Plasma-Assisted Synthesis of Multicomponent Nanoparticles Containing Carbon, Tungsten Carbide and Silver as Multifunctional Filler for Polylactic Acid Composite Films

Multicomponent nanoparticles containing carbon, tungsten carbide and silver (carbon-WC-Ag nanoparticles) were simply synthesized via in-liquid electrical discharge plasma, the so-called solution plasma process, by using tungsten electrodes immersed in palm oil containing droplets of AgNO3 solution as carbon and silver precursors, respectively. The atomic ratio of carbon:W:Ag in carbon-WC-Ag nanoparticles was 20:1:3. FE-SEM images revealed that the synthesized carbon-WC-Ag nanoparticles with particle sizes in the range of 20–400 nm had a spherical shape with a bumpy surface. TEM images of carbon-WC-Ag nanoparticles showed that tungsten carbide nanoparticles (WCNPs) and silver nanoparticles (AgNPs) with average particle sizes of 3.46 nm and 72.74 nm, respectively, were dispersed in amorphous carbon. The carbon-WC-Ag nanoparticles were used as multifunctional fillers for the preparation of polylactic acid (PLA) composite films, i.e., PLA/carbon-WC-Ag, by solution casting. Interestingly, the coexistence of WCNPs and AgNPs in carbon-WC-Ag nanoparticles provided a benefit for the co-nucleation ability of WCNPs and AgNPs, resulting in enhanced crystallization of PLA, as evidenced by the reduction in the cold crystallization temperature of PLA. At the low content of 1.23 wt% carbon-WC-Ag nanoparticles, the Young’s modulus and tensile strength of PLA/carbon-WC-Ag composite films were increased to 25.12% and 46.08%, respectively. Moreover, the PLA/carbon-WC-Ag composite films possessed antibacterial activities.


Introduction
Nowadays, due to increasing environmental concerns and climate change worldwide, bio-derived and biodegradable polymers such as polylactic acid (PLA), polyhydroxybutyrate (PHB) and poly(3-hydroxybutyrate-co-3-hydroxyvalerate) (PHBV) have received much attention as alternatives to petroleum-based polymers [1][2][3]. Among bio-derived and biodegradable polymers, PLA is one of the most studied polymers and has been investigated for many applications, such as packaging materials [4], membranes for separation processes [5] and biomaterials for biomedical applications [6]. Nevertheless, the major drawbacks of PLA that limit its utilization as a replacement for petroleum-based polymers are low thermal stability, inferior mechanical properties and low crystallization rate when compared with petroleum-based polymers. Therefore, the incorporation of fillers into PLA to obtain PLA composites has been considered as an effective method to overcome these limitations. To date, PLA composites have been developed by the incorporation of a wide variety of fillers, such as clay [7], silver nanoparticles [8], zinc oxide (ZnO) [9], tungsten disulfide (WS 2 ) nanotubes [10] and various types of carbon materials [11][12][13].
days, carbon-supported AgNPs are extensively used as reinforcing fillers for polymer composites [22,56,57]. According to the literature, carbon-supported AgNPs can be synthesized by several methods, such as hydrothermal reduction [58], thermal annealing [56] and sputtering deposition [59]. However, the preparation of carbon-supported AgNPs is generally based on multi-step processes together with the use of reducing agents and long reaction times.
In this study, multicomponent nanoparticles containing carbon, tungsten carbide and silver, i.e., carbon-WC-Ag nanoparticles, were synthesized in one step via SPP by using palm oil containing droplets of silver nitrate (AgNO 3 ) solution as carbon and silver precursors, respectively. By applying SPP, carbon and AgNPs were synthesized from palm oil and AgNO 3 , respectively, whereas tungsten carbide nanoparticles (WCNPs) were generated by the sputtering of tungsten electrodes together with the simultaneous formation of carbon during plasma discharge. The morphology and elemental composition of carbon-WC-Ag nanoparticles were characterized. Carbon-WC-Ag nanoparticles were then used as multifunctional fillers for the preparation of polylactic acid (PLA) composite films, i.e., PLA/carbon-WC-Ag, by solution casting. The effect of carbon-WC-Ag nanoparticles on the non-isothermal crystallization behavior and mechanical and thermal properties of the obtained PLA composite films was investigated. The antibacterial activities of PLA/carbon-WC-Ag composite films against Escherichia coli, a Gram-negative bacterium, and Staphylococcus aureus, a Gram-positive bacterium, were also examined.

Preparation of Carbon-WC, Carbon-Ag and Carbon-WC-Ag Nanoparticles via SPP
The experimental setup of SPP is shown in Figure 1a. The plasma discharge was carried out at room temperature and atmospheric pressure by using a bipolar pulsed power supply (model Pekuris MPS-06K01C-WP1 from Kurita Seisakusho Co., Ltd., Kyoto, Japan). The plasma discharge was generated between a pair of metal electrodes equipped in a glass reactor that was filled with palm oil (40 mL). Two types of metal electrodes, i.e., tungsten (W) and silver (Ag) electrodes, were used to synthesize carbon-WC and carbon-Ag nanoparticles, respectively. The metal electrodes were insulated by ceramic tubes. The gap between the electrodes, voltage, pulse frequency, pulse width and plasma discharge time were 0.5 mm, 1.64 kV, 15 kHz, 2 µs and 90 min, respectively. Palm oil was used as a carbon precursor to synthesize carbon via SPP, whereas tungsten carbide nanoparticles (WCNPs) were generated by sputtering of tungsten electrodes and subsequently combining tungsten and carbon. For the synthesis of carbon-WC-Ag nanoparticles, AgNO 3 solution (10 mL) at a concentration of 0.02 M was added into palm oil (40 mL) under strong agitation to form small droplets of AgNO 3 solution that dispersed in palm oil while plasma discharge was taking place. The operating conditions for plasma discharge were the same as those for the synthesis of carbon-WC and carbon-Ag nanoparticles.
(WCNPs) were generated by sputtering of tungsten electrodes and subsequently combining tungsten and carbon. For the synthesis of carbon-WC-Ag nanoparticles, AgNO3 solution (10 mL) at a concentration of 0.02 M was added into palm oil (40 mL) under strong agitation to form small droplets of AgNO3 solution that dispersed in palm oil while plasma discharge was taking place. The operating conditions for plasma discharge were the same as those for the synthesis of carbon-WC and carbon-Ag nanoparticles. By applying SPP and using tungsten electrodes, palm oil and AgNO3 solution acted as carbon and Ag precursors to synthesize carbon-WC-Ag nanoparticles in one step. Based on the types of electrodes, i.e., tungsten and silver electrodes, there were three types of synthesized carbon-based nanoparticles, i.e., carbon-tungsten carbide (carbon-WC), carbon-silver (carbon-Ag) and carbon-tungsten carbide-silver (carbon-WC-Ag) nanoparticles, as illustrated in Figure 1b. After the plasma discharge, the synthesized carbon- By applying SPP and using tungsten electrodes, palm oil and AgNO 3 solution acted as carbon and Ag precursors to synthesize carbon-WC-Ag nanoparticles in one step. Based on the types of electrodes, i.e., tungsten and silver electrodes, there were three types of synthesized carbon-based nanoparticles, i.e., carbon-tungsten carbide (carbon-WC), carbonsilver (carbon-Ag) and carbon-tungsten carbide-silver (carbon-WC-Ag) nanoparticles, as illustrated in Figure 1b. After the plasma discharge, the synthesized carbon-based nanoparticles were collected and separated from palm oil by centrifugation at a rotational speed of 12,000 rpm for 15 min. Then, the synthesized carbon-based nanoparticles were rinsed with an excess amount of hexane to remove the residual oil, followed by centrifugation at a rotational speed of 12,000 rpm for 15 min. The washing process was repeated 3 times. The synthesized carbon-based nanoparticles were dried in an oven at 60 • C for 3 h.

Preparation of Neat PLA and PLA Composite Films
For preparation of neat PLA films, a PLA solution at a concentration of 4% (w/v) was prepared by dissolving PLA pellets of 4 g in chloroform 100 mL, followed by stirring at 60 • C for 2 h until PLA pellets were completely dissolved [60]. Then, the PLA solution was cast on Petri dishes and left at room temperature for 48 h to obtain neat PLA films. For preparation of PLA composite films, the fillers, i.e., activated charcoal, carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles, were dispersed in the PLA solutions, followed by sonication for 10 min. The filler contents in the PLA composite films were varied to be 0.25, 0.75, 1.23, 1.72 and 2.20 wt%, as shown in Table 1. After this, the PLA solutions containing each type of filler were cast on Petri dishes and left at room temperature for 48 h to evaporate the solvent, and PLA composite films having a thickness of 95.5 µm were obtained.

Characterization
The synthesized carbon-based nanoparticles were characterized in comparison with the commercial activated charcoal. Wide angle X-ray diffraction (WAXD) measurements were done by using SmartLab (Rigaku Corporation, Tokyo, Japan) with CuKα radiation (λ = 0.154 nm) operating at 40 kV and 30 mA. The values of degree of crystallinity (χ c ) of neat PLA and the PLA composite films were determined according to Equation (1): A c represents the area under the total crystalline region and A a represents the area under the total amorphous region [61].
Chemical compositions of activated charcoal and the synthesized carbon-based nanoparticles were analyzed by XPS (model Kratos Axis Ultra DLD from Kratos Analytical Co., Ltd., Manchester, UK) with an Al Kα X-ray source at 15 kV. Raman spectra of the synthesized carbon-based nanoparticles were detected by Spectra GX (Perkin Elmer Inc., Waltham, MA, USA). TEM and FE-SEM images of the synthesized carbon-based nanoparticles were taken using a JEOL (model JEM-2100 from JEOL Co., Ltd., Tokyo, Japan) and Hitachi (model s-4800 from Hitachi Co., Ltd., Tokyo, Japan), respectively. The elemental compositions of activated charcoal and the synthesized carbon-based nanoparticles were determined by scanning electron microscopy with energy dispersive X-ray (SEM-EDX) (Hitach Co., Ltd., Tokyo, Japan).
Surface and cross-sectional morphology of neat PLA and PLA composite films was observed by FE-SEM (Hitachi s-4800, Japan). All samples were coated with platinum before measurements. The thermal properties of neat PLA and PLA composite films were investigated using TGA (model Netzsch 209F3 from Netzsch Co., Ltd., Selb, Germany) under a nitrogen atmosphere. All samples were heated from 35 • C to 900 • C at a heating rate of 10 • C/min. The crystallization behavior of neat PLA and PLA composite films was investigated by differential scanning calorimetry (DSC) (model Netzsch 204F1 Phoenix from Netzsch Co., Ltd., Selb, Germany) under a nitrogen atmosphere. For all samples, the first heating scan was performed by heating the samples to 200 • C at a heating rate of 10 • C/min to eliminate thermal histories. After this, the samples were cooled down to 25 • C at a cooling rate of 10 • C/min. The second heating scan was performed by heating the samples to 200 • C at a heating rate of 10 • C/min. The glass transition temperature (T g ), the cold crystallization temperature (T cc ) and the melting temperature (T m ) were determined from the second heating scan. Alumina crucible pans (Netzsch Co., Ltd., Selb, Germany) were used for TGA and DSC measurements. Young's modulus and tensile strength of neat PLA and PLA composite films were measured by using a universal testing machine (model Lloyd LRX from Lloyd Instruments Co., Ltd., West Sussex, UK) according to the ASTM D882 with a 500-N load cell. Each datum was the average of 5 specimens. Antibacterial activities of neat PLA, PLA/activated charcoal, PLA/carbon-WC and PLA/carbon-WC-Ag composite films against Escherichia coli (E. coli) and Staphylococcus aureus (S. aureus) were investigated by using the colony-forming unit assay according to the modified procedure of Janpetch et al. 2016 [62]. The bacterial reduction rate (BRR) was calculated according to Equation (2): where N 1 represents the number of colonies from the blank cell suspension and N 2 represents the number of colonies from the cell suspension containing PLA samples.

Statistical Analysis
The significant differences in the selected parameters were evaluated via analysis of variance (ANOVA) according to Turkey's HSD (honestly significant difference) test at p-value < 0.05 using IBM SPSS Statistics 26 software (SPSS Inc., Chicago, IL, USA).

Characterization of Carbon-WC and Carbon-WC-Ag Nanoparticles
According to the previous studies on SPP, active species such as H, C 2 and W radicals were generated during plasma discharge in organic solvents by using tungsten electrodes due to the dissociation of the molecules of organic solvents and the sputtering of tungsten electrodes [26,33]. The formation of carbon mainly depended on the interactions of the generated C 2 radicals with each other, resulting in the formation of polycyclic structures. In this study, the pathways of carbon formation from palm oil by SPP were postulated to involve the transformation of hydrocarbon moieties of fatty acids existing in palm oil to cyclic compounds. Subsequently, the cyclic compounds underwent recombination to form polycyclic structures and eventually converted to a network structure of carbon, as described in previous studies [33,36].
In addition, tungsten carbide (WC) could be formed during plasma discharge by the reaction between W and C 2 radicals and subsequently embedded in the simultaneously generated carbon, resulting in the formation of carbon containing tungsten carbide (carbon-WC). Figure  , were also observed in the XRD pattern of carbon-WC [33,63]. Furthermore, a peak at 2θ = 38.5 • corresponding to the (110) plane of tungsten metal appeared at a very low intensity. This might be explained by the fact that tungsten metal originated from the erosion of tungsten electrodes during plasma discharge [33,64]. The amount of tungsten metal incorporated into carbon-WC was relatively low due to the very low intensity of the peak of tungsten metal. Accordingly, carbon-WC synthesized by SPP in this study was referred to as the synthesized carbon that contained metastable tungsten carbide and a negligible amount of tungsten metal. tungsten metal originated from the erosion of tungsten electrodes during plasma discharge [33,64]. The amount of tungsten metal incorporated into carbon-WC was relatively low due to the very low intensity of the peak of tungsten metal. Accordingly, carbon-WC synthesized by SPP in this study was referred to as the synthesized carbon that contained metastable tungsten carbide and a negligible amount of tungsten metal. In Figure 2b, the Raman spectrum of carbon-WC consists of two peaks at 1350 cm −1 and 1580 cm −1 which correspond to the D band and G band, respectively. The D band is attributed to the occurrence of defects and disorder in the graphitic structure, whereas the G band is attributed to the formation of a well-organized graphitic structure. According to the obtained Raman spectrum, the intensity of the D band was slightly higher than the intensity of the G band, indicating an amorphous state of carbon-WC.
The wide-scan XPS spectra of carbon-WC and carbon-WC-Ag nanoparticles are shown in Figure 2c. The peaks of carbon C 1s and oxygen O 1s were detected for carbon-WC and carbon-WC-Ag nanoparticles, whereas the wide-scan XPS spectrum of carbon-WC-Ag nanoparticles shows the characteristic peaks of Ag 3d at 368.05 eV and 374.1 eV and the characteristic peaks of Ag 3p at 572.98 eV and 604.3 eV [20]. The narrow-scan XPS In Figure 2b, the Raman spectrum of carbon-WC consists of two peaks at 1350 cm −1 and 1580 cm −1 which correspond to the D band and G band, respectively. The D band is attributed to the occurrence of defects and disorder in the graphitic structure, whereas the G band is attributed to the formation of a well-organized graphitic structure. According to the obtained Raman spectrum, the intensity of the D band was slightly higher than the intensity of the G band, indicating an amorphous state of carbon-WC.
The wide-scan XPS spectra of carbon-WC and carbon-WC-Ag nanoparticles are shown in Figure 2c. The peaks of carbon C 1s and oxygen O 1s were detected for carbon-WC and carbon-WC-Ag nanoparticles, whereas the wide-scan XPS spectrum of carbon-WC-Ag nanoparticles shows the characteristic peaks of Ag 3d at 368.05 eV and 374.1 eV and the characteristic peaks of Ag 3p at 572.98 eV and 604.3 eV [20]. The narrow-scan XPS spectra of activated charcoal and carbon-WC-Ag nanoparticles are shown in Figure 2d C=O, respectively. The C=O was present in carbon-WC-Ag nanoparticles but was absent in activated charcoal. It was suggested that carbonyl groups could be incorporated into the structure of carbon prepared by SPP [27,65].
FE-SEM images of carbon-WC and carbon-WC-Ag nanoparticles are shown in Figure 3a,b, respectively. It was found that the particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were in the ranges of 10-50 nm and 20-400 nm, respectively. Additionally, the average particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were 22.60 nm and 129.06 nm, respectively. The particle size distribution of carbon-WC and carbon-WC-Ag nanoparticles is shown in Figure S1a,b. Interestingly, the FE-SEM image of carbon-WC-Ag nanoparticles (Figure 3b) shows spherical nanoparticles with bumpy surfaces. The presence of WC nanoparticles (WCNPs) in carbon-WC and carbon-WC-Ag nanoparticles was evidenced by TEM images, as shown in Figure 4b-d. It can be seen that WCNPs with particle sizes in the range of 2-5 nm were dispersed in amorphous carbon, whereas the TEM image of activated charcoal (Figure 4a) confirmed the amorphous state of activated charcoal. In Figure 4c,d, TEM images of carbon-WC-Ag nanoparticles show that AgNPs having particle sizes in the range of 10-400 nm and an average particle size of 72.74 nm were embedded in amorphous carbon, where WCNPs also dispersed. The particle size distribution of AgNPs existing in carbon-WC-Ag nanoparticles is shown in Figure S1c. The results of TEM are in good agreement with the results of XRD and Raman spectroscopy. spectra of activated charcoal and carbon-WC-Ag nanoparticles are shown in Figure 2d,e, respectively. For activated charcoal, the C 1s spectra consisted of three peaks located at 283.70 eV, 284.00 eV and 285.3 eV, which corresponded to C=C, C-C and C-O, respectively. For carbon-WC-Ag nanoparticles, the C 1s spectra consisted of four peaks located at 284.64 eV, 285.09 eV, 286.26 eV and 288.59 eV, which corresponded to C=C, C-C, C-O and C=O, respectively. The C=O was present in carbon-WC-Ag nanoparticles but was absent in activated charcoal. It was suggested that carbonyl groups could be incorporated into the structure of carbon prepared by SPP [27,65].
FE-SEM images of carbon-WC and carbon-WC-Ag nanoparticles are shown in Figure  3a,b, respectively. It was found that the particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were in the ranges of 10-50 nm and 20-400 nm, respectively. Additionally, the average particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were 22.60 nm and 129.06 nm, respectively. The particle size distribution of carbon-WC and carbon-WC-Ag nanoparticles is shown in Figure S1a,b. Interestingly, the FE-SEM image of carbon-WC-Ag nanoparticles (Figure 3b) shows spherical nanoparticles with bumpy surfaces. The presence of WC nanoparticles (WCNPs) in carbon-WC and carbon-WC-Ag nanoparticles was evidenced by TEM images, as shown in Figure 4b-d. It can be seen that WCNPs with particle sizes in the range of 2-5 nm were dispersed in amorphous carbon, whereas the TEM image of activated charcoal (Figure 4a) confirmed the amorphous state of activated charcoal. In Figure 4c   spectra of activated charcoal and carbon-WC-Ag nanoparticles are shown in Figure 2d,e, respectively. For activated charcoal, the C 1s spectra consisted of three peaks located at 283.70 eV, 284.00 eV and 285.3 eV, which corresponded to C=C, C-C and C-O, respectively. For carbon-WC-Ag nanoparticles, the C 1s spectra consisted of four peaks located at 284.64 eV, 285.09 eV, 286.26 eV and 288.59 eV, which corresponded to C=C, C-C, C-O and C=O, respectively. The C=O was present in carbon-WC-Ag nanoparticles but was absent in activated charcoal. It was suggested that carbonyl groups could be incorporated into the structure of carbon prepared by SPP [27,65].
FE-SEM images of carbon-WC and carbon-WC-Ag nanoparticles are shown in Figure  3a,b, respectively. It was found that the particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were in the ranges of 10-50 nm and 20-400 nm, respectively. Additionally, the average particle sizes of carbon-WC and carbon-WC-Ag nanoparticles were 22.60 nm and 129.06 nm, respectively. The particle size distribution of carbon-WC and carbon-WC-Ag nanoparticles is shown in Figure S1a   Furthermore, atomic percentages of each element in activated charcoal, carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles were investigated by scanning electron microscopy with energy dispersive X-ray (SEM-EDX) analysis and the results are shown in Table 2. The tungsten contents in carbon-WC and carbon-WC-Ag nanoparticles were 3.59% and 3.81%, respectively, whereas the silver contents in carbon-Ag and carbon-WC-Ag nanoparticles were 10.81% and 11.20%, respectively. Table 2. Elemental compositions of activated charcoal, carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles (n = 3).

Type of Elements
Atomic Percentage (%) ± SD

Morphology of Neat PLA and PLA Composite Films
The SEM images of the surface morphology of neat PLA and PLA/carbon-WC-Ag composite films with different filler contents of 0.25, 0.75, 1.23, 1.72 and 2.20 wt% were taken ( Figure S2). While the neat PLA film ( Figure S2a) had a smooth surface, the PLA/carbon-WC-Ag composite films ( Figure S2b-f) had rugged surfaces due to the presence of carbon-WC-Ag nanoparticles in the composite films. The SEM images of the composite films indicated that, at the filler contents of 0.25, 0.75 and 1.23 wt% ( Figure S2b-d), carbon-WC-Ag nanoparticles had low aggregation and could maintain random dispersion in the PLA matrix. However, at the higher filler contents of 1.72 and 2.20 wt% ( Figure S2e-f), the aggregation of carbon-WC-Ag nanoparticles in the PLA matrix was obviously observed. Accordingly, the PLA/carbon-WC-Ag composite films with the filler content of 1.23 wt% were used for further studies. In addition, an SEM image of the cross-sectional morphology of the PLA/carbon-WC-Ag composite film at the filler content of 1.23 wt% was taken ( Figure S3). It is clearly shown that carbon-WC-Ag nanoparticles were embedded in the PLA matrix and the average film thickness was measured to be 95.5 ± 0.52 µm (n = 3).

Thermogravimetric Analysis
TGA of neat PLA and PLA composite films, i.e., PLA/activated charcoal, PLA/carbon-WC, PLA/carbon-Ag and PLA/carbon-WC-Ag, at the filler content of 1.23 wt%, was performed and the values of the initial degradation temperature (T int ), the 50% weight loss temperature (T 50 ) and the degradation temperature (T max ) are listed in Table 3. According to the TGA results, the T int of PLA/carbon-WC-Ag composite film was significantly higher than that of the neat PLA film, indicating the increment of thermal stability of the PLA/carbon-WC-Ag composite film at the initial state of thermal degradation. This might be due to the heat capacity of WCNPs and AgNPs, which could absorb heat during the initial state of thermal degradation. It is known that various types of transition metals and alkali earth metal oxides favor the thermal decomposition of PLA, leading to a reduction in the thermal stability of PLA [7,[66][67][68]. Compared with the neat PLA film, a reduction in T 50 and T max of PLA/carbon-WC composite films was observed. This result suggested that the presence of carbon-WC in the composite films could accelerate the thermal degradation of PLA. On the contrary, only a slight reduction in thermal stability of PLA/carbon-Ag composite film was observed when compared with the neat PLA film. Similarly, it has been reported that the presence of silver in the PLA matrix slightly affected the thermal stability of PLA composites [69,70]. Table 3. Initial degradation temperature (T int ), 50% weight loss temperature (T 50 ) and degradation temperature (T max ) of neat PLA and PLA composite films at a filler content of 1.23 wt%. The superscript letter "a" refers to significant differences among T int , T 50 and T max of the PLA composite films at p-value < 0.05. The superscript letter "b" refers to non-significant difference between T 50 of PLA/activated charcoal and PLA/carbon-Ag and non-significant difference between T max of PLA/activated charcoal and PLA/carbon-WC-Ag at p-value < 0.05.

Composite Films T int ( • C) T 50 ( • C) T max ( • C)
Considering the T 50 and T max of PLA/carbon-WC-Ag composite films, the reduction in the thermal stability of PLA/carbon-WC-Ag composite films was less than that of PLA/carbon-WC composite films but higher than that of PLA/carbon-Ag composite films. As mentioned previously, carbon-WC could accelerate the thermal degradation of PLA, whereas AgNPs slightly affected the thermal stability of the composite films. It might be implied that the coexistence of AgNPs in carbon-WC-Ag could hinder the effect of WCNPs on the degradation of PLA upon heating. Nevertheless, the PLA/carbon-WC-Ag composite films had intrinsic thermal degradation properties. Therefore, the PLA/carbon-WC-Ag composite film is a potential candidate for use as an environmentally friendly material.

Differential Scanning Calorimetry
The effect of the incorporation of the fillers, i.e., activated carbon, carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles, into PLA on the non-isothermal crystallization behavior of PLA was investigated by DSC via heating-cooling-heating scans and the results are shown in Figure 5. The glass transition temperature (T g ), the cold crystallization temperature (T cc ) and the melting temperature (T m ) of neat PLA and the PLA composite films are detailed in Table 4. No significant change in the T g of all the PLA composite films was observed when compared with the neat PLA film, indicating that the presence of the synthesized carbon-based nanoparticles, i.e., carbon-WC, carbon-Ag and carbon-WC-Ag, in PLA matrix did not affect the mobility of PLA chains in amorphous regions [39,71]. Table 3. Initial degradation temperature (Tint), 50% weight loss temperature (T50) and degradation temperature (Tmax) of neat PLA and PLA composite films at a filler content of 1.23 wt%. The superscript letter "a" refers to significant differences among Tint, T50 and Tmax of the PLA composite films at p-value < 0.05. The superscript letter "b" refers to non-significant difference between T50 of PLA/activated charcoal and PLA/carbon-Ag and non-significant difference between Tmax of PLA/activated charcoal and PLA/carbon-WC-Ag at p-value < 0.05.

Tint (°C) T 50 (°C) T max (°C)
Considering the T50 and Tmax of PLA/carbon-WC-Ag composite films, the reduction in the thermal stability of PLA/carbon-WC-Ag composite films was less than that of PLA/carbon-WC composite films but higher than that of PLA/carbon-Ag composite films. As mentioned previously, carbon-WC could accelerate the thermal degradation of PLA, whereas AgNPs slightly affected the thermal stability of the composite films. It might be implied that the coexistence of AgNPs in carbon-WC-Ag could hinder the effect of WCNPs on the degradation of PLA upon heating. Nevertheless, the PLA/carbon-WC-Ag composite films had intrinsic thermal degradation properties. Therefore, the PLA/carbon-WC-Ag composite film is a potential candidate for use as an environmentally friendly material.

Differential Scanning Calorimetry
The effect of the incorporation of the fillers, i.e., activated carbon, carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles, into PLA on the non-isothermal crystallization behavior of PLA was investigated by DSC via heating-cooling-heating scans and the results are shown in Figure 5. The glass transition temperature (Tg), the cold crystallization temperature (Tcc) and the melting temperature (Tm) of neat PLA and the PLA composite films are detailed in Table 4. No significant change in the Tg of all the PLA composite films was observed when compared with the neat PLA film, indicating that the presence of the synthesized carbon-based nanoparticles, i.e., carbon-WC, carbon-Ag and carbon-WC-Ag, in PLA matrix did not affect the mobility of PLA chains in amorphous regions [39,71].  Table 4. Glass transition temperature (T g ), cold crystallization temperature (T cc ) and melting temperature (T m ) at the second heating scan of neat PLA and the PLA composite films at a filler content of 1.23 wt%. The superscript letter "a" refers to significant differences among T cc of the PLA composite films at p-value < 0.05. The superscript letter "b" refers to non-significant differences among T g and T m of the PLA composite films at p-value < 0.05.

Composite
On the other hand, it was found that the incorporation of carbon-WC, carbon-Ag and carbon-WC-Ag nanoparticles as fillers in the PLA composite films resulted in shifts in the T cc of the PLA composite films to lower temperatures compared with that of the neat PLA film, indicating the nucleating effect of the fillers. Due to the presence of polar functional groups such as carbonyl groups and high surface area, the synthesized carbonbased nanoparticles could interact with PLA and create nucleating sites to initiate the crystallization of PLA, resulting in an increase in the crystallization of PLA.
The presence of WCNPs and AgNPs in the synthesized carbon-based nanoparticles affected the nucleation ability of the synthesized carbon-based nanoparticles on the crystallization of PLA. It was found that the cold crystallization peak of PLA/carbon-WC was sharper and shifted to a lower temperature when compared to that of PLA/carbon-Ag ( Figure 5). The lower T cc in the second heating scan indicated the faster crystallization of PLA, which was induced by the added carbon-WC [10]. It might be implied that the presence of WCNPs in the synthesized carbon-based nanoparticles could promote the interaction between the synthesized carbon-based nanoparticles and PLA chains and subsequently enhance the nucleation ability of the synthesized carbon-based nanoparticles to accelerate the crystallization process of PLA.
Moreover, the T cc of PLA/carbon-WC-Ag was lower than those of PLA/carbon-WC and PLA/carbon-Ag, suggesting the synergetic effect of the nucleation ability of WCNPs and AgNPs, accelerating the crystallization process of PLA. The T m of all the PLA composite films shifted to lower temperatures when compared with that of the neat PLA film. This might be due to the transformation of the crystalline structure of PLA to the imperfect crystal forms during cold crystallization and the imperfect crystal forms could re-melt at a lower temperature [9,72]. Figure 6 shows XRD patterns of neat PLA and the PLA composite films, i.e., PLA/activated charcoal, PLA/carbon-Ag, PLA/carbon-WC and PLA/carbon-WC-Ag, at the filler content of 1.23%wt. The XRD pattern of the neat PLA film exhibited a diffraction peak at 2θ = 16.64 • , which corresponds to the (110)/(200) planes of crystalline PLA [73]. It was found that the intensity of the diffraction peak at 2θ = 16.64 • in the XRD pattern of PLA/carbon-WC-Ag was much higher than those of neat PLA, PLA/activated charcoal, PLA/carbon-Ag and PLA/carbon-WC. From XRD analysis, it was found that the values of the degree of crystallinity (χ c ) of neat PLA, PLA/activated charcoal, PLA/carbon-Ag, PLA/carbon-WC and PLA/carbon-WC-AgNPs were 1.43%, 1.52%, 2.20%, 5.94% and 14.23%, respectively. This evidence confirmed that carbon-WC-Ag nanoparticles could lead to an improved crystalline structure of PLA by the co-nucleation ability of WCNPs and AgNPs coexisting in carbon-WC-Ag nanoparticles.

Mechanical Test
In general, there are two possible factors that can influence the mechanical properties of PLA. The first is the dispersion of fillers in the PLA matrix and the second is the crystallinity of PLA, which depends largely on the crystallization behavior of PLA [39,74]. In this study, the Young's modulus of the neat PLA film was 6.45 GPA. At the filler content of 1.23 wt%, the values of the Young's modulus of PLA/activated charcoal, PLA/carbon-WC, PLA/carbon-Ag and PLA/carbon-WC-Ag composite films were 7.24, 7.74, 7.97 and 8.07 GPa, respectively. These results indicated that the presence of activated charcoal, carbon-WC, carbon-Ag and carbon-WC-Ag in the PLA matrix led to an increase in the Young's modulus of PLA. The increased Young's modulus was related to the DSC results showing that the co-nucleation of WCNPs and AgNPs coexisting in carbon-WC-Ag nanoparticles could accelerate the crystallization process of PLA, resulting in a better crystalline structure and higher Young's modulus of PLA/carbon-WC-Ag composite films.
The values of tensile strength of the neat PLA, PLA/activated charcoal, PLA/carbon-WC, PLA/carbon-Ag and PLA/carbon-WC-Ag composite films were 19.92, 26.75, 21.16, 31.02 and 29.10 MPa, respectively. Due to the presence of some degree of aggregation of carbon-WC in the PLA matrix, the tensile strength of the PLA/carbon-WC composite film was not much higher than that of the neat PLA film. However, the incorporation of 1.23 wt% carbon-WC-Ag nanoparticles into the PLA matrix resulted in an increase in the tensile strength of PLA/carbon-WC-Ag composite films by 46.08% when compared with that of the neat PLA film. Since carbon-WC-Ag nanoparticles had bumpy surfaces, as evidenced by the SEM images, the surface roughness of carbon-WC-Ag nanoparticles might help to reduce the aggregation of carbon-WC-Ag nanoparticles in the PLA matrix, leading to a decrease in the stress concentrated point and consequently an increase in tensile strength [75]. Accordingly, it might be concluded that the incorporation of carbon-WC-Ag nanoparticles as fillers in the PLA matrix, even at a low filler content of 1.23 wt%, could significantly improve the Young's modulus and tensile strength of the resulting PLA/carbon-WC-Ag composite films.

Antibacterial Test
Antibacterial activities against E. coli and S. aureus of the neat PLA and the PLA composite films were evaluated by colony-forming unit assay. The cell suspensions without

Mechanical Test
In general, there are two possible factors that can influence the mechanical properties of PLA. The first is the dispersion of fillers in the PLA matrix and the second is the crystallinity of PLA, which depends largely on the crystallization behavior of PLA [39,74]. In this study, the Young's modulus of the neat PLA film was 6.45 GPA. At the filler content of 1.23 wt%, the values of the Young's modulus of PLA/activated charcoal, PLA/carbon-WC, PLA/carbon-Ag and PLA/carbon-WC-Ag composite films were 7.24, 7.74, 7.97 and 8.07 GPa, respectively. These results indicated that the presence of activated charcoal, carbon-WC, carbon-Ag and carbon-WC-Ag in the PLA matrix led to an increase in the Young's modulus of PLA. The increased Young's modulus was related to the DSC results showing that the co-nucleation of WCNPs and AgNPs coexisting in carbon-WC-Ag nanoparticles could accelerate the crystallization process of PLA, resulting in a better crystalline structure and higher Young's modulus of PLA/carbon-WC-Ag composite films.
The values of tensile strength of the neat PLA, PLA/activated charcoal, PLA/carbon-WC, PLA/carbon-Ag and PLA/carbon-WC-Ag composite films were 19.92, 26.75, 21.16, 31.02 and 29.10 MPa, respectively. Due to the presence of some degree of aggregation of carbon-WC in the PLA matrix, the tensile strength of the PLA/carbon-WC composite film was not much higher than that of the neat PLA film. However, the incorporation of 1.23 wt% carbon-WC-Ag nanoparticles into the PLA matrix resulted in an increase in the tensile strength of PLA/carbon-WC-Ag composite films by 46.08% when compared with that of the neat PLA film. Since carbon-WC-Ag nanoparticles had bumpy surfaces, as evidenced by the SEM images, the surface roughness of carbon-WC-Ag nanoparticles might help to reduce the aggregation of carbon-WC-Ag nanoparticles in the PLA matrix, leading to a decrease in the stress concentrated point and consequently an increase in tensile strength [75]. Accordingly, it might be concluded that the incorporation of carbon-WC-Ag nanoparticles as fillers in the PLA matrix, even at a low filler content of 1.23 wt%, could significantly improve the Young's modulus and tensile strength of the resulting PLA/carbon-WC-Ag composite films.

Antibacterial Test
Antibacterial activities against E. coli and S. aureus of the neat PLA and the PLA composite films were evaluated by colony-forming unit assay. The cell suspensions without the addition of tested samples were used as controls. It was found that the neat PLA film had no antibacterial activity against E. coli and S. Aureus, whereas the presence of activated charcoal and carbon-WC in the PLA composite films resulted in negligible inhibitory effects on E. coli and S. Aureus. The bacterial reduction rate (BRR) of the PLA composite film containing 1.23 wt% of carbon-WC-Ag nanoparticles against E. coli and S. aureus was 61.22% and 52.17%, respectively. It is well-known that AgNPs are used as a powerful antimicrobial agent. However, the deposition of AgNPs on a supporting material such as carbon may hinder the diffusion of AgNPs, resulting in lower antimicrobial activity than the corresponding unbound AgNPs. On the other hand, this may lead to better biocompatibility [22,76,77] when AgNPs deposited on a supporting material are incorporated into biomaterials for use in contact with living cells, such as in medical implants. Accordingly, the PLA/carbon-WC-Ag composites may be further developed for not only packaging materials but also biomedical applications.

Conclusions
Carbon-WC-Ag nanoparticles were simply synthesized in one step with the aid of SPP by using palm oil containing droplets of AgNO 3 solution as carbon and silver precursors, respectively. Instead of using chemical agents, highly active species generated during plasma discharge induced the formation of carbon-WC-Ag nanoparticles. The synthesized carbon-WC-Ag nanoparticles were subsequently examined as multifunctional fillers for the preparation of PLA composite films fabricated by solution casting. The optimum content of carbon-WC-Ag nanoparticles in the PLA/carbon-WC-Ag composite film was 1.23 wt%. Interestingly, WCNPs and AgNPs coexisting in carbon-WC-Ag nanoparticles exhibited a conucleation ability to accelerate the crystallization process of PLA, resulting in an enhanced crystalline structure of the PLA/carbon-WC-Ag composite films. It was found that the degree of crystallinity of PLA/carbon-WC-Ag composite films was roughly ten times higher than that of neat PLA film. Consequently, the Young's modulus and tensile strength of the PLA/carbon-WC-Ag composite films could be significantly improved. Moreover, WCNPs in the PLA composite films might be involved in the enhancement of the thermal degradation of PLA, leading to an advantage in their degradation. Due to the presence of AgNPs, the PLA/carbon-WC-Ag composite films exhibited antibacterial activities against E. coli and S. aureus. The evidence in this study indicates that SPP is a powerful tool for the synthesis of multicomponent nanoparticles. Moreover, multicomponent nanoparticles such as carbon-WC-Ag nanoparticles are useful as multifunctional fillers for the development of PLA composites aimed at packaging and biomaterial applications.