Performance of Thyme Oil@Na-Montmorillonite and Thyme Oil@Organo-Modified Montmorillonite Nanostructures on the Development of Melt-Extruded Poly-L-lactic Acid Antioxidant Active Packaging Films

Today, the use of natural biodegradable materials in the production processes is more and more adopted by industry to achieve cyclic economy targets and to improve environmental and human health indexes. Active packaging is the latest trend for food preservation. In this work, nanostructures were prepared by incorporation of thyme oil with natural natrium-montmorillonite and organo-montmorillonite with two different techniques, direct impregnation and the green evaporation–adsorption process. Such nanostructures were mixed with poly-L-lactic-acid for the first time via an extrusion molding process to develop a new packaging film. Comparisons of morphological, mechanical, and other basic properties for food packaging were carried out via XRD, FTIR, TG, SEM/EDS, oxygen and water vapor permeation, and antimicrobial and antioxidant activity for the first time. Results showed that poly-L-lactic-acid could be modified with clays and essential oils to produce improved active packaging films. The final product exhibits food odor prevention characteristics and shelf-life extension capabilities, and it could be used for active packaging. The films based on OrgMt clay seems to be more promising, while the thyme oil addition improves their behavior as active packaging. The PLLA/3%TO@OrgMt and PLLA/5%TO@OrgMt films were qualified between the tested samples as the most promising materials for this purpose.

PLLA shows its most intense diffraction peaks at 2θ values of 16.6 and 18.96 degrees, which is in agreement with previous reports [23,24]. The intension of such peaks decreased in all XRD plots of PLLA/NaMt, PLLA/TO@NaMt, PLLA/OrgMt, and PLLA/TO@OrgMT nanocomposites. This fact indicates the interplay between PLLA molecules and nanoclay platelets. The decrease of intense of the characteristic PLLA peaks is higher for OrgMt-and TO@OrgMt-based nanocomposites than for NaMt-and TO@NaMt-based nanocomposites.
It is obvious from Figure 1a,c that the major diffraction peak of NaMt clay is at around 2theta = 7.0 • . The TO@NaMt modified nanostructure exhibits a broader peak at 2theta = 6.8 • . According to previous reports [14,20], TO molecules were encapsulated on the external surface of NaMt layers, causing a partial exfoliation of clay platelets. The small shift of 2theta angle from 7.0 to 6.8 • occurs probably due to the insertion of water molecules in the NaMt's interlayer space. It is also obvious from Figure 1a,c that the blending of both NaMt clay and TO@NaMt nanostructure with PLLA chains resulted to XRD plots with a very broad peak at 2theta around 4.8 and 5.0 degrees. Thus, it seems that PLLA/NaMt and PLLA/TO@NaMt nanocomposites favored the formation of an exfoliated nanocomposite structure [12].
In Figure 1b,d, the basal space of OrgMt clay is observed at 2theta = 3.50 • . TO@OrgMt hybrid nanostructure exhibits a clear shift at 2theta = 2.88 • degrees. This result is in accordance with previous report [20]. In this report, it was shown [20] that TO molecules encapsulated in the internal space of OrgMt clay platelets. The basal space peak of PLLA/1OrgMt, PLLA/3OrgMt, and PLLA/5OrgMt film was at 2theta, 2.55 • , 2.59 • , and 2.64 • , respectively, while the basal space peak of all PLLA/1O@OrgMt, PLLA/3TO@OrgMt, and PLLA/5TO@OrgMt films was at around 2theta = 2.53 • . These results indicated the formation of an intercalated nanostructure in all cases, and the boost that TO molecules provided to PLLA chains to insert in the OrgMt clay interlayer space.  (Figure 2b) nanocomposite films as well as FTIR spectra of "blank" PLLA film for comparison. In all spectra, the main characteristic peaks of both PLLA are observed. As it is denoted (see dot lines in Figure 2a,b), at 3510 cm −1 the OH stretch band, at 2941 and 2993 cm −1 the CH and CH3 stretching bands, and at 1750 cm −1 the characteristic band of the CO ester group of PLLA chain is observed [25].

FTIR
In such polymer/clay nanocomposite films, the interplay with clay platelets is indicated by the new bands at 3630, 918, 660, and 470 cm −1 , which are accredited to O-H stretching of structural hydroxyl groups, Al-O stretching, Mg-O bond, and Si-O stretching of the tetrahedral silica layers of modified clays, respectively [26,27]. In the case of both NaMt-and OrgMt-based nanocomposites, the bands at 3630, and 470 cm −1 of Al-O and Si-O stretchings are most identified (see dot line in Figure 2a,b) and imply the interplay between clay platelets and PLLA chains. With a more careful look at Figure 2 (see the band at 470 cm −1 ), it is observed a higher interplay for OrgMt-based than NaMt-based samples. In advance, this interplay is higher for TO@NaMt and TO@OrgMt films as compared to NaMt and OrgMt films, correspondingly. This probably occurs due to the hydrophobic nature of the PLLA, which is matched with the hydrophobic nature of the TO. The absence of FTIR peaks, which indicate the existence of TO molecules and its derivatives, implies that such molecules are inside the polymer matrix and not on the surface of it. Moreover, the TO amount is too low compared to that of the PLLA and the clay.

TG-DTA
In Figure 3, the TG plots of pure PLLA, "blank" PLLA/NaMt, and PLLA/OrgMt samples as well as all obtained PLLA/TO@NaMt and PLLA/TO@OrgMt nanocomposite films are presented. For all samples, the degradation step starts at around 300-320 • C and ends at 350-400 • C. In such polymer/clay nanocomposite films, the interplay with clay platelets is indicated by the new bands at 3630, 918, 660, and 470 cm −1 , which are accredited to O-H stretching of structural hydroxyl groups, Al-O stretching, Mg-O bond, and Si-O stretching of the tetrahedral silica layers of modified clays, respectively [26,27]. In the case of both NaMt-and OrgMt-based nanocomposites, the bands at 3630, and 470 cm −1 of Al-O and Si-O stretchings are most identified (see dot line in Figure 2a,b) and imply the interplay between clay platelets and PLLA chains. With a more careful look at Figure 2 (see the band at 470 cm −1 ), it is observed a higher interplay for OrgMt-based than NaMt-based samples. In advance, this interplay is higher for TO@NaMt and TO@OrgMt films as compared to NaMt and OrgMt films, correspondingly. This probably occurs due to the hydrophobic nature of the PLLA, which is matched with the hydrophobic nature of the TO. The absence of FTIR peaks, which indicate the existence of TO molecules and its derivatives, implies that such molecules are inside the polymer matrix and not on the surface of it. Moreover, the TO amount is too low compared to that of the PLLA and the clay.

TG-DTA
In Figure 3, the TG plots of pure PLLA, "blank" PLLA/NaMt, and PLLA/OrgMt samples as well as all obtained PLLA/TO@NaMt and PLLA/TO@OrgMt nanocomposite films are presented. For all samples, the degradation step starts at around 300-320 °C and ends at 350-400 °C. The temperature value where the degradation process starts is indicative for the thermal strength of such PLLA/nanoclay nanocomposite films. DTG plots for each sample are depicted in Figure 3, and the calculated degradation temperature for each sample is listed. In the case of NaMt-based samples, the addition of extra NaMt caused a slightly increase to the degradation temperature of samples. Moreover, the addition of TO caused a slight The temperature value where the degradation process starts is indicative for the thermal strength of such PLLA/nanoclay nanocomposite films. DTG plots for each sample are depicted in Figure 3, and the calculated degradation temperature for each sample is listed. In the case of NaMt-based samples, the addition of extra NaMt caused a slightly increase to the degradation temperature of samples. Moreover, the addition of TO caused a slight decrease to the degradation temperature compared with samples without TO. The addition of extra OrgMt to the OrgMt-based nanocomposites showed a higher increase of the degradation temperature, compared to respective of the NaMt-based samples. The addition of TO caused a slight increase to the degradation temperature of PLLA/1TO@OrgMt as compared to the respective of the PLLA/1OrgMt sample but a slight decrease to the degradation temperature of the PLLA/3TO@OrgMt and PLLA/5TO@OrgMt samples as compared to the respective of the PLLA/3OrgMt and PLLA/5OrgMt samples. The higher increase in thermal stability obtained for OrgMt-based samples as compared to NaMt-based samples is expected following XRD results where intercalated nanocomposite structures were obtained for all OrgMt-based samples, while exfoliated nanocomposite structures were obtained for all NaMt-based samples. The slight decrease of thermal stability of samples containing TO as compared to the samples that do not contain TO is indicative of the plasticization effect caused by the TO addition.

Tensile Properties
Young's modulus as well as tensile strength and elongation at break values of the tested films are tabulated in Table 2. It is obvious that the addition of NaMt in all cases decrease stiffness, strength, and elongation at break values of PLLA. Addition of modified TO@NaMt nanostructure leads to higher stiffness, strength, and elongation at break values of obtained PLLA/TO@NaMt films compared to the relevant PLLA/NaMt films, but only PLLA/3TO@NaMt films exhibit a little higher stiffness, strength, and elongation at brake values compared to the values exhibited by pure PLLA film. In contrast, addition of OrgMt in the PLLA matrix seems to be more effective. Because of this, the PLLA3OrgMt sample showed higher stiffness, strength, and elongation at break values than pure PLLA. Moreover, addition of TO@OrgMt nanostructure leads to the even higher stiffness, strength, and elongation at break values. In other words, it seems that the OrgMt nanostructure exhibits better interplay with the PLLA matrix than the NaMt nanostructure. This result is in accordance with [17]. The addition of TO boosts the dispersion of both NaMt and OrgMt nanostructures in the PLLA matrix. Optimum interplay is observed for the PLLA/TO@OrgMt system. The highest stiffness, strength, and elongation at break values were observed for PLLA/3TO@OrgMt active film.

SEM/EDS Results
The surface morphology of the pure PLLA and PLLA/clay nanocomposite films was investigated using a SEM instrument equipped with an EDS detector. EDS mapping analysis from different areas of the studied nanocomposite films was recorded, and the results confirmed that the clays were homogeneously dispersed in the polymer matrix.
The image in Figure 4 shows the expected smooth morphology of the neat polymer, and in Figure 5 the EDS spectra certify the existence of carbon. Surface and relative cross-section images of PLLA/1TO@NaMt, PLLA/3TO@NaMt, and PLLA/5TO@NaMt are presented in Figure 6. It is obvious from Figure 7a,c,e that the increase of clay content in the nanocomposite materials increases the aggregation degree. This fact can be identified by SEM using a secondary electron signal. EDS was then used to map specific elements of the clay nanostructure and identify especially the presence of silicon. As it is observed in Figure 8, clay agglomeration took place, and the increase in clay concentration led to increased silicon signal.   The results from SEM/EDS measurements are in accordance with the XRD resu where an intercalated nanocomposite structure for TO@OrgMt-based films and an exfo ated nanocomposite structure for TO@NaMt-based films was confirmed. Both XRD a SEM/EDS results are in total agreement with the higher tensile and thermal streng which was observed for TO@OrgMt-based films compared to the respective properties the TO@NaMt-based films.   The results from SEM/EDS measurements are in accordance with the XRD results where an intercalated nanocomposite structure for TO@OrgMt-based films and an exfoliated nanocomposite structure for TO@NaMt-based films was confirmed. Both XRD and SEM/EDS results are in total agreement with the higher tensile and thermal strength, which was observed for TO@OrgMt-based films compared to the respective properties of the TO@NaMt-based films.   Figure 9 shows the surface (b,d,f) and cross-section (a,c,e) topology of the PLLA/1TO@OrgMt, PLLA/3TO@OrgMt, and PLLA/5TO@OrgMt nanocomposites, indicating significant clay dispersion within the PLLA polymer matrix. In contrast to the TO@NaMt nanocomposites, the disperse of the TO@OrgMt clays in the polymer matrix led to nonaggregated distributions. This is indicated by the Si signal through EDS mapping. The SEM images and EDS mapping analysis of the PLLA/xTO@OrgMt materials confirm the enhanced compatibility of the TO@OrgMt clay with the PLLA polymer matrix compared to the compatibility of the TO@NaMt clay, which led to rougher PLLA/xTO@NaMt surfaces.
The results from SEM/EDS measurements are in accordance with the XRD results where an intercalated nanocomposite structure for TO@OrgMt-based films and an exfoliated nanocomposite structure for TO@NaMt-based films was confirmed. Both XRD and SEM/EDS results are in total agreement with the higher tensile and thermal strength, which was observed for TO@OrgMt-based films compared to the respective properties of the TO@NaMt-based films.   Table 3 lists the measured Water Vapor Transmission Rate (WVTR) and Oxygen Transmission Rate (OTR) values as well as the calculated water vapor diffusion coefficient (D WV ) and oxygen permeability coefficient (Pe O2 ) values. Water vapor diffusion coefficient values (D WV ) and oxygen permeability coefficient values (Pe O2 ) were calculated according to Fick law, oxygen permeability through polymers equation, and assumptions described in [28]. According to this literature, we can calculate the water vapor diffusion coefficient D (cm 2 ·s −1 ) for every film as follows:

Barrier Properties
where WVTR [G·cm −2 ·s −1 )] is the water vapor transmission rate, ∆x (cm) is the film thickness, and ∆C (g·cm −3 ) is the humidity concentration gradient in the two opposite sides of the film. Furthermore, we can calculate oxygen permeability through films as follows: where J/A (mol·cm −2 ·s −1 ) is the specific amount of gas pass through the membrane, Pe O2 (cm 2 ·s −1 ) is the permeability coefficient, ∆C (mol·cm −3 STP) is the pressure gradient in the two opposite sides of the membrane, and ∆x (cm) is the membrane thickness.    Table 3 lists the measured Water Vapor Transmission Rate (WVTR) and Oxygen Transmission Rate (OTR) values as well as the calculated water vapor diffusion coefficient (DWV) and oxygen permeability coefficient (PeO2) values. Water vapor diffusion coefficient values (DWV) and oxygen permeability coefficient values (PeO2) were calculated according to Fick law, oxygen permeability through polymers equation, and assumptions described in [28]. According to this literature, we can calculate the water vapor diffusion coefficient D (cm 2 •s −1 ) for every film as follows:

Barrier Properties
where WVTR [G•cm −2 •s −1 )] is the water vapor transmission rate, Δx (cm) is the film thickness, and ΔC (g•cm −3 ) is the humidity concentration gradient in the two opposite sides of the film. Furthermore, we can calculate oxygen permeability through films as follows: Rearranging Equation (1), we can express the permeability coefficient as follows: Based on these two mass transfer parameters and considering the value of 5 wt% as the maximum additive concentration in the PLLA matrix, it is obvious from Table 3 that the addition of NaMt clay in the PLLA matrix decreases the water vapor barrier, while the addition of OrgMt clay increases this property. The presence of TO in both types of clay increases the water vapor barrier further. In contrast, the oxygen barrier increases by the addition of either NaMt or OrgMt in the PLLA matrix. Similarly to the water vapor diffusion case, the addition of TO in both types of clay leads to higher oxygen barrier values. In conclusion, we can say that the exfoliated PLLA/NaMt samples exhibit lower water vapor barrier values, even from values of the pure PLLA, compared to the intercalated PLLA/OrgMt samples, which exhibit higher water vapor barrier values from the values of both the pure PLLA and the PLLA/NaMt samples. In all cases, the oxygen permeability barrier increases.  Table 3 reports the antioxidant activity values calculated from Equation (4). All tested films exhibit significant antioxidant activity, which indicates that, potentially, they could be used as active packaging films. It is obvious from measurements that the antioxidant activity increases as the content of TO@NaMt and TO@OrgMt nanostructure increases. Antioxidant activity was calculated by absorbance measurements of DPPH ethanolic solution at 517 nm. The presence of film pieces in such solutions decreases the absorbance values. The following equation estimates the % antioxidant activity of each sample film: % Antioxidant activity = (Abs control − Abs sample )/Abs control × 100 (4) where Abs control is the absorbance value of pure DPPH ethanolic solution and Abs sample is absorbance value of DPPH ethanolic solution after incubation with 30 mg sample film for 24 h in a dark place and at 25 • C. TO@OrgMt-based films exhibit higher antioxidant activity compared to that of the TO@NaMt-based films. This result could be attributed to the higher TO content of TO@OrgMt nanostructure (36.2 wt%) over that of TO@NaMt nanostructure (22.0 wt%).

Antimicrobial Properties
Antibacterial activity of thyme oil and PLLA films was tested against four food pathogenic bacteria, E. coli, S. aureus, S. enterica, and L. monocytogenes. The inhibition zones indicated strong antimicrobial activity of pure thyme oil against the tested bacteria. Thyme oil totally inhibited the E. coli and L. monocytogenes and also exhibited good antibacterial activity against S. aureus and S. enterica. The mean inhibition zone diameter for the last two microorganisms was 55 mm and 27 mm, respectively. On the contrary, the tested films did not show antibacterial effect neither in terms of surrounding clear zone nor underneath the film. Many parameters could affect the film's antimicrobial properties, e.g., the nature of the EO, the quantity or the mass ratio of EO into the polymer, and maybe the combination of some of them. By reviewing the results, it seems that the film formation process by hot-pressing at high temperatures (160 • C) could evaporate the EO's volatile and bioactive compounds, leading to a high decrease of their antibacterial activity. Additionally, this hot-pressing process probably removes the EO from the tested film and reduces drastically the EO's concentration in films, causing a non-antimicrobial effect. Finally, it was reported in the literature the possibility that the controlled EO's releasing from the polymer films could limit the diffusion of the EO's active components [29].

Used Clay
(i) Sodium exchanged montmorillonite (NaMt) with code name Nanomer ® PGV with mass density 2.6 g/cm 3 and CEC value 145 meq/100 g was produced by Nanocor Company

Preparation of TO@NaMt and TO@OrgMt Nanostructures
The encapsulation of TO in both NaMt and OrgMt clays was performed via a green evaporation/adsorption process described in detail previously [20]. The final TO loading on obtained TO@NaMt and TO@OrgMt nanostructures was calculated gravimetrically and was approx. 22.0 wt% and 36.2 wt%, respectively.

Preparation of PLLA/TO@NaMt and PLLA/TO@OrgMt Films
The PLLA/TO@NaMt and PLLA/TO@OrgMt films were prepared via a melt-mixing process. For the preparation, a minilab co-rotating twin extruder (Haake Mini Lab II, ThermoScientific, ANTISEL, S.A., Athens, Greece) was used. The uniform operating temperature was 170 • C at a screw speed of 100 rpm for 5 min total processing time. The nominal compositions of TO@NaMt and TO@OrgMt nanohybrids added to PLLA were fixed to 1 wt%, 3 wt%, and 5 wt%. "Blank" samples were also prepared for comparison by mixing PLLA with commercial NaMt and OrgMt with the same nominal compositions. The obtained melt compound strands were cut into small granules using a granulating machine. Finally, films were produced with approx. 10 cm diameter by hot-pressing of approximately 2 g of the obtained granules at 160 • C under 3.0 megapascal (MPa) constant pressure for 3 min using a hydraulic press with heated platens.

FTIR Spectrometry
The chemical structure and the possible interactions of PLLA chains with NaMt, OrgMt, TO@NaMt, and TO@OrgMt nanostructures of all PLLA/NaMt, PLLA/TO@NaMt, PLLA/OrgMt, and PLLA/TO@OrgMt films were studied by IR spectra measurements. The obtained infrared (FTIR) plots were the average of 32 scans at 2 cm −1 resolution and were measured using an FT/IR-6000 JASCO Fourier transform spectrometer (JASCO, Interlab, S.A., Athens, Greece) in the wavenumber range of 4000-400 cm −1 .

Thermal Studies TG-DTA
Thermogravimetric (TGA) and differential thermal analysis (DTA) were carried out on all obtained films. Measurements were performed using a PerkinElmer Pyris Diamond TGA/DTA instrument (Interlab, S.A., Athens, Greece). Samples of approximately 5 mg were heated under N 2 flow from 25 to 700 • C at a rate of 5 • C/min.

Tensile Properties
Tensile measurements were carried out on all prepared films according to the ASTM D638 method. A Simantzü AX-G 5 kNt instrument (Simantzu. Asteriadis, S.A., Athens, Greece) was used. Three to five samples of each film were tensioned at an across head speed of 2 mm/min. The samples were dumbbell-shaped with gauge dimensions of 10 mm × 3 mm × 0.22 mm. Force (N) and deformation (mm) were recorded during the test.

Scanning Electron Microscopy (SEM)/Energy Dispersive Spectroscopy (EDS)
Scanning electron microscopy (SEM) images were obtained using a JEOL JSM-6510 LV SEM Microscope (JEOL Ltd., Tokyo, Japan) equipped with an X-Act EDS detector by Oxford Instruments, Abingdon, Oxfordshire, UK (an acceleration voltage of 20 kV was applied) for elemental and mapping analysis. The specimens were sputtered with an Au-Pd thin film (4-8 nm) using a mini sputter coater SC7620 from Quorum Technologies LTD (Kent, UK).

Water Vapor Transmission Rate (WVTR)
WVTR of all obtained films was determined. Experimental conditions were fixed at 38 • C and 50% RH according to the ASTM E96/E96M-05 method. Using a handmade apparatus and following the methodology described extensively in a previous publication [30] and modified recently [22,28], WVTR measurements were carried out. For such measurements, film disks of 2.5 cm diameter and 100 µm thickness were used.

Oxygen Permeability (OP)
The oxygen transition rate (OTR) of all obtained films was analyzed using an oxygen permeation analyzer (8001, Systech Illinois Instruments Co., Johnsburg, IL, USA). All samples were tested at 23 • C and 0% RH according to the ASTM D 3985 method. OTR values were expressed at cc O 2 /m 2 /day. The average film thickness of the tested samples was in the range of 350 to 400 µm. The mean OTR value for each kind of film resulted from the measurements of three samples.

Antioxidant Activity
The antioxidant activity of films was evaluated using 300 mg of small pieces (approximately 3 mm × 3 mm) of each film. The sample was placed in a dark-colored glass bottle with a plastic screw cap and filled with 10 mL DPPH ethanolic solution of 50 ppm (mg/L) concentration. After incubation at 25 • C for 24 h in darkness, the % antioxidant activity values of the films were calculated according to Equation (4). Antioxidant measurements were carried out using a JASCO V530 UV-VIS instrument (JASCO International CO., Ltd., Tokyo, Japan).

Antimicrobial Assay
PLLA films were tested by agar diffusion method for their efficacy against Gram-negative bacteria Escherichia coli (ATCC 25922) and Salmonella enterica subsp. enterica (DSMZ 17420) and Gram-positive bacteria Staphylococcus aureus (DSMZ 12463) and Listeria monocytogenes (DSMZ 27575). The above bacteria isolates were provided from the Institute of Technology of Agricultural Products, ELGO-DEMETER, Lykovryssi, Greece.
The stock bacteria colonies were cultured overnight in Mueller-Hinton broth to obtain a range of 10 7 -10 8 CFU mL −1 . Then, a sterile cotton swab was used to inoculate the surface of Mueller-Hinton agar dishes. To achieve homogeneous growth, the plates were rotated every 60 • during the inoculation process.
Films were cut into 6 mm discs by a circular knife and sterilized using a UV lamp. Film discs were placed on the surface of Mueller-Hinton agar plates, and the diameter of inhibitory zones was measured after 24 h of incubation at 37 • C. Moreover, the growth of bacteria on the contact area between the films and the agar surface was also evaluated. Thyme oil antibacterial activity was examined by the agar well diffusion method. The EO was cast into Mueller-Hinton agar wells with 6 mm diameter, and the clear zone of inhibition was recorded. The experiment was repeated three times.

Statistical Analysis
According to the literature, it is usual in such studies to measure every property at least three times under the same conditions to achieve accurate mean values standard deviation values and standard error. Moreover, it is usual to test the inequality of mean values between all kind of samples to promote the better material which exhibits superior properties. All the experimental data for E, σ uts , ε b (%), WVTR, % water sorption, OTR, E. coli, S. aureus, S. enterica, and L. monocytogenes were statistically treated using the statistical software SPSS ver. 20. Statistical tests were carried the way described in previous literature reports [28].

Conclusions
Characterization techniques indicated that the interplay and compatibility between PLLA chains and clay platelets was more intense in the case of the intercalated OrgMt clay compared to that of the partially exfoliated NaMt clay. This also means a better mixing of these two materials, i.e., PLLA and OrgMt. Furthermore, in both cases of clay addition, the presence of TO boosted the mixing process. The thermal stability of the PLLA matrix was improved by addition of either NaMt or OrgMt clay. In the case of the OrgMt clay, the increase of such stability was higher. Nevertheless, there was an optimum addition around 3 wt% for optimum mechanical properties. The exfoliated PLLA/NaMt samples exhibited lower water vapor barrier values, even from values of the pure PLLA, compared to the intercalated PLLA/OrgMt samples, which exhibited higher water vapor barrier values from the values of both the pure PLLA and the PLLA/NaMt samples. In all cases, the oxygen barrier increased, and the TO addition decreased, water vapor diffusion and oxygen permeability. Higher TO adsorption capacity of OrgMt-based materials led to higher antioxidant activity. As an overall validation of the materials in our study, all samples could be potentially used for active food packaging applications, but the PLLA/5%TO@OrgMt film seems to be the most advantageous. Funding: This research was funded by University of Patras, Greece, the funding program was "MEDICUS", Project F.K. 81541.

Data Availability Statement:
The datasets generated for this study are available on request to the corresponding author.