Mechanical, Hydrophobic, and Barrier Properties of Nanocomposites of Modified Polypropylene Reinforced with Low-Content Attapulgite

Attapulgite (ATT) has never been used as a barrier additive in polypropylene (PP). As a filler, ATT should be added in high content to PP. However, that would result in increased costs. Moreover, the compatibility between ATT and the PP matrix is poor due to the lack of functional groups in PP. In this study, carboxylic groups were introduced to PP to form a modified polypropylene (MPP). ATT was purified, and a low content of it was added to MPP to prepare MPP/ATT nanocomposites. The analysis from FTIR indicated that ATT could react with MPP. According to the results of oxygen and water permeability tests, the barrier performance of the nanocomposite was optimal when the ATT content was 0.4%. This great improvement in barrier performance might be ascribed to the following three reasons: (1) The existence of ATT extended the penetration path of O2 or H2O molecules; (2) O2 or H2O molecules may be adsorbed and stored in the porous structure of ATT; (3) Most importantly, –COOH of MPP reacted with –OH on the surface of ATT, thereby the inner structure of the nanocomposite was denser, and it was less permeable to molecules. Therefore, nanocomposites prepared by adding ATT to MPP have excellent properties and low cost. They can be used as food packaging materials and for other related applications.


Introduction
Industrial technology has been continually developed. Alongside this development, the demand for polymers has increased [1,2]. One of the commonly used polymers is polypropylene (PP). Relative to other general-purpose plastics, PP is a colorless, odorless, nontoxic, and translucent solid substance [3]. It has the advantages of small density, excellent processability, strong mechanical properties, low grid, and a wide range of sources [4][5][6][7][8]. PP is widely used in various products such as automotive, electrical appliances, daily necessities and furniture, and packaging [9][10][11][12][13][14][15][16]. However, PP also has some weaknesses; for example, it has low strength and is easy to age. These limitations hamper its varied applications. Therefore, it should be appropriately modified and strengthened through ways such as copolymerization, grafting, blending, or filling [17][18][19].
it can improve the barrier performance of PP. At present, there is no relevant research on the use of ATT as a barrier additive for PP. Our present study introduced carboxylic acid groups to PP to form MPP to improve its interfacial compatibility with ATT and to improve the modification effect. The mechanical, thermal, and barrier properties, as well as the hydrophilicity, of the nanocomposites with varying low content of ATT (0-0.8%) were characterized, with the goal of determining the optimal amount of ATT that should be added. The results obtained from this present study would expand and enrich the application of nanocomposites.

Purified Attapulgite and Preparation of Nanocomposites
The purification method of ATT was the same as that in a previous study [22]. Figure  1 indicates the process of fabricating MPP/ATT nanocomposites, and the composition of the nanocomposites is shown in Table 1.

Fourier Transform Infrared Spectroscopy
The spectra of nanocomposites were measured using a Fourier transmission infrared spectrometer (Nicolet 6700 FTIR). The measurement range was 4000-400 cm −1 , and it was performed at a resolution of 1 cm −1 . The nanocomposites were formed into a powder, and then mixed with KBr and pressed into circular samples for testing.

Mechanical Properties
Samples of MPP and MPP/ATT nanocomposites were prepared following ASTM-D638 test standard and tested to determine the tensile properties by using a tensile testing machine (speed = 50 mm/min −1 ). Five to seven samples for each nanocomposite were tested for tensile properties, and the average value was calculated.

X-ray Diffraction
X-ray diffractometry was used. The instrument was from Bruker, Germany (D8 Advance). It was operated at a voltage of 40 KV.

Morphology Characterization
Scanning electron microscopy (SEM) was applied to obtain the morphology of the nanocomposites. The tensile fractured surface of all samples was scanned by SEM (Tescan, Czech Republic).

Thermal Analysis
Differential scanning calorimetry (DSC-200 F3 calorimeter) was from Netzsch, Germany. The nanocomposites were subjected to a second heating at a rate of 10 • C/min from room temperature to 180 • C and held at that high temperature for 5 min. Then, they were cooled down to room temperature at a rate of 10 • C/min to obtain crystallization peaks. The equation for calculating the MPP crystallinity was as follows: In Equation (1), Xc = degree of crystallinity, wt% = percentage of MPP in the sample, ∆H was the enthalpy of fusion for MPP and its nanocomposites, and ∆H 0 the enthalpy of fusion for 100% PP polymer [37].

Thermogravimetric Analysis
Thermal gravimetric analysis (TGA, Model HTG-1, Beijing Hengjiu Experimental Equipment Co., Ltd., Beijing, China) was applied to test the samples. The nanocomposites were heated from room temperature to 750 • C under nitrogen environment (flow rate = 70 mL/min) at a heating rate of 10 • C/min,

Water Vapor Barrier Properties
A water vapor permeability (WVP) tester was operated at 25 • C, and the humidity difference on both sides of the nanocomposites reached 90%.

Oxygen Barrier Properties
The oxygen transmission rate (OTR) in MPP and MPP/ATT nanocomposites was measured with a gas permeability meter (Labthink VAC-V2, Jinan, China). It was operated at 23 • C and 50% humidity.

Water Absorption
All nanocomposites were immersed in deionized water for 48 h. They were then weighed, and the water absorption was calculated as follows: In Equation (2), W A represented the water absorption, W was the initial weight of the nanocomposites, and W 0 the weight of the sample after soaking [38].

Contact Angle Test
A contact angle machine was used to evaluate contact angles (CA). First, all nanocomposites were dried in an oven at 110 • C for 12 h. Then, deionized water was dropped using a pipette onto the nanocomposite samples.

Elemental Content Analysis
Data on EDS of unpurified ATT and purified ATT are shown in Figure 2. Table 2 lists the elemental composition of both ATT. Purified ATT has a higher composition of C, but a slightly lower composition of each other elements. This may be caused by the removal of a large number of impurities from the unpurified ATT.

Water Absorption
All nanocomposites were immersed in deionized water for 48 h. They were then weighed, and the water absorption was calculated as follows: In Equation (2), WA represented the water absorption, W was the initial weight of the nanocomposites, and W0 the weight of the sample after soaking [38].

Contact Angle Test
A contact angle machine was used to evaluate contact angles (CA). First, all nanocomposites were dried in an oven at 110 °C for 12 h. Then, deionized water was dropped using a pipette onto the nanocomposite samples.

Elemental Content Analysis
Data on EDS of unpurified ATT and purified ATT are shown in Figure 2. Table 2 lists the elemental composition of both ATT. Purified ATT has a higher composition of C, but a slightly lower composition of each other elements. This may be caused by the removal of a large number of impurities from the unpurified ATT.     Figure 3 represents the FTIR spectra of unpurified ATT, purified ATT, MPP, and MPP 99.6 ATT 0.4 . In the FTIR of unpurified ATT, symmetrical and asymmetrical stretching vibration peaks in the 900-1100 cm −1 region refer to the silicon-oxygen bond. The vibration peak at about 3419 cm −1 denotes the silanol structure, indicating that ATT has a large number of hydroxyl groups [39]. Compared with unmodified ATT, purified ATT exhibits a higher intensity of absorption peak, which was probably caused by the removal of some impurities such as quartz. In the FTIR of MPP, the obvious peak that occurs in the band of about 3435 cm −1 corresponds to the hydroxyl group of MPP [40,41]. The characteristic peak near 1623 cm −1 is the bending vibration peak of -CH 2 -in the infrared spectrum of MPP 99.6 ATT 0.4 [42]. Symmetrical and asymmetrical telescopic vibration peaks in the 900-1100 cm −1 region are equivalent to the silicon-oxygen bond absorption peaks. In addition, a new feature peak is observed at 1747 cm −1 in the enlarged local plot of Figure 3b, and the characteristic peak is due to the C=O peak in the ester group [17]. The Polymers 2022, 14, 3696 6 of 16 characteristic peak is caused by the reaction between -OH on the ATT surface and -COOH on MPP. FTIR results show that ATT can react with MPP, and this increases the reinforcing effect of nanofillers on polymers [43].

Fourier Transform Infrared Spectra
higher intensity of absorption peak, which was probably caused by the removal of impurities such as quartz. In the FTIR of MPP, the obvious peak that occurs in the of about 3435 cm −1 corresponds to the hydroxyl group of MPP [40,41]. The characte peak near 1623 cm −1 is the bending vibration peak of -CH2-in the infrared spectru MPP99.6ATT0.4 [42]. Symmetrical and asymmetrical telescopic vibration peaks in the 1100 cm −1 region are equivalent to the silicon-oxygen bond absorption peaks. In add a new feature peak is observed at 1747 cm −1 in the enlarged local plot of Figure 3b, an characteristic peak is due to the C=O peak in the ester group [17]. The characteristic is caused by the reaction between -OH on the ATT surface and -COOH on MPP. results show that ATT can react with MPP, and this increases the reinforcing effect o ofillers on polymers [43].

Tensile Strength
The tensile properties of all samples with various amounts of purified ATT we tained. Figure 4 shows the difference in the tensile properties of MPP and MPP/ATT composites with different ATT content. Compared with the tensile strength of neat that of the MPP/ATT nanocomposites is remarkably enhanced. The tensile strength proved with an increase in the ATT content from 0 to 0.4%. The tensile strength re its maximum value when ATT is 0.4%, demonstrating that ATT could enhance the t properties of the polymer matrix. This may also be due to the reaction between COOH in MPP and the hydroxyl group in ATT, leading to improvement in the t strength of the nanocomposites [44,45]. However, when the nanofiller is ≥ 0.6%, the t strength decreases [46]. This may be due to the fact that ATT does not disperse eas the substrate, thereby aggregation is increased. The poor compatibility between the ofiller and MPP results in stress concentration in the nanocomposites and, in turn, creased mechanical strength [47,48].

Tensile Strength
The tensile properties of all samples with various amounts of purified ATT were obtained. Figure 4 shows the difference in the tensile properties of MPP and MPP/ATT nanocomposites with different ATT content. Compared with the tensile strength of neat MPP, that of the MPP/ATT nanocomposites is remarkably enhanced. The tensile strength is improved with an increase in the ATT content from 0 to 0.4%. The tensile strength reaches its maximum value when ATT is 0.4%, demonstrating that ATT could enhance the tensile properties of the polymer matrix. This may also be due to the reaction between the -COOH in MPP and the hydroxyl group in ATT, leading to improvement in the tensile strength of the nanocomposites [44,45]. However, when the nanofiller is ≥0.6%, the tensile strength decreases [46]. This may be due to the fact that ATT does not disperse easily in the substrate, thereby aggregation is increased. The poor compatibility between the nanofiller and MPP results in stress concentration in the nanocomposites and, in turn, in decreased mechanical strength [47,48].

X-ray Diffraction Patterns
Figure 5a displays XRD patterns for ATT before and after purification. The peak of purified ATT is higher and sharper, probably because of the great reduction in impurities. In Figure 5b, MPP has strong peaks around 14.3° and 17.2°. The characteristic peaks of the nanocomposite materials are hardly shifted, suggesting that adding purified ATT may not affect the crystal planes of MPP. There is no major change in the crystalline morphology

X-ray Diffraction Patterns
Figure 5a displays XRD patterns for ATT before and after purification. The peak of purified ATT is higher and sharper, probably because of the great reduction in impurities. In Figure 5b, MPP has strong peaks around 14.3 • and 17.2 • . The characteristic peaks of the nanocomposite materials are hardly shifted, suggesting that adding purified ATT may not affect the crystal planes of MPP. There is no major change in the crystalline morphology of MPP, showing that the compatibility between MPP and ATT is good [49]. Relative to MPP, the nanocomposites have increased crystallinity. Additionally, MPP 99.6 ATT 0.4 has the largest crystallinity. It might be ascribed to the heterogeneous nucleation of ATT that improves the crystallinity [50].

X-ray Diffraction Patterns
Figure 5a displays XRD patterns for ATT before and after purification. The pe purified ATT is higher and sharper, probably because of the great reduction in impur In Figure 5b, MPP has strong peaks around 14.3° and 17.2°. The characteristic peaks o nanocomposite materials are hardly shifted, suggesting that adding purified ATT ma affect the crystal planes of MPP. There is no major change in the crystalline morpho of MPP, showing that the compatibility between MPP and ATT is good [49]. Relati MPP, the nanocomposites have increased crystallinity. Additionally, MPP99.6ATT0.4 ha largest crystallinity. It might be ascribed to the heterogeneous nucleation of ATT tha proves the crystallinity [50].  Figure 6 shows the morphological SEM images for the tensile section of MPP MPP/ATT nanocomposites. It is observed that the tensile section morphology of the n composite with 0.4% ATT is very similar to that of MPP and MPP with an ATT conte 0.2%. This may be because both 0.2 and 0.4% ATT can be uniformly distributed in M and nanomaterials with a high specific surface area can have a good interaction wit matrix despite tensile fracture. This is consistent with the results of tensile properties  Figure 6 shows the morphological SEM images for the tensile section of MPP and MPP/ATT nanocomposites. It is observed that the tensile section morphology of the nanocomposite with 0.4% ATT is very similar to that of MPP and MPP with an ATT content of 0.2%. This may be because both 0.2 and 0.4% ATT can be uniformly distributed in MPP, and nanomaterials with a high specific surface area can have a good interaction with the matrix despite tensile fracture. This is consistent with the results of tensile properties. The two compositions of 0.2 and 0.4% ATT greatly enhance the tensile strength of the nanocomposites. Due to the tight connection between ATT and MPP, the fracture surface appears to have a structure of uneven surface [51]. However, the addition of ATT ≥ 0.6 results in an uneven distribution of nanoparticles. This may be because of the poor interfacial adhesion between the nanofillers and the MPP matrix. The result is a decrease in the mechanical properties of MPP/ATT, and the tensile section of the nanocomposite shows a unidirectional fiber-like structure [52,53]. It may be a more brittle fracture surface caused by the uneven dispersion of nanofillers.  Table 3. Tm and Xc of neat MPP are 150.3 • C and 43.40%. The nanocomposites containing ATT show a decreasing trend of Tm with increasing ATT content. The reason for the slight decrease in Tm may be due to that ATT makes the crystal size of MPP smaller, so that the nanocomposite melts early during the heating process [54]. On the other hand, Xc for nanocomposite materials reveals an increasing trend. It might be ascribed to the heterogeneous nucleation of ATT that improves the crystallinity. Figure 7 shows that the crystallization peak for the MPP nanocomposite materials becomes sharp, indicating that the existence of ATT reduces the crystallization time and greatly improves the crystallization rate.

Thermal Stability Analysis
composites. Due to the tight connection between ATT and MPP, the fracture surface appears to have a structure of uneven surface [51]. However, the addition of ATT ≥ 0.6 results in an uneven distribution of nanoparticles. This may be because of the poor interfacial adhesion between the nanofillers and the MPP matrix. The result is a decrease in the mechanical properties of MPP/ATT, and the tensile section of the nanocomposite shows a unidirectional fiber-like structure [52,53]. It may be a more brittle fracture surface caused by the uneven dispersion of nanofillers.   Table 3. Tm and Xc of neat MPP are 150.3 °C and 43.40%. The nanocomposites containing ATT show a decreasing trend of Tm with increasing ATT content. The reason for the slight decrease in Tm may be due to that ATT makes the crystal size of MPP smaller, so that the nanocomposite melts early during the heating process [54]. On the other hand, Xc for nanocomposite materials reveals an increasing trend. It might be ascribed to the heterogeneous nucleation of ATT that improves the crystallinity. Figure 7 shows that the crystallization peak for the MPP nanocomposite materials becomes sharp, indicating that the existence of ATT reduces the crystallization time and greatly improves the crystallization rate.   Figure 8 shows the TGA and DTG curves for MPP and its nanocomposites. Table 4 lists TGA and DTG data taken from Figure 8. Tonset pertains to the beginning of sample degradation, while Tend to the ending of sample degradation, and Td indicates the peaks from DTG. The data clearly shows that adding ATT could increase the Tonset, Tend, and Td of the nanocomposites. This can be primarily attributed to the excellent heat resistance of ATT and the dense structure of the nanocomposites. Alternatively, carboxyl from MPP and hydroxyl from ATT undergo chemical reactions. Therefore, more energy is required for the decomposition during the heating process, so the thermal stability of the nanocomposites increases [55]. When the ATT content is ≥0.6%, the Td of the samples is reduced, which may be due to the ATT agglomeration in the MPP matrix. Incompatibility between the matrix and the nanofillers sets in and, in turn, affects thermal degradation [56,57].    Figure 8 shows the TGA and DTG curves for MPP and its nanocomposites. Table 4 lists TGA and DTG data taken from Figure 8. T onset pertains to the beginning of sample degradation, while T end to the ending of sample degradation, and T d indicates the peaks from DTG. The data clearly shows that adding ATT could increase the T onset , T end , and T d of the nanocomposites. This can be primarily attributed to the excellent heat resistance of ATT and the dense structure of the nanocomposites. Alternatively, carboxyl from MPP and hydroxyl from ATT undergo chemical reactions. Therefore, more energy is required for the decomposition during the heating process, so the thermal stability of the nanocomposites increases [55]. When the ATT content is ≥0.6%, the T d of the samples is reduced, which may be due to the ATT agglomeration in the MPP matrix. Incompatibility between the matrix and the nanofillers sets in and, in turn, affects thermal degradation [56,57].  Figure 9 shows the variation in water permeability for MPP and MPP/ATT nanocomposite materials. With the addition of ATT nanomaterials, the water permeability coefficient tends to decrease first and then increase. When the ATT content is 0.4%, the water vapor permeability coefficient is the lowest. The reason for the decrease in the permeability coefficient may be because the addition of ATT increases the permeability path for the water molecules [58,59]. Another reason is that when MPP reacts with ATT, the internal structure of the nanocomposite becomes tight, causing more difficulty for the water molecules to penetrate. When the ATT addition is between 0.6 and 0.8%, the water permeability coefficient of the nanocomposites increases, which may be due to the excessive addition of ATT. Consequently, the dispersion of ATT in the matrix becomes poor, and agglomeration of ATT occurs, resulting in defects in the interior of the nanocomposites, allowing the water molecules to pass through the gap.   Figure 9 shows the variation in water permeability for MPP and MPP/ATT nanocomposite materials. With the addition of ATT nanomaterials, the water permeability coefficient tends to decrease first and then increase. When the ATT content is 0.4%, the water vapor permeability coefficient is the lowest. The reason for the decrease in the permeability coefficient may be because the addition of ATT increases the permeability path for the water molecules [58,59]. Another reason is that when MPP reacts with ATT, the internal structure of the nanocomposite becomes tight, causing more difficulty for the water molecules to penetrate. When the ATT addition is between 0.6 and 0.8%, the water permeability coefficient of the nanocomposites increases, which may be due to the excessive addition of ATT. Consequently, the dispersion of ATT in the matrix becomes poor, and agglomeration of ATT occurs, resulting in defects in the interior of the nanocomposites, allowing the water molecules to pass through the gap. Polymers 2022, 14, x FOR PEER REVIEW 11 of 17 Figure 9. Variation in water permeability coefficients for MPP and MPP/ATT nanocomposite materials.

Analysis of Oxygen Barrier Performance
We see in Figure 10 that the oxygen permeability coefficient (OPC) for MPP is 3.183 × 10 -10 cm 3 cm cm −2 s −1 Pa −1 . As the content of ATT increases, the oxygen permeability shows a trend of first decreasing and then increasing. The OPC of all nanocomposites is lower than that of pure MPP. When the added ATT nanofiller is 0.4%, OPC reaches the minimum value. However, when the nanofiller is ≥0.6%, OPC reverts to increasing. The reason is that the high ATT content causes an uneven dispersion and incompatible defects. Therefore, the arrangement of ATT in the matrix becomes chaotic, and the structure of the nanocomposites is destroyed [53].

Analysis of Oxygen Barrier Performance
We see in Figure 10 that the oxygen permeability coefficient (OPC) for MPP is 3.183 × 10 −10 cm 3 cm cm −2 s −1 Pa −1 . As the content of ATT increases, the oxygen permeability shows a trend of first decreasing and then increasing. The OPC of all nanocomposites is lower than that of pure MPP. When the added ATT nanofiller is 0.4%, OPC reaches the minimum value. However, when the nanofiller is ≥0.6%, OPC reverts to increasing. The reason is that the high ATT content causes an uneven dispersion and incompatible defects. Therefore, the arrangement of ATT in the matrix becomes chaotic, and the structure of the nanocomposites is destroyed [53].

Analysis of Oxygen Barrier Performance
We see in Figure 10 that the oxygen permeability coefficient (OPC) for MPP is 3.183 × 10 -10 cm 3 cm cm −2 s −1 Pa −1 . As the content of ATT increases, the oxygen permeability shows a trend of first decreasing and then increasing. The OPC of all nanocomposites is lower than that of pure MPP. When the added ATT nanofiller is 0.4%, OPC reaches the minimum value. However, when the nanofiller is ≥0.6%, OPC reverts to increasing. The reason is that the high ATT content causes an uneven dispersion and incompatible defects. Therefore, the arrangement of ATT in the matrix becomes chaotic, and the structure of the nanocomposites is destroyed [53].  The trend in Figure 10 is very similar to the results of water permeability coefficients in Figure 9. ATT plays an important role in the oxygen and water vapor barrier properties of MPP. This may be due to the following three reasons: (1) The addition of ATT nanomaterials would extend the path for the passage of water molecules; (2) ATT has a porous structure, which can adsorb water or oxygen molecules into the internal pores of ATT; (3) -COOH of MPP reacts with -OH on the surface of ATT. The MPP and ATT have good interfacial compatibility, which makes the internal structure of the nanocomposite material more compact, and the extent of the permeation of H 2 O or O 2 is less [60]. Figure 11 shows the path of H 2 O or O 2 molecules through the nanocomposite. Solid dots represent ATT dispersed in the nanocomposite. O 2 or H 2 O molecules would directly pass through a sample of MPP (Figure 11a). The path of water or oxygen molecules through the nanocomposites may be described in two ways. One way is that the molecules may not pass through the ATT nanofillers and move around them (Figure 11b). Another way is that the molecules may penetrate and linger within ATT and eventually exit from there ( Figure 11c). In the nanocomposite, the -COOH in MPP reacts with -OH on the ATT surface, and then the MPP molecular chains become more tightly connected, causing a reduction in the transmittance of H 2 O or O 2 molecules (Figure 11d).
The trend in Figure 10 is very similar to the results of water permeability coefficients in Figure 9. ATT plays an important role in the oxygen and water vapor barrier properties of MPP. This may be due to the following three reasons: (1) The addition of ATT nanomaterials would extend the path for the passage of water molecules; (2) ATT has a porous structure, which can adsorb water or oxygen molecules into the internal pores of ATT; (3) -COOH of MPP reacts with -OH on the surface of ATT. The MPP and ATT have good interfacial compatibility, which makes the internal structure of the nanocomposite material more compact, and the extent of the permeation of H2O or O2 is less [60]. Figure 11 shows the path of H2O or O2 molecules through the nanocomposite. Solid dots represent ATT dispersed in the nanocomposite. O2 or H2O molecules would directly pass through a sample of MPP (Figure 11a). The path of water or oxygen molecules through the nanocomposites may be described in two ways. One way is that the molecules may not pass through the ATT nanofillers and move around them (Figure 11b). Another way is that the molecules may penetrate and linger within ATT and eventually exit from there (Figure 11c). In the nanocomposite, the -COOH in MPP reacts with -OH on the ATT surface, and then the MPP molecular chains become more tightly connected, causing a reduction in the transmittance of H2O or O2 molecules (Figure 11d).  Figure 12 presents data on the water absorption in MPP/ATT nanocomposites. The results indicate that the water absorption rate for MPP is high. With increasing ATT con-  Figure 12 presents data on the water absorption in MPP/ATT nanocomposites. The results indicate that the water absorption rate for MPP is high. With increasing ATT content, the nanocomposite materials show a trend of decreasing water absorption rates. ATT has a good water absorption performance owing to its porous and rod-like structure. However, when the ATT-OH reacts with the MPP-COOH, the nanocomposite forms a tighter mesh structure. The MPP tightly wraps the water-absorbing ATT inside, and this reduces the water absorption of the nanocomposite.  Figure 13 shows the results of contact angle tests, in wh to touch the surface of MPP and MPP/ATT nanocomposite With an increase in the ATT content, the contact angles of crease and then decrease. When the ATT content is 0.4%, the This may be because ATT nanomaterials are widely and uni trix. As such, the nanomaterials are more compact in structu state. This is in agreement with the results of water permeab permeability tests. When ATT > 0.4%, it shows an uneven d structure of the nanocomposites has more defects, and the wa to enter the nanocomposites. In addition, ATT itself is a poro and when the ATT content is too much, the hydrophilicity increase. The results show that the contact angle of each na  Figure 13 shows the results of contact angle tests, in which water droplets are made to touch the surface of MPP and MPP/ATT nanocomposite samples for 2, 10, and 60 s. With an increase in the ATT content, the contact angles of the nanocomposites first increase and then decrease. When the ATT content is 0.4%, the contact angle is the largest. This may be because ATT nanomaterials are widely and uniformly dispersed in the matrix. As such, the nanomaterials are more compact in structure and show a hydrophobic state. This is in agreement with the results of water permeability coefficients and oxygen permeability tests. When ATT > 0.4%, it shows an uneven dispersion in the matrix. The structure of the nanocomposites has more defects, and the water molecules are more likely to enter the nanocomposites. In addition, ATT itself is a porous water-absorbing material, and when the ATT content is too much, the hydrophilicity of the nanocomposites may increase. The results show that the contact angle of each nanocomposite is greater than that of MPP. The results show that the hydrophobicity of the nanocomposite can be improved with the optimal amount of ATT. permeability tests. When ATT > 0.4%, it shows an uneven dispersion in the matrix. The structure of the nanocomposites has more defects, and the water molecules are more likely to enter the nanocomposites. In addition, ATT itself is a porous water-absorbing material, and when the ATT content is too much, the hydrophilicity of the nanocomposites may increase. The results show that the contact angle of each nanocomposite is greater than that of MPP. The results show that the hydrophobicity of the nanocomposite can be improved with the optimal amount of ATT. According to the analysis of data on the contact angle, barrier properties, and tensile properties, incorporating 0.4% ATT into MPP can make the nanocomposite film have the most compact structure, the highest hydrophobicity, and the best tensile strength. This nanocomposite film with the optimum amount of added ATT has the potential possibilities to be used as a packaging material.

Conclusions
The introduction of ATT significantly improved the performance of MPP. The presence of ATT improved the barrier efficiency of the nanocomposite. Not only ATT could extend the path for oxygen or water molecules in the nanocomposite, but also ATT itself could hold the molecules within its storage for some time. Moreover, MPP could have a chemical reaction with ATT, which would make its internal structure more compact. The results showed that when the ATT content was 0.4%, the nanocomposite demonstrated the best mechanical, thermal, and barrier properties. Hence, it has potential applications and can be further explored in many fields.