# Enhanced Thermal Insulation and Flame-Retardant Properties of Polyvinyl Alcohol-Based Aerogels Composited with Ammonium Polyphosphate and Chitosan

Authors: MinYi Luo; Jiayou Xu; Shu Lv; XueFeng Yuan; Xiaolan Liang
Journal: International Journal of Polymer Science
 (2021)

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## Abstract

Polyvinyl alcohol- (PVA-) based aerogels have attracted widespread attention owing to their low cost, eco-friendliness, and low density. However, the applications of PVA-based aerogels are limited by their flammability. In this study, a flame retardant, ammonium polyphosphate (APP), and a biopolymer, chitosan (CS), were added to polyvinyl alcohol (PVA), and the polymer was further crosslinked using boric acid (H3BO3). In the PVA aerogels, the negatively charged APP and positively charged CS formed a polyelectrolyte complex (PEC) through ionic interaction. Cone calorimetry and vertical burning tests (UL-94) indicated that the PVA composite aerogels have excellent flame retardancy; they could decrease the heat release rate, total heat release rate, and carbon dioxide (CO2) generation. Both PVA/H3BO3 and APP-CS in the composite aerogel could be burned to carbon, and the foamed char layer could act together to impart the PVA composite aerogels with good flame retardancy. Further, the decrease in the temperature at the backside of the aerogels with increasing APP-CS content, as determined by the flame-spraying experiment, indicated that the PVA-based aerogels with APP-CS can also serve as thermal insulation materials. This work provides an effective and promising method for the preparation of PVA-based aerogels with good flame retardancy and thermal insulation property for construction materials.


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## Body

## 1. Introduction

With rapid economic development, the demand for energy is growing. In particular, energy consumption related to buildings has continuously increased over the past decades [1]. Therefore, energy conservation in buildings is a very important development trend. Currently, wall insulation is most commonly used for this purpose globally. For example, adding a polymer-based aerogel material between walls can effectively preserve house heat and provide insulation. Polymer-based aerogels have attracted significant attention as construction materials owing to their unique advantages, such as low density, high specific surface area, and low thermal conductivity [2–5]. Among the various polymer matrices, water-soluble polyvinyl alcohol (PVA) is a versatile and low-cost polymer [6] that can be used to prepare aerogels. However, its application as a building material is limited by its flammability. The fire hazards associated with the application of such polymer materials can result in loss of life and property [7, 8]. Therefore, it is necessary to develop materials with good flame retardancy and thermal insulation as construction materials for modern buildings, which remains a significant challenge.A common method to improve the fire resistance and thermal stability of polymer materials is to incorporate fire-retardant materials as additives. Intumescent flame retardants (IFRs) are the most widely used additives for forming foamed char on the surface of burning materials. This induces a barrier effect to prevent or mitigate heat transfer from the heat source to the polymer and mass transfer from the external surface of the polymer to the bulk of the polymer. An IFR consists of three components: an acid source, gas source, and carbon source. Ammonium polyphosphate (APP) is typically used as an acid and gas source in IFRs. It is generally composited with other additives to improve the flame retardancy of the polymers [9]. Further, chitosan (CS) is a highly abundant and naturally occurring biopolymer that is composed of amine-containing 2-deoxyglucan. It is thought to be a promising green charring agent because of the presence of multiple hydroxyl and amino groups in its structure [10, 11].Herein, we prepared flame-retardant PVA-based aerogels with different loadings of APP-CS. The negatively charged APP and positively charged CS act as a complementary pair to form a polyelectrolyte complex (PEC) that can serve as a flame retardant. The microstructure, flammability, and thermal insulation properties of the prepared PVA-based aerogels were evaluated. The results demonstrate that the composite aerogels developed in this work have great potential as heat insulation and flame-retardant materials.


## 2. Materials and Methods

### 2.1. Materials

Poly(vinyl alcohol) (PVA) with a polymerization degree of 1000 or more and a saponification degree of >99 mol% (PVA-1799) was supplied by Kelong Chemical Reagent Corporation (Chengdu, China). APP was purchased from Macklin Reagent (Shanghai, China). CS (deacetylation degree, ≥95%) was obtained from Aladdin Chemistry Co., Ltd. (Shanghai, China). Boric acid was procured from Xilong Science Co., Ltd. (Shantou, China). All the chemicals were of laboratory grade and were utilized as received without further purification unless otherwise specified.


### 2.2. Preparation of the PVA Composite Aerogels

The preparation process of the PVA composite aerogels is schematically illustrated in Figure1. 8 wt% PVA aqueous solution was prepared by dissolving 8 g PVA in 92 ml DI water at 95°C under stirring for 3 h. To prepare a PVA/APP-CS solution, 0 g, 5 g, 10 g, and 15 g APP-CS (APP:CS=3:1 mass ratio) were mixed with 100 ml of 8 wt% PVA solution at 14000 rpm (A-555, INAYOU, China). Then, dissolve 0.8 g of boric acid in 10 ml of water and add to the above solution to prepare the hydrogels. After that, the resulting hydrogels were cast into a glass dish and frozen in a refrigerator, followed by freeze-drying in an FD-1A-50 freeze dryer (Yuming Instrument Co., Ltd., Shanghai, China) at −40°C under vacuum. And the as-obtained PVA composite aerogels are denoted as PVA/H3BO3, PVA/5APP-CS/H3BO3, PVA/10APP-CS/H3BO3, and PVA/15APP-CS/H3BO3.Figure 1
Preparation procedure of the PVA composite aerogel.


### 2.3. Characterization

Fourier-transform infrared (FTIR) spectra were recorded with a VERTEX70 spectrometer (Bruker Instrument Co., Ltd., Dresden, Germany) with thin films of KBr at room temperature. The measurement was carried out in the optical range of 4000–500 cm−1.X-ray diffractometry (XRD) was performed on a Neo Confucianism D/Max-2400 diffractometer (Rigaku, Tokyo, Japan), and the2θ scans were conducted in the range of 5° to 80°.The morphology of the samples was observed by scanning electron microscopy (SEM) using JSM-7001F (Japan Electron Optics Laboratory Co., Ltd., Tokyo, Japan).Thermogravimetric analysis (TGA) was performed on a TGA400 thermo-analyzer instrument (PerkinElmer, Inc., Fremont, CA, USA) from room temperature to 700°C at a linear heating rate of 10°C·min−1 under nitrogen atmosphere.The fire behavior of the aerogels was characterized by the UL-94 test (ASTM D-635-77) and the cone calorimeter test (CCT). The UL-94 test was performed on a CZF-2 vertical burning test instrument using aerogel sheets with dimensions of125×10×10mm3. CCT was performed using a Fire Testing Technology cone calorimeter on samples of 100×100×10mm3 dimensions, according to ISO 5660-1, with an external heat flux of 50 kW/m2.The flame-spraying experiment was conducted using a butane flame with a central flame temperature of 1300°C. The flame was perpendicular to the surface of the aerogel samples, which were40×40×6mm3 in size. The distance between the flame tip and the sample was fixed at 60 mm. The temperature on the backside of the aerogel was measured using an infrared thermometer at 1 min intervals. Triplicate measurements were conducted for each sample.The mechanical performance of the composites was examined using Instron universal test machine UT4304 (SANS Instrument Co., Ltd., Shanghai, China) at a crosshead speed of 20 mm/min. The sample size was150×10×4mm for the tensile test. Compression strength was conducted using an electronic universal testing machine (CMT4104, SANS Co., Ltd., China), fitted with a 10 kN load cell, at a crosshead of 20 mm/min. The dimension of all samples is about 20 mm in diameter and height.Rheological properties were characterized by using an Anton Paar Physica MCR 301 rotational rheometer equipped with a CTD 450 convection oven (Graz, Austria). The dynamic frequency scanning tests were performed in the range of 0.01−100 rad s−1 at 110°C.


## 2.1. Materials

Poly(vinyl alcohol) (PVA) with a polymerization degree of 1000 or more and a saponification degree of >99 mol% (PVA-1799) was supplied by Kelong Chemical Reagent Corporation (Chengdu, China). APP was purchased from Macklin Reagent (Shanghai, China). CS (deacetylation degree, ≥95%) was obtained from Aladdin Chemistry Co., Ltd. (Shanghai, China). Boric acid was procured from Xilong Science Co., Ltd. (Shantou, China). All the chemicals were of laboratory grade and were utilized as received without further purification unless otherwise specified.


## 2.2. Preparation of the PVA Composite Aerogels

The preparation process of the PVA composite aerogels is schematically illustrated in Figure1. 8 wt% PVA aqueous solution was prepared by dissolving 8 g PVA in 92 ml DI water at 95°C under stirring for 3 h. To prepare a PVA/APP-CS solution, 0 g, 5 g, 10 g, and 15 g APP-CS (APP:CS=3:1 mass ratio) were mixed with 100 ml of 8 wt% PVA solution at 14000 rpm (A-555, INAYOU, China). Then, dissolve 0.8 g of boric acid in 10 ml of water and add to the above solution to prepare the hydrogels. After that, the resulting hydrogels were cast into a glass dish and frozen in a refrigerator, followed by freeze-drying in an FD-1A-50 freeze dryer (Yuming Instrument Co., Ltd., Shanghai, China) at −40°C under vacuum. And the as-obtained PVA composite aerogels are denoted as PVA/H3BO3, PVA/5APP-CS/H3BO3, PVA/10APP-CS/H3BO3, and PVA/15APP-CS/H3BO3.Figure 1
Preparation procedure of the PVA composite aerogel.


## 2.3. Characterization

Fourier-transform infrared (FTIR) spectra were recorded with a VERTEX70 spectrometer (Bruker Instrument Co., Ltd., Dresden, Germany) with thin films of KBr at room temperature. The measurement was carried out in the optical range of 4000–500 cm−1.X-ray diffractometry (XRD) was performed on a Neo Confucianism D/Max-2400 diffractometer (Rigaku, Tokyo, Japan), and the2θ scans were conducted in the range of 5° to 80°.The morphology of the samples was observed by scanning electron microscopy (SEM) using JSM-7001F (Japan Electron Optics Laboratory Co., Ltd., Tokyo, Japan).Thermogravimetric analysis (TGA) was performed on a TGA400 thermo-analyzer instrument (PerkinElmer, Inc., Fremont, CA, USA) from room temperature to 700°C at a linear heating rate of 10°C·min−1 under nitrogen atmosphere.The fire behavior of the aerogels was characterized by the UL-94 test (ASTM D-635-77) and the cone calorimeter test (CCT). The UL-94 test was performed on a CZF-2 vertical burning test instrument using aerogel sheets with dimensions of125×10×10mm3. CCT was performed using a Fire Testing Technology cone calorimeter on samples of 100×100×10mm3 dimensions, according to ISO 5660-1, with an external heat flux of 50 kW/m2.The flame-spraying experiment was conducted using a butane flame with a central flame temperature of 1300°C. The flame was perpendicular to the surface of the aerogel samples, which were40×40×6mm3 in size. The distance between the flame tip and the sample was fixed at 60 mm. The temperature on the backside of the aerogel was measured using an infrared thermometer at 1 min intervals. Triplicate measurements were conducted for each sample.The mechanical performance of the composites was examined using Instron universal test machine UT4304 (SANS Instrument Co., Ltd., Shanghai, China) at a crosshead speed of 20 mm/min. The sample size was150×10×4mm for the tensile test. Compression strength was conducted using an electronic universal testing machine (CMT4104, SANS Co., Ltd., China), fitted with a 10 kN load cell, at a crosshead of 20 mm/min. The dimension of all samples is about 20 mm in diameter and height.Rheological properties were characterized by using an Anton Paar Physica MCR 301 rotational rheometer equipped with a CTD 450 convection oven (Graz, Austria). The dynamic frequency scanning tests were performed in the range of 0.01−100 rad s−1 at 110°C.


## 3. Results and Discussion

### 3.1. Characterization of the APP-CS Composite

FTIR spectroscopy was used to obtain direct evidence of chemical reactions between APP and CS (Figure2). The characteristic absorption bands of APP at 3400–3000, 1430, 1242, 1072, 1016, and 877 cm−1 are ascribed to –NH4+, –NH4+, P=O, PO (symmetric stretching), PO2, and POP/PO (asymmetric stretching), respectively [12]. The characteristic absorption bands observed at 3500–3300, 1620, 1430, 1378, 1160, 1079, and 1032 cm−1 for CS are ascribed to –OH and –NH2, C=O, O-H, (CN, amide), (CO, bridge oxygen), (COC component), and (COC component), respectively [13–15]. The FTIR spectrum of APP-CS showed no apparent differences as compared with that of APP. This indicates that either no new derivatives were formed by the reaction of APP and CS or the APP peaks were of high intensity and overlapped with the CS peaks. APP and CS carry negative and positives charges, respectively, and form a polyelectrolyte complex through hydrogen bonding and ionic interaction (Figure 3).Figure 2
FTIR spectra of PVA, APP, CS, APP-CS, and H3BO3.Figure 3
Schematic illustration of the interaction between APP and CS.Further, the absence of chemical reactions between APP and CS was also confirmed by XRD (Figure4). The XRD pattern of CS, which is semicrystalline in nature, yields typical broad diffraction peaks at ~10° and 20° [16]. APP, which is crystalline, yields sharp characteristic peaks at 14.6°, 15.5°, 20.2°, 26°, 27.5°, 29.1°, 30.5°, 35.6°, 36.5°, 37.9°, and 43.2° [17–19]. No obvious differences could be identified between the XRD patterns of APP and APP-CS.Figure 4
XRD patterns of APP, CS, and APP-CS.


### 3.2. Rheological Properties of PVA Composite Hydrogels

The composite of PVA/H3BO3 and APP-CS formed a double-network hydrogel system. To study the bonding in the PVA composite hydrogels, their rheological properties were evaluated (Figure 5). In the frequency range of 0–100 rad/s, the storage modulus (G′) was greater than the loss modulus (G″), and the PVA composite hydrogels behaved like an elastic gel. The G′ values increased with increasing APP-CS content in the hydrogel. This suggests that with higher APP-CS content, APP and CS exhibit stronger interactions to form a polyelectrolyte through ionic interaction, which results in a higher storage modulus (G′).Figure 5
Dependence of (a)G′, (b) G″, and (c) η∗ on frequency for the PVA composite aerogels.
(a)(b)(c)All samples exhibit a decrease in viscosity (η∗) with the increasing shear rate and finally approached zero at 100 rad/s (Figure 5(c)). That is, the PVA-based hydrogel changed from a gel state to a quasi-liquid state. This indicates that the crosslinking bonds between PVA and H3BO3, as well as the ionic interactions between APP and CS, were likely destroyed with the increasing shear rate.


### 3.3. Mechanical Properties

The stress-strain curves of the hydrogels are displayed in Figure6(a). The strain at break of the hydrogels increased with the APP-CS content; however, the tensile strength decreased (Figure 7). This is because APP-CS acted as a filler in the PVA-based aerogel. That is, as the APP-CS content increased, the crosslinking density decreased, resulting in an increased strain at break and compromised tensile strength. However, the tensile strength did not significantly vary between the samples.Figure 6
(a) Stress-strain and (b) compressive stress-strain curves of the PVA composite aerogels.
(a)(b)Figure 7
Tensile strengths of the PVA composite hydrogels with different APP-CS contents.Figure6(b) clearly demonstrates that the APP-CS content has a negligible effect on the compressive stress-strain curves of the hydrogel samples, indicating that the overall mechanical properties of the PVA composite aerogels did not change with the addition of APP-CS. In addition, the peak stress value increased with increasing APP-CS content.


### 3.4. Basic Features of the PVA Composite Aerogels

The density, thermal conductivity, and porosity of the aerogels containing APP-CS are listed in Table1. The SEM image (Figure 8) shows that the aerogel without APP-CS had a few pores, and it easily collapsed because it was not supported by APP and CS. In contrast, the aerogels with APP-CS had a porous microstructure. However, the porosity of the aerogels with higher APP-CS content (10 g and 15 g) decreased owing to the barrier effect created by APP-CS, which increases the thermal conductivity and density of the samples.Table 1
Density, thermal conductivity, and porosity of the PVA composite aerogels.
Sample IDCompositesDensity (g/cm3)Thermal conductivity (W/mK)Porosity (%)1PVA/H3BO30.635±0.0020.1223±0.000373.22PVA/5APP-CS/H3BO30.482±0.0010.0910±0.000387.13PVA/10APP-CS/H3BO30.644±0.0020.1239±0.000383.04PVA/15APP-CS/H3BO30.763±0.0020.1279±0.000378.3Figure 8
SEM images of the PVA composite aerogels: (a) PVA/H3BO3, (b) PVA/5APP-CS/H3BO3, (c) PVA/10APP-CS/H3BO3, and (d) PVA/15APP-CS/H3BO3.
(a)(b)(c)(d)


### 3.5. Thermal Stability of the PVA Composite Aerogels

The effect of APP-CS on the thermal stability of the PVA-based aerogels was determined by TGA of the PVA composite aerogels with different amounts of APP-CS. Figure9 shows the respective TG and DTG curves, and the corresponding data are listed in Table 2. T5% is defined as the initial decomposition temperature. The T5% of the PVA composite aerogels with APP-CS is higher than that of the PVA aerogel without APP-CS (Table 2), indicating that APP-CS improved the thermal stability of the composites. The weight loss observed below 100°C is attributed to the removal of water from the aerogel, which contains a large amount of water. The highest weight loss at 200–500°C is attributed to the decomposition of the PVA backbone [20]. Further, the decomposition peak at 280–370°C is attributed to the degradation of APP-CS into polyphosphoric acid, which catalyzes the dehydration reaction between the –OH group of APP and the –NH2 group of CS. This causes an increase in the char residue of the PVA composite aerogels at 700°C as compared to that of the PVA/H3BO3 without APP-CS (residual char content: 10.3%).Figure 9
(a) TGA weight loss and (b) the corresponding DTG curves of the PVA composite aerogels.
(a)(b)Table 2
TGA data of the flame-retardant composites obtained in N2.
Sample IDCompositesT5% (°C)Rmax (%·min−1)Tmax (°C)Residue at 700°C (%)1PVA/H3BO381.514.0250.410.32PVA/5APP-CS/H3BO383.12.9290.146.13PVA/10APP-CS/H3BO3138.83.3284.347.34PVA/15APP-CS/H3BO3132.82.4294.647.5In particular, the aerogel containing 15 g APP-CS (APP:CS=3:1 mass ratio) generated 47.5% of residual char. This implies that CS in combination with APP has an excellent char-forming capacity and may significantly improve the flame retardancy of the PVA-based aerogels [21, 22]. The intumescent char layer provides a strong protective barrier (condensed-phase flame retardancy), which prevents the contact of oxygen with the substrate and the subsequent heat transfer, thereby preventing further burning of the substrate [23–25].


### 3.6. Combustion Behaviors of the PVA Composite Aerogels

The UL-94 vertical burning test has been widely used to evaluate the flame retardancy of materials [26–28]. The results obtained for the PVA composite aerogels are listed in Table 3. When APP-CS were added to PVA/H3BO3, the UL-94 rating increased from NR to V-0 and the dripping phenomenon was improved. The synergistic effect of APP and CS was clearly manifested, which is consistent with the TGA results.Table 3
UL-94 test results of the PVA composite aerogels.
Sample IDCompositesUL-94 test (3.2 mm)t1 (s)t2 (s)DrippingIgnite cottonRating1PVA/H3BO3354YesYesNR2PVA/5APP-CS/H3BO3517NoYesV-13PVA/10APP-CS/H3BO331NoNoV-04PVA/15APP-CS/H3BO321NoNoV-0CCT is a useful tool for evaluating flame-retardant materials and can be used to simulate real fire conditions [29–31]. The time to ignition (TTI), total heat release rate (THR), heat release rate (HRR), and carbon dioxide (CO2) production are presented in Figure 10 and Table 4. A longer TTI implies that the material is difficult to burn and has better flame retardancy. The TTI of the PVA/H3BO3 was only 66 s, while that of the PVA composite aerogel increased with increasing APP-CS content. Thus, it indicates an improved flame retardancy in the latter.Figure 10
(a) Heat release rate (HRR), (b) total heat release rate (THR), and (c) CO2 production curves of the PVA composite aerogels.
(a)(b)(c)Table 4
Combustion parameters obtained from cone calorimeter tests.
Sample IDCompositesTTI (s)PHRR (kW/m2)THR (MJ/m2)TTPHRRa (s)TSRb (m2/m2)FGRc (kW/m2 s)1PVA/H3BO366294.921.588273.03.352PVA/5APP-CS/H3BO367189.619.3107641.21.693PVA/10APP-CS/H3BO376121.117.8140480.90.864PVA/15APP-CS/H3BO315668.117.5240716.60.28aTTPHRR = time to PHRR. bTSR = total smoke release. cFGR=PHRR/TPHRR.The HRR curves of the aerogels are shown in Figure10(a). The peak HRR (PHRR) of the PVA/H3BO3 was 294.9 kW/m2, while that of the PVA composite aerogels with 15 g APP-CS (APP:CS=3:1 mass ratio) was decreased to 68.1 kW/m2 (Table 4). Furthermore, the THR curves presented in Figure 10(b) show considerable differences, while those of the PVA composite aerogels with APP-CS were decreased to 17.5 MJ/m2. This indicates that the PVA composite aerogel with APP-CS reduced the THR of the fuel available for combustion. Similarly, the CO2 output decreased with increasing APP-CS content (Figure 10(c)). The fire growth rate (FGR) (Table 4) reveals that the PVA/H3BO3 was easy to flash, implying a higher fire risk. However, when APP-CS were added, the FGR decreased considerably to 0.28 kW/m2 s, indicating that this aerogel can significantly increase the chance of withstanding an indoor fire.To further study the flame-retardant mechanism, the morphology of the char layer of the aerogels was characterized by SEM (Figure11), which shows increased residual char after combustion and a significant improvement in the integrity of the char layer. A dense and integrated char layer formed on the surface of the composite material can act as a physical barrier to decrease heat and mass transfer, thereby reducing the flammability of the composite. During combustion, PVA/H3BO3 decomposes into carbon [32]. Moreover, APP-CS also decomposes into carbon because APP decomposes into polyphosphoric acid, which catalyzes the dehydration reaction between the –OH groups of APP and –the NH2 groups of CS. The expanded char layer formed by the degradation of PVA/H3BO3 and APP-CS synergistically inhibits the heat and mass transfer to the underlying material, thereby preventing further flaming of the substrate.Figure 11
SEM images of the char residues of the PVA composite aerogels: (a) PVA/H3BO3, (b) PVA/5APP-CS/H3BO3, (c) PVA/10APP-CS/H3BO3, and (d) PVA/15APP-CS/H3BO3.
(a)(b)(c)(d)To study the fire resistance of the aerogels, a flame-spraying experiment was conducted out using a butane flame, as depicted in Figure12(a). The temperature-time curve is shown in Figure 12(b). For all the aerogels, the temperature measured on the backside of the aerogels increased with time. The maximum temperature of the PVA/H3BO3 was 256.4°C, while the maximum temperature of the composite aerogels with 15 g APP-CS (APP:CS=3:1 mass ratio) was 219.6°C. The higher the APP-CS content, the lower the temperature, indicating that the aerogels were thermally insulating to a certain degree.Figure 12
Fire resistance of the PVA-based aerogels. (a) Schematic of the fire resistance test. (b) Maximum temperature at the back of the aerogels versus time. (c) Photographs of the samples after burning for 10 min.
(a)(b)(c)Figure12(c) shows the aerogels after burning for 10 min. It is apparent that the PVA/H3BO3 was quickly ignited, was easily deformed, and had a smaller carbon area. However, the composite aerogels showed better structural integrity (i.e., the shape was retained) with increasing APP-CS content. After burning for 10 min, the PVA composite aerogel substrates with APP-CS remained impervious to the flames, indicating that APP-CS improved the thermal insulation and flame retardancy of the PVA-based aerogel.


## 3.1. Characterization of the APP-CS Composite

FTIR spectroscopy was used to obtain direct evidence of chemical reactions between APP and CS (Figure2). The characteristic absorption bands of APP at 3400–3000, 1430, 1242, 1072, 1016, and 877 cm−1 are ascribed to –NH4+, –NH4+, P=O, PO (symmetric stretching), PO2, and POP/PO (asymmetric stretching), respectively [12]. The characteristic absorption bands observed at 3500–3300, 1620, 1430, 1378, 1160, 1079, and 1032 cm−1 for CS are ascribed to –OH and –NH2, C=O, O-H, (CN, amide), (CO, bridge oxygen), (COC component), and (COC component), respectively [13–15]. The FTIR spectrum of APP-CS showed no apparent differences as compared with that of APP. This indicates that either no new derivatives were formed by the reaction of APP and CS or the APP peaks were of high intensity and overlapped with the CS peaks. APP and CS carry negative and positives charges, respectively, and form a polyelectrolyte complex through hydrogen bonding and ionic interaction (Figure 3).Figure 2
FTIR spectra of PVA, APP, CS, APP-CS, and H3BO3.Figure 3
Schematic illustration of the interaction between APP and CS.Further, the absence of chemical reactions between APP and CS was also confirmed by XRD (Figure4). The XRD pattern of CS, which is semicrystalline in nature, yields typical broad diffraction peaks at ~10° and 20° [16]. APP, which is crystalline, yields sharp characteristic peaks at 14.6°, 15.5°, 20.2°, 26°, 27.5°, 29.1°, 30.5°, 35.6°, 36.5°, 37.9°, and 43.2° [17–19]. No obvious differences could be identified between the XRD patterns of APP and APP-CS.Figure 4
XRD patterns of APP, CS, and APP-CS.


## 3.2. Rheological Properties of PVA Composite Hydrogels

The composite of PVA/H3BO3 and APP-CS formed a double-network hydrogel system. To study the bonding in the PVA composite hydrogels, their rheological properties were evaluated (Figure 5). In the frequency range of 0–100 rad/s, the storage modulus (G′) was greater than the loss modulus (G″), and the PVA composite hydrogels behaved like an elastic gel. The G′ values increased with increasing APP-CS content in the hydrogel. This suggests that with higher APP-CS content, APP and CS exhibit stronger interactions to form a polyelectrolyte through ionic interaction, which results in a higher storage modulus (G′).Figure 5
Dependence of (a)G′, (b) G″, and (c) η∗ on frequency for the PVA composite aerogels.
(a)(b)(c)All samples exhibit a decrease in viscosity (η∗) with the increasing shear rate and finally approached zero at 100 rad/s (Figure 5(c)). That is, the PVA-based hydrogel changed from a gel state to a quasi-liquid state. This indicates that the crosslinking bonds between PVA and H3BO3, as well as the ionic interactions between APP and CS, were likely destroyed with the increasing shear rate.


## 3.3. Mechanical Properties

The stress-strain curves of the hydrogels are displayed in Figure6(a). The strain at break of the hydrogels increased with the APP-CS content; however, the tensile strength decreased (Figure 7). This is because APP-CS acted as a filler in the PVA-based aerogel. That is, as the APP-CS content increased, the crosslinking density decreased, resulting in an increased strain at break and compromised tensile strength. However, the tensile strength did not significantly vary between the samples.Figure 6
(a) Stress-strain and (b) compressive stress-strain curves of the PVA composite aerogels.
(a)(b)Figure 7
Tensile strengths of the PVA composite hydrogels with different APP-CS contents.Figure6(b) clearly demonstrates that the APP-CS content has a negligible effect on the compressive stress-strain curves of the hydrogel samples, indicating that the overall mechanical properties of the PVA composite aerogels did not change with the addition of APP-CS. In addition, the peak stress value increased with increasing APP-CS content.


## 3.4. Basic Features of the PVA Composite Aerogels

The density, thermal conductivity, and porosity of the aerogels containing APP-CS are listed in Table1. The SEM image (Figure 8) shows that the aerogel without APP-CS had a few pores, and it easily collapsed because it was not supported by APP and CS. In contrast, the aerogels with APP-CS had a porous microstructure. However, the porosity of the aerogels with higher APP-CS content (10 g and 15 g) decreased owing to the barrier effect created by APP-CS, which increases the thermal conductivity and density of the samples.Table 1
Density, thermal conductivity, and porosity of the PVA composite aerogels.
Sample IDCompositesDensity (g/cm3)Thermal conductivity (W/mK)Porosity (%)1PVA/H3BO30.635±0.0020.1223±0.000373.22PVA/5APP-CS/H3BO30.482±0.0010.0910±0.000387.13PVA/10APP-CS/H3BO30.644±0.0020.1239±0.000383.04PVA/15APP-CS/H3BO30.763±0.0020.1279±0.000378.3Figure 8
SEM images of the PVA composite aerogels: (a) PVA/H3BO3, (b) PVA/5APP-CS/H3BO3, (c) PVA/10APP-CS/H3BO3, and (d) PVA/15APP-CS/H3BO3.
(a)(b)(c)(d)


## 3.5. Thermal Stability of the PVA Composite Aerogels

The effect of APP-CS on the thermal stability of the PVA-based aerogels was determined by TGA of the PVA composite aerogels with different amounts of APP-CS. Figure9 shows the respective TG and DTG curves, and the corresponding data are listed in Table 2. T5% is defined as the initial decomposition temperature. The T5% of the PVA composite aerogels with APP-CS is higher than that of the PVA aerogel without APP-CS (Table 2), indicating that APP-CS improved the thermal stability of the composites. The weight loss observed below 100°C is attributed to the removal of water from the aerogel, which contains a large amount of water. The highest weight loss at 200–500°C is attributed to the decomposition of the PVA backbone [20]. Further, the decomposition peak at 280–370°C is attributed to the degradation of APP-CS into polyphosphoric acid, which catalyzes the dehydration reaction between the –OH group of APP and the –NH2 group of CS. This causes an increase in the char residue of the PVA composite aerogels at 700°C as compared to that of the PVA/H3BO3 without APP-CS (residual char content: 10.3%).Figure 9
(a) TGA weight loss and (b) the corresponding DTG curves of the PVA composite aerogels.
(a)(b)Table 2
TGA data of the flame-retardant composites obtained in N2.
Sample IDCompositesT5% (°C)Rmax (%·min−1)Tmax (°C)Residue at 700°C (%)1PVA/H3BO381.514.0250.410.32PVA/5APP-CS/H3BO383.12.9290.146.13PVA/10APP-CS/H3BO3138.83.3284.347.34PVA/15APP-CS/H3BO3132.82.4294.647.5In particular, the aerogel containing 15 g APP-CS (APP:CS=3:1 mass ratio) generated 47.5% of residual char. This implies that CS in combination with APP has an excellent char-forming capacity and may significantly improve the flame retardancy of the PVA-based aerogels [21, 22]. The intumescent char layer provides a strong protective barrier (condensed-phase flame retardancy), which prevents the contact of oxygen with the substrate and the subsequent heat transfer, thereby preventing further burning of the substrate [23–25].


## 3.6. Combustion Behaviors of the PVA Composite Aerogels

The UL-94 vertical burning test has been widely used to evaluate the flame retardancy of materials [26–28]. The results obtained for the PVA composite aerogels are listed in Table 3. When APP-CS were added to PVA/H3BO3, the UL-94 rating increased from NR to V-0 and the dripping phenomenon was improved. The synergistic effect of APP and CS was clearly manifested, which is consistent with the TGA results.Table 3
UL-94 test results of the PVA composite aerogels.
Sample IDCompositesUL-94 test (3.2 mm)t1 (s)t2 (s)DrippingIgnite cottonRating1PVA/H3BO3354YesYesNR2PVA/5APP-CS/H3BO3517NoYesV-13PVA/10APP-CS/H3BO331NoNoV-04PVA/15APP-CS/H3BO321NoNoV-0CCT is a useful tool for evaluating flame-retardant materials and can be used to simulate real fire conditions [29–31]. The time to ignition (TTI), total heat release rate (THR), heat release rate (HRR), and carbon dioxide (CO2) production are presented in Figure 10 and Table 4. A longer TTI implies that the material is difficult to burn and has better flame retardancy. The TTI of the PVA/H3BO3 was only 66 s, while that of the PVA composite aerogel increased with increasing APP-CS content. Thus, it indicates an improved flame retardancy in the latter.Figure 10
(a) Heat release rate (HRR), (b) total heat release rate (THR), and (c) CO2 production curves of the PVA composite aerogels.
(a)(b)(c)Table 4
Combustion parameters obtained from cone calorimeter tests.
Sample IDCompositesTTI (s)PHRR (kW/m2)THR (MJ/m2)TTPHRRa (s)TSRb (m2/m2)FGRc (kW/m2 s)1PVA/H3BO366294.921.588273.03.352PVA/5APP-CS/H3BO367189.619.3107641.21.693PVA/10APP-CS/H3BO376121.117.8140480.90.864PVA/15APP-CS/H3BO315668.117.5240716.60.28aTTPHRR = time to PHRR. bTSR = total smoke release. cFGR=PHRR/TPHRR.The HRR curves of the aerogels are shown in Figure10(a). The peak HRR (PHRR) of the PVA/H3BO3 was 294.9 kW/m2, while that of the PVA composite aerogels with 15 g APP-CS (APP:CS=3:1 mass ratio) was decreased to 68.1 kW/m2 (Table 4). Furthermore, the THR curves presented in Figure 10(b) show considerable differences, while those of the PVA composite aerogels with APP-CS were decreased to 17.5 MJ/m2. This indicates that the PVA composite aerogel with APP-CS reduced the THR of the fuel available for combustion. Similarly, the CO2 output decreased with increasing APP-CS content (Figure 10(c)). The fire growth rate (FGR) (Table 4) reveals that the PVA/H3BO3 was easy to flash, implying a higher fire risk. However, when APP-CS were added, the FGR decreased considerably to 0.28 kW/m2 s, indicating that this aerogel can significantly increase the chance of withstanding an indoor fire.To further study the flame-retardant mechanism, the morphology of the char layer of the aerogels was characterized by SEM (Figure11), which shows increased residual char after combustion and a significant improvement in the integrity of the char layer. A dense and integrated char layer formed on the surface of the composite material can act as a physical barrier to decrease heat and mass transfer, thereby reducing the flammability of the composite. During combustion, PVA/H3BO3 decomposes into carbon [32]. Moreover, APP-CS also decomposes into carbon because APP decomposes into polyphosphoric acid, which catalyzes the dehydration reaction between the –OH groups of APP and –the NH2 groups of CS. The expanded char layer formed by the degradation of PVA/H3BO3 and APP-CS synergistically inhibits the heat and mass transfer to the underlying material, thereby preventing further flaming of the substrate.Figure 11
SEM images of the char residues of the PVA composite aerogels: (a) PVA/H3BO3, (b) PVA/5APP-CS/H3BO3, (c) PVA/10APP-CS/H3BO3, and (d) PVA/15APP-CS/H3BO3.
(a)(b)(c)(d)To study the fire resistance of the aerogels, a flame-spraying experiment was conducted out using a butane flame, as depicted in Figure12(a). The temperature-time curve is shown in Figure 12(b). For all the aerogels, the temperature measured on the backside of the aerogels increased with time. The maximum temperature of the PVA/H3BO3 was 256.4°C, while the maximum temperature of the composite aerogels with 15 g APP-CS (APP:CS=3:1 mass ratio) was 219.6°C. The higher the APP-CS content, the lower the temperature, indicating that the aerogels were thermally insulating to a certain degree.Figure 12
Fire resistance of the PVA-based aerogels. (a) Schematic of the fire resistance test. (b) Maximum temperature at the back of the aerogels versus time. (c) Photographs of the samples after burning for 10 min.
(a)(b)(c)Figure12(c) shows the aerogels after burning for 10 min. It is apparent that the PVA/H3BO3 was quickly ignited, was easily deformed, and had a smaller carbon area. However, the composite aerogels showed better structural integrity (i.e., the shape was retained) with increasing APP-CS content. After burning for 10 min, the PVA composite aerogel substrates with APP-CS remained impervious to the flames, indicating that APP-CS improved the thermal insulation and flame retardancy of the PVA-based aerogel.


## 4. Conclusion

In this study, two flame-retardant materials, ammonium polyphosphate and chitosan, were added to PVA/H3BO3 to prepare aerogels by a freeze-drying method. The anionic APP and cationic CS formed a polyelectrolyte complex by ionic interaction. It was observed that the APP-CS composite decreased the PHRR and THR values and CO2 emission of the PVA-based aerogels owing to the formation of a char layer by the decomposition of PVA/H3BO3 and APP-CS during combustion. The expanded char layer exerts a flame-retardant effect on the PVA-based aerogel. In addition, the PVA composite aerogels with a porous structure have an excellent thermal insulation property and low thermal conductivity (as low as 0.0879 W m–1 K–1). Hence, the PVA composite aerogels with good flame-retardant and thermal insulation properties can be potentially applied to building materials.



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*Source: 5555916-2021-05-29.xml*