A Highly Effective, UV-Curable, Intumescent, Flame-Retardant Coating Containing Phosphorus, Nitrogen, and Sulfur, Based on Thiol-Ene Click Reaction

In this paper, a flame-retardant, UV-cured coating was prepared on the fiber composites’ (FC) surface via a thiol-ene click reaction using pentaerythritol tetra(3-mercaptopropionate) (PETMP), triallyl cyanurate (TAC), and 2-hydroxyethyl methacrylate phosphate (PM-2). The synergistic effectiveness of phosphorus (P), nitrogen (N), and sulfur (S) was studied in detail by changing the proportion of these reactants. Sample S4(N3P2)6, with a molar ratio of N and P elements of 3:2, and the thiol and vinyl groups of 4:6 had the highest LOI value (28.6%) and was self-extinguishing in the horizontal combustion test. It had the lowest peak heat release rate (PHRR) value (279.25 kW/m2) and total smoke production (2.18 m2). Moreover, the thermogravimetric analysis (TG) showed that the decomposition process of the coated composites was delayed. The conversion rate of the double bond and the thiol of S4(N3P2)6 was 100% and 92.0%, respectively, which showed that the cross-linked network structure was successfully formed. The tensile strength and the flexural strength of coated composites improved, and the transparency of the coating can reach 90%. These characteristics showed that the UV-cured coatings could be used in industrial production to effectively prevent fires.


Introduction
A UV-curable coating can be used on different substrates [1][2][3][4] to enhance the materials with various properties, such as fire resistance [5,6], anti-fouling [7], and good optical transparency [8]. Compared with ordinary polymer coatings, UV-curable coatings have the advantages of short reaction time, low energy consumption, and simple operation [9]. The functional UV-curable coating is based on the modification of unsaturated resinunsaturated polyester, acrylic resin, etc. These systems have problems that need to be solved urgently, such as high viscosity, large volume shrinkage after curing, oxygen inhibition, and a non-uniform crosslinking network [10,11]. Among them, oxygen inhibition is the main obstacle in the UV-cured process [12,13]. Oxygen reacts with the free radicals initiated by the photoinitiator in the chain growth step and finally generates peroxy free radicals with lower activity, which leads to the failure of the curing of the coating surface and the low conversion rate of the UV-cured film. So far, the most commonly used method in the industry is curing under an N 2 atmosphere, using more photoinitiators or using multiple initiators to form a photoinitiating system [12,14]. However, these methods lead to a sharp increase in curing costs and greater volume shrinkage of the coating, which results in a decrease of the adhesion of UV-cured coatings, an increase of internal stress, and the deterioration of mechanical properties [11].
The thiol-ene click reaction uses vinyl monomers and thiol monomers as prepolymers. The polymerization reaction is a free-radical step-growth reaction with the participation of

Preparation of Samples
The flax fiber, kenaf fiber, and polypropylene fiber were blended in the mass ratio of 1:1:2 to prepare the needle-punched nonwoven felts. The non-woven felts were hot-pressed into fiber composites (FC) at 180 • C and 8 MPa. The formulation of UV curable coatings is shown in Table 1. The coatings were obtained by mixing four materials in different proportions, which included a prepolymer containing thiol groups (PETMP), a prepolymer TAC containing nitrogen, a phosphate functional monomer (PM-2), and the photoinitiator BAPO. There is one C=C bond in PM-2 and three C=C bonds in TAC; the thiol monomer contains four thiol groups, and the ratio of monomers meets C=C: SH=1:1. From this, the best ratio of nitrogen and phosphorus can be explored. On this basis, the relationship between the ratio and the conversion rate can also be studied by changing the ratio of C=C and SH. Thereafter, the prepolymer solution was mixed thoroughly with the photoinitiator BAPO (3 wt% of the total weight of TAC, PM-2, and PETMP) at 60 • C for 30 min to obtain a clear liquid. The homogeneous mixture was coated on the fiber composites with a 200 µm film-applicator to form uniform films. Samples were cured under a 395 nm light from a UV lamp (Zhongshan Guzhen Yanxizhao Lighting Appliance Factory, AC90V-240V 395 nm 35W, Zhongshan, China) at a distance of 10 cm for 1 min or more to ensure an adequate click reaction. The structure of the prepolymers and a brief description of preparation for an idealized cross-linked network via a thiol-ene click reaction is shown in Figure 1. The photopolymerization kinetics were studied by the TENSOR 27 FTIR spectrometer (Germany Bruker, Berlin) in the range of 4000-400 cm −1 . The double bond conversation was monitored by measuring the area under the peak of 1637 cm −1 , and the peak at 2572 cm −1 was used to measure the thiol group conversation. The peak at 1730 cm −1 represented the stretching vibration peak of C=O, and the intensity of the peak did not change significantly during the FTIR tests. As a result, the peak at 1730 cm −1 was used as an internal standard peak to neutralize the variation in the coatings caused by rapid curing [2,5,20]. The double bond conversation rate (DC) could be calculated according to Equation (1): The thiol group conversation (TC) could be calculated according to Equation (2): where A 0 (1637 cm −1 ), A 0 (1730 cm −1 ), and A 0 (2572 cm −1 ) represent the integral peak area of C=C, C=O, and -SH, before curing, respectively; the t at A t represents the UV-curing time.

Limiting Oxygen Index (LOI)
The LOI of the coated composites was obtained by an LOI instrument (JF-3, Seoul, Korea FESTEC Company) according to GB/T 2406.2-2009 (China) oxygen index method. The sample size used for the test was 100 × 10 × 3 mm 3 .

Horizontal Burning Rate (HBR)
The HBR test was performed using a burning test instrument (H1011D, Changchun-shiHosly apply technique graduate school, Changchun, China). The test was measured according to the Flammability of automotive interior materials (GB 8410-2006). The composites were ignited for 15 s, and then the fire was removed. Burning length and time were recorded to calculate the burning rate. The sample size used for HBR tests was 150 × 75 × 3 mm 3 .

Thermo-Gravimetric Analysis (TG)
The thermogravimetric (TG) analysis results were obtained on a Q500 thermal analyzer (TA Instruments, New Castle, DE, USA) under a nitrogen atmosphere (50 mL/min), and under an air atmosphere with a heating rate of 10 • C/min. About 5-10 mg of the samples was placed in an alumina crucible and heated from 25-800 • C.

Cone Calorimetry Test (CCT)
The CCT is one of the best methods to evaluate the combustion characteristics of the samples. The CCT was performed with a cone calorimeter apparatus (FTT0242, West Sussex, UK) according to ISO 5660 (2002). In the test, the coated composites were exposed to a radiation cone with a heat flux of 50.0 kW/m 2 . The sample size was 100 × 100 × 3 mm 3 .

Mechanical Properties
The mechanical tests, including the tensile strength and the bending strength, were performed using a universal testing machine WSM-5KN (Changchun intelligent instrument equipment Co., Ltd., Changchun, China) according to the TL52448. The dimensions of each specimen were 100 × 25 × 3 mm 3, and the strain rate was 3 mm/min. All mechanical data had an effective average of 5.

Adhesion Test
The adhesion test was measured using the single blade pocket knife in accordance with ISO 2409:2013. The number of cuts in each direction was 6, and the cross-cut spacing was 3 mm.

Optical Transparency
The optical transparency of the UV-cured coatings was recorded using a UV-6100s Scanning UV-Vis Spectrophotometer (Shanghai Mepda Instrument Co., Ltd., Shanghai, China) in the range of 200-1100 nm.

Morphology Observation
The char residues after HBR tests were observed via scanning electron microscopy (SEM, 30 kv/Magellan400, FEI NanoPorts, Hillsboro, Oregon, USA). The energy-dispersive spectrometer (EDS, Magellan400, FEI NanoPorts, Hillsboro, Oregon, USA) on the SEM was used to observe the surface of the coated samples after HBR tests and compare the content of C, O, N, P, and S of the coatings on the surface of coated composites before and after the HBR test.

Curing Kinetics and Double Bond Conversion
In order to study the effect of the relative changes of ratio of -SH to C=C and the TAC to PM-2 on the curing performance of the coating, the FTIR technique was employed to monitor the chemical structure changes of the S 5 N x P y and S x (N 3 P 2 ) y series coatings before and after curing. As shown in Figure 2, the FTIR spectra of sample S 4 (N 3 P 2 ) 6 was recorded at different UV-irradiation times (5 s, 10 s, 20 s, 30 s, 60 s, and 300 s) [2,4,20,21]. The conversion rate of the thiol and vinyl groups gradually stabilized after 20 s. Besides, the C=C and -SH peak intensity remained almost unchanged at 60-300 s, which indicated that the curing process was complete and the double bond and the thiol had formed the cross-linked network structure. Thus, the coating formed when the curing time was 60 s. Figure 2c showed that the relative change of PM-2 and TAC content had little effect on the double bond conversion rate. However, when the -SH and C=C molar ratio was 1:1, as the content of PM-2 increased, the -SH conversion rate gradually decreased as in Figure 2d. This may be because there were acrylate groups in PM-2; the double bond tended to undergo homopolymerization and does not copolymerize with thiol during the UV-curing process, which led to a higher double bond conversion rate than the thiol conversion rate (Figure 2c,d). The final conversion rate of thiol and double bond is shown in Table 2; the conversion rate of the double bond of coating S 3 (N 3 P 2 ) 7 and S 4 (N 3 P 2 ) 6 reached 100%; and the conversion rate of thiol reached 96.2% and 92%, respectively. The double bond and thiol had an optimal ratio of homopolymerization and copolymerization, and the coatings had good film-forming properties. However, excessive C=C content led to homopolymerization and lower thiol conversion rate (Figure 2e,f), and the -SH conversion rates of samples S 1 (N 3 P 2 ) 9 and S 2 (N 3 P 2 ) 8 decreased to 87.6% and 81.8%, respectively. At this time, the oxygen inhibition effect in the homopolymerization reaction gradually appeared, so the double bond conversion rate also decreased to a certain extent. However, the double bond conversion rate of sample S 1 (N 3 P 2 ) 9 remained at 92.8%. This showed that the presence of -SH can effectively counter oxygen inhibition and ensure the coating has good filmforming properties. To sum up, the entire coatings system had good curing efficiency, good film-forming performance, and could form a complete cross-linked network structure. Figure 2. The Fourier Transform Infrared Spectroscopy (FTIR) spectra of sample S 4 (N 3 P 2 ) 6 , which were recorded during the UV-curing (a); the enlarged FTIT spectra of the thiol group (2572 cm −1 ) and the acrylate double bond (1637 cm −1 ) of the coating S 4 (N 3 P 2 ) 6, after being subjected to UV-irradiation for various durations (b); the double bond conversion rate versus the irradiation time (c,e); and the thiol group conversion versus the irradiation time (d,f).  6 28.6 85 s 100 92.0 S 3 (N 3 P 2 ) 7 27.0 140 s 100 96.2 S 2 (N 3 P 2 ) 8 25.9 214 s 97.1 87.6 S 1 (N 3 P 2 ) 9 25.5 220 s 92.8 81.8

Flame Retardancy of Fiber Composites
The formulation of the coating is the main factor affecting the flame-retardant performance. From Table 2, the proportion of flame-retardant elements was appropriate when the molar ratio of N and P was 3:2, and it played a synergistic flame-retardant role. The sample S 5 N 3 P 2 had the best flame-retardant performance among the S 5 N x P y series. The LOI value reached 27.2%, and was extinguished after 79 s. In addition, when the molar ratio of SH and C=C was 4:6, sample S 4 (N 3 P 2 ) 6 had the highest LOI value, up to 28.6%. In the horizontal combustion test, it quickly extinguished after being ignited for 85 s, which showed that S could also be used as a flame-retardant element and synergistically a flame-retardant with N and P elements. Figure 3 showed the carbon residue morphology of some samples after the horizontal combustion test. It can be seen that samples FC and S 5 N 5 P 0 were not self-extinguishing during the horizontal combustion test. The FC carbon layer was an amorphous and loose coke residue, and no dense carbon layer was formed. Sample S 5 N 5 P 0 formed a part of the carbon layer on the surface, but the carbon layer was disconnected and broken and thus did not effectively prevent the material from burning. The samples containing P elements all self-extinguished, indicating that P elements have obvious solid-phase flame-retardant effects. In general, when the N, P, and S elements coexisted in the coating, it showed an obvious synergistic effect of the gas-phase flame retardant and a solid-phase flame retardant, and it obtained better flame retardancy. layer was an amorphous and loose coke residue, and no dense carbon layer was formed. Sample S5N5P0 formed a part of the carbon layer on the surface, but the carbon layer was disconnected and broken and thus did not effectively prevent the material from burning. The samples containing P elements all self-extinguished, indicating that P elements have obvious solid-phase flame-retardant effects. In general, when the N, P, and S elements coexisted in the coating, it showed an obvious synergistic effect of the gas-phase flame retardant and a solid-phase flame retardant, and it obtained better flame retardancy.

Combustion Behavior
The cone calorimetry test can obtain the ignition time (TTI), the heat release rate (HRR), the peak heat release rate (PHRR), the total heat release rate (THR), the effective heat of combustion (EHC), the smoke production rate (SPR), the total smoke release (TSP), the CO and CO2 production, and other important parameters that can evaluate the potential fire hazard of materials [4,22]. Samples S5N5P0, S5N3P2, S5N0P5, S4(N3P2)6, and S1(N3P2)9 were selected for cone calorimetry analysis to further study the flame-retardant properties of the coating. The test results are shown in Figure 4 and Table 3. It is worth noting that due to the presence of flame-retardant elements such as N, P, and S, the coating formed an expanded carbon layer on the surface of the composites in the combustion process. The carbon layer could be used as a good thermal insulation layer, so HRR had a downward trend in 40-70 s, resulting in the first peak of the HRR curve. Subsequently, the matrix

Combustion Behavior
The cone calorimetry test can obtain the ignition time (TTI), the heat release rate (HRR), the peak heat release rate (PHRR), the total heat release rate (THR), the effective heat of combustion (EHC), the smoke production rate (SPR), the total smoke release (TSP), the CO and CO 2 production, and other important parameters that can evaluate the potential fire hazard of materials [4,22]. Samples S 5 N 5 P 0 , S 5 N 3 P 2 , S 5 N 0 P 5 , S 4 (N 3 P 2 ) 6 , and S 1 (N 3 P 2 ) 9 were selected for cone calorimetry analysis to further study the flame-retardant properties of the coating. The test results are shown in Figure 4 and Table 3. It is worth noting that due to the presence of flame-retardant elements such as N, P, and S, the coating formed an expanded carbon layer on the surface of the composites in the combustion process. The carbon layer could be used as a good thermal insulation layer, so HRR had a downward trend in 40-70 s, resulting in the first peak of the HRR curve. Subsequently, the matrix composites gradually burned, degraded, and released flammable products from the cracks of the carbon layer under the action of heat. The existence of the fireproof layer prevented the spread of flame and the combustion of the matrix materials, which resulted in a second peak in the HRR curve. In the HRR curve, sample S 4 (N 3 P 2 ) 6 exhibited the lowest PHRR value, indicating that sample S 4 (N 3 P 2 ) 6 had a good flame-retardant effect. As shown in Figure 4b and Table 3, the THR values of all the coated composites were not much different because all samples were completely consumed during the cone calorimetry. The types of flame-retardant elements contained in the coating could slightly affect the overall flammability of the fiber composites. When the coating contained only S and N (sample S 5 N 5 P 0 ) or only S and P (sample S 5 N 0 P 5 ), the HRR of the composites was 52.44 MJ/m 2 and 50.89 MJ/m 2 , which was higher than the coatings containing N, P, and S elements (around 47 MJ/m 2 ). This could indicate that the three flame-retardant elements of N, P, and S had a synergistic flame-retardant effect. However, the three elements' molar ratio had little effect on the HRR values of combustion. In addition, it must be mentioned that the TTI value of the coating samples with more phosphorus content decreased slightly, which might be attributed to the rapid rupture of the P-O-C bond and promoted the formation of the flame-retardant carbon layer.
Generally speaking, smoke and toxic gases will threaten people's health by poisoning and suffocating them in a real-life fire scene. The curves of the SPR and TSP of the samples are shown in Figure 4c,d, and the relevant data are summarized in Table 3. The trend of the SPR curve was similar to the HRR curve. As shown in Figure 4c, the composites reached the first peak in 20 s and then decreased rapidly in 20-60 s. Sample S 4 (N 3 P 2 ) 6 had a higher initial peak value, which was mainly attributed to the violent combustion of the phosphorous-contained coatings, and then the phosphate groups formed a dense carbon layer during the combustion process. This caused the second peak of the SPR curve of sample S 4 (N 3 P 2 ) 6 to be lower than other samples. Therefore, sample S 4 (N 3 P 2 ) 6 had the lowest TSP value, reaching 2.18 m 2 . This showed that the synergistic effect of N, S, and P elements could reduce smoke production in an appropriate proportion. CO and CO 2 production (Figure 4e,f) were also obtained to study the toxicity of burning products [22]. An increase in the CO production value of the coated composite was observed in the first 30 s, which might have been caused by rapid degradation and incomplete combustion of the coating. In the first 100 s since the formed carbon layer effectively prevented the escape of combustible gas CO, the CO production was significantly reduced within 100-200 s. However, there was a slow increase in CO production at the end of the combustion. This might have been because the early combustion consumed a lot of oxygen, resulting in insufficient oxygen content and incomplete combustion in the later stage of the combustion. Meanwhile, the TSP and CO production of the coatings with the N element were significantly reduced, indicating that the N element had an obvious gas-phase flame-retardant effect, which could effectively reduce the smoke emission. In addition, compared with other coating composites, sample S 4 (N 3 P 2 ) 6 had significantly lower CO 2 production, which could effectively reduce the risk of suffocation in a real fire.

Thermogravimetric Analysis
The influence of the changes of S, N, and P elements in the coating on the thermal stability of the composite was studied by TG and DTG curves. The TG and DTG curves of UV-coated composites are shown in Figures 5 and 6. Table 4 showed the thermogravimetric parameters, including the initial degradation temperature (T 5% ), the temperature corresponding to the maximum degradation rate (T max1 , T max2 ), and the carbon residue Y c at 700 • C. The sample FC had a high initial degradation temperature, and Y c can only reach 6.55% and 0.79% in N 2 and Air, respectively. With the increase of PM-2 content, the initial degradation temperature of the coated composites was gradually decreasing. This was mainly due to the lower bond energy of the P-O-C bond, which was not as stable as the C-C bond [23,24]. A small amount of the degradation of the coated composites below 200 • C was mainly due to the volatilization and degradation of a small part of the smallmolecule impurities that were not fixed in the cross-linked network. In the DTG curve, the degradation process of FC corresponds to the thermal decomposition of hemicellulose (250-300 • C), cellulose (320-390 • C), and polypropylene (400-500 • C). The degradation peak (240-400 • C) in the first stage of the coated composites mainly corresponded to the breaking of the C-S bond in the cross-linking network, the volatilization of volatiles containing C and S (SO 2 , SO 3, and CO 2 ), the decomposition of the phosphate group in the PM-2 structure, the scission of long chain branches in the solidified layer, and the preliminary formation of the carbon layer. The degradation of the cellulose and hemicellulose of the matrix composites was also included in this degradation peak. The degradation peak in the second stage was mainly the rupture of the cross-linked network and the main chain of the polypropylene product in the matrix material. Then, the entire matrix of the composites was almost completely degraded, leaving only part of the carbon residue [25,26]. In air atmosphere, the first degradation peak is at 200-300 • C and the second degradation peak ranges from 300-450 • C. Both decomposition stages are advanced, which indicates that the presence of oxygen accelerates the degradation process of the composite. The third degradation peak (at 500-600 • C) occurs for the thermal degradation in an air atmosphere, which is mainly attributed to the degradation of unstable carbon layers at high temperatures. It can be seen from Table 4 that, compared with S 1 (N 3 P 2 ) 9 , S 4 (N 3 P 2 ) 6 and S 5 N 3 P 2 exhibited a good synergistic flame-retardant effect due to the appropriate relative proportions of N, P, and S, and T max2 was also higher than other coating composites. The gas-phase and the solid-phase flame-retardant mechanism worked together and delayed the degradation process to a certain extent. In the S 5 N x P y series, sample S 5 N 0 P 5 had the highest Y c at 700 • C. However, in the samples of the S x (N 3 P 2 ) y series, even if the PM-2 content increased, Y c did not change significantly. This was mainly due to the decrease in the content of PETMP, which was the carbon chain provider. In addition, it can be observed from the DTG curves that due to the presence of the coating, the peak degradation rate of all coated composites was much lower than that of the uncoated fiber composite materials, which shows that the coating effectively reduced the degradation rate. rate of all coated composites was much lower than that of the uncoated fiber composite materials, which shows that the coating effectively reduced the degradation rate.   rate of all coated composites was much lower than that of the uncoated fiber composite materials, which shows that the coating effectively reduced the degradation rate.

Char Residues Surface Morphologies Analysis and Elements Analysis
After the horizontal combustion test, all samples were imaged by SEM to evaluate the surface morphology and chemical composition of the residual carbon ( Figure 7). According to the previous literature [27], the dense carbon layer could isolate thermal oxygen and other volatile combustible gases well, thereby improving the flame retardancy [28]. The coating with a high content of PM-2 had a complete carbon layer structure. When the content of the PETMP groups was reduced (Figure 7f), the sufficient carbon layer could not form completely on the surface of the composites. There were cracks and through holes on the carbon layer. Meanwhile, the gas-phase flame-retardant did not have a sufficient effect to achieve a relative balance with the solid-phase flame-retardant mechanism, so the flame-retardant effect gradually decreased. In contrast, in the S 5 N 3 P 2 and S 4 (N 3 P 2 ) 6 coatings (Figure 7c,e), pores and closed bubbles appear in the carbon layer, which are caused by the release of incombustible gas during the combustion process. The carbon layer showed a honeycomb structure, which formed a temperature gradient on the carbon residue layer, inhibiting heat transfer, preventing oxygen diffusion, and providing better heat insulation performance for the base material [24,27,29,30].

Char Residues Surface Morphologies Analysis and Elements Analysis
After the horizontal combustion test, all samples were imaged by SEM to evaluate the surface morphology and chemical composition of the residual carbon ( Figure 7). According to the previous literature [27], the dense carbon layer could isolate thermal oxygen and other volatile combustible gases well, thereby improving the flame retardancy [28]. The coating with a high content of PM-2 had a complete carbon layer structure. When the content of the PETMP groups was reduced (Figure 7f), the sufficient carbon layer could not form completely on the surface of the composites. There were cracks and through holes on the carbon layer. Meanwhile, the gas-phase flame-retardant did not have a sufficient effect to achieve a relative balance with the solid-phase flame-retardant mechanism, so the flame-retardant effect gradually decreased. In contrast, in the S5N3P2 and S4(N3P2)6 coatings (Figure 7 (c)(e)), pores and closed bubbles appear in the carbon layer, which are caused by the release of incombustible gas during the combustion process. The carbon layer showed a honeycomb structure, which formed a temperature gradient on the carbon residue layer, inhibiting heat transfer, preventing oxygen diffusion, and providing better heat insulation performance for the base material [24,27,29,30].  The micro-morphologies of the char layer structure of the uncoated composite FC (a) and the coated composites samples of S 5 N 5 P 0 (b), S 5 N 3 P 2 (c), S 5 N 0 P 5 (d), S 4 (N 3 P 2 ) 6 (e), and S 1 (N 3 P 2 ) 9 (f), after horizontal burning rate (HBR) tests.
According to EDS analysis (Figure 8), the N element in samples completely disappeared, which indicated that the N element completely generated non-flammable gas during the combustion process ( Table 5). The carbon residue on the surface of the S 4 (N 3 P 2 ) 6 carbon layer contained 69.53 wt% of C, 6.55 wt% of P, and 1.42 wt% of S. Compared with the element content before the combustion (Table 6), the content of S element was reduced, which showed the element S participated in the flame-retardant reaction through the gas phase flame-retardant mechanism. The phosphate group in the coatings generated polyphosphoric acid and its derivatives to promote the formation of the carbon layer during combustion. The P element in the coating was almost completely deposited in the carbon layer. In summary, the coating formed a carbonaceous layer rich in phosphorus on the surface of the composites in the combustion process, which delayed the pyrolysis reaction during the combustion process and had a good flame-retardant effect. According to EDS analysis (Figure 8), the N element in samples completely disappeared, which indicated that the N element completely generated non-flammable gas during the combustion process ( Table 5). The carbon residue on the surface of the S4(N3P2)6 carbon layer contained 69.53 wt% of C, 6.55 wt% of P, and 1.42 wt% of S. Compared with the element content before the combustion (Table 6), the content of S element was reduced, which showed the element S participated in the flame-retardant reaction through the gas phase flame-retardant mechanism. The phosphate group in the coatings generated polyphosphoric acid and its derivatives to promote the formation of the carbon layer during combustion. The P element in the coating was almost completely deposited in the carbon layer. In summary, the coating formed a carbonaceous layer rich in phosphorus on the surface of the composites in the combustion process, which delayed the pyrolysis reaction during the combustion process and had a good flame-retardant effect.    Table 5. The element percentage content of the char layer surface of S 5 N 0 P 5 , S 5 N 3 P 2 , S 5 N 5 P 0 , S 4 (N 3 P 2 ) 6, and S 1 (N 3 P 2 ) 9, according to EDS tests.  9 68.79 20.71 0 10.5 0 Table 6. The mass fractions of N, P, and S contained in films of S 5 N 0 P 5 , S 5 N 3 P 2 , S 5 N 5 P 0 , S 4 (N 3 P 2 ) 6, and S 1 (N 3 P 2 ) 9 .  Table 7 shows the tensile strength, flexural strength, and adhesion of the coated composites. When the molar ratio of -SH and C=C was 1:1, the change of TAC and PM-2 content had relatively little effect on adhesion. The coating did not fall off at all after the tests, and the adhesion grade was 0. This was mainly due to the fact that the thiol and the double bond underwent a click reaction via a free-radical step-by-step copolymerization [5,7,31,32]. The cross-linked network structure formed in this way had low shrinkage and high monomer conversion. In addition, PM-2 formed the anchor effect with PP on the surface of the composites through the penetration of its phosphate ester, so the coatings had better adhesion. Because of the formation of flexible thioether bonds, the lack of rigid structure led to the poor mechanical properties of the coating [33], so the tensile strength of the S 5 N x P y samples did not obviously increase. However, due to the better toughness of the coating produced by this method, the bending strength fluctuated about 42.6 Mpa, which was an increase of 24.3% compared with the uncoated composites.  6 26.11 ± 1.83 42.02 ± 2.74 3 1 S 3 (N 3 P 2 ) 7 28.34 ± 2.52 48.11 ± 1.64 5 1 S 2 (N 3 P 2 ) 8 28.95 ± 0.53 50.29 ± 2.29 14 2 S 1 (N 3 P 2 ) 9 30.67 ± 2.63 52.31 ± 1.98 48 4

Adhesion and Mechanical Testing
By fixing the relative content of TAC and PM-2 and changing the ratio of thiol to a double bond, the following dynamic emerged: the lower the thiol content, the worse the adhesion of the coating. The peeling rate of sample S 1 (N 3 P 2 ) 9 after the adhesion test even reached 48%. As the content of double bonds increases, the cross-linking of the coating tends to homopolymerize between the double bonds. The internal stress was not released due to the rapid curing of the coating, and the formed coating had a large volume shrinkage rate and high surface tension [7,34], thereby reducing the adhesion between the coating and the substrate. Additionally, the influence of the coating on the mechanical properties was related to the crosslinking method of the coating. The cross-linking density of the coating formed by the double-bond homopolymerization reaction became larger, which increased the hardness of the coating. Therefore, the tensile strength and flexural strength increased with the increase of the double bond content. Figure 9 is the optical transparency spectrum of the UV-cured coatings. The thickness of the coatings was 200 µm. It was obvious from the digital photos of Figure 9b that the crosslinked coating had good transparency. The UV-vis spectrum showed that the transparency of these coatings at visible light wavelengths (400-800 nm) was about 90%, which was consistent with the performance of digital photos. The transmittance of the coating was close to 0 under 300 nm UV light, which indicated that the coating had a good blocking effect on short-wave UV light [20]. The relative content changes of PETMP, PM-2, and TAC in the film had little effect on the optical transparency of the UV curable film [5]. This kind of film with high transparency showed obvious application potential.  Figure 9 is the optical transparency spectrum of the UV-cured coatings. The thickness of the coatings was 200 μm. It was obvious from the digital photos of Figure 9b that the crosslinked coating had good transparency. The UV-vis spectrum showed that the transparency of these coatings at visible light wavelengths (400-800 nm) was about 90%, which was consistent with the performance of digital photos. The transmittance of the coating was close to 0 under 300 nm UV light, which indicated that the coating had a good blocking effect on short-wave UV light [20]. The relative content changes of PETMP, PM-2, and TAC in the film had little effect on the optical transparency of the UV curable film [5]. This kind of film with high transparency showed obvious application potential.

Conclusions
The UV-cured, flame-retardant coatings containing N/P/S were successfully prepared on the surface of the composites via a thiol-ene click reaction. The effect of the element ratio on the flame-retardant properties of the coating was investigated. Among the PETMP/TAC/PM-2 crosslinked networks, sample S4(N3P2)6 showed the best flame retardancy, which was determined by LOI, HBR, and CCT. The LOI value of sample S4(N3P2)6 reached 28.6%, and its self-extinguishing time was 85 s in the horizontal combustion test. Meanwhile, it had the lowest THR value, the lowest PHRR value, and the lowest TSP value. All these results confirmed the synergistic effectiveness of flame retardants between PETMP, TAC, and the PM-2. The thermal degradation results of the UV-cured coatings revealed that the P-containing prepolymers could promote the carbon chain into a compact and stable char layer in a timely fashion, which demonstrated that P and C exert a synergistic flame retardancy in the condensed phase. Moreover, the coatings consumed oxygen and generated CO2 and SO2, and N2 and NH3, which could dilute combustible gas produced during combustion around the fiber composites. This indicated that N and S exert flame retardancy in the gas phase, leading to the formation of the honeycomb porous carbon layer. This carbon layer was monitored in the SEM test. In addition, the UV-curable coating S4(N3P2)6 also had a high double bond conversion rate and thiol conversion rate (100% and 92%, respectively) and had good mechanical properties. The flexural strength of the composites was increased to 42.02MPa. The coating had good adhesion, and the shedding rate was within 5%. The transparency of this coating was about 90%, and it had good optical properties. The aforementioned results indicated that the PETMP/TAC/PM-2 cross-linked network had potential in the flame-retardant coating field. Therefore, this research provided new ideas for the development of flame-retardant coatings that meet the needs of practical applications.

Conclusions
The UV-cured, flame-retardant coatings containing N/P/S were successfully prepared on the surface of the composites via a thiol-ene click reaction. The effect of the element ratio on the flame-retardant properties of the coating was investigated. Among the PETMP/TAC/PM-2 crosslinked networks, sample S 4 (N 3 P 2 ) 6 showed the best flame retardancy, which was determined by LOI, HBR, and CCT. The LOI value of sample S 4 (N 3 P 2 ) 6 reached 28.6%, and its self-extinguishing time was 85 s in the horizontal combustion test. Meanwhile, it had the lowest THR value, the lowest PHRR value, and the lowest TSP value. All these results confirmed the synergistic effectiveness of flame retardants between PETMP, TAC, and the PM-2. The thermal degradation results of the UV-cured coatings revealed that the P-containing prepolymers could promote the carbon chain into a compact and stable char layer in a timely fashion, which demonstrated that P and C exert a synergistic flame retardancy in the condensed phase. Moreover, the coatings consumed oxygen and generated CO 2 and SO 2 , and N 2 and NH 3 , which could dilute combustible gas produced during combustion around the fiber composites. This indicated that N and S exert flame retardancy in the gas phase, leading to the formation of the honeycomb porous carbon layer. This carbon layer was monitored in the SEM test. In addition, the UV-curable coating S 4 (N 3 P 2 ) 6 also had a high double bond conversion rate and thiol conversion rate (100% and 92%, respectively) and had good mechanical properties. The flexural strength of the composites was increased to 42.02MPa. The coating had good adhesion, and the shedding rate was within 5%. The transparency of this coating was about 90%, and it had good optical properties. The aforementioned results indicated that the PETMP/TAC/PM-2 cross-linked network had potential in the flame-retardant coating field. Therefore, this research provided new ideas for the development of flame-retardant coatings that meet the needs of practical applications.

Data Availability Statement:
The data presented in this study are available upon request from the corresponding author.