Preparation of Poly(L-lactide)-b-poly(ethylene glycol)-b-poly(L-lactide)/Zinc Oxide Nanocomposite Bioplastics for Potential Use as Flexible and Antibacterial Food Packaging

High-molecular-weight poly(L-lactide)-b-poly(ethylene glycol)-b-poly(L-lactide) (PLLA-PEG-PLLA) is a flexible and biodegradable bioplastic that has promising potential in flexible food packaging but it has no antibacterial ability. Thus, in this work, the effect of zinc oxide nanoparticles (nano-ZnOs) which have antimicrobial activity on various properties of PLLA-PEG-PLLA was determined. The addition of nano-ZnOs enhanced the crystallization, tensile, UV-barrier, and antibacterial properties of PLLA-PEG-PLLA. However, the crystallization and tensile properties of nanocomposite films decreased again as the nano-ZnO increased beyond 2 wt%. The nano-ZnO was well distributed in the PLLA-PEG-PLLA matrix when the nano-ZnO content did not exceed 2 wt% and exhibited some nano-ZnO agglomerates when the nano-ZnO content was higher than 2 wt%. The thermal stability and moisture uptake of the PLLA-PEG-PLLA matrix decreased and the film’s opacity increased as the nano-ZnO content increased. The PLLA-PEG-PLLA/ZnO nanocomposite films showed good antibacterial activity against bacteria such as Escherichia coli and Staphylococcus aureus. It can be concluded that nano-ZnOs can be used as a multi-functional filler of the flexible PLLA-PEG-PLLA. As a result, the addition of nano-ZnOs as a nucleating, reinforcing, UV-screening, and antibacterial agent in the flexible PLLA-PEG-PLLA matrix may provide protection for both the food and the packaging during transportation and storage.


Introduction
In the past few decades, biodegradable plastics have been extensively investigated for use as food packaging in place of non-biodegradable petroleum-based plastics because they might circumvent the serious problems of plastic waste.Furthermore, biodegradable bio-based plastics, also known as biodegradable bioplastics, have received a lot of attention for use as food packaging because of their environmentally friendly properties such as biocompatibility, renewability, and sustainability, etc. [1][2][3].Among biodegradable bioplastics, poly(L-lactic acid) or poly(L-lactide) (PLLA) synthesized from bio-derived L-lactic acid is the one that has received the most attention.The reason for this is that PLLA has good thermal processability [3][4][5], good mechanical properties [6], and market availability [7].Therefore, PLLA demonstrates acceptable qualities for food packaging that involves food contact.
For food packaging, maintaining the freshness and quality of the food during transportation and storage is important, and will extend the shelf life of food and also reduce food waste [3,8,9].Thus, antimicrobial packaging was developed in order to extend the Polymers 2024, 16, 1660 2 of 19 shelf life storage of food and reduce food waste [1,3].PLLA-based materials with antimicrobial ability for use in food packaging applications have been prepared by incorporating various antimicrobial agents [1].
However, a major disadvantage of PLLA that limits its widespread use is its low flexibility due to its high glass-transition-temperature (T g about 60 • C) [28].High-molecularweight PLLA-b-poly(ethylene glycol)-b-PLLA (PLLA-PEG-PLLA) triblock copolymers exhibited greater flexibility than the PLLA [28,29].The PEG middle-blocks acted as plasticizing sites to decrease the T g of PLLA end-blocks.The PEG chains are biocompatible and biodegradable and are FDA-approved materials [30].Moreover, PLLA-PEG-PLLA showed a faster biodegradation rate than PLLA due to the hydrophilicity of PEG middleblocks [31].Therefore, the biodegradable PLLA-PEG-PLLA has great potential as singleuse food packaging materials with excellent flexibility.However, PLLA-PEG-PLLA/ZnO nanocomposites with antimicrobial properties have not been prepared and reported so far.
In this study, we propose flexible and antibacterial PLLA-PEG-PLLA, in which are incorporated nano-ZnOs as antimicrobial agents.The PLLA-PEG-PLLA nanocomposites containing nano-ZnOs in the range of 1 wt% to 4 wt% were prepared for the first time by a melt blending method.The effect of the nano-ZnO content on crystallization, thermal decomposition, morphological, mechanical, UV-barrier, and antibacterial properties of the PLLA-PEG-PLLA were investigated and compared with the pure PLLA-PEG-PLLA.In particular, the goal of this work was to prepare flexible and biodegradable materials for use in food packaging with improved crystallization, mechanical, UV-barrier, and antibacterial properties.

Materials
High-molecular-weight PLLA-PEG-PLLA was synthesized through in situ chain extension and ring-opening polymerization of L-lactide monomer in the presence of 2.0 phr chain extender at 165 • C for 6 h, as previously described by us [32,33].PEG with molecular weight of 20,000 and stannous octoate were used as the initiating system.Joncryl TM ADR-4368 (BASF, Bangkok, Thailand) was used as a chain extender.The number-averaged molecular weight (M n ) and dispersity (Ð) obtained from gel permeation chromatography (GPC) of the PLLA-PEG-PLLA were 108,500 and 2.2, respectively [33].ZnO nanoparticles (nano-ZnOs) with purity of 99.5% and averaged particle size of 33 nm were purchased from Nanoscience Technology Co., Ltd.(Bangkok, Thailand) and used without further purification.Figure 1 shows an SEM image of ZnO nanoparticles.

Preparation of PLLA-PEG-PLLA/ZnO Nanocomposites
PLLA-PEG-PLLA/ZnO nanocomposites were prepared by melt blending using an internal mixer (HAAKE, Polylab OS System, Waltham, MA, USA) at 190 °C for 10 min with a rotor speed of 100 rpm.Both the PLLA-PEG-PLLA and the nano-ZnO were dried in a vacuum oven at 50 °C overnight to remove residue moisture before melt blending.Nano-ZnO contents of 1 wt%, 2 wt%, 3 wt%, and 4 wt% were investigated.Nanocomposite films with 0.2-0.3mm thickness were prepared by compression molding using a compression molding machine (Carver, Auto CH, Wabash, IN, USA).The nanocomposites were dried in a vacuum oven at 50 °C overnight to remove residual moisture before compression molding.The nanocomposites were heated at 190 °C for 3 min without compression force before compressing under 5 MPa load for 3 min.The resulting films were then cooled with water-cooled plates under 5 MPa load for 3 min.The obtained films were kept in a desiccator at room temperature for 24 h before characterization.For comparison, the pure PLLA-PEG-PLLA film was also prepared by the same conditions.

Characterization of PLLA-PEG-PLLA/ZnO Nanocomposites
Thermal transition properties of the samples were determined with a non-isothermal and isothermal differential scanning calorimeter (DSC) (PerkinElmer, Pyris Diamond, Waltham, MA, USA) under a nitrogen flow.For DSC heating scans, the samples were maintained at 200 °C for 3 min to remove thermal history before quickly quenching to 0 °C.The samples were then scanned from 0 °C to 200 °C at a heating rate of 10 °C/min under a nitrogen flow.The samples were then scanned from 200 °C to 0 °C at a cooling rate of 10 °C/min for DSC cooling scans.
The degree of crystallinity of the samples from DSC (DSC−Xc) of PLLA crystallites was determined from DSC heating scans using the following equation.

Preparation of PLLA-PEG-PLLA/ZnO Nanocomposites
PLLA-PEG-PLLA/ZnO nanocomposites were prepared by melt blending using an internal mixer (HAAKE, Polylab OS System, Waltham, MA, USA) at 190 • C for 10 min with a rotor speed of 100 rpm.Both the PLLA-PEG-PLLA and the nano-ZnO were dried in a vacuum oven at 50 • C overnight to remove residue moisture before melt blending.Nano-ZnO contents of 1 wt%, 2 wt%, 3 wt%, and 4 wt% were investigated.Nanocomposite films with 0.2-0.3mm thickness were prepared by compression molding using a compression molding machine (Carver, Auto CH, Wabash, IN, USA).The nanocomposites were dried in a vacuum oven at 50 • C overnight to remove residual moisture before compression molding.The nanocomposites were heated at 190 • C for 3 min without compression force before compressing under 5 MPa load for 3 min.The resulting films were then cooled with water-cooled plates under 5 MPa load for 3 min.The obtained films were kept in a desiccator at room temperature for 24 h before characterization.For comparison, the pure PLLA-PEG-PLLA film was also prepared by the same conditions.

Characterization of PLLA-PEG-PLLA/ZnO Nanocomposites
Thermal transition properties of the samples were determined with a non-isothermal and isothermal differential scanning calorimeter (DSC) (PerkinElmer, Pyris Diamond, Waltham, MA, USA) under a nitrogen flow.For DSC heating scans, the samples were maintained at 200 • C for 3 min to remove thermal history before quickly quenching to 0 • C. The samples were then scanned from 0 • C to 200 • C at a heating rate of 10 • C/min under a nitrogen flow.The samples were then scanned from 200 • C to 0 • C at a cooling rate of 10 • C/min for DSC cooling scans.
The degree of crystallinity of the samples from DSC (DSC-X c ) of PLLA crystallites was determined from DSC heating scans using the following equation.
where ∆H m and ∆H cc are the enthalpies of melting and cold crystallization, respectively, and 93.6 J/g is 100% DSC-X c of PLLA [34].W PLLA is the weight fraction of PLLA.
For isothermal DSC scans, the samples were cooled from 200 • C to 120 • C at a rate of 50 • C/min after melting at 200 • C for 3 min to remove thermal history.The samples were then isothermally scanned at 120 • C until they were completely crystallized.
Thermal decomposition properties of the samples were characterized with a nonisothermal thermogravimetric analyzer (TGA) (TA-Instruments, SDT Q600, New Castle, DE, USA).For the TGA test, a sample (~10 mg) was scanned from 50 • C to 800 • C at a heating rate of 20 • C/min under a nitrogen flow.
Phase morphology of the film samples was observed from the cryo-fractured film surfaces with a scanning electron microscope (SEM) (JEOL, JSM-6460LV, Tokyo, Japan) at 20 kV.The film samples were sputter-coated with gold before SEM analysis.
Crystalline structures of the film samples were determined with a wide-angle X-ray diffractometer (XRD) (Bruker Corporation, D8 Advance, Karlsruhe, Germany) with a CuKα radiation of 40 kV and 40 mA.Scan speed was 3 • /min.The degree of crystallinity of film samples from XRD (XRD−X c ) was calculated using the following equation.
where A c is the peak area of PLLA crystallites and A a is the halo area of the amorphous phase.Mechanical properties comprising ultimate tensile stress, strain at break, and Young's modulus of the film samples were measured with a universal testing machine (Dongguan Liyi Environmental Technology Co., Ltd., LY-1066B, Dongguan, China) according to the standard test method of American Society for Testing and Materials (ASTM) standard: designation of D882.Film samples with 10 mm width were tested at 25 • C and 50% relative humidity with a gauge length of 50 mm, a speed tensile test of 50 mm/min, and a load cell of 100 kg.The tensile properties were averaged from five measurements.
Opacity of the film samples was determined from absorbance at a wavelength of 600 nm (A 600 ) measured with a UV-vis spectrophotometer (Agilent Technologies, Cary 60, Mulgrave, VIC, Australia).The following equation was used to calculate the opacity of film samples [35,36].The opacity value was averaged from three determinations.

Opacity (mm
where A 600 is the film's absorbance at a wavelength of 600 nm and X is the film's thickness (mm).
The UV-barrier property of the film samples was determined with a UV-vis spectrophotometer (Agilent Technologies, Cary 60, Mulgrave, VIC, Australia) at a wavelength range of 200 nm to 550 nm [15].
Moisture uptake of the film samples (20 mm × 20 mm) was investigated by placing the film sample in a desiccator with 90 ± 5% relative humidity maintained with a saturated sodium chloride solution at 25 • C. At time intervals (1,3,6,12,24, and 48 h), the weight of film samples was determined.Prior to testing, the film samples were dried in a vacuum oven at room temperature for 48 h before weighing.The following equation was used to calculate the moisture uptake of film samples [37].The averaged moisture uptake was obtained from three different measurements.

Moisture uptake (
where W i and W f are the weights of film samples before and after test. The antibacterial properties of the film samples were evaluated using Gram-negative E. coli TISTR 780 and Gram-positive S. aureus TISTR 1466.A single colony of each bacterium was propagated in nutrient broth (NB) under agitation at 37 • C for 18 h.Before utilization, the bacterial concentration was meticulously adjusted to an absorbance at 600 nm wavelength (A 600 ) of 0.1.The film samples with 10 mm diameter were rendered sterile by submersion in 95% ethanol, followed by a drying period of 10 min under ultraviolet light.Subsequently, 100 µL of bacterial suspension, adjusted to A 600 of 0.1, was evenly distributed onto nutrient agar (NA).The film samples were then placed on the surface of the NA, which had been spread with bacteria.The plates were incubated at 37 • C for 18 h after which the diameter of the inhibition zone for each film was meticulously measured (mm) and documented.The diameter of inhibition zone was averaged from triplicate tests.

Thermal Transition Properties
The thermal transition properties of the pure PLLA-PEG-PLLA and PLLA-PEG-PLLA/ZnO nanocomposites were investigated by isothermal and non-isothermal DSCs.The DSC heating curves of the samples are compared in Figure 2 and their DSC results are summarized in Table 1.It was found that T g and T m values were in the range of 29-32 • C and 157-160 • C, respectively.Figure 3 shows the T g regions of the DSC heating curves.The T cc and DSC-X c values of pure PLLA-PEG-PLLA were 81 • C and 13.4%, respectively.Table 1 shows that the T cc peaks shifted from 81 • C to 64 • C when the 1 wt% nano-ZnO was incorporated and the T cc peak disappeared when the 2 wt% nano-ZnO was incorporated.Shifting to lower temperatures of T cc peaks indicated that the cold crystallization of PLLA end-blocks can occur at lower temperatures [25,36].The disappearance of T cc peaks in DSC heating scans of the nanocomposites suggested a heterogeneous nucleation effect had occurred by addition of a nucleating agent [34].This result could indicate that PLLA crystallization was accelerated by the added nano-ZnO.In addition, the DSC-X c values of nanocomposites largely increased as the nano-ZnO content increased up to 2 wt%.This supports the suggestion that the nano-ZnO induced a heterogeneous nucleating effect for PLLA-PEG-PLLA, thereby increasing the number of heterogeneous nucleation sites [38].Table 1.Results from DSC heating curves of pure PLLA-PEG-PLLA and PLLA-PEG-PLLA/ZnO nanocomposites.2. The pure PLLA-PEG-PLLA had Tc and ΔHc values of 99 °C and 1 J/g, respectively.Table 2 also indicates that the Tc peaks shifted to higher temperatu and the ΔHc values increased as the nano-ZnO content increased up to 2 wt%.This s ports a nucleation effect for PLLA-PEG-PLLA occurring during DSC cooling scans, wh was enhanced by the added nano-ZnO, as attested by the increasing Tc and ΔHc val However, the T cc peaks shifted to higher temperatures again and the DSC-X c values decreased again when the nano-ZnO content increased beyond 2 wt%.This may have been due to the ZnO nanoparticles becoming agglomerated to reduce the effective nucleation during PLLA-PEG-PLLA's crystallization, which SEM analysis will subsequently verify.In addition, the excessive nano-ZnO in the PLLA crystalline phase may have caused the compact structure of PLLA crystals to break [36].

Nano-ZnO Content (wt%)
Figure 4 compares DSC cooling curves of the samples and their DSC results are summarized in Table 2.The pure PLLA-PEG-PLLA had T c and ∆H c values of 99 • C and 10.5 J/g, respectively.Table 2 also indicates that the T c peaks shifted to higher temperatures and the ∆H c values increased as the nano-ZnO content increased up to 2 wt%.This supports a nucleation effect for PLLA-PEG-PLLA occurring during DSC cooling scans, which was enhanced by the added nano-ZnO, as attested by the increasing T c and ∆H c values [38][39][40].However, the T c peaks shifted to lower temperatures again and the ∆H c values decreased again when the nano-ZnO content exceeded 2 wt%.The results of DSC cooling curves confirmed that the nano-ZnO in the range of 1-2 wt% enhanced nucleating effects for PLLA-PEG-PLLA according to the results of the above DSC heating analysis.
Polymers 2024, 16, 1660 7 of 19 [38][39][40].However, the Tc peaks shifted to lower temperatures again and the ΔHc values decreased again when the nano-ZnO content exceeded 2 wt%.The results of DSC cooling curves confirmed that the nano-ZnO in the range of 1-2 wt% enhanced nucleating effects for PLLA-PEG-PLLA according to the results of the above DSC heating analysis.The nucleation effect of added nano-ZnO on PLLA-PEG-PLLA matrices was also investigated from isothermal DSC scans at 120 °C as shown in Figure 5a.It can be seen that the isothermal crystallization-peaks significantly shifted to shorter times when the nano-ZnO content increased up to 2 wt%, suggesting that the crystallization of PLLA-PEG-PLLA was accelerated [41].This was followed by the isothermal crystallization-peaks shifting to longer times again as the nano-ZnO content increased beyond 2 wt%, suggesting that the crystallization of PLLA-PEG-PLLA was decelerated.Polymer samples with a 50% relative crystallinity were obtained at the crystallization half-time (t1/2) through isothermal DSC scans as indicated in Figure 5b.The pure PLLA-PEG-PLLA had a t1/2 value of 3.5 min.The resulting t1/2 values of nanocomposites with nano-ZnO contents of 1 wt%, 2 wt%, 3 wt%, and 4 wt% were 2.0, 1.9, 2.4, and 2.9 min, respectively.It can be seen that the t1/2 values steadily decreased when the nano-ZnO content increased up to 2 wt%, followed by increasing the t1/2 value again as the nano-ZnO content increased beyond 2 wt%.The results of DSC isothermal scans confirmed that the nano-ZnO in the range of 1-2 wt% enhanced the heterogeneous nucleation effect for PLLA-PEG-PLLA according to the results of the above DSC heating and cooling analyses.From the DSC results, it can be  The nucleation effect of added nano-ZnO on PLLA-PEG-PLLA matrices was also investigated from isothermal DSC scans at 120 • C as shown in Figure 5a.It can be seen that the isothermal crystallization-peaks significantly shifted to shorter times when the nano-ZnO content increased up to 2 wt%, suggesting that the crystallization of PLLA-PEG-PLLA was accelerated [41].This was followed by the isothermal crystallization-peaks shifting to longer times again as the nano-ZnO content increased beyond 2 wt%, suggesting that the crystallization of PLLA-PEG-PLLA was decelerated.Polymer samples with a 50% relative crystallinity were obtained at the crystallization half-time (t 1/2 ) through isothermal DSC scans as indicated in Figure 5b.The pure PLLA-PEG-PLLA had a t 1/2 value of 3.5 min.The resulting t 1/2 values of nanocomposites with nano-ZnO contents of 1 wt%, 2 wt%, 3 wt%, and 4 wt% were 2.0, 1.9, 2.4, and 2.9 min, respectively.It can be seen that the t 1/2 values steadily decreased when the nano-ZnO content increased up to 2 wt%, followed by increasing the t 1/2 value again as the nano-ZnO content increased beyond 2 wt%.The results of DSC isothermal scans confirmed that the nano-ZnO in the range of 1-2 wt% enhanced the heterogeneous nucleation effect for PLLA-PEG-PLLA according to the results of the above DSC heating and cooling analyses.From the DSC results, it can be concluded that the crystallization properties of the nanocomposites can be improved by low incorporation (up to 2 wt%) of nano-ZnO within the PLLA-PEG-PLLA matrix.

Thermal Decomposition Properties
The thermal decomposition properties of the pure PLLA-PEG-PLLA and PLLA-PE PLLA/ZnO nanocomposites were determined from the mean of TGA as shown in Fig 6 .The TGA results are summarized in Table 3. Thermal decomposition behavior of pure PLLA-PEG-PLLA exhibited two decomposition steps of PLLA (250-350 °C) and P (350-450 °C) blocks.The pure PLLA-PEG-PLLA had a decomposition temperature at weight loss (5%-Td) from a thermogravimetric (TG) thermogram at 282 °C (Figure 6a).T 5%-Td values decreased as the nano-ZnO content increased.This suggests that the therm stability of PLLA-PEG-PLLA matrices decreased as the nano-ZnO content increased has been reported that the nano-ZnO was not completely thermally decomposed at 800 [26].Therefore, the residue weight or ash at 800 °C of the nanocomposite samples was d to nano-ZnOs.As would be expected, the residue weight at 800 °C of the nanocompo samples steadily increased as the nano-ZnO content increased.
The thermal decomposition behavior of the samples was also determined from rivative TG (DTG) thermograms as shown in Figure 6b.Peaks of decomposit

Thermal Decomposition Properties
The thermal decomposition properties of the pure PLLA-PEG-PLLA and PLLA-PEG-PLLA/ZnO nanocomposites were determined from the mean of TGA as shown in Figure 6.The TGA results are summarized in Table 3. Thermal decomposition behavior of the pure PLLA-PEG-PLLA exhibited two decomposition steps of PLLA (250-350 • C) and PEG (350-450 • C) blocks.The pure PLLA-PEG-PLLA had a decomposition temperature at 5% weight loss (5%-T d ) from a thermogravimetric (TG) thermogram at 282 • C (Figure 6a).The 5%-T d values decreased as the nano-ZnO content increased.This suggests that the thermal stability of PLLA-PEG-PLLA matrices decreased as the nano-ZnO content increased.It has been reported that the nano-ZnO was not completely thermally decomposed at 800 • C [26].Therefore, the residue weight or ash at 800 • C of the nanocomposite samples was due to nano-ZnOs.As would be expected, the residue weight at 800 • C of the nanocomposite samples steadily increased as the nano-ZnO content increased.peratures as the nano-ZnO content increased.It may be hypothesized that the ZnO nanoparticles activated depolymerization of PLLA end-blocks [27,42,43], whereas the PEG-Td,max peaks slightly shifted to lower temperatures as the nano-ZnO content increased.The TGA results support the conclusion that the addition of nano-ZnOs reduced the thermal stability of the PLLA-PEG-PLLA.However, the TGA results indicated that these nanocomposites were stable up to 250 °C, thus melt processing at 190 °C should still be possible for use in packaging applications.  Obtained from TG thermograms. 2Obtained from DTG thermograms.  1 Obtained from TG thermograms. 2Obtained from DTG thermograms.
The thermal decomposition behavior of the samples was also determined from derivative TG (DTG) thermograms as shown in Figure 6b.Peaks of decomposition temperature at the maximum rate for PLLA blocks (PLLA-T d,max ) and for PEG blocks (PEG-T d,max ) were found.The resulting PLLA-T d,max and PEG-T d,max values are also summarized in Table 3, which shows that the PLLA-T d,max peaks were significantly shifted to lower temperatures as the nano-ZnO content increased.It may be hypothesized that the ZnO nanoparticles activated depolymerization of PLLA end-blocks [27,42,43], whereas the PEG-T d,max peaks slightly shifted to lower temperatures as the nano-ZnO content increased.The TGA results support the conclusion that the addition of nano-ZnOs reduced the thermal stability of the PLLA-PEG-PLLA.However, the TGA results indicated that these nanocomposites were stable up to 250 • C, thus melt processing at 190 • C should still be possible for use in packaging applications.

Phase Morphology
Figure 7 shows SEM images of cryo-fractured film surfaces which were used to investigate their phase morphology.In the figure, ZnO nanoparticles can be observed throughout the PLLA-PEG-PLLA matrices.The nanocomposite films containing 1 wt% and 2 wt% nano-ZnO in Figure 7a,b, respectively, exhibited a good distribution of the ZnO nanoparticles in PLLA-PEG-PLLA matrices, indicative of good phase compatibility between the ZnO nanoparticles and the PLLA-PEG-PLLA matrices.The SEM results supported a conclusion that a good distribution of 1 wt% and 2 wt% nano-ZnOs enhanced the crystallization properties of PLLA-PEG-PLLA, as described in the above DSC analysis.

Phase Morphology
Figure 7 shows SEM images of cryo-fractured film surfaces which were used to investigate their phase morphology.In the figure, ZnO nanoparticles can be observed throughout the PLLA-PEG-PLLA matrices.The nanocomposite films containing 1 wt% and 2 wt% nano-ZnO in Figure 7a,b, respectively, exhibited a good distribution of the ZnO nanoparticles in PLLA-PEG-PLLA matrices, indicative of good phase compatibility between the ZnO nanoparticles and the PLLA-PEG-PLLA matrices.The SEM results supported a conclusion that a good distribution of 1 wt% and 2 wt% nano-ZnOs enhanced the crystallization properties of PLLA-PEG-PLLA, as described in the above DSC analysis.
However, the agglomeration of some ZnO nanoparticles was also observed when the nano-ZnO contents were 3 wt% and 4 wt%, as indicated by white circles in Figure 7d,e, respectively.The addition of high-content inorganic fillers usually results in the agglomeration of filler particles in polymer matrices due to differences in hydrophilicity between the filler and polymer matrices [26,27,44].The nano-ZnO agglomerates then reduced the nucleation effective for PLLA-PEG-PLLA matrices, which supported the above DSC analysis.

Crystalline Structures
The XRD profiles in Figure 8 were used to investigate the crystalline structures of film samples.The XRD profile of pure PLLA-PEG-PLLA film in Figure 8a showed a small broad peak at the 2-theta of 16.9°, which was assigned to the PLLA crystals [40].Intensities of this peak significantly increased as the nano-ZnO content increased up to 2 wt%, followed by a decrease in the peak intensities again as the nano-ZnO content increased beyond 2 wt%.For nanocomposite films containing 2 wt% and 3 wt% nano-ZnOs in Figure 8c,d, respectively, the characteristic peaks at the 2-theta of 14.9°, 19.1°, and 22.5° due to the PLLA crystals were also detected [41,45].Therefore, the crystalline structures of the PLLA end-blocks in PLLA-PEG-PLLA did not change upon the addition of nano-ZnOs.However, the agglomeration of some ZnO nanoparticles was also observed when the nano-ZnO contents were 3 wt% and 4 wt%, as indicated by white circles in Figure 7d,e, respectively.The addition of high-content inorganic fillers usually results in the agglomeration of filler particles in polymer matrices due to differences in hydrophilicity between the filler and polymer matrices [26,27,44].The nano-ZnO agglomerates then reduced the nucleation effective for PLLA-PEG-PLLA matrices, which supported the above DSC analysis.

Crystalline Structures
The XRD profiles in Figure 8 were used to investigate the crystalline structures of film samples.The XRD profile of pure PLLA-PEG-PLLA film in Figure 8a showed a small broad peak at the 2-theta of 16.9 • , which was assigned to the PLLA crystals [40].Intensities of this peak significantly increased as the nano-ZnO content increased up to 2 wt%, followed by a decrease in the peak intensities again as the nano-ZnO content increased beyond 2 wt%.For nanocomposite films containing 2 wt% and 3 wt% nano-ZnOs in Figure 8c,d, respectively, the characteristic peaks at the 2-theta of 14.9 • , 19.1 • , and 22.5 • due to the PLLA crystals were also detected [41,45].Therefore, the crystalline structures of the PLLA end-blocks in PLLA-PEG-PLLA did not change upon the addition of nano-ZnOs.
hanced the nucleation effect on film matrices according to the above DSC analysis.However, the XRD-Xc values decreased again to 27.6% and 14.4% as the nano-ZnO contents were 3 wt% and 4 wt%, respectively.This may be explained by the nano-ZnOs having agglomerated [27] as described in the above SEM analysis.The XRD results confirmed that nano-ZnOs can act as an effective nucleating agent for PLLA-PEG-PLLA when the nano-ZnO content does not exceed 2 wt%.

Tensile Properties
Tensile properties of film samples (stress at yield, stress at break, strain at break, and Young's modulus) were determined from stress-strain curves as shown in Figure 9.The tensile results are summarized in Table 4.The tensile properties of the nanocomposite film containing 4 wt% nano-ZnOs could not be measured because of its brittleness.From stress-strain curves, it is seen that all film samples exhibited a yield point, suggesting that all the film samples were highly flexible.From Table 4, the pure PLLA-PEG-PLLA film is seen to have had a stress at a yield of 21.2 MPa, a stress at break of 17.4 MPa, a strain at break of 102%, and a Young's modulus of 312 MPa.When the 1 wt% and 2 wt% nano-ZnOs were incorporated, the values of stress at yield, stress at break, and Young's modulus of nanocomposite films significantly increased compared to the pure PLLA-PEG-PLLA film.This indicates the added ZnO nanoparticles induced a reinforcing effect that improved these tensile properties of PLLA-PEG-PLLA matrices.The fine distribution of filler particles in the polymer matrix and good interfacial adhesion between the filler particles and the polymer matrix enhanced the mechanical properties of the polymer matrices [13,36,44].
However, the values of stress at yield, stress at break, and Young's modulus of nanocomposite films dramatically decreased when 3 wt% nano-ZnOs were incorporated compared to the pure PLLA-PEG-PLLA film.This may be explained by the agglomeration of nano-ZnOs at a high content, leading to the non-homogeneity of the nanocomposite films that reduced stress transfer between the polymer matrices and filler [46,47].The strains at break of PLLA-PEG-PLLA films steadily decreased as the ZnO content increased compared to the pure PLLA-PEG-PLLA film because the reinforcing effect of inorganic filler limits the mobility and ductile flow of the polymer chains [44,48].It should be noted that The pure PLLA-PEG-PLLA film had an XRD-X c value of 10.3%.The XRD-X c values of PLLA-PEG-PLLA film matrices increased to 19.4% and 39.0% as 1 wt% and 2 wt% nano-ZnOs were incorporated, respectively.This supports the contention that nano-ZnOs enhanced the nucleation effect on film matrices according to the above DSC analysis.However, the XRD-X c values decreased again to 27.6% and 14.4% as the nano-ZnO contents were 3 wt% and 4 wt%, respectively.This may be explained by the nano-ZnOs having agglomerated [27] as described in the above SEM analysis.The XRD results confirmed that nano-ZnOs can act as an effective nucleating agent for PLLA-PEG-PLLA when the nano-ZnO content does not exceed 2 wt%.

Tensile Properties
Tensile properties of film samples (stress at yield, stress at break, strain at break, and Young's modulus) were determined from stress-strain curves as shown in Figure 9.The tensile results are summarized in Table 4.The tensile properties of the nanocomposite film containing 4 wt% nano-ZnOs could not be measured because of its brittleness.From stress-strain curves, it is seen that all film samples exhibited a yield point, suggesting that all the film samples were highly flexible.From Table 4, the pure PLLA-PEG-PLLA film is seen to have had a stress at a yield of 21.2 MPa, a stress at break of 17.4 MPa, a strain at break of 102%, and a Young's modulus of 312 MPa.When the 1 wt% and 2 wt% nano-ZnOs were incorporated, the values of stress at yield, stress at break, and Young's modulus of nanocomposite films significantly increased compared to the pure PLLA-PEG-PLLA film.This indicates the added ZnO nanoparticles induced a reinforcing effect that improved these tensile properties of PLLA-PEG-PLLA matrices.The fine distribution of filler particles in the polymer matrix and good interfacial adhesion between the filler particles and the polymer matrix enhanced the mechanical properties of the polymer matrices [13,36,44].
However, the values of stress at yield, stress at break, and Young's modulus of nanocomposite films dramatically decreased when 3 wt% nano-ZnOs were incorporated compared to the pure PLLA-PEG-PLLA film.This may be explained by the agglomeration of nano-ZnOs at a high content, leading to the non-homogeneity of the nanocomposite films that reduced stress transfer between the polymer matrices and filler [46,47].The strains at break of PLLA-PEG-PLLA films steadily decreased as the ZnO content increased compared to the pure PLLA-PEG-PLLA film because the reinforcing effect of inorganic filler limits the mobility and ductile flow of the polymer chains [44,48].It should be noted that these nanocomposite films still had more flexibility than PLLA films because they still had a higher strain at break (29-57%) than the pure PLLA film (about 5%) [33].
these nanocomposite films still had more flexibility than PLLA films because they still had a higher strain at break (29-57%) than the pure PLLA film (about 5%) [33].

Opacity and UV-Barrier Property
The opacity of film samples was calculated from Equation (3), as also summarized in Table 4.The pure PLLA-PEG-PLLA film had an opacity of 0.29 mm −1 .The film's opacity dramatically increased up to 1.19 mm −1 when the 1 wt% nano-ZnO was incorporated.The addition of nano-ZnO filler increased the opacity of polymer-based films because of the opaque character of nano-ZnOs, which has been reported in earlier works [15,25].The opacities of films increased as the ZnO content increased.As shown in Figure 10, PLLA-PEG-PLLA/ZnO nanocomposite films appeared to have higher opacity than the pure PLLA-PEG-PLLA film.However, the words obscured by the composite films were still readable and easily visible.Thus, these nanocomposite films could be used as food packaging where the food characteristics are still visible.

Opacity and UV-Barrier Property
The opacity of film samples was calculated from Equation (3), as also summarized in Table 4.The pure PLLA-PEG-PLLA film had an opacity of 0.29 mm −1 .The film's opacity dramatically increased up to 1.19 mm −1 when the 1 wt% nano-ZnO was incorporated.The addition of nano-ZnO filler increased the opacity of polymer-based films because of the opaque character of nano-ZnOs, which has been reported in earlier works [15,25].The opacities of films increased as the ZnO content increased.As shown in Figure 10, PLLA-PEG-PLLA/ZnO nanocomposite films appeared to have higher opacity than the pure PLLA-PEG-PLLA film.However, the words obscured by the composite films were still readable and easily visible.Thus, these nanocomposite films could be used as food packaging where the food characteristics are still visible.The absorbance in the 200-550 nm wavelength range was used to determine the UVbarrier properties of pure PLLA-PEG-PLLA and the nanocomposite films, as illustrated in Figure 11.It was found that the absorbance of film samples in the 200-550 nm wavelength range increased as the ZnO content increased, indicating that the UV-barrier properties of the PLLA-PEG-PLLA films were improved by the addition of nano-ZnOs.This is because the nano-ZnO is a UV absorber [15,[49][50][51].The addition of nano-ZnOs can improve the effectiveness of the PLLA-PEG-PLLA matrix to shield it from UV radiation.Therefore, the resulting nanocomposites could be used as UV-shielding food packaging.

Moisture Uptake
Figure 12 shows the moisture uptake of the pure PLLA-PEG-PLLA and nanocomposite films for 48 h.It can be seen that the equilibrium values were reached after an incubation time of 24 h.The pure PLLA-PEG-PLLA film exhibited the highest moisture uptake.The addition of nano-ZnOs decreased the moisture uptake of the film.Moisture uptake decreased as the nano-ZnO content increased.This may have been due to the added nano-ZnOs extending the tortuous diffusion pathways of the water vapor, thereby enhancing the performance of the water vapor barrier in the PLLA-PEG-PLLA matrix [1,36].In addition, the increasing crystallinity of the PLLA-PEG-PLLA matrix caused by the addition of nano-ZnOs may also have led to the extensive tortuosity of the water vapor transport pathways [23].The absorbance in the 200-550 nm wavelength range was used to determine the UVbarrier properties of pure PLLA-PEG-PLLA and the nanocomposite films, as illustrated in Figure 11.It was found that the absorbance of film samples in the 200-550 nm wavelength range increased as the ZnO content increased, indicating that the UV-barrier properties of the PLLA-PEG-PLLA films were improved by the addition of nano-ZnOs.This is because the nano-ZnO is a UV absorber [15,[49][50][51].The addition of nano-ZnOs can improve the effectiveness of the PLLA-PEG-PLLA matrix to shield it from UV radiation.Therefore, the resulting nanocomposites could be used as UV-shielding food packaging.The absorbance in the 200-550 nm wavelength range was used to determine the U barrier properties of pure PLLA-PEG-PLLA and the nanocomposite films, as illustrat in Figure 11.It was found that the absorbance of film samples in the 200-550 nm wav length range increased as the ZnO content increased, indicating that the UV-barrier pro erties of the PLLA-PEG-PLLA films were improved by the addition of nano-ZnOs.This because the nano-ZnO is a UV absorber [15,[49][50][51].The addition of nano-ZnOs can i prove the effectiveness of the PLLA-PEG-PLLA matrix to shield it from UV radiatio Therefore, the resulting nanocomposites could be used as UV-shielding food packagin

Moisture Uptake
Figure 12 shows the moisture uptake of the pure PLLA-PEG-PLLA and nanocomp site films for 48 h.It can be seen that the equilibrium values were reached after an incub tion time of 24 h.The pure PLLA-PEG-PLLA film exhibited the highest moisture uptak The addition of nano-ZnOs decreased the moisture uptake of the film.Moisture upta decreased as the nano-ZnO content increased.This may have been due to the added nan ZnOs extending the tortuous diffusion pathways of the water vapor, thereby enhanci the performance of the water vapor barrier in the PLLA-PEG-PLLA matrix [1,36].In ad tion, the increasing crystallinity of the PLLA-PEG-PLLA matrix caused by the addition nano-ZnOs may also have led to the extensive tortuosity of the water vapor transpo pathways [23].

Moisture Uptake
Figure 12 shows the moisture uptake of the pure PLLA-PEG-PLLA and nanocomposite films for 48 h.It can be seen that the equilibrium values were reached after an incubation time of 24 h.The pure PLLA-PEG-PLLA film exhibited the highest moisture uptake.The addition of nano-ZnOs decreased the moisture uptake of the film.Moisture uptake decreased as the nano-ZnO content increased.This may have been due to the added nano-ZnOs extending the tortuous diffusion pathways of the water vapor, thereby enhancing the performance of the water vapor barrier in the PLLA-PEG-PLLA matrix [1,36].In addition, the increasing crystallinity of the PLLA-PEG-PLLA matrix caused by the addition of nano-ZnOs may also have led to the extensive tortuosity of the water vapor transport pathways [23].

Antibacterial Properties
The antibacterial properties of the film samples were evaluated by quantifying t growth inhibition of E. coli (Gram-negative bacteria) and S. aureus (Gram-positive bacte as shown in Figure 13.These bacteria were selected as representative bacteria in this wo because they have been recognized as hospital-associated infections [52].The antibacter test resulted in a clear circular area around the film samples which was an inhibition zo in which the bacterial colonies did not grow.The diameter of the inhibition zone direc related to the antibacterial ability of the film samples.Inhibition zones were clearly o served for all the nanocomposite films but not for the pure PLLA-PEG-PLLA film.T suggests that the pure PLLA-PEG-PLLA film had no antibacterial ability, whereas all t nanocomposite films can inhibit and prevent the growth of both types of bacteria.The fore, the addition of nano-ZnOs introduced antibacterial abilities to the PLLA-PEG-PLL films.
The diameters of the inhibition zones of film samples are summarized in Table 5. T inhibition zone diameter of the nanocomposite films increased as the nano-ZnO conte increased.The results indicated that the antibacterial ability of the films increased w the nano-ZnO content.This was due to the high antibacterial ability of nano-Zn [1,13,51].This may involve the integrity of the bacteria cells being damaged by the relea of Zn 2+ ions and by photocatalytic reactions yielding reactive oxygen species (RO [15,26,53].In Table 5, it is seen that the diameters of inhibition zones for S. aureus bacte of the nanocomposite films were higher than E. coli bacteria for the same nano-ZnO co tent.This suggests the nanocomposite films showed greater antibacterial ability agai Gram-positive S. aureus than the Gram-negative E. coli, which concurs with the previo report in the literature [15,53].This is due to differences in the cell-wall structures of the bacteria [53].

Antibacterial Properties
The antibacterial properties of the film samples were evaluated by quantifying the growth inhibition of E. coli (Gram-negative bacteria) and S. aureus (Gram-positive bacteria) as shown in Figure 13.These bacteria were selected as representative bacteria in this work because they have been recognized as hospital-associated infections [52].The antibacterial test resulted in a clear circular area around the film samples which was an inhibition zone in which the bacterial colonies did not grow.The diameter of the inhibition zone directly related to the antibacterial ability of the film samples.Inhibition zones were clearly observed for all the nanocomposite films but not for the pure PLLA-PEG-PLLA film.This suggests that the pure PLLA-PEG-PLLA film had no antibacterial ability, whereas all the nanocomposite films can inhibit and prevent the growth of both types of bacteria.Therefore, the addition of nano-ZnOs introduced antibacterial abilities to the PLLA-PEG-PLLA films.
The diameters of the inhibition zones of film samples are summarized in Table 5.The inhibition zone diameter of the nanocomposite films increased as the nano-ZnO content increased.The results indicated that the antibacterial ability of the films increased with the nano-ZnO content.This was due to the high antibacterial ability of nano-ZnOs [1,13,51].This may involve the integrity of the bacteria cells being damaged by the release of Zn 2+ ions and by photocatalytic reactions yielding reactive oxygen species (ROS) [15,26,53].In Table 5, it is seen that the diameters of inhibition zones for S. aureus bacteria of the nanocomposite films were higher than E. coli bacteria for the same nano-ZnO content.This suggests the nanocomposite films showed greater antibacterial ability against Grampositive S. aureus than the Gram-negative E. coli, which concurs with the previous report in the literature [15,53].This is due to differences in the cell-wall structures of these bacteria [53].
16,  x FOR PEER REVIEW 3 of 18 from Nanoscience Technology Co., Ltd.(Bangkok, Thailand) and used without further purification.Figure1shows an SEM image of ZnO nanoparticles.

Figure 4 compares
Figure 4 compares DSC cooling curves of the samples and their DSC results are su marized in Table2.The pure PLLA-PEG-PLLA had Tc and ΔHc values of 99 °C and 1 J/g, respectively.Table2also indicates that the Tc peaks shifted to higher temperatu and the ΔHc values increased as the nano-ZnO content increased up to 2 wt%.This s ports a nucleation effect for PLLA-PEG-PLLA occurring during DSC cooling scans, wh was enhanced by the added nano-ZnO, as attested by the increasing Tc and ΔHc val
16,  x FOR PEERREVIEW  8 o    concluded that the crystallization properties of the nanocomposites can be improved low incorporation (up to 2 wt%) of nano-ZnO within the PLLA-PEG-PLLA matrix.

Figure 11 .
Figure 11.UV-vis spectra in UV region of pure PLLA-PEG-PLLA film and PLLA-PEG-PLLA/Z nanocomposite films with various contents of nano-ZnOs.