A Novel Inherently Flame-Retardant Composite Based on Zinc Alginate/Nano-Cu2O

A novel flame-retardant composite material based on zinc alginate (ZnAlg) and nano-cuprous oxide (Cu2O) was prepared through a simple, eco-friendly freeze-drying process and a sol-gel method. The composites were characterized and their combustion and flammability behavior were tested. The composites had high thermal stability and achieved nearly non-flammability with a limiting oxygen index (LOI) of 58. The results show remarkable improvement of flame-retardant properties in the ZnAlg/Cu2O composites, compared to ZnAlg. Furthermore, the pyrolysis behavior was determined by pyrolysis–gas chromatography–mass spectrometry (Py-GC-MS) and the flame-retardant mechanism was proposed based on the combined experimental results. The prepared composites show promising application prospects in building materials and the textile industry.


Introduction
Sodium alginate (NaAlg) is a hydrophilic and biodegradable linear polysaccharide copolymer consisting of two different ratios of spatially different 1,4-linked α-L guluronic acid and β-D mannuronic acid repeating unit composition [1][2][3]. The unique properties of sodium alginate are biological origin, non-toxic, hydrophilic, biocompatible, biodegradable and low-cost, making it highly applicable in various fields [4,5]. The most important characteristic of NaAlg is that it can react with polyvalent metal cations to form strong gels or insoluble polymers [6][7][8], thereby improving water resistance, mechanical properties, barrier properties, cohesiveness and rigidity during cross-linking with multivalent cations [9]. Zinc alginate is a material with excellent biological activity and is widely used in flame-retardant and antibacterial applications [10,11].
Nanomaterials have a wide range of applications in flame retardancy [12]. Norouzi et al. investigated the effect of the addition of different nanomaterials on the flame retardancy of textiles and found that most nanoparticles can improve the thermal stability and flame-resistant textile polymers [13]. Nanoparticles of different kinds of materials, such as silver, titanium dioxide and zinc oxide, have been reported to be functionalized for fibers and fabrics to achieve significantly improved products with new macroscopic properties [14]. Nano-Cu 2 O is a new type of p-type oxide semiconductor material that can be excited by visible light. It has an active electron-hole pair system and exhibits good catalytic activities [15][16][17]. In addition, it shows excellent adsorption properties and low-temperature paramagnetism, and has potential applications in organic synthesis, photoelectric conversion, new energy, photolysis of water, dye bleaching, sterilization, superconductivity and other In this study, ZnAlg/Cu2O composite materials were prepared by a simple, economical and environmentally friendly sol-gel method. The composites were characterized by scanning electron microscopy (SEM), X-ray diffractometry (XRD), X-ray photoelectron spectroscopy (XPS), Fourier transform infrared spectrum (FTIR), and thermogravimetric analysis (TG). The combustion and flammability behaviors of the composites were assessed by the limiting oxygen index (LOI), vertical burning rate (UL-94) and cone calorimetry (CONE). Additionally, the pyrolysis products of the composites, SEM of the char residue, were investigated to reveal the flame-retardant mechanism of the prepared materials.

Materials
NaAlg was supplied by the Institute of Photosynthetic Fine Chemicals (Tianjin, China). Cupric sulfate (CuSO4·5H2O) was purchased from Tianjin Beichen Founder Reagent Factory (Tianjin, China). Zinc acetate dehydrate (C4H6O4Zn·2H2O) and L-Ascorbic acid (VC) were obtained from Sinopharm Chemical Reagent Co., Ltd. (Shanghai, China). Ammonia solution (NH3·H2O) was purchased from Kant Chemical Co., Ltd. (Laiyang, China). All the chemicals were not further purified and all the solutions were prepared using deionized water.

Preparation of ZnAlg
Firstly, 20.00 g of NaAlg was added in 500 mL deionized water and stirred to form a uniform sol. After standing for 24 h, the NaAlg sol was shaped in a square mold. Then, 3 wt % C4H6O4Zn·2H2O solution was added and crosslinked with NaAlg for 48 h. The final product was washed several times with deionized water and dried in a freeze dryer (FD-1A-50, Billing Instrument Manufacturing Co., Ltd, Shanghai, China).

Preparation of ZnAlg/Cu2O Composites
The ZnAlg/Cu2O composites were prepared as illustrated in Scheme 1. Briefly, CuSO4·5H2O (2.34 g) was dissolved in 450 mL deionized water and stirred to uniform dispersion in deionized water. Then, 7.5 mL of NH3·H2O was added and stirred to form a copper complex solution. Subsequently, 20.00 g of NaAlg was slowly added and stirred to form a uniform mixed gel solution. After standing for 24 h, 50 mL 13.67 wt % VC solution was slowly added to the mixed gel solution and stirred until it turned yellow to produce the NaAlg/Cu2O mixed gel solution. The as-prepared gel solution was poured and shaped in a square mold, followed by the addition of 3 wt % C4H6O4Zn·2H2O (500 mL) solution. Crosslinked reaction was proceeded for 24 h to obtain the ZnAlg/Cu2O composites. The final product was washed several times with deionized water and dried in a freeze dryer for further use.

Measurements
The morphology and microstructure of the samples were examined by SEM (SIGMA, Zeiss, Oberkochen, Germany). All samples on the surface of the study were sprayed with gold.

Measurements
The morphology and microstructure of the samples were examined by SEM (SIGMA, Zeiss, Oberkochen, Germany). All samples on the surface of the study were sprayed with gold.
The XRD of the prepared sample was carried out on a D8 Advance diffractometer (Bruker, Karlsruhe, Germany). The sample was scanned in 2θ to 90 • in continuous mode.
The XPS was recorded on an ESCALAB 250Xi (Thermo Fisher Scientific, Waltham, MA, USA). The orbit of Cu element is 2p orbital.
The chemical bonds in the samples were determined by FTIR spectroscopy (NICOLET iS50, Thermo Fisher Scientific, Madison, WI, USA). The wavenumbers ranged from 4000 to 500 cm −1 .
The TG was carried out on an SDT Q600 thermogravimetric analyzer (TA Instrument, New Castle, DE, USA), and the samples were raised from 25 to 900 • C at a heating rate of 10 • C /min in ambient environment as well as nitrogen atmosphere.
The combustion properties of the samples were measured using an FTT-0242 cone calorimeter device (Fire Testing Technology, East Grinstead, UK) under an external heat flux of 35 kW/m 2 according to standard ISO 5660. The dimensions of all samples were 100 mm × 100 mm × 3 mm.
Py-GC-MS was performed by a thermal cracker (EGA/PY-3030D, Frontier, Koriyama, Japan) and gas chromatography-mass spectrometer (TRACE 1310-ISQLT, Thermo Fisher Scientific, Waltham, MA, USA). The pyrolysis temperature was 250, 450, and 750 • C, and the carrier gas was He. The GC temperature program was started at 50 • C, and stayed in the pose for 3 min, and then rose to 300 • C at the speed of 20 • C/min.

Characterizations
The morphology of the prepared samples was investigated by SEM and the images are shown in Figure 1. It can be observed from Figure 1a that the surface of ZnAlg showed a network structure and was relatively rough. As can be seen from Figure 1b, spherical nano-Cu 2 O was embedded in ZnAlg, ranging from 100-400 nm in size, indicating a successful preparation of the ZnAlg/Cu 2 O composites. Moreover, the addition of nano-Cu 2 O made the surface of ZnAlg smoother. The XRD of the prepared sample was carried out on a D8 Advance diffractometer (Bruker, Karlsruhe, Germany). The sample was scanned in 2θ to 90° in continuous mode.
The XPS was recorded on an ESCALAB 250Xi (Thermo Fisher Scientific, Waltham, MA, USA). The orbit of Cu element is 2p orbital.
The chemical bonds in the samples were determined by FTIR spectroscopy (NICOLET iS50, Thermo Fisher Scientific, Madison, WI, USA). The wavenumbers ranged from 4000 to 500 cm −1 .
The TG was carried out on an SDT Q600 thermogravimetric analyzer (TA Instrument, New Castle, DE, USA), and the samples were raised from 25 to 900 °C at a heating rate of 10 °C /min in ambient environment as well as nitrogen atmosphere.
The combustion properties of the samples were measured using an FTT-0242 cone calorimeter device (Fire Testing Technology, East Grinstead, UK) under an external heat flux of 35 kW/m 2 according to standard ISO 5660. The dimensions of all samples were 100 mm × 100 mm × 3 mm.
Py-GC-MS was performed by a thermal cracker (EGA/PY-3030D, Frontier, Koriyama, Japan) and gas chromatography-mass spectrometer (TRACE 1310-ISQLT, Thermo Fisher Scientific, Waltham, MA, USA). The pyrolysis temperature was 250, 450, and 750 °C, and the carrier gas was He. The GC temperature program was started at 50 °C, and stayed in the pose for 3 min, and then rose to 300 °C at the speed of 20 °C/min.

Characterizations
The morphology of the prepared samples was investigated by SEM and the images are shown in Figure 1. It can be observed from Figure 1a that the surface of ZnAlg showed a network structure and was relatively rough. As can be seen from Figures 1b, spherical nano-Cu2O was embedded in ZnAlg, ranging from 100-400 nm in size, indicating a successful preparation of the ZnAlg/Cu2O composites. Moreover, the addition of nano-Cu2O made the surface of ZnAlg smoother. The diffraction peaks at 36.46°, 42.34° and 61.43° of the ZnAlg/Cu2O samples can be seen in Figure 2a, which can be assigned to Cu2O, indicating a successful introduction of Cu2O for the sample preparation [24]. Moreover, no other obvious peaks can be observed in the images, suggesting high purity of Cu2O in the material. Figure 2b displays the XPS spectrum of the ZnAlg/Cu2O composites. As seen, the two peaks at 932.7 and 953.2 eV can be corresponded to the Cu 2p3/2 and Cu 2p1/2 binding energies of Cu2O. The preparation [24]. Moreover, no other obvious peaks can be observed in the images, suggesting high purity of Cu 2 O in the material. results reflect the high purity of Cu2O in ZnAlg/Cu2O, which is in good agreement with that of previous reports [25][26][27][28]. Moreover, as shown in Figure S1 (in Supplementary Materials), the content of Cu was 0.75 at. %, while that of Zn was 2.17 at. %.
. The FTIR spectra of the samples are shown in Figure 3. A series of characteristic absorption peaks were observed, of which 3240 cm −1 (O-H stretching vibration), 2923 cm −1 (-CH2), 1584 cm −1 (C=O stretching vibration) [29], 1429 cm −1 (symmetric and asymmetric vibrations of -COO), 1029 and 914 cm −1 (symmetric and asymmetric vibrations of C-O-C), respectively. No significant differences between the infrared peaks of ZnAlg/Cu2O and ZnAlg can be noticed, indicating that the addition of Cu2O did not break the structure of ZnAlg [30,31].

Thermal Stability
The thermal stability of the materials was tested in the air as well as the nitrogen atmosphere, and the results show both materials had similar degradation trends. It can be observed from Figure  4a and 4b that, under air, from the start of heating to 200 °C, there was about 18% weight loss, which was caused by evaporation of free water and crystal water in the materials, suggesting high natural moisture regain of the materials [31]. From 200 to 450 °C, the masses of ZnAlg/Cu2O and ZnAlg were dropped sharply, which was mainly due to the cleavage of glycosidic bonds in the alginate, as well as decarboxylation and decarbonylation [32]. Over 450 °C, the mass of ZnAlg remained nearly unchanged, and the phase change mainly occurred during this period [8], while the mass of  The results reflect the high purity of Cu 2 O in ZnAlg/Cu 2 O, which is in good agreement with that of previous reports [25][26][27][28]. Moreover, as shown in Figure S1 (in Supplementary Materials), the content of Cu was 0.75 at. %, while that of Zn was 2.17 at. %.
The FTIR spectra of the samples are shown in Figure 3. A series of characteristic absorption peaks were observed, of which 3240 cm −1 (O-H stretching vibration), 2923 cm −1 (-CH 2 ), 1584 cm −1 (C=O stretching vibration) [29], 1429 cm −1 (symmetric and asymmetric vibrations of -COO), 1029 and 914 cm −1 (symmetric and asymmetric vibrations of C-O-C), respectively. No significant differences between the infrared peaks of ZnAlg/Cu 2 O and ZnAlg can be noticed, indicating that the addition of Cu 2 O did not break the structure of ZnAlg [30,31]. results reflect the high purity of Cu2O in ZnAlg/Cu2O, which is in good agreement with that of previous reports [25][26][27][28]. Moreover, as shown in Figure S1 (in Supplementary Materials), the content of Cu was 0.75 at. %, while that of Zn was 2.17 at. %.
. The FTIR spectra of the samples are shown in Figure 3. A series of characteristic absorption peaks were observed, of which 3240 cm −1 (O-H stretching vibration), 2923 cm −1 (-CH2), 1584 cm −1 (C=O stretching vibration) [29], 1429 cm −1 (symmetric and asymmetric vibrations of -COO), 1029 and 914 cm −1 (symmetric and asymmetric vibrations of C-O-C), respectively. No significant differences between the infrared peaks of ZnAlg/Cu2O and ZnAlg can be noticed, indicating that the addition of Cu2O did not break the structure of ZnAlg [30,31].

Thermal Stability
The thermal stability of the materials was tested in the air as well as the nitrogen atmosphere, and the results show both materials had similar degradation trends. It can be observed from Figure  4a and 4b that, under air, from the start of heating to 200 °C, there was about 18% weight loss, which was caused by evaporation of free water and crystal water in the materials, suggesting high natural moisture regain of the materials [31]. From 200 to 450 °C, the masses of ZnAlg/Cu2O and ZnAlg were dropped sharply, which was mainly due to the cleavage of glycosidic bonds in the alginate, as well as decarboxylation and decarbonylation [32]. Over 450 °C, the mass of ZnAlg remained nearly unchanged, and the phase change mainly occurred during this period [8], while the mass of

Thermal Stability
The thermal stability of the materials was tested in the air as well as the nitrogen atmosphere, and the results show both materials had similar degradation trends. It can be observed from Figure 4a,b that, under air, from the start of heating to 200 • C, there was about 18% weight loss, which was caused by evaporation of free water and crystal water in the materials, suggesting high natural moisture regain of the materials [31]. From 200 to 450 • C, the masses of ZnAlg/Cu 2 O and ZnAlg were dropped sharply, which was mainly due to the cleavage of glycosidic bonds in the alginate, as well as decarboxylation and decarbonylation [32]. Over 450 • C, the mass of ZnAlg remained nearly unchanged, and the phase change mainly occurred during this period [8], while the mass of ZnAlg/Cu 2 O increased, which was caused by the oxidation of Cu 2 O to CuO (2Cu 2 O + O 2 = 4CuO) [33,34]. The results show that ZnAlg/Cu 2 O produced more residues than ZnAlg, which was about 6% higher, indicating better thermal stability of ZnAlg/Cu 2 O [35,36].
In nitrogen atmosphere, displayed in Figure 4c and 4d, from the beginning to 200 °C, the ZnAlg curve ran above the ZnAlg/Cu2O curve, indicating that the natural moisture regain of ZnAlg/Cu2O was higher, and the addition of Cu2O accelerated the dehydration of ZnAlg. At 200-300 °C, ZnAlg and ZnAlg/Cu2O almost lost weight simultaneously, suggesting that Cu2O did not play its part within this period. After 450 °C, the mass of ZnAlg/Cu2O continued to decrease in the nitrogen environment, while the mass of ZnAlg/Cu2O increased under air, which further confirmed the oxidation of Cu2O. The weight loss rate of ZnAlg/Cu2O was significantly lower than that of ZnAlg, suggesting that O2 can be absorbed during the oxidation of Cu2O to CuO, thereby suppressing combustion [35]. It can be inferred that CuO can act as dust on ZnAlg, to absorb heat and dissipate in the combustion area, thus inhibited the degradation of ZnAlg [31].

Flame Retartancy
The flame-retardant properties of the two prepared samples were investigated by LOI and UL-94 tests and the test data are listed in Table 1. As seen, both ZnAlg/Cu2O and ZnAlg had a high LOI. Moreover, the LOI of ZnAlg was increased from 49 to 58, indicating that the introduction of Cu2O can efficiently improve the flame retardancy of the basic material. ZnAlg/Cu2O was extinguished within 10 s after being ignited in the vertical burning test, and it passed the test without any dripping, which is favorable for its further real application. In nitrogen atmosphere, displayed in Figure 4c,d, from the beginning to 200 • C, the ZnAlg curve ran above the ZnAlg/Cu 2 O curve, indicating that the natural moisture regain of ZnAlg/Cu 2 O was higher, and the addition of Cu 2 O accelerated the dehydration of ZnAlg. At 200-300 • C, ZnAlg and ZnAlg/Cu 2 O almost lost weight simultaneously, suggesting that Cu 2 O did not play its part within this period. After 450 • C, the mass of ZnAlg/Cu 2 O continued to decrease in the nitrogen environment, while the mass of ZnAlg/Cu 2 O increased under air, which further confirmed the oxidation of Cu 2 O. The weight loss rate of ZnAlg/Cu 2 O was significantly lower than that of ZnAlg, suggesting that O 2 can be absorbed during the oxidation of Cu 2 O to CuO, thereby suppressing combustion [35]. It can be inferred that CuO can act as dust on ZnAlg, to absorb heat and dissipate in the combustion area, thus inhibited the degradation of ZnAlg [31].

Flame Retartancy
The flame-retardant properties of the two prepared samples were investigated by LOI and UL-94 tests and the test data are listed in Table 1. As seen, both ZnAlg/Cu 2 O and ZnAlg had a high LOI. Moreover, the LOI of ZnAlg was increased from 49 to 58, indicating that the introduction of Cu 2 O can efficiently improve the flame retardancy of the basic material. ZnAlg/Cu 2 O was extinguished within

Combustion Behavior
CONE has been widely employed to evaluate the combustion behavior of the polymers [37,38]. The most important flame-retardant parameters that CONE can give out are ignition time, heat release rate (HRR) and total heat release (THR), as these parameters may be related to flame growth and toxic gas emissions during combustion [1,39]. The detailed data are collected in Table 1 and the related curves are displayed in Figure 5. The ignition time of ZnAlg was 22 s, while that of ZnAlg/Cu 2 O was 37 s, indicating that the polymers were more difficult to be burnt. HRR is an important parameter for evaluating fire safety [40,41]. As shown in Figure 5a, the HRR value of ZnAlg/Cu 2 O was much lower than that of ZnAlg in the most part of the combustion processes. Moreover, the peak heat release rate (PHRR) of ZnAlg/Cu 2 O was only 83.18 kW/m 2 , compared to that of ZnAlg which was 162.31 kW/m 2 . As seen in Table 1, ZnAlg was burnt completely at 387 s, while ZnAlg/Cu 2 O continued and completed at 610 s, indicating that ZnAlg was more easily flammable than ZnAlg/Cu 2 O, and that the catalytic and carbon formation function of Cu 2 O reduced the combustion properties of the material. It can be observed from Figure 5b,c that the THR and TSR values of the two samples were increased with time. ZnAlg/Cu 2 O showed lower THR and TSR values, suggesting lower heat release and less smoke release than ZnAlg. This may be attributed to the fact that O 2 can be absorbed during the oxidation process of Cu 2 O to CuO at high temperatures. The generated CuO can act as a dust layer on the ZnAlg, absorbing heat in the combustion zone and blocking the release of smoke. In addition, the residual amount of ZnAlg/Cu 2 O was higher than that of ZnAlg. Combining these results, the ZnAlg/Cu 2 O composites showed remarkably better flame retardancy than ZnAlg.

Combustion Behavior
CONE has been widely employed to evaluate the combustion behavior of the polymers [37,38]. The most important flame-retardant parameters that CONE can give out are ignition time, heat release rate (HRR) and total heat release (THR), as these parameters may be related to flame growth and toxic gas emissions during combustion [1,39]. The detailed data are collected in Table 1 and the related curves are displayed in Figure 5. The ignition time of ZnAlg was 22 s, while that of ZnAlg/Cu2O was 37 s, indicating that the polymers were more difficult to be burnt. HRR is an important parameter for evaluating fire safety [40,41]. As shown in Figure 5a, the HRR value of ZnAlg/Cu2O was much lower than that of ZnAlg in the most part of the combustion processes. Moreover, the peak heat release rate (PHRR) of ZnAlg/Cu2O was only 83.18 kW/m 2 , compared to that of ZnAlg which was 162.31 kW/m 2 . As seen in Table 1, ZnAlg was burnt completely at 387 s, while ZnAlg/Cu2O continued and completed at 610 s, indicating that ZnAlg was more easily flammable than ZnAlg/Cu2O, and that the catalytic and carbon formation function of Cu2O reduced the combustion properties of the material. It can be observed from Figures 5b and 5c that the THR and TSR values of the two samples were increased with time. ZnAlg/Cu2O showed lower THR and TSR values, suggesting lower heat release and less smoke release than ZnAlg. This may be attributed to the fact that O2 can be absorbed during the oxidation process of Cu2O to CuO at high temperatures. The generated CuO can act as a dust layer on the ZnAlg, absorbing heat in the combustion zone and blocking the release of smoke. In addition, the residual amount of ZnAlg/Cu2O was higher than that of ZnAlg. Combining these results, the ZnAlg/Cu2O composites showed remarkably better flame retardancy than ZnAlg.

Flame-Retardant Mechanism
Py-GC-MS is mainly used to analyze the main components of gaseous products produced during the pyrolysis of materials [42]. The chromatograms of ZnAlg/Cu2O obtained by Py-GC-MS at 250, 450 and 750 °C are shown in Figure 6, respectively, and the major pyrolysis products determined by comparison with the NIST library are listed in Table 2. The main compounds

Flame-Retardant Mechanism
Py-GC-MS is mainly used to analyze the main components of gaseous products produced during the pyrolysis of materials [42]. The chromatograms of ZnAlg/Cu 2 O obtained by Py-GC-MS at 250, 450 and 750 • C are shown in Figure 6, respectively, and the major pyrolysis products determined by comparison with the NIST library are listed in Table 2. The main compounds produced at 450 • C were CO 2 , CO, furfural, acetic acid, propanoicacid, 2-oxo-, n-hexadecanoic acid and 9-hexadecenoic acid. As can be seen, the main products can be divided into four groups, including CO, CO 2 , organic acids and aldehydes, respectively [43]. As the temperature increased, more aromatic hydrocarbons, alcohols and ketones were produced. Figure S2 (in Supplementary Materials) displays the chromatograms of ZnAlg obtained by Py-GC-MS at 750 • C, and the main pyrolysis products identified based on the comparison with the NIST library are listed in Table S1 (in Supplementary Materials). Compared with ZnAlg, ZnAlg/Cu 2 O produced less compounds, indicating that the addition of Cu 2 O increased the char yield of ZnAlg. The formed carbon layer covered the surface of the matrix material, hindering the heat transfer and exchange of combustible gases between the matrix material and the outside. It had well protective function to the matrix material, thereby can improve its thermal stability [30,31].

Flame-Retardant Mechanism
Py-GC-MS is mainly used to analyze the main components of gaseous products produced during the pyrolysis of materials [42]. The chromatograms of ZnAlg/Cu2O obtained by Py-GC-MS at 250, 450 and 750 °C are shown in Figure 6, respectively, and the major pyrolysis products determined by comparison with the NIST library are listed in Table 2. The main compounds produced at 450 °C were CO2, CO, furfural, acetic acid, propanoicacid, 2-oxo-, n-hexadecanoic acid and 9-hexadecenoic acid. As can be seen, the main products can be divided into four groups, including CO, CO2, organic acids and aldehydes, respectively [43]. As the temperature increased, more aromatic hydrocarbons, alcohols and ketones were produced. Figure S2 Table S1 (in Supplementary Materials). Compared with ZnAlg, ZnAlg/Cu2O produced less compounds, indicating that the addition of Cu2O increased the char yield of ZnAlg. The formed carbon layer covered the surface of the matrix material, hindering the heat transfer and exchange of combustible gases between the matrix material and the outside. It had well protective function to the matrix material, thereby can improve its thermal stability [30,31].                            According to the test results of Py-GC-MS, the proposed thermal degradation mechanisms of ZnAlg/Cu 2 O are depicted in Scheme 2. Below 200 • C, the decomposition products of the composites contained a large amount of H 2 O, indicating massive loss of free and bound water. From 200 to 450 • C, the glycosidic bond of ZnAlg/Cu 2 O was broken, while esterification and decarboxylation reaction occurred. Furthermore, as the degradation mechanism is complicated, thus an intramolecular esterification process (or between different rings) can more likely occur during the process and contribute to the cross-linking of the organic material to form carbon layers [44,45]. From 450 to 750 • C, dehydroxylation, decarboxylation, esterification, decarbonylation, rupture and rearrangement were believed to contribute to the improvement of char formation, releasing CO 2 , CO, organic acids and aldehydes, such as furfural, acetic acid, propanoicacid, 2-oxo-, n-hexadecanoic acid, 9-hexadecenoic acid and etc. The above chemical reactions may be catalyzed by CuO. At 750 • C, the residue may be further degraded by condensation reaction. Cu 2 O accelerated the dehydration of ZnAlg at low temperatures, which caused the formation of a carbon barrier. Furthermore, O 2 can be absorbed during the Cu 2 O oxidation to CuO at high temperatures. The generated CuO can act as dust covered on ZnAlg, absorbing heat and dissipating in the combustion zone. According to the theory of wall effect, the flame cannot grow if dust is sufficient in the air [46]. Therefore, it can be inferred from the combined results that the introduction of Cu 2 O to ZnAlg significantly improved its flame retardancy. According to the test results of Py-GC-MS, the proposed thermal degradation mechanisms of ZnAlg/Cu2O are depicted in Scheme 2. Below 200 °C, the decomposition products of the composites contained a large amount of H2O, indicating massive loss of free and bound water. From 200 to 450 °C, the glycosidic bond of ZnAlg/Cu2O was broken, while esterification and decarboxylation reaction occurred. Furthermore, as the degradation mechanism is complicated, thus an intramolecular esterification process (or between different rings) can more likely occur during the process and contribute to the cross-linking of the organic material to form carbon layers [44,45]. From 450 to 750 °C, dehydroxylation, decarboxylation, esterification, decarbonylation, rupture and Scheme 2. Proposed thermal degradation mechanism of ZnAlg/Cu 2 O.

Conclusions
A new intrinsic flame-retardant composite based on ZnAlg/nano-Cu 2 O was first prepared through a simple, economical and environmentally friendly method. The prepared material exhibited excellent flame-retardant properties. It was found that the addition of nano-Cu 2 O can promote the conversion of ZnAlg to carbon-based materials. Moreover, O 2 can be absorbed during the oxidation of Cu 2 O to CuO at high temperatures. The CuO in the polymer can act as dust on the substrate material, covering on its surface when burnt. Thus, it can hinder the heat transfer between the matrix material and the outside and provided good protection on the matrix material. Therefore, the prepared materials can be highly prospective for application in building insulation materials and textile industry.
Author Contributions: Q.L. and Z.L. conceived and designed the experiments; P.X. and P.S. performed the experiments; Q.Z., W.C., Z.L. and Q.L. analyzed the data; P.X. and Z.L. wrote the paper.
Funding: This work was supported by the National Natural Science Foundation of China (grant number 51773102).

Conflicts of Interest:
The authors declare no conflict of interest.