applications where wood aspect is desired such as automotive parts and construction materials (i.e., windows, frames, furniture, decking, etc.) without the need of additional additives such as dyes.

Chemical Structure and Infrared Spectroscopy
In order to explain better the chemical composition of the green composites, the samples were analyzed by means of Fourier-transform infrared spectroscopy (FTIR). Figure 8a shows the spectrums of rPP, SHF, PP-g-MA, and MLO from 4000 to 650 cm −1 . These values allow a better understanding of the possible interactions and chemical bonds of each of them. Furthermore, the expected chemical reaction for each compatibilization strategy is shown in Scheme 1. One of the most common processes to modify cellulose in order to improve its interaction with polymers is the esterification process. In order to carry out the process, carboxylic acids such as maleic anhydride (MAH) are used to initiate an acylation reaction [79]. In this sense, the use of MLO and PP-g-MA involves the introduction of MAH groups that interact with the OH groups of cellulose in the esterification process. In Scheme 1, the resulting structure from the esterification of the anhydride groups with the cellulose is highlighted in blue [32]. On the other hand, from the point of view of rPP in conjunction with PP-g-MA and MLO, there is a clear interaction due to the affinity between the hydrophobics of the elements, a factor that can be seen highlighted in red in Scheme 1. By using both additives, it is possible to create a bridging structure between the filler and the matrix to improve its final properties, as can be seen for example in the mechanical properties. Regarding the polypropylene copolymer (PP-g-MA), the spectrum is very similar t that of rPP, since it is a polypropylene-based compound. However, an increase in the car bonyl band at 1785-1790 cm −1 characteristic of the anhydride functions can be seen [80 Regarding the polypropylene copolymer (PP-g-MA), the spectrum is very similar to that of rPP, since it is a polypropylene-based compound. However, an increase in the carbonyl band at 1785-1790 cm −1 characteristic of the anhydride functions can be seen [80]. In relation to the SHF, a large number of peaks appear with small intensities. This factor is due to the fiber format and the difficulty of being analyzed with the FTIR tool. In this context, a peak of pectin carboxylic groups can be seen at 1739 cm −1 [81]. Furthermore, a peak at 1114 cm −1 can also be appreciated due to the symmetric glycosidic stretching of the C-O-C bond in polysaccharide compounds of cellulose. Moreover, little absorption bands in the 1500 and 1130 cm −1 region can be observed, which indicate the presence of characteristic groups of cellulose, hemicellulose, and lignin. Other relevant peaks in this type of fiber are the bands of carboxylate groups at 1740 cm −1 and acetyl group and methyl ester at 1590 and 1240 cm −1 [82]. Finally, a broad absorption band is observed between 3600 and 3000 cm −1 , which corresponds to the O-H stretching vibrations characteristic of the hydrogen bonds of the hydroxyl groups (-OH) [32]. In relation to the MLO spectrum, a first peak located at 3006 cm −1 , corresponding to the =C-H stretching of the carbon-carbon double bonds, and those at 2925 and 2850 cm −1 refer to the antisymmetric and symmetric C-H stretching of the saturated carbon-carbon (C-C) bonds, respectively [32]. Furthermore, the band centered at 1735 cm −1 represents the carbonyl (C=O) stretching [83]. Finally, the band at 1462 cm −1 is due to the C-H bending vibration, while the absorption peaks at 1862 and 1784 cm −1 are attributed to the anhydride groups. Similar results have been reported by Jorda-Reolid et al. [84] for this type of natural compatibilizer. Figure 8b shows the infrared spectra of all the green composites obtained. The incorporation of short hemp fibers in the rPP generates an increase in the 1744 cm −1 bands. This is closely related to the above-mentioned and the bonds derived from this type of natural fibers. Being more significant in the composite with a high percentage of fiber loading (30%), this band can be attributed to the esterification of the OH groups of hemicellulose and lignin and maleic groups, as mentioned above [35]. The addition of MLO in the structure of biocomposites causes a decrease in the peaks of the 2852 cm −1 band corresponding to the symmetrical stretching of C-H bonds, as suggested by Domici et al. [85], and the interaction between the fiber and the matrix is improved, resulting in increased mechanical properties, as discussed throughout the work. Finally, as a result of the esterification reaction between cellulose and MAH groups and the hydrophilic affinity between rPP and MLO, a green composite with good chemical affinity was generated.

Conclusions
Wood plastic composites based on a recycled polypropylene matrix reinforced with short hemp fibers were successfully obtained by injection molding. Different load-matrix compatibilization elements were analyzed, and their effect was demonstrated by the representation of the resulting chemical structures after the injection-molding process. Through this work, it was possible to determine that the recycling process to which the polypropylene textile wastes were subjected does not have a notable effect on its behavior, having practically the same characteristics as virgin polypropylene. However, it was observed that the final properties of the composites are directly related to the amount of fiber loading as well as to the quality of the interaction of the reinforcing fiber with the polymeric matrix. To improve this interaction, different compatibilizers were incorporated during manufacturing. The use of PP-g-MA as compatibilizer resulted in a remarkable improvement in the interaction of the polymeric matrix with the reinforcing fibers, as observed in the FESEM images, consequently significantly reducing the water absorption. Tensile tests indicated that increasing the amount of compatibilized short hemp fiber with PP-g-MA provides the desired reinforcing effect, which is reflected in increased stiffness as a consequence of the improvement in the interfacial strength, in addition to increasing the nucleating effect that is generally obtained by adding lignocellulosic fillers. On the other hand, the incorporation of MLO gives a plasticizing effect to the compounds, and this results in an increase of the ductile properties of the composites, improving the energy dissipated in the Charpy impact test, as well as a decrease of the glass transition temperature (T g ). It was observed that the thermal stability is directly affected by the increase in loading, meaning that the higher the amount of hemp fiber loading, the thermal stability of the composites decreases tending to the thermal behavior of the fibers, but proving enough thermal stability for processing conditions as well as the intended use. Finally, it should be noted that the incorporation of short hemp fibers in a rPP matrix gives a color like oak wood. The best results were found for the sample compatibilized with PP-g-MA and loaded with 30 wt.% of short hemp fibers (rPP-H30-C), since this sample showed a very good interface between the matrix and the reinforcement phase, leading to an improvement of the overall thermo-mechanical performance as well as with improved hydrophobicity.
According to all these results, recycled PP textile wastes reinforced with compatibilized SHF, mainly with PP-g-MA, processed by injection molding can serve as a possible more sustainable substitute for materials currently used in several industrial applications such as automotive, construction, and furniture materials (i.e., windows, frames, decking, etc.). Funding: AITEX wants to thank the European Regional Development Fund (ERDF) from the European Union for co-funding the project "NABITEX-Innovative technical textiles based on SUDOE natural fibers to be applied in Habitat Sector" through the Interreg SUDOE Program (SOE2/P1/P0524). AITEX wants to acknowledge that the MELTEX project (CIRCULAR ECONOMY APPLIED TO TEX-TILE WASTE OF THERMOPLASTIC ORIGIN) was funded by the Conselleria d'Economia Sostenible, Sectors Productius, Comerç i Treball de la Generalitat Valenciana, through IVACE and was co-funded by ERDF from the European Commission within the framework of the Operational Programme FEDER for the Comunitat Valenciana 2014-2020 (IMAMCI/2020/1).

Conflicts of Interest:
The authors declare no conflict of interest.