Preparation and Properties of Poly(butylene adipate-co-terephthalate)/thermoplastic Hydroxypropyl Starch Composite Films Reinforced with Nano-Silica

The use of biodegradable plastics is gradually increasing, but its expensive cost limits promotion. In this study, poly(butylene adipate-co-terephthalate)/thermoplastic hydroxypropyl starch reinforced with nano-silica (PBAT/TPHSg-SiO2) composite films with high hydroxypropyl starch content were prepared in a two-step process. The effect of reinforced thermoplastic hydroxypropyl starch on the mechanical, thermal, processing properties, and micromorphology of the composite films was investigated. The results showed that the tensile strength of the composite films was significantly improved by the addition of nano-silica, with 35% increase in horizontal tensile strength and 21% increase in vertical tensile strength after the addition of 4 phr of nano-silica. When the content of thermoplastic hydroxypropyl starch reinforced with nano-silica (TPHSg-4SiO2) is 40%, the horizontal and vertical tensile strengths of the films are 9.82 and 12.09 MPa, respectively, and the elongation at break of the films is over 500%. Electron micrographs show that TPHSg-4SiO2 is better homogeneously dispersed in the PBAT and exhibits a bi-continuous phase structure at a TPHSg-4SiO2 content of 40%. In this study, the blowing PBAT/TPHSg-4SiO2 composite films effectively reduce the cost and still show better mechanical properties, which are suitable for packaging applications.


Introduction
With the increasing awareness of environmental protection, biodegradable plastics have received a great deal of attention. PBAT has been the most widely used petroleumbased fully biodegradable polyester so far and has similar processing and usability to low density polyethylene (LDPE) [1]. It has received widespread attention for applications in the packaging industry, biomedical, industrial, and agricultural sectors [2][3][4]. Due to the high production costs of PBAT products, difficulties have been encountered in large-scale commercial applications. Reducing the manufacturing cost of PBAT packaging materials has become the most important factor affecting the widespread use of PBATbased materials. Blending PBAT with inexpensive inorganic non-metallic powders [5][6][7][8] or naturally degradable polymers such as starch [9][10][11][12][13][14], lignin [15,16], bamboo flour [17], and corn marmalade [18] was an important way to prepare low-cost PBAT-based composites.
Starch was considered to be one of the most promising fillers for PBAT-based composites due to its abundant source, low cost, renewable, and fully biodegradable characteristics [19,20]. It reduced the cost of PBAT materials without compromising the biodegradable

Preparation of Composite Film Materials
Hydroxypropyl starch (HS) was dried in an oven at 80 • C for 8 h, and nano-silica was dried at 105 • C for 2 h. Hydroxypropyl starch, glycerol, and nano-silica were mixed in a FW100 high speed mixers by Tianjin Teste Instruments Co., Ltd. (Tianjin, China) at room temperature for 20 min according to the formula of Table 2 and stored in a sealed container until use. The mixtures were compounded into TPHS g-SiO2 pellets by extrusion, using a KTE-20 laboratory twin-screw extruder (Nanjing Keke Extrusion Equipment Co., Ltd., Nanjing, China) with a screw diameter (D) of 21.6 mm and length of 40 D. The barrel temperatures from the feed zone to the die zone were 100, 130, 140, 145, 150, 145 • C. The screw speed was 100 rpm. The extruded strands were air-cooled, cut into pellets, and stored in a sealed container until used.  100  40  0  TPHS g-1SiO2  100  40  1  TPHS g-2SiO2  100  40  2  TPHS g-3SiO2  100  40  3  TPHS g-4SiO2  100  40  4  TPHS g-5SiO2  100  40  5 phr is weight parts.
PBAT and TPHS g-4SiO2 were then mixed according to the formulation in Table 3 and extruded with the same laboratory twin-screw extruder. The barrel temperatures from the feed zone to the die zone were 150, 155, 160, 165, 160, 155 • C. The screw speed was 120 rpm. The extruded strands were water-cooled, cut into pellets, and dried in a vacuum oven at 80 • C for 12 h, stored in a sealed container until use. When exploring the optimum nano-silica content, the ratio of PBAT/TPHS g-SiO2 was 8/2 and the nano-silica content in TPHS was 1, 2, 3, 4, and 5 phr; the ratios for PBAT/TPHS g-4SiO2 composite films with different starch content were explored as shown in Table 2 and the nano-silica content in TPHS was 4 phr. Different percentages of PBAT/TPHS g pellets were prepared in the same way. The films were prepared using a JFYC-28 laboratory small testing film-blowing machine by Guangzhou Jinfang Yuan Machinery Manufacturing Co., Ltd. (Guangzhou, China) with a die diameter of 40 mm. The film-blowing conditions consisted of a screw speed of 15 rpm and extrusion temperature profiles of 135, 165, 155, and 140 • C, with a blow-up ratio of 2.8-3.0 and a traction ratio of 3.0. The film thickness was kept at 50-60 µm (80 ± 5 µm for samples with 50% TPHS g content, 60% TPHS g-4SiO2 content samples cannot be blown due to the material phase structure with TPHS g as a continuous phase).

Characterization of the Composite Films
The static tensile tests were performed using a CMT6104 tensile tester by Meters Industrial Systems (China) Co., Ltd. (Shenzhen, China). The tensile strength (TS) and elongation at break (EB) of the films were evaluated according to GB/T 1040. . Film samples were cut into strips (200 mm long and 20 mm wide), with a spacing of 50 mm and a stretching rate of 200 mm/min. The thickness of the film was measured using a digital flush micrometer gauge, measuring five positions on each film, and taking the average. The tests were performed with at least ten replicates for each sample.
The thermal properties of the composite films were characterized using a Q20 differential scanning calorimeter by TA instruments (New Castle, DE, USA). An about 5-6 mg sample was weighed and placed in a crucible under nitrogen atmosphere. The test temperature was first increased from 40 • C to 180 • C, held for 5 min to eliminate the thermal history of the sample, then cooled to −60 • C, held for 5 min, and then increased to 200 • C, at a rate of 10 • C/min. The crystallization temperature (T c ) and the heat of crystallization (∆H c ) were obtained from the first temperature reduction, while the glass transition temperature (T g ), the melting temperature (T m ), and the heat of melt (∆H m ) were determined in the second temperature increase, and the degree of crystallinity was calculated from the following equation.
where ∆H c is the heat of crystallization of the sample; ∆H 0 c is the heat of crystallization of pure PBAT, 70.69 J/g; a is the weight fraction of thermoplastic hydroxypropyl starch.
Note: According to the NMR test data, the mass proportion of PBT segment in the PBAT was 48.75%, and the enthalpy of crystallization of PBT segment was 145 J/g. Therefore, the heat of complete crystallization (∆H 0 c ) of pure PBAT sample was 70.69 J/g. The thermal stability properties of the PBAT/TPHS g-SiO2 composite film material were characterized using the thermogravimetric analyzer (TG-209, NETZSCH Scientific Instruments Trading (Shanghai) Ltd., Shanghai, China). The testing temperature program was 30 • C, heating to 800 • C with a heating rate of 10 • C/min under a nitrogen atmosphere and sample mass of 8-9 mg.
Scanning electron microscope (ZEISS Ultra 55, CarlZeiss Jena, Oberkochen, Germany) was used to observe the surface and cross-sectional morphology of the composite films. The films were frozen in liquid nitrogen. The samples were placed in water for 24 h, allowing the TPHS g-SiO2 phase to be completely removed from the film. The film samples were placed on the device and plated with gold using plasma sputtering for 20 min before observation.
The PBAT/TPHS g-SiO2 composites were tested for the melt flow index according to GB/T 3682-2000. The tests were carried out at 150 • C and 190 • C, respectively, with a weight of 2160 g. The melt flow index values in g/10 min were calculated using Equation (2).
where: t re f is the reference time, s (600 s); m is the average mass of cut sections, g; t is the time interval between cut sections, s. Data in this work was expressed as the mean along with its corresponding standard deviation (SD). The analysis of variance (ANOVA) was performed with SPSS (version  27.0 for windows, IBM, New York, NY, USA) and the Tukey test was used to determine significant difference between means (p < 0.05). Figure 1 shows the tensile strength ( Figure 1a) and elongation at break (Figure 1b) of the composite films prepared by PBAT with 20% of thermoplastic hydroxypropyl starch with different nano-silica contents. The horizontal and vertical tensile strengths of the film tend to increase with the amount of nano-silica in the thermoplastic hydroxypropyl starch, reaching a maximum of 4 phr of nano-silica. Compared to the sample without silica, the horizontal tensile strength of the film increased from 10.63 MPa to 14.34 MPa, with an increase of 35%, and the vertical tensile strength increased from 11.17 MPa to 13.52 MPa, with an increase of 21%. Elongation at break of the film was between 600 and 800%. The increase in the tensile strength of the composite film is mainly due to the increased mechanical strength of the thermoplastic hydroxypropyl starch, which effectively disperses the stress during film stretching and thus increases the overall tensile strength of the film. According to the findings of Zhu et al. [33], nano-silica has been shown to enhance hydroxypropyl starch by the mechanism shown in Figure 2, mainly due to the interfacial adhesion between the starch and the SiO 2 nanoparticles, which is caused by the C-O-Si chemical bond, the formation of hydrogen bonds between the silicon hydroxyl groups on the surface of the silica nanoparticles, and the large number of silicon hydroxyl groups in the starch matrix [43].

Mechanical Properties
where: is the reference time, s (600 s); m is the average mass of cut sections, g; t is the time interval between cut sections, s. Data in this work was expressed as the mean along with its corresponding standard deviation (SD). The analysis of variance (ANOVA) was performed with SPSS (version 27.0 for windows, IBM, New york, NY, USA) and the Tukey test was used to determine significant difference between means (p < 0.05). Figure 1 shows the tensile strength ( Figure 1a) and elongation at break (Figure 1b) of the composite films prepared by PBAT with 20% of thermoplastic hydroxypropyl starch with different nano-silica contents. The horizontal and vertical tensile strengths of the film tend to increase with the amount of nano-silica in the thermoplastic hydroxypropyl starch, reaching a maximum of 4 phr of nano-silica. Compared to the sample without silica, the horizontal tensile strength of the film increased from 10.63 MPa to 14.34 MPa, with an increase of 35%, and the vertical tensile strength increased from 11.17 MPa to 13.52 MPa, with an increase of 21%. Elongation at break of the film was between 600 and 800%. The increase in the tensile strength of the composite film is mainly due to the increased mechanical strength of the thermoplastic hydroxypropyl starch, which effectively disperses the stress during film stretching and thus increases the overall tensile strength of the film. According to the findings of Zhu et al. [33], nano-silica has been shown to enhance hydroxypropyl starch by the mechanism shown in Figure 2, mainly due to the interfacial adhesion between the starch and the SiO2 nanoparticles, which is caused by the C-O-Si chemical bond, the formation of hydrogen bonds between the silicon hydroxyl groups on the surface of the silica nanoparticles, and the large number of silicon hydroxyl groups in the starch matrix [43].  Figure 3a shows the tensile strength of PBAT/TPHS g-4SiO2 and PBAT/TPHS g composite films with different TPHS content. As the content of TPHS in the film increases, the tensile strength of the film gradually decreases, and the vertical tensile strength of the composite film is slightly higher than the horizontal tensile strength. The horizontal and vertical tensile strength of the PBAT/TPHS g-4SiO2 composite film is significantly higher than that of the PBAT/TPHS g composite film with the same amount of thermoplastic starch. It shows that the reinforcement of thermoplastic hydroxypropyl starch by nano-silica is an effective way to improve the tensile strength of PBAT/TPHS composite films. At a TPHS g-4SiO2 content of 40%, the film also maintains horizontal and vertical tensile strengths of 9.82 MPa and 12.09 MPa, both of which meet the requirements for commercial films, according to the relevant standards, such as GB/T 18893-2002, GB/T 4456-1996, and GB/T 38082-2019. When the content of TPHS g-4SiO2 is 50%, the horizontal and vertical tensile strengths of the film are 6.20 MPa and 8.21 MPa, respectively, which can still meet the mechanical property requirements of agricultural film materials, according to the relevant standards, such as GB/T 35795-2017, showing a good prospect of use in the field of fully biodegradable agricultural ground cover films.   Figure 3a shows the tensile strength of PBAT/TPHSg-4SiO2 and PBAT/TPHSg composite films with different TPHS content. As the content of TPHS in the film increases, the tensile strength of the film gradually decreases, and the vertical tensile strength of the composite film is slightly higher than the horizontal tensile strength. The horizontal and vertical tensile strength of the PBAT/TPHSg-4SiO2 composite film is significantly higher than that of the PBAT/TPHSg composite film with the same amount of thermoplastic starch. It shows that the reinforcement of thermoplastic hydroxypropyl starch by nano-silica is an effective way to improve the tensile strength of PBAT/TPHS composite films. At a TPHSg-4SiO2 content of 40%, the film also maintains horizontal and vertical tensile strengths of 9.82 MPa and 12.09 MPa, both of which meet the requirements for commercial films, according to the relevant standards, such as GB/T 18893-2002, GB/T 4456-1996, and GB/T 38082-2019. When the content of TPHSg-4SiO2 is 50%, the horizontal and vertical tensile strengths of the film are 6.20 MPa and 8.21 MPa, respectively, which can still meet the mechanical property requirements of agricultural film materials, according to the relevant standards, such as GB/T 35795-2017, showing a good prospect of use in the field of fully biodegradable agricultural ground cover films. Figure 3b shows the change in elongation at break for the composite films. The vertical elongation at break of the composite films ranged from 800 to 900%, which is similar to the 812% of pure PBAT. After adding TPHSg-4SiO2 as a filler to reduce costs, the PBAT/TPHSg-4SiO2 composite film maintains a good elongation at break, avoiding the disadvantages of thermoplastic starches with low elongation at break and brittle materials. However, the horizontal elongation at break of the film has a clear tendency to decrease as the TPHSg-4SiO2 content increases, and the rate of decrease increases significantly after the TPHSg-4SiO2 content reaches 40%, decreasing to 666% at 40% TPHSg-4SiO2 content and 554% at 50% TPHSg-4SiO2 content, 40.1% reduction compared to PBAT films. The reason for the drastic decrease in elongation at break may be that the PBAT/TPHSg-4SiO2 composite film changed from an island structure to a bi-continuous phase structure (as shown in Figure 4e), the PBAT and TPHSg-4SiO2 phases were oriented in the vertical direction during the blowing of the film, and the PBAT phase was no longer continuous in the horizontal direction of the film. Since the mechanical strength of the thermoplastic starch phase is much lower than the PBAT phase, when the bi-continuous phase structure appears, the composite film easily breaks during stretching due to defects in the starch    Figure 3b shows the change in elongation at break for the composite films. The vertical elongation at break of the composite films ranged from 800 to 900%, which is similar to the 812% of pure PBAT. After adding TPHS g-4SiO2 as a filler to reduce costs, the PBAT/TPHS g-4SiO2 composite film maintains a good elongation at break, avoiding the disadvantages of thermoplastic starches with low elongation at break and brittle materials. However, the horizontal elongation at break of the film has a clear tendency to decrease as the TPHS g-4SiO2 content increases, and the rate of decrease increases significantly after the TPHS g-4SiO2 content reaches 40%, decreasing to 666% at 40% TPHS g-4SiO2 content and 554% at 50% TPHS g-4SiO2 content, 40.1% reduction compared to PBAT films. The reason for the drastic decrease in elongation at break may be that the PBAT/TPHS g-4SiO2 composite film changed from an island structure to a bi-continuous phase structure (as shown in Figure 4e), the PBAT and TPHS g-4SiO2 phases were oriented in the vertical direction during the blowing of the film, and the PBAT phase was no longer continuous in the horizontal direction of the film. Since the mechanical strength of the thermoplastic starch phase is much lower than the PBAT phase, when the bi-continuous phase structure appears, the composite film easily breaks during stretching due to defects in the starch phase, which is also the reason why the tensile strength decreases when the TPHS g-4SiO2 content increases.  In addition, the mechanical properties of PBAT/TPHS g-4SiO2 composite films are comparable to LDPE materials which are commonly used in packaging and agriculture. The thermoplastic starch content of 50% still has good mechanical properties, PBAT improves the mechanical properties and flexibility of the thermoplastic starch. Zhai et al. [44] reported PBAT/TPS composite films prepared with glycerol and citric acid as plasticizers and nanoclay as reinforcing agent. The horizontal and vertical tensile strengths of the films at 50% of thermoplastic starch were 5.3 and 7.4 MPa. PBAT/TPS composite films with a thermoplastic starch content of 50% were prepared by Pan et al. [38] The horizontal and vertical tensile strengths were 4.4/4.6 MPa, and the films had 256/277% elongation at break in the horizontal and vertical directions. In this work, the mechanical properties of PBAT/TPHS g-4SiO2 composite films were improved by adding nano-silica as reinforcing agent for thermoplastic hydroxypropyl starch. Table 4 shows the melt flow index of PBAT and thermoplastic hydroxypropyl starch composites. The melt flow index of the material increases and then decreases with the increase in TPHS g-4SiO2 phase content, and the MFR is maximum at the TPHS g-4SiO2 content of 20%. The reason may be that at low TPHS g-4SiO2 content, the small molecules of glycerol in the TPHS g-4SiO2 transferred to PBAT and the melting index of the composite increases. When the TPHS g-4SiO2 content reaches 30%, the phase structure of the composites is transformed. As shown in the SEM results, the phase structure is changed into a two-phase continuous structure at a high TPHS g-4SiO2 content, and the high viscosity of the TPHS g-4SiO2 phase itself restricts the flow of the composites, which reduces the fluidity of the composites and leads to the reduction of the melt index of the composites. When the content of TPHS g-4SiO2 reaches 60%, it does not have the ability to blow film at 140-160 • C blowing temperature because the flowability is poor, and it has been cooled at the die.  Figure 4 shows the cross-sectional morphology of the composite films. The contents of thermoplastic hydroxypropyl starch in Figure 4a-f are 0%, 10%, 20%, 30%, 40%, and 50%, respectively. The film sections were freeze-fragmentations in liquid nitrogen and dipped in distilled water for one day to remove the starch phase from the film completely. Figure 4a shows the cross-sectional morphology of pure PBAT with smooth cross-section. As the content of TPHS g-4SiO2 gradually increased, the number of holes increased significantly, and the holes show spherical or sphere-like shapes. When the content of TPHS g-4SiO2 was 40% and above, the TPHS g-4SiO2 balls were deformed and connected, and the phase structure of the composites changed from island structures to two-phase continuous structures. This also leads to a dramatic decrease in mechanical strength and decrease in elongation at break of the film in the horizontal direction.

Scanning Electron Microscope
When the TPHS g-4SiO2 content varied from 10% to 30%, electron micrographs show the thermoplastic starch microspheres changing from 3 µm to smaller than 0.5 µm. Due to the strong hydrogen bonding of the starch and the lower viscosity of PBAT, the TPHS g-4SiO2 spheres cannot disperse easily, so the diameter of TPHS g-4SiO2 spheres is larger. When the TPHS g-4SiO2 content increased, the TPHS g-4SiO2 spheres squeeze each other and break, making the diameter of the spheres smaller. Figure 5 shows a comparison of the cross-sectional morphology of both 70PBAT/30TPHS g and 70PBAT/30TPHS g-4SiO2 composite films. It is clear that the number of holes of the 70PBAT/30TPHS g composite film is fewer than the one observed for the 70PBAT/30TPHS g-4SiO2 composite film, but the diameter of the holes in the former is significantly larger than the latter. This is due to the thermoplastic starch having a higher melt strength after reinforcement with nano-silica. During the melt blending process, the interaction between thermoplastic starch pellets is more significant, resulting in the fragmentation of the starch pellets. Therefore, the reinforced thermoplastic starch is better dispersed in PBAT. Better dispersion not only allows the PBAT phase to maintain continuity, but also prevents the breakage of starch granules during the stretching process, which can lead to defects and film breakage. This is the same result as the tensile strength of the PBAT/TPHS g-4SiO2 composite film was higher than that of the PBAT/TPHS g composite film.
interaction between thermoplastic starch pellets is more significant, resulting in the fragmentation of the starch pellets. Therefore, the reinforced thermoplastic starch is better dispersed in PBAT. Better dispersion not only allows the PBAT phase to maintain continuity, but also prevents the breakage of starch granules during the stretching process, which can lead to defects and film breakage. This is the same result as the tensile strength of the PBAT/TPHSg-4SiO2 composite film was higher than that of the PBAT/TPHSg composite film.

Differential Scanning Calorimetry
Differential scanning calorimetric analyses were performed on PBAT and PBAT/TPHSg-4SiO2 composites to obtain the crystallization temperature, glass transition temperature, melting temperature, enthalpy of crystallization, enthalpy of melting, and crystallinity of the composites. Figure 6a shows the process of the first temperature reduction. The Tc temperature of pure PBAT was 65.73 °C. The crystallization temperature increased after the addition of TPHSg-4SiO2 and gradually increased as the content of TPHSg-4SiO2 increased. This is due to the TPHSg-4SiO2 acting as a nucleating agent and promoting the crystallization of PBAT. And as the TPHSg-4SiO2 content increases, the crystallization enthalpy of the composite film material gradually decreases. Chen et al. [45] demonstrated that the reduced crystallinity of polyester was beneficial to the degradation of the composite film. No crystallization process of TPHSg-4SiO2 was observed during the tests. Figure 6b shows the second temperature rise process, which obverses the glass transition temperature and the melting temperature of the material. The glass transition temperature of the PBAT phase was reduced with the addition of TPHSg-4SiO2. It is possi-

Differential Scanning Calorimetry
Differential scanning calorimetric analyses were performed on PBAT and PBAT/TPHS g-4SiO2 composites to obtain the crystallization temperature, glass transition temperature, melting temperature, enthalpy of crystallization, enthalpy of melting, and crystallinity of the composites. Figure 6a shows the process of the first temperature reduction. The T c temperature of pure PBAT was 65.73 • C. The crystallization temperature increased after the addition of TPHS g-4SiO2 and gradually increased as the content of TPHS g-4SiO2 increased. This is due to the TPHS g-4SiO2 acting as a nucleating agent and promoting the crystallization of PBAT. And as the TPHS g-4SiO2 content increases, the crystallization enthalpy of the composite film material gradually decreases. Chen et al. [45] demonstrated that the reduced crystallinity of polyester was beneficial to the degradation of the composite film. No crystallization process of TPHS g-4SiO2 was observed during the tests. Figure 6b shows the second temperature rise process, which obverses the glass transition temperature and the melting temperature of the material. The glass transition temperature of the PBAT phase was reduced with the addition of TPHS g-4SiO2 . It is possible that the transfer of the glycerol from TPHS g-4SiO2 into the PBAT phase increases the mobility of the PBAT molecular chain segments and decreases the glass transition temperature. It can also be seen that the melting points of the composites are all higher than pure PBAT. This is mainly due to the fact that the composites crystallize at higher temperatures, where the molecular chain segments are more mobile, have enough time to adjust, and the crystals are more perfect. However, the melting temperature of the composites did not change much and the crystallinity of PBAT did not change. As can be seen in Table 5, the crystallinity of the composite film material gradually decreases as the TPHS g-4SiO2 content increases. This is due to the increase in TPHS g-4SiO2 content, the increase in the crystallization sites of PBAT in the material, the faster crystallization of the PBAT phase, and the decrease in crystallinity.
adjust, and the crystals are more perfect. However, the melting temperature of the composites did not change much and the crystallinity of PBAT did not change. As can be seen in Table 5, the crystallinity of the composite film material gradually decreases as the TPHSg-4SiO2 content increases. This is due to the increase in TPHSg-4SiO2 content, the increase in the crystallization sites of PBAT in the material, the faster crystallization of the PBAT phase, and the decrease in crystallinity.   Figure 7 and Table 6 show the TG curves of pure PBAT and PBAT/TPHSg-4SiO2 composite film materials and Figure 8 shows the DTG curves of pure PBAT and PBAT/TPHSg-4SiO2 composite film materials. In Figure 8, it can be seen that there is a first weight loss step from 150 to 260 °C, which is a crystalline water weight loss step of the TPHSg-4SiO2 phase and increases as the TPHSg-4SiO2 content increases. When the content of TPHSg-4SiO2 is 50%, the weight loss step increases significantly, caused firstly by the increase in water of crystallization due to the increased TPHS content, and secondly by the shift in the phase structure of the material. The transformation from island structures to  3.5. Thermogravimetric Analysis Figure 7 and Table 6 show the TG curves of pure PBAT and PBAT/TPHS g-4SiO2 composite film materials and Figure 8 shows the DTG curves of pure PBAT and PBAT/TPHS g-4SiO2 composite film materials. In Figure 8, it can be seen that there is a first weight loss step from 150 to 260 • C, which is a crystalline water weight loss step of the TPHS g-4SiO2 phase and increases as the TPHS g-4SiO2 content increases. When the content of TPHS g-4SiO2 is 50%, the weight loss step increases significantly, caused firstly by the increase in water of crystallization due to the increased TPHS content, and secondly by the shift in the phase structure of the material. The transformation from island structures to two-phase continuous structures is shown in the SEM characterization results. At low TPHS g-4SiO2 content, the crystalline water from TPHS g-4SiO2 needs to pass through the PBAT phase. However, with the increase of the TPHS g-4SiO2 content, the precipitation of the crystalline water no longer needs to pass through the PBAT phase and the precipitation capacity of the crystalline water increases, resulting in a significantly larger weight loss step for the crystalline water.

Conclusions
The blend of thermoplastic hydroxypropyl starch and PBAT with the addition of silica as reinforcing agent exhibits good mechanical properties, with a substantial increase in mechanical properties compared to the sample without the addition of nano-silica. Even with a thermoplastic hydroxypropyl starch content of 40%, the film has horizontal and vertical tensile strengths of 9.82 and 12.09 MPa, respectively, which meet the requirements for packaging film. Furthermore, at thermoplastic hydroxypropyl starch levels below 50%, the processing properties of the composites are similar to those of PBAT, enabling the preparation of composite films by blowing. The micrographs also show that the thermoplastic hydroxypropyl starch is homogeneously distributed in PBAT, while the thermoplastic hydroxypropyl starch which was reinforced by nano-silica is better dispersed in PBAT, and that the content below 40% does not affect the continu- The decomposition onset temperature of pure TPHS g-4SiO2 was 275.4 • C. After compounding with PBAT, the decomposition temperature of the starch phase increased and gradually decreased as the TPHS g-4SiO2 content increased. The decomposition peak of the starch phase gradually increases with the increase of the TPHS g-4SiO2 content, as shown in Figure 8. The decomposition onset temperature of pure PBAT was 400.7 • C. The addition of TPHS g-4SiO2 to the mix decreased the onset decomposition temperature of PBAT and showed a decreasing trend with the increase of the TPHS g-4SiO2 content.

Conclusions
The blend of thermoplastic hydroxypropyl starch and PBAT with the addition of silica as reinforcing agent exhibits good mechanical properties, with a substantial increase in mechanical properties compared to the sample without the addition of nano-silica. Even with a thermoplastic hydroxypropyl starch content of 40%, the film has horizontal and vertical tensile strengths of 9.82 and 12.09 MPa, respectively, which meet the requirements for packaging film. Furthermore, at thermoplastic hydroxypropyl starch levels below 50%, the processing properties of the composites are similar to those of PBAT, enabling the preparation of composite films by blowing. The micrographs also show that the thermoplastic hydroxypropyl starch is homogeneously distributed in PBAT, while the thermoplastic hydroxypropyl starch which was reinforced by nano-silica is better dispersed in PBAT, and that the content below 40% does not affect the continuous structure of the PBAT phase. Therefore, it is feasible to enhance the TPHS g-4SiO2 phase in PBAT/TPHS g-4SiO2 composite films by adding nano-silica, thus enabling the enhancement of the mechanical properties of the composite films, and the color of the composite films will be whiter after the addition of nano-silica. Our study provides an effective way to prepare PBAT-based composite films with high starch content.

Institutional Review Board Statement: Not applicable.
Data Availability Statement: All data included in this study are available upon request to the corresponding author.

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