Influence of Newly Organosolv Lignin-Based Interface Modifier on Mechanical and Thermal Properties, and Enzymatic Degradation of Polylactic Acid/Chitosan Biocomposites

This article aimed to study the effects of chitosan fiber and a newly modifying agent, based on organosolv lignin, on mechanical and thermal performances and the enzymatic degradation of PLA/chitosan biocomposites. A newly modifying agent based on polyacrylic acid-grafted organosolv lignin (PAA-g-OSL) was synthesized via free radical copolymerization using t-butyl peroxide as the initiator. The biocomposites were prepared using an internal mixer and the hot-pressed method at various fiber loadings. The results demonstrate that the addition of chitosan fiber into PLA biocomposites remarkably decreases tensile strength and elongation at break. However, it improves the Young’s modulus. The modified biocomposites clearly demonstrat an improvement in tensile strength by approximately 20%, with respect to the unmodified ones, upon the presence of PAA-g-OSL. Moreover, the thermal stability of the modified biocomposites was enhanced significantly, indicating the effectiveness of the thermal protective barrier of the lignin’s aromatic structure belonging to the modifying agent during pyrolysis. In addition, a slower biodegradation rate was exhibited by the modified biocomposites, relative to the unmodified ones, that confirms the positive effects of their improved interfacial interaction, resulting in a decreased area that was degraded through enzyme hydrolysis.


Introduction
The manufacture of composite materials using ecologically friendly technologies is of great of interest to many academic and industrial practitioners in the areas of polymer science and engineering [1]. This trend is mainly driven by environmental considerations regarding the negative impact of petroleum-derived materials on the environment after their end-use, which are difficult to decompose in a landfill, and also by aiming to attain composite materials that possess the desired properties [2]. Composite materials often contain bio-based polymer. Among the bio-based polymers, polylactic acid (PLA) is the best biopolymer alternative for petro-polymers because of its renewability, biodegradability, biocompatibility, and good thermomechanical performance [3,4]. This biopolymer is derived from plants, such as corn and cassava, and it is known to have a relatively high melting point, strength, and versatility, with performance characteristics similar to synthetic polymers, such as polyethylene terephthalate, polyethylene, etc., [5][6][7].
PLA is regarded as a valuable and important biopolymer that can be utilized to replace synthetic counterparts in many applications, ranging from automotive parts to electronic devices [8][9][10]. However, PLA has some limitations that consequently restrict its widespread application, involving a low thermal resistance, heat distortion temperature, and crystallization rate, whereas other specific properties may be necessary in some agent in polymer composites include low dispersion and poor interfacial adhesion, both of which are caused by incompatibility with the hydrophobic matrix polymer. This is demonstrated by the difficulties of the polar hydroxyl groups located on the chitosan surface in building a well-bonded interface with a nonpolar matrix polymer, as strength improvement is dependent on stress transfer at the composite's interface when an external force is applied [22]. If the interface is poor, the fiber-matrix adhesion will diminish with no enhancement in performance [23]. Consequently, this problem reduces the benefits of using potential reinforcements in polymer composites.
To address the issue of interaction, the interfacial adhesion in the composite material is chemically altered. Chemical modification has been frequently utilized to enhance the interfacial adhesion in composite systems, since it is an effective technique for reducing the hydrophilic properties of natural fibers. Previous research used treated chitosan fiber as a natural filler in polypropylene composites. The results show that the incorporation of chitosan fiber into the composites increased the tensile modulus and the impact strength, while decreasing the tensile strength significantly [24]. Therefore, the current research is focused on employing chitosan fibers to increase the performances of PLA biocomposites by filler surface modification using a newly developed modifying agent based on grafted organosolv lignin. To the best of our knowledge, investigations involving the utilization of grafted organosolv-lignin-based modifying agents in biocomposites have been less reported in the literature.
Lignin is well-known as a byproduct of the wood pulping process and is one of the abundant vegetal-derived compounds [25]. Because of its complex aromatic structure, which is linked by an ester-bridge, lignin is a highly stable polymer. It has a strong polarity that results from the existence of a huge number of hydroxyl groups, both aliphatic and aromatic [26][27][28]. The lignin used in this study was obtained from lignocellulosic fiber using an established organosolv method with organic solvent and water [29]. The procedure produces lignin with a low molecular weight and a huge number of reaction sites available, making this kind of lignin a suitable surface-modifying agent. However, because of the complexity of its structure, lignin is difficult to dissolve in conventional solvents, causing the limitation of its chemical reactivity [30]. Therefore, a simple copolymerization reaction with acrylic acid was used to improve the lignin reactivity and solubility. The lignin alteration produces a pendant carboxylic moiety, which provides a site for additional reactive reactions.
This research is aimed at studying the effects of chitosan fiber and a newly developed modifying agent based on grafted organosolv lignin on the mechanical and thermal performances of PLA/chitosan biocomposites. Furthermore, the weight loss of the PLA/chitosan biocomposites during enzymatic degradation is examined.  Table 1. Commercial-grade diastase (sourced from malt) was supplied by Sigma Aldrich (St. Louis, MO, USA). The ethanol (98%.v/v), hydrochloric acid, t-butyl peroxide, acrylic acid, acetic acid, NaOH, sodium acetate and the sulphuric acid (98%.v/v) were obtained from Sigma Aldrich and used without further purification.

Extraction of Organosolv Lignin (OSL) from Lignocellulosic Fiber
The extraction procedure of organosolv lignin (OSL) from lignocellulosic fiber was conducted following the established organosolv method [31]. The fiber was first treated using a mixture of aqueous ethanol and a catalyst (sulphuric acid) at a temperature set of 190 • C for 1 h, with the solid to liquid ratio adjusted at 1:8. The pretreated fiber was then rinsed with aqueous ethanol. The washes were mixed, and 5 vol% of distilled water was added to precipitate the organosolv lignin. The OSL was centrifuged and then dried in an oven at a temperature of 80 • C for 24 h.

Preparation of PAA-grafted OSL
The chemical grafting reaction of OSL with acrylic acid was carried out by utilizing t-butyl peroxide as the initiator in a copolymerization reaction. Three grams of lignin sample and t-butyl peroxide were mixed with 60 ml of distilled water in the reactor. Acrylic acid was subsequently added slowly into the reaction mixture under constant stirring. The mixture pH was adjusted from around 8.5 to 9.0 by adding 2% NaOH solution. After the reaction was completed, the product was precipitated by adding 6 M HCl. The solid was allowed to stay overnight upon discarding the supernatant. The solid product was rinsed using acidified water (pH = 2-3) prior to drying in an oven.

Chemical Modification of Chitosan
PAA-g-OSL was used to chemically modify the chitosan surface in an ethanol medium. The amount of PAA-g-OSL used was 3% by weight of chitosan fiber. Chitosan fiber was added to the PAA-g-OSL solution, and then vigorously stirred for 4 h. Afterward, the chitosan suspension was filtered and dried for 24 h in an oven at a temperature of 80 • C.

Preparation of PLA/Chitosan Biocomposites
PLA/chitosan biocomposites were prepared in an internal mixer (MCN ELEC Co., Taichung, Taiwan) at 160 • C and 50 rpm. PLA was firstly fed into the mixer to initiate the melt mixing process for 12 minutes. Afterward, chitosan fiber was slowly added, and the compounding was carried out for another 3 min. Next, the compounds were removed and sheeted through a laboratory mill at a 2.0 mm nip setting. The compounds were compression molded at 120 kg·cm −2 in an electrically heated hydraulic press. The hot-press procedure consists of three-consecutive steps, involving preheating at 190 • C for 9 min, compression for 3 min at 190 • C, and then cooling pressure for 3 min. A similar procedure was carried out to synthesize the modified PLA/chitosan biocomposites. The formulation of unmodified and modified PLA/chitosan composites is exhibited in Table 2.

Characterization
Tensile tests were conducted using an Instron 5582 machine (Instron, Norwood, MA, USA)according to ASTM D 638-91. A Wallace die cutter was utilized to cut at least five dumbbell specimens of each composition, 1 mm thick, from the molded sheets. The test was conducted at 25 ± 3 • C with a crosshead speed of 20 mm/min. Thermogravimetric (TGA) and derivative thermogravimetric (DTG) analyses were carried out using a TGA Q500 (TA Instruments, New Castle, Germany). The samples were thermally scanned at a temperature range of 30 to 600 • C, at a heating rate of 20 • C/min, with a nitrogen flow of 50 mL/min. Differential scanning calorimetry (DSC) analysis was performed using a DSC Q 1000 (TA Instruments). Samples were scanned at a temperature range of 25 to 250 • C, at a heating rate of 20 • C/min, with a nitrogen flow of 50 ml/min. The instrument software was used to calculate the melting points (T m ), glass transition temperature (T g ), crystallization temperature (T c ), and the enthalpies of the PLA/chitosan biocomposites. The crystallinity of the composites (X c ) was manually calculated using Equation (1): where, ∆H f is the fusion enthalpy of the PLA and biocomposites, and ∆H f • is the thermodynamic fusion enthalpy belonging to a fully crystalline PLA (93.6 J/g) [32]. Data from the second heating scan was taken for each sample. An average value from three samples of each specimen was recorded.
A morphological study of the fracture surfaces of PLA/chitosan biocomposites was performed using a scanning electron microscope (SEM), JEOL model JSM 6260 LE. The fracture ends of the specimens were mounted on aluminum stubs and sputter-coated with palladium to avoid electrostatic charging during analysis.
Fourier transform infrared spectroscopy (FTIR) was conducted on unmodified and modified chitosan in ATR mode (Perkin Elmer 1600 Series). Samples were scanned at a resolution of 4 cm −1 from 650 to 4000 cm -1 .
The number of the average molecular weight (M n ), and weight average molecular weight (M w ), of the lignin were measured using gel permeation chromatography (GPC) after the acetylation of the lignin to allow dissolution in THF [33]. GPC analysis was carried out using a Perkin Elmer instrument (Waltham, MA, USA) equipped with an interface (PE Series 900).
The biodegradation test was performed in a diastase-enzyme-containing solution with an activity of 480 KNU·g −1 . A buffer solution (pH = 7.3) was prepared in a beaker by mixing 5 mL of 0.2 M acetic acid with 45 mL of 0.2 M sodium acetate solution. The biocomposites were submerged in the solution for 30 days in an incubator (New Brunswich Scientific) at 37 • C. The samples were taken every 5 days and rinsed thoroughly with distilled water before a conditioning step in an oven at 60 • C for 24 h.
In the weight loss measurement, each specimen was taken periodically and wiped and dried to a constant weight at 60 • C in a vacuum oven. The weight loss percentage was measured using an analytical balance, and calculated using Equation (2): where, W initial and W final stand for the weights of the biocomposites before and after the biodegradation test, respectively. The average value of the three measurements from each biocomposite was reported.

Structural Analysis of Modified Chitosan
The OSL had a weight-average molecular weight (M w ) of 3429, and a number-average molecular weight (Mn) of 2506. The polydispersity (M w /M n ) of the OSL obtained was 1.37. These values were calculated from the chromatogram produced by the gel permeation chromatography. These results suggest that the extraction significantly ruptured the complex macromolecular structure of the lignin. A low polydispersity value indicates a narrow molecular weight distribution. Figure 1 shows FTIR spectra for unmodified chitosan fiber, and modified chitosan with PAA-g-OSL. The FTIR analysis was aimed at investigating the possibility of a chemical bonding formation between the PAA-g-OSL modifying agent and the chitosan fiber. The IR spectra belonging to unmodified chitosan demonstrate the existence of characteristic peaks at 3358 cm −1 (O-H stretch), 2872 cm −1 (C-H stretch), 1675 cm −1 (N-H bend), and 1590 cm −1 (C=O stretch). The differences between the absorption spectra of the modified and unmodified chitosan indicates an alteration in the chemical structure of chitosan upon the esterification process. The distinct change in the absorption spectrum, occurring on the peak between 1760-1712 cm -1 and 3400-3200 cm -1 , was caused by the carboxyl groups (C-OH) of the modifying agent linked to the hydroxyl groups (-OH), chitosan-fiber-formed ester linkages (C-O-C), and the decrease of the content of chitosan's hydroxyl groups. The formation of ester bonds (C-O-C) resulted in a decrease in hydrophilic moieties on the chitosan surface. The modified chitosan had less hydrophilicity (24.2% lower) than the unmodified chitosan. It was shown by a relatively lower intensity of the peak at 3292 cm -1 of the modified chitosan with PAA-g-OSL than that of the peak at 3358 cm -1 of unmodified chitosan. Figure 2 shows a possible schematic of the chemical reaction between chitosan fiber and esterified lignin.   Figure 3 shows typical stress-vs-strain traces obtained from the tensile tests for neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites, respectively. All of the PLA biocomposites contained 20 php of chitosan fiber. All curves clearly show the same trend, where the incorporation of chitosan decreased the strength and strain of the PLA biocomposites, corresponding to poor interface interaction between the PLA and chitosan. Chitosan is a natural polymer that possesses polar hydrophilic properties, whereas PLA is a nonpolar hydrophobic polymer. The differences in the affinities and polarity diminished the interaction on the filler-matrix interface [34]. The modified PLA/chitosan biocomposite with PAA-g-OSL, on the other hand, demonstrated a greater strength than those of the neat PLA and the unmodified biocomposites, which indicates the enhanced interfacial adhesion upon the existence of PAA-g-OSL on the chitosan surface. Interestingly, the strain increased by 24.57% when compared with the unmodified biocomposite, reflecting the enhanced chain mobility of the PLA matrix within the biocomposite. Overall, it can be observed that the interfacial compatibility improves  Figure 3 shows typical stress-vs-strain traces obtained from the tensile tests for neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites, respectively. All of the PLA biocomposites contained 20 php of chitosan fiber. All curves clearly show the same trend, where the incorporation of chitosan decreased the strength and strain of the PLA biocomposites, corresponding to poor interface interaction between the PLA and chitosan. Chitosan is a natural polymer that possesses polar hydrophilic properties, whereas PLA is a nonpolar hydrophobic polymer. The differences in the affinities and polarity diminished the interaction on the filler-matrix interface [34]. The modified PLA/chitosan biocomposite with PAA-g-OSL, on the other hand, demonstrated a greater strength than those of the neat PLA and the unmodified biocomposites, which indicates the enhanced interfacial adhesion upon the existence of PAA-g-OSL on the chitosan surface. Interestingly, the strain increased by 24.57% when compared with the unmodified biocomposite, reflecting the enhanced chain mobility of the PLA matrix within the biocomposite. Overall, it can be observed that the interfacial compatibility improves the composites' strength. Although chemical modification had no effect on the stress-versus-strain trace character of the modified biocomposites, it did influence the measured strength at failure.

Mechanical Properties of PLA/Chitosan Biocomposites
Polymers 2021, 13, x FOR PEER REVIEW 7 of 1 the composites' strength. Although chemical modification had no effect on the stress-ver sus-strain trace character of the modified biocomposites, it did influence the measure strength at failure. The tensile strength of unmodified and modified PLA/chitosan biocomposites at var ious fiber loading are exhibited in Figure 4. The tensile strength of the PLA biocomposite was inversely proportional to the chitosan content. However, the modified biocomposite showed a higher tensile strength than that of the unmodified biocomposites at a simila chitosan content. The tensile strength of the modified biocomposites improved by 36.43% as compared with the unmodified ones, indicating the enhanced filler-matrix interfacia interaction. This enhanced strength was clearly attributed to the high reactivity of PAA g-OSL, which effectively facilitated surface modification, resulting in improved interfacia adhesion.  The tensile strength of unmodified and modified PLA/chitosan biocomposites at various fiber loading are exhibited in Figure 4. The tensile strength of the PLA biocomposites was inversely proportional to the chitosan content. However, the modified biocomposites showed a higher tensile strength than that of the unmodified biocomposites at a similar chitosan content. The tensile strength of the modified biocomposites improved by 36.43% as compared with the unmodified ones, indicating the enhanced filler-matrix interfacial interaction. This enhanced strength was clearly attributed to the high reactivity of PAA-g-OSL, which effectively facilitated surface modification, resulting in improved interfacial adhesion.
Polymers 2021, 13, x FOR PEER REVIEW 7 of 14 the composites' strength. Although chemical modification had no effect on the stress-versus-strain trace character of the modified biocomposites, it did influence the measured strength at failure. The tensile strength of unmodified and modified PLA/chitosan biocomposites at various fiber loading are exhibited in Figure 4. The tensile strength of the PLA biocomposites was inversely proportional to the chitosan content. However, the modified biocomposites showed a higher tensile strength than that of the unmodified biocomposites at a similar chitosan content. The tensile strength of the modified biocomposites improved by 36.43% as compared with the unmodified ones, indicating the enhanced filler-matrix interfacial interaction. This enhanced strength was clearly attributed to the high reactivity of PAAg-OSL, which effectively facilitated surface modification, resulting in improved interfacial adhesion.   Figure 5 shows the Young's modulus of unmodified and modified PLA biocomposites at different chitosan loading. The Young's modulus of the PLA/chitosan biocomposites increased as the chitosan content increased. The dispersion of chitosan fiber within the PLA matrix clearly improved the composite's stiffness, indicating the limited segmental molecular mobility of the PLA chain upon interacting with the fiber. The Young's modulus of the modified biocomposites was remarkably higher than the unmodified biocomposites. It increased by 55.33% as compared with the unmodified ones. The rigid nature of the filler, the high crystallinity index, and the presence of the modifying agent played an essential role in the improvement of the Young's modulus of the PLA biocomposites. The presence of esterified lignin improves the stiffness of the biocomposites by increasing the filler-matrix interfacial adhesion.
Polymers 2021, 13, x FOR PEER REVIEW Figure 5 shows the Young's modulus of unmodified and modified PLA bio sites at different chitosan loading. The Young's modulus of the PLA/chitosan bio sites increased as the chitosan content increased. The dispersion of chitosan fibe the PLA matrix clearly improved the composite's stiffness, indicating the limited s tal molecular mobility of the PLA chain upon interacting with the fiber. The Young ulus of the modified biocomposites was remarkably higher than the unmodified b posites. It increased by 55.33% as compared with the unmodified ones. The rigid of the filler, the high crystallinity index, and the presence of the modifying agent an essential role in the improvement of the Young's modulus of the PLA biocom The presence of esterified lignin improves the stiffness of the biocomposites by inc the filler-matrix interfacial adhesion.

SEM Image Analysis
Morphological images of the tensile fractured surfaces of the PLA matrix, u fied PLA biocomposite containing 20 php and 40 php of chitosan fiber, and modif composite filled with 40 php of chitosan fiber, are shown in Figure 6A-D, respe The surface of the PLA matrix was quite smooth, as seen in the SEM image (Figur few voids, on the other hand, appeared on the fractured surface of the unmodif composite ( Figure 6B,C), exhibiting the fiber pulled out from the matrix phase. It to the matrix's poor wetting of the filler, which could lead to the breakage at the i of the chitosan and the PLA matrix. The difference in the affinities between both nents has resulted in weak interaction at the interface. Meanwhile, a relatively surface with fewer voids was seen on the fracture surface of the modified bioco ( Figure 6D). This was clearly related to a good wetting of the filler by the matrix s PAA-g-OSL modifying agents substantially modified the chitosan surface to beco hydrophilic, leading to improved interaction with the polymer matrix. As a res modified composites had significantly fewer detached filler traces from the matri

SEM Image Analysis
Morphological images of the tensile fractured surfaces of the PLA matrix, unmodified PLA biocomposite containing 20 php and 40 php of chitosan fiber, and modified PLA composite filled with 40 php of chitosan fiber, are shown in Figure 6A-D, respectively. The surface of the PLA matrix was quite smooth, as seen in the SEM image ( Figure 6A). A few voids, on the other hand, appeared on the fractured surface of the unmodified biocomposite ( Figure 6B,C), exhibiting the fiber pulled out from the matrix phase. It pointed to the matrix's poor wetting of the filler, which could lead to the breakage at the interface of the chitosan and the PLA matrix. The difference in the affinities between both components has resulted in weak interaction at the interface. Meanwhile, a relatively smooth surface with fewer voids was seen on the fracture surface of the modified biocomposite ( Figure 6D). This was clearly related to a good wetting of the filler by the matrix since the PAA-g-OSL modifying agents substantially modified the chitosan surface to become less-hydrophilic, leading to improved interaction with the polymer matrix. As a result, the modified composites had significantly fewer detached filler traces from the matrix phase.  Figure 7A,B show the TGA and DTG curves of neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites, respectively. The thermal decomposition of neat PLA occurred over a one-stage process between 300 and 415 °C, leading to the formation of gaseous products. This degradation pathway was associated with the molecular structure of PLA that is composed of carbon-carbon linkages, where the degradation/depolymerisation occurs at the weak sites within the PLA backbone chain [35]. On the other hand, the PLA/chitosan biocomposites demonstrated three distinct stages of thermal decomposition. They were observed within the temperature ranges of 160-180 °C, 260-340 °C, and 400-490 °C, respectively. The similarity in the general patterns was exemplified by these typical thermograms. However, the biocomposites were indicated by their distinct temperature and weight losses. The first stage involved the release of typical strong hydrogen-bonded water and the evaporation of volatile compounds from the samples, while the second stage included the degradation and depolymerization of both the chitosan fiber and a modifying agent. The third stage could be attributed to the decomposition of char residue formed in the second stage.  Figure 7A,B show the TGA and DTG curves of neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites, respectively. The thermal decomposition of neat PLA occurred over a one-stage process between 300 and 415 • C, leading to the formation of gaseous products. This degradation pathway was associated with the molecular structure of PLA that is composed of carbon-carbon linkages, where the degradation/depolymerisation occurs at the weak sites within the PLA backbone chain [35]. On the other hand, the PLA/chitosan biocomposites demonstrated three distinct stages of thermal decomposition. They were observed within the temperature ranges of 160-180 • C, 260-340 • C, and 400-490 • C, respectively. The similarity in the general patterns was exemplified by these typical thermograms. However, the biocomposites were indicated by their distinct temperature and weight losses. The first stage involved the release of typical strong hydrogen-bonded water and the evaporation of volatile compounds from the samples, while the second stage included the degradation and depolymerization of both the chitosan fiber and a modifying agent. The third stage could be attributed to the decomposition of char residue formed in the second stage.

Thermal Properties of PLA/Chitosan Biocomposites
The weight loss percentage for neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites are tabulated in Table 3. An analysis of the weight loss data shows that 10% of the weight loss occurred at 328 • C for the unmodified biocomposites, and at 335 • C for the modified biocomposites. The temperature increased to 414 • C for the unmodified biocomposites, and to 440 • C for the modified biocomposites, when the weight loss was 50%. The obtained results clearly indicate that the modified biocomposites were more thermally stable than the unmodified ones. The attachment of the PAA-g-OSL modifying agent on the chitosan surface enabled it to perform as a thermal protective barrier for the biocomposites against thermo-decomposition.
160-180 °C, 260-340 °C, and 400-490 °C, respectively. The similarity in the general patterns was exemplified by these typical thermograms. However, the biocomposites were indicated by their distinct temperature and weight losses. The first stage involved the release of typical strong hydrogen-bonded water and the evaporation of volatile compounds from the samples, while the second stage included the degradation and depolymerization of both the chitosan fiber and a modifying agent. The third stage could be attributed to the decomposition of char residue formed in the second stage.  Lignin is composed of a three-dimensional network of aromatic structures that can slow down the thermo-decomposition of polymeric materials. This, along with the complex heterogeneity of the chemical bonds in the cross-linked aromatic and aliphatic structures, is one of its primary defences against decomposition [36]. Furthermore, the data indicates that the modified biocomposites had higher thermal stability than the unmodified biocomposites. Despite the fact that chemical modification had no effect on the thermal decomposition mechanism of the PLA/chitosan biocomposites, the resulting different degradation profiles is indicative of the changing of the chemical structure and the thermal stability. Figure 8 exhibits the DSC curves for neat PLA, unmodified PLA biocomposites, and modified PLA biocomposites, respectively. Table 4 provides the melting temperature (T m ), the glass transition temperature (T g ), crystallization temperature (T c ), and the degree of crystallinity (X c ) of all biocomposite categories. For all biocomposite categories, the endothermic peak was observed at a maximum temperature range of 150 to 155 • C. Neat PLA had a T g of 57.6 • C, and a T m of 152 • C. The addition of chitosan fiber increased both the T g and T m of neat PLA, while the crystallinity degree (X c ) value slightly declined. This decreased crystallinity indicated that the addition of chitosan in PLA biocomposites apparently became an obstacle for the nuclei crystal growth of the PLA chain, causing the crystallization process to be hindered. [37]. In addition, a crystallization peak (T c ) also appeared at a temperature of 115 • C, corresponding to the formation of the metastable crystalline phase within the biocomposites.  On the other hand, a higher endothermic heat flow was observed fo biocomposites as compared to that for the unmodified biocomposites. Bot of the modified biocomposites demonstrated a slight decrease; however, t ously higher than that of the unmodified ones. It is thought that the presen OSL-based modifying agent improved the interfacial interaction between t the PLA matrix, contributing significantly to the increased crystallinity o biocomposites. It should be noted that the hydrophobic segment belongin lignin may contribute to the effectiveness of the nucleation process, as we of the spherulitic structure in PLA biocomposites. The aromatic molecula the chemical composition of organosolv lignin are expected as factors th the nucleation process. A previous study reported that some crystallizati when the fibers used contain sufficient quantities of lignin [38]. Nonethe not show a significant change.  Table 4. DSC data obtained for unmodified and modified PLA/chitosan biocomposites. On the other hand, a higher endothermic heat flow was observed for the modified biocomposites as compared to that for the unmodified biocomposites. Both the T g and T c of the modified biocomposites demonstrated a slight decrease; however, the X c was obviously higher than that of the unmodified ones. It is thought that the presence of a PAA-g-OSL-based modifying agent improved the interfacial interaction between the chitosan and the PLA matrix, contributing significantly to the increased crystallinity of the modified biocomposites. It should be noted that the hydrophobic segment belonging to organosolv lignin may contribute to the effectiveness of the nucleation process, as well as the growth of the spherulitic structure in PLA biocomposites. The aromatic molecular structure and the chemical composition of organosolv lignin are expected as factors that can enhance the nucleation process. A previous study reported that some crystallization might occur when the fibers used contain sufficient quantities of lignin [38]. Nonetheless, the T m did not show a significant change. Figure 9 exhibits the weight loss rate of neat PLA, unmodified PLA/chitosan biocomposites, and modified PLA/chitosan biocomposites as a function of the biodegradation days. As time passed, all the biocomposite categories degraded further, as evidenced by the increase in weight loss. The degradation of neat PLA was slower as compared to that of the two-biocomposite category. On the other hand, the addition of chitosan fiber apparently contributed to the increase in the biodegradation rate of the PLA biocomposites. The weight loss of the unmodified biocomposites was found to be about two-fold greater than that of the neat PLA, which confirmed the chitosan fiber dispersion within the PLA matrix and remarkably enhanced the degradation rate of the biocomposites. The chitosan fiber contributed to the high polarity of the biocomposites, resulting in decreased tensile strength. The improved biodegradation rate of the PLA/chitosan biocomposites was most likely because of the existence of the hydroxyl and amine groups belonging to chitosan, which, when dispersed in PLA, play a critical role in provoking the increasing hydrolytic degradation of the PLA main chain [39]. On the other hand, the biodegradation rates of the modified PLA/chitosan biocomposites were lower than that of the unmodified biocomposites, demonstrating that the chemical modification essentially enhanced the barrier performances of the composites and limited enzyme diffusion. The enhanced interfacial interaction between the PLA matrix and the chitosan fiber resulted from the PAA-g-OSL modifying effects, which decreased the area degraded through enzyme hydrolysis, leading to lower biodegradation rates.

Weight Loss Analysis
Polymers 2021, 13, x FOR PEER REVIEW 1 strength. The improved biodegradation rate of the PLA/chitosan biocomposites wa likely because of the existence of the hydroxyl and amine groups belonging to chi which, when dispersed in PLA, play a critical role in provoking the increasing hyd degradation of the PLA main chain [39]. On the other hand, the biodegradation ra the modified PLA/chitosan biocomposites were lower than that of the unmodifie composites, demonstrating that the chemical modification essentially enhanced th rier performances of the composites and limited enzyme diffusion. The enhanced in cial interaction between the PLA matrix and the chitosan fiber resulted from the P OSL modifying effects, which decreased the area degraded through enzyme hydr leading to lower biodegradation rates. One of the most important practical criteria for determining material degrada the loss of mechanical properties. Table 5 provides tensile strength and the Young's ulus of neat PLA, unmodified PLA/chitosan biocomposite, and modified PLA/ch biocomposite at a 0-and 30-day biodegradation time. Before immersion in the en containing solution, the tensile strength of neat PLA was observed to have decr along with the addition of 20 php of chitosan fiber. On the other hand, the Young's ulus improved. The presence of PAA-g-OSL on the chitosan surface contributed improvement in the tensile strength and the Young's modulus of the modified bioco sites as compared to the unmodified biocomposite. The results show a decrease tensile strength and the Young's modulus after 30 days of biodegradation. The act the enzyme in the solution resulted in the apparent partial destruction of filler-matr hesion, void formation, and the subsequent random chain scission in the polymer c resulting in the decreased tensile properties. Table 5. Tensile strength and Young's modulus of neat PLA, PLA/chitosan biocomposites, with and without treatment, a 0-and 30-day biodegradation times. One of the most important practical criteria for determining material degradation is the loss of mechanical properties. Table 5 provides tensile strength and the Young's modulus of neat PLA, unmodified PLA/chitosan biocomposite, and modified PLA/chitosan biocomposite at a 0-and 30-day biodegradation time. Before immersion in the enzyme-containing solution, the tensile strength of neat PLA was observed to have decreased along with the addition of 20 php of chitosan fiber. On the other hand, the Young's modulus improved. The presence of PAA-g-OSL on the chitosan surface contributed to the improvement in the tensile strength and the Young's modulus of the modified biocomposites as compared to the unmodified biocomposite. The results show a decrease in the tensile strength and the Young's modulus after 30 days of biodegradation. The action of the enzyme in the solution resulted in the apparent partial destruction of filler-matrix adhesion, void formation, and the subsequent random chain scission in the polymer chains, resulting in the decreased tensile properties.

Conclusions
PLA-chitosan biocomposites modified with PAA-g-OSL were prepared. The properties of the modified biocomposites were investigated and are briefly discussed. The obtained organosolv lignin had a low molecular weight, which resulted in a higher efficiency of chitosan modification of up to 21.3%. The PAA-g-OLS-based modifying agent significantly altered the chitosan surface, resulting in improved interfacial adhesion within the biocomposites. The mechanical strength of the modified biocomposites was greater than the mechanical strength of the unmodified biocomposites. The SEM images clearly show that the modified biocomposites had fewer voids on their tensile surface. The TGA and DSC results show that the modified biocomposites had improved thermal stability and crystallinity. Moreover, the modified biocomposites had a higher crystallinity degree than the unmodified biocomposites. Overall, the obtained results clearly suggest the advantages in utilizing grafted organosolv lignin-based modifying agents, and other lignin derivatives, in the manufacturing of natural fiber-reinforced biocomposite materials, thereby opening up the "door" to the potential for a renewable low-cost chemical reagent alternative to synthetic reagents.