Four-needle zinc oxide whisker (T-ZnOw) incorporated into microcrystalline cellulose/maleic anhydride grafted polypropylene/random copolymer polypropylene (MCC/PP-g-MA/rPP) composite was prepared by melt blending. 5 wt% PP-g-MA was used as a coupling agent to improve the interfacial compatibility between fillers and rPP. The effect of T-ZnOw on MCC/PP-g-MA/rPP composite was investigated by mechanical testing, thermogravimetric analysis (TGA), differential scanning calorimetry (DSC), and scanning electron microscopy (SEM). Addition of T-ZnOw enhanced the mechanical properties of composites with tensile and flexural strengths increasing by 10% and 6%, respectively. SEM studies showed an improvement in the compatibility of fracture surfaces, which was evident from the absence of gaps between fillers and rPP. Additionally, initial thermal decomposition temperature and maximum weight loss temperature of T-ZnOw/MCC/PP-g-MA/rPP composite were both higher than those of MCC/PP-g-MA/rPP composite. Thermal degradation kinetics suggested that T-ZnOw has a weak catalytic effect on MCC, resulting in the early degradation of MCC and adhesion to the surface of rPP. Because of the presence of inorganic whiskers, the remaining weight percent was more than that of other composites at the end of the reaction. Crystallization temperature of the T-ZnOw/MCC/PP-g-MA/rPP composite was almost 3~5°C higher than that of MCC/PP-g-MA/rPP composite and close to the crystallization temperature of pure rPP.

1. Introduction

Polypropylene (PP) has been widely used for its high thermal stability, low density, low-cost, and recyclability [14]. However, PP suffers from insufficient rigidity at high temperatures and high brittleness at low temperatures. These shortcomings are typically overcome by methods like filling, blending, and reinforcing modification [59]. Among these approaches, filling modification is the most common method. In previous researches, fillers such as talc and calcium carbonate have been used to modify PP [1015]. Recently, natural cellulose has been used as filler due to not only ease of availability, but also being biodegradable and environment-friendly. Natural cellulose is widely used as reinforcement, like cotton, coconut shell, bagasse, hemp, and wood flour [1623]. In addition to natural cellulose, microcrystalline cellulose (MCC) has also been widely applied in polymer reinforcement, owing to its large length diameter ratio and biodegradability. MCC also has the advantages of high elastic modulus, high rigidity, high crystallinity, and high mechanical properties like strength. Due to these properties, it has been used to prepare low-cost polymer composites which have high strength [2427]. Inorganic whiskers, including zinc oxide, titanates, magnesium oxysulfate, and calcium sulfate, have also been used as reinforcement to improve the properties of thermoplastic polymers [2833]. For example, four-needle zinc oxide whisker (T-ZnOw) is widely used for its unique three-dimensional structure and bacteriostatic, antistatic, and abrasion resistance properties [3437]. Due to the structural feature of T-ZnOw, it has been used to prepare composites with isotropy rather than anisotropy [38]. PP used in the previous studies was mostly isotactic polypropylene (iPP) or recycled waste polypropylene (r-PP). This PP generally has a high processing temperature, which would decompose cellulose. Therefore, in this paper, low-melting random copolymer polypropylene (rPP) is studied by filling, in order to prevent the decomposition of cellulose.

Mixing or blending of MCC/T-ZnOw and rPP can lead to inhomogeneity and incompatibility problems. Hence, maleic anhydride grafted polypropylene (PP-g-MA) usually serves as a coupling agent. Since there are many polyhydroxy groups around the surface of MCC and T-ZnOw, they impart a polar nature to MCC and T-ZnOw. Thermoplastic polymers such as rPP are typically nonpolar in nature. In contrast, PP-g-MA can form a covalent bond with the hydroxyl groups of MCC or T-ZnOw and the nonpolar group of rPP, thus improving the compatibility of composites [39, 40].

In this work, T-ZnOw/MCC/PP-g-MA/rPP composite was prepared for the first time and obtained by melt blending. It was proved that mechanical properties and thermal behavior of T-ZnOw mixed with MCC as fillers in rPP based composites determine the optimal T-ZnOw mixing fraction. The prepared composite was characterized for mechanical properties by RGT-20A mechanical tester, morphological properties by SEM, and thermal behaviors by TGA and DSC.

2. Experimental

2.1. Materials

Random copolymer polypropylene (rPP) grade FL7632L supplied by Polyolefins Co., Ltd., Singapore, with a melt flow rate (MFR) of 7 g·(10 min)−1 and a density of 0.9 g·cm−3. rPP was made of propene and ethane. Microcrystalline cellulose (MCC) grade 170218A was supplied by Tianli Pharmaceutical Excipient Company, Qufu, China, with an average diameter of 25 μm. Four-needle zinc oxide whiskers (T-ZnOw) were provided by Chengdu Crystal Technology Co., Ltd., China. The compatibilizer, maleic anhydride grafted polypropylene (PP-g-MA) code P613, was supplied by DuPont, USA, with a density of 0.903 g·cm−3.

2.2. Preparation of Composites

Firstly, rPP, PP-g-MA, MCC, and T-ZnOw were dried in an oven for 4 hours at 80°C and 105°C, respectively. All the raw materials were dried to minimize the moisture content. Then the raw materials of rPP, MCC, T-ZnOw, and PP-g-MA were mixed in the torque rheometer (RM-200C, Harbin Hapro Electrical Technology Co., Ltd., China). Both compositions of composites had been listed in Table 1. All the blends were mixed in the torque rheometer for 10 min with the speed of 50 r·min−1 and then pressed into 4 mm thick sheet by flat press. Finally, all samples were cut by a saw and the size was 80 mm × 10 mm × 4 mm (length × width × thickness) for experiment. Both processing and the flat press temperatures were 165°C.

2.3. Mechanical Properties

The tensile strength was measured by a RGT-20A mechanical tester (Shenzhen Reger Instrument Co., Ltd., China) at a speed of 10 mm·min−1 according to the standard ASTM D638. The flexural strength was measured by the same mechanical tester at a strain rate of 2 mm·min−1 followed by ASTM D790 method.

The notched Izod impact strengths were measured with a XJC-25D impact tester (Chengde Tester Machine Co., Ltd., China) under ASTM D256 method and the maximum impact energy was 1 J. All samples were prefabricated with a notch of about 2 mm before testing.

All mechanical specimens were balanced at 23 ± 2°C for 48 hours before testing and all tests were measured at this temperature. Each sample was measured five times to obtain an average value.

The stress-strain curves of composites were tested by a Linkam TST350 tensile hot stage (Linkam Scientific Instruments, Ltd., UK). The sizes of samples were 30 mm × 10 mm × 0.5 mm (length × width × thickness). The test speed was 10 μm·s−1 and measured at room temperature. The tensile data were collected and analyzed with the Linksys 32 software. The stress and strain in this study are both engineering stress and strain obtained from the tensile hot stage.

2.4. Density Determination

Density was measured by ASTM D 1895 standard [41]. The density of composites was calculated by the following formula:

wherem is the mass of fiber/matrix;V is the volume of fiber/matrix.

2.5. Void Content of Composites

For determining the voids of hybrid composites, ASTM-D-2734-70 method was used [42]. The void content was determined by the following formula, calculated by the theoretical and experimental density of the composites [4143]:


where is the mass ratio of resin in composite; is the density of the resin matrix; is the mass ratio of reinforcement in composite; is the density of the reinforcement; is the theoretical density of composite; is the experimental density of composite.

2.6. Scanning Electron Microscopy

The morphologies of composites were investigated by scanning electron microscopy (SEM) with a JSM-7500F SEM (Japan Electronics Co., Ltd.) at an accelerating voltage of 5 kV. The samples were quenched in liquid nitrogen and plated with gold on the fracture surface before SEM observations.

2.7. Thermogravimetric Analysis

Thermal behavior was measured using a thermogravimetric analyzer instrument (PerkinElmer, Pyris 1, Inc., USA) with a temperature from 50 to 800°C at a heating rate of 10°C·min−1 in nitrogen atmosphere. The samples of thermal degradation behavior at a heating rate of 5, 10, 20, 30, and 50°C·min−1, respectively. About 5~8 mg of each sample was used for analysis.

2.8. Differential Scanning Calorimetry

The samples were weighted with a range of 3~5 mg, sealed in aluminum pans, and then tested by the differential scanning calorimeter (PerkinElmer, Pyris Diamond, USA) in nitrogen atmosphere. For nonisothermal crystallization, the samples were first heated from -20°C to 200°C at a heating rate of 20°C·min−1, then maintained at 200°C for 5 mins to eliminate any thermal history, and finally cooled to -20°C at various cooling rates of 10, 20, 30, 40, and 50°C·min−1, respectively. Finally, the samples were heated from -20°C to 200°C with a heating rate of 20°C·min−1.

3. Results and Discussion

3.1. Mechanical Properties
3.1.1. Mechanical Properties of MCC/rPP Composite with or without PP-g-MA

Mechanical properties of MCC/PP-g-MA/rPP composite and MCC/rPP composite are compared in Figures 1(a)1(d). A significant improvement can be observed in the mechanical properties of MCC/PP-g-MA/rPP composite. The increase of tensile strength was due to maleic anhydride groups reacting with the hydroxyl groups of microcrystalline cellulose [44], thereby decreasing the agglomeration of cellulose and PP-g-MA. In this way, MCC can be entangled and dispersed in rPP matrix. This result has also been confirmed by SEM. The flexural strength and flexural modulus of blends increased with the presence of filler in matrix because of the high rigidity of fillers. In addition, the stress transmission between the matrix resin and fibers improved, which was consistent with the results of previous reports [4547].

From the stress-strain curves (Figure 2(a)), it is evident that the fracture mode of the composite changed from ductile fracture to brittle fracture, in the presence of fillers. The fillers also enhanced the rigidity of the matrix and decreased its toughness. The decrease in elongation at break was mainly affected by fillers [48]. In addition, the tensile modulus had an obvious increase (Figure 1) and its changes were higher than the expected values. Since cellulose has a high modulus, the interaction of maleic anhydride groups grafted onto PP chains with -OH groups of cellulose increases the adhesion between cellulose and matrix. When MCC content was 40 wt%, the tensile modulus of the composite exhibited a maximum value. It can be seen from Figure 1 that with high loadings the mechanical properties of the composite still showed good performances. For example, when the MCC loading was 60 wt%, the tensile strength of the composite was 25.59 MPa which was similar to rPP (27.78 MPa). The flexural strength was 48.39 MPa and improved by 54% as compared to pure rPP (31.23 MPa).

In the impact test, the presence of PP-g-MA could effectively resist the crack propagation due to higher interfacial adhesion. The impact strength increased along with the increase in fiber content. However, the trend of impact strength was increased firstly and then decreased, since the impact properties of fibers were lower than rPP. Filling more MCC tends to increase stress concentration of the materials, making the cracks more prominent. However, from the overall trend of mechanical properties in Figure 1, it could be seen that the mechanical properties of the composite with 60 wt% MCC were relatively stable. Since MCC is inexpensive, large filling could save cost without affecting the performance of the composite. Besides, MCC is biodegradable, which makes it more economical, environment-friendly, and useful as compared to pure PP. Therefore, MCC/PP-g-MA/rPP composite with mass ratio of 60/5/35 was used in following experiments.

3.1.2. Mechanical Properties of MCC/PP-g-MA/rPP Composite with T-ZnOw

Mechanical properties of MCC/PP-g-MA/rPP composite with T-ZnOw as additive are shown in Figures 2(b)2(e), where they increased initially and then decreased with the increase of whisker fraction. When T-ZnOw content was 5 wt%, composite generally showed relatively good performance, as the optimal amount of T-ZnOw had enhanced toughening effect on rPP, and the compatibilizer PP-g-MA had improved the interfacial compatibility between fillers and the matrix. More importantly, an appropriate amount of T-ZnOw has a “nail” effect on the composite [49], and its three-dimensional structural features could act as a framework that could disperse the stress transmitted by the matrix resin, thereby hindering the formation of stress concentration points. Therefore, these two reinforcement fillers improved the mechanical properties of the composites as confirmed in Figure 2. On the other hand, due to the unique spatial three-dimensional structure of T-ZnOw, the impact energy of the composite could be absorbed. With further increase of the T-ZnOw, the mechanical properties of the composite showed a decreasing trend. This could be explained by the increasing of internal defects due to the high content of whiskers. Under external force, these defects promoted crack growth. Besides, the presence of T-ZnOw could promote an increase in crystal size resulting in a decrease in mechanical properties. More importantly, when the content of T-ZnOw was higher, the fracture mode of the material changed from ductile fracture to brittle fracture and led to a reduction in mechanical properties [50]. Therefore, adding 5 wt% T-ZnOw as reinforcing agent into MCC/PP-g-MA/rPP composite was selected for best performance.

3.2. Density and Void Content of Composites

The theoretical and experimental densities of composites were shown in Table 2. In the MCC/PP-g-MA/rPP composites, it is clearly evident that the density of the composite is increasing with the increase of the MCC content. It is understandable as the specific gravity of matrix (0.900 g·cm−3) is less than MCC (1.244 g·cm−3). However, the density of T-ZnOw/MCC/PP-g-MA/rPP composites is decreasing with the increase of T-ZnOw content, as the density of T-ZnOw is extremely low (0.2 g·cm−3).

The void content is the difference of theoretical and practical density of composites. During impregnating the fibers into the matrix or manufacturing the fiber reinforced composites, the trapped air or other volatiles exist in composites and make the void space. The voids were caused in this way, and this had been confirmed by some researchers [51, 52]. The void contents (%) of composites were presented in Table 2. It can be seen that the void content of composites increased with the increase of fillers. And the presence of the void in composites would reduce the mechanical and physical properties of composites [43].

In the MCC/PP-g-MA/rPP composites, the content of voids increased with the increase of MCC. When adding 60 wt% MCC, the void content was 7.83%. The little void indicated that dispersion of MCC in matrix is well and the PP-g-MA still acts as compatibilizer. Foremost and little voids have little effect on the mechanical properties of composites.

In the T-ZnOw/MCC/PP-g-MA/rPP composite, the void content of the composite increases with the addition of T-ZnOw. Because of the fluffy morphology of T-ZnOw, much air would be trapped in the composite and form a gap during the manucaption of composites. When adding 5 wt% T-ZnOw, the void content of the composite was 19.13%. When little T-ZnOw was added in composites, the unique spatial structure of T-ZnOw could not be exhibited in the material. But when much T-ZnOw is added, the crystallization size of the matrix would increase and weaken the mechanical properties of the composite. Therefore, MCC/PP-g-MA/rPP composites would have high mechanical properties after adding 5 wt% T-ZnOw to it.

3.3. Morphological Properties

Figure 3 shows the SEM micrographs of the fracture surfaces of rPP based composites, with Figures 3(a) and 3(b) showing the microstructures of 5 wt% PP-g-MA/rPP composite. It is evident that the surface was very smooth after adding compatibilizer which indicated that the PP chains in PP-g-MA had been crosslinked with the matrix resin. The surface morphologies of MCC/rPP composite are shown in Figures 3(c) and 3(d), where obvious boundaries and gaps can be observed between MCC and rPP. From the cross-section it is observed that fibers were pulled out, which indicates poor adhesion between the filler and the matrix along with low compatibility.

Figures 3(e) and 3(f) show the SEM micrographs of MCC/rPP composite with 5 wt% PP-g-MA. MCC at the cross-section was tightly bonded to matrix with no fiber pull-out. This is because most of the MCC was embedded in the matrix resin and cellulose had been torn at the cross-section. This is attributed to PP-g-MA in the composite, which improved the adhesion and interface compatibility between the two phases. This result has been further corroborated in mechanical properties of MCC/PP-g-MA/rPP composite. Figures 3(g) and 3(h) show microscopic morphologies of 5 wt%-T-ZnOw/PP-g-MA/rPP, where it is evident that whiskers were wrapped by the resin. This resulted in some white spots but no voids were formed. Since T-ZnOw plays a “skeleton” role in the composite, the stress could be transmitted from the matrix resin to whiskers after being subjected to an external force. When the composite is subjected to a force, whiskers can hinder the propagation of cracks and change the direction of expansion of the material. The phenomenon of crack deflection increased the area of crack so that more energy would be absorbed when the composite was broken. Moreover, T-ZnOw could be seen in the fracture surface as embedded in the matrix, which indicates that PP-g-MA also promoted the adhesion of the interface between the inorganic whisker T-ZnOw and rPP. The micrographs after adding 5 wt% T-ZnOw in MCC/PP-g-MA/rPP composites are shown in Figures 3(i) and 3(j), where it can be observed that the body of whiskers was wrapped by the matrix resin even though some whisker needles were pulled out. Some rough cavities also remained but there was no obvious interface gap in the section.

3.4. Thermal Properties

The thermal behavior of MCC/rPP, MCC/PP-g-MA/rPP, pure rPP, MCC, and T-ZnOw/MCC/PP-g-MA/rPP composites is shown in Figure 4. Table 3 lists the initial degradation temperatures (T-5%) and maximum weight loss temperatures (T1, T2) in the TGA and DTG curves. Only one decomposition process occurred in the pure rPP and MCC, as evident from the TGA curves. However, the TGA curves of rPP based composites showed two distinct decomposition stages. The first decomposition stage was in the range of 280-380°C, which is attributed to cellulose, whereas the second decomposition stage occurred between 400 and 480°C, mainly due to PP decomposition. T-5% and T2 of pure rPP were 363.3°C and 440.2°C, respectively. And the T-5% and T1 of MCC were 310.4°C and 367.0°C, respectively. It could be observed that the thermal stability of MCC was lower than rPP. However, when MCC was introduced into rPP, the T-5% and T2 of rPP/MCC composite were improved and the T1 was decreased. The initial decomposition temperature of the composite increased possibly due to the fiber protection function of PP although the interfacial bonding in MCC/rPP composite was a limiting factor. There were gaps around the fiber, which was beneficial to the diffusion of thermal decomposition products. This accelerated the decomposition rate of cellulose, so T1 of the composite shifted to lower temperature. With the inclusion of PP-g-MA, T-5% of the composite was decreased, which could be affected by unreacted PP-g-MA or anhydride groups resulting in the degradation of cellulose during the reaction [53].

With the addition of T-ZnOw, the initial decomposition temperature of T-ZnOw/MCC/PP-g-MA/rPP (5/55/5/35) composite and the heat decomposition temperature of rPP shifted to a higher temperature, as evident from Figure 4 and Table 3. The residue generated by the decomposition of cellulose existed on the surface of the matrix and played a hysteresis role in the decomposition process of the matrix. This resulted in an increase in the decomposition temperature of the matrix.

3.5. Thermal Degradation Kinetic Analysis

In order to further analyze the effect of fillers on the thermal degradation of polymers, thermal degradation kinetics studies were performed to analyze the following rPP based composites: pure rPP, MCC/rPP, MCC/PP-g-MA/rPP, and T-ZnOw/MCC/PP-g-MA/rPP composites. Flynn-Wall-Ozawa (OFW) equation (4) was used to analyze thermal degradation of composites. The activation energy (Ea) of composites was calculated from the temperature T corresponding to the different weight loss rate (α) at different heating rates (). According to OFW, from the 1n() versus 1000/T plot, the slope of the line (-Ea/R) yields the thermal degradation activation energy (Ea) of pure rPP and its composites, as listed in Table 4.where β is the heating rate, K·min−1;A refers to the prefactor, min−1;α is the composite material mass loss rate, %;T is the temperature corresponding to certain α of the composite material, K;R is gas constant.

ln()~1000/T (Figures 5(a)5(d)) showed a good linear relationship at different conversion rates, which indicates that the results of the activation energy calculated by this method are reliable.

It can be observed from the Table 4 that the variation of values of Ea of composites corresponds to the two parts of thermal decomposition behavior, which is consistent with the TGA analysis. The thermal degradation activation energy of MCC/rPP composite was higher than pure rPP. When α is in the range from 5% to 40%, the energy used for cellulose decomposition involved breaking the bond force, hydrogen bonding force between the molecules, and the Vander Waals force between cellulose and matrix. Hence, the energy consumption was high during the decomposition process. Ea of composites increased sharply when α was greater than 40%, which may be due to the hindrance of the residue formed by the degradation of the cellulose during the decomposition of the polymer matrix. The Ea values of MCC/PP-g-MA/rPP composite with incorporation of compatibilizer were significantly higher, because the addition of PP-g-MA made MCC disperse evenly in the matrix, thereby reducing the gap. The interaction between MCC and PP became stronger and increased the bond energy, as corroborated by SEM. Therefore, the decomposition of MCC is unfavorable at low temperature, which enhanced the barrier of heat transfer and increased thermal stability along with thermal degradation activation energy of the composite. After adding 5 wt% T-ZnOw in MCC/PP-g-MA/rPP composite, the activation energy of the composite was slightly reduced due to low density of T-ZnOw. It was the reason for the poor heat insulation ability of T-ZnOw. The thermal degradation of composites had a catalytic effect, mainly manifested in the thermal degradation of MCC. However, at high temperature MCC could dehydrate to carbon and adhere to the surface of the polymer to form a dense insulating carbon layer to reduce the amount of heat transferred from the outside to the inside. When was greater than 80%, a larger residual amount of the polymer remained due to the inorganic filler.

3.6. Nonisothermal Crystallization Kinetics Analysis

The crystallization curves of rPP and its composites with different cooling rates are shown in Figure 6. When the cooling rate increased, the crystallization temperature () of the rPP and its composites decreased and the crystallization peak broadened. This is because the activity of molecular chains weakened at low temperature. As a result, the samples could not crystallize completely leading to shortened crystallization time and low crystallization temperature.

It could be seen from Table 5 that of MCC/rPP composites was lower than that of the pure rPP at the same cooling rate. of MCC/rPP composites shifted to a low temperature because MCC is a polar organic filler, whereas rPP resin is nonpolar. Interface incompatibility occurred when the two phases were melted and blended without any treatment. MCC could hinder the movement of rPP molecular chains and hinder the crystallization of rPP, thereby causing the to shift to a low temperature. of MCC/PP-g-MA/rPP (107.9-120.3°C) was higher than MCC/rPP (106.1-118.2°C). The presence of PP-g-MA improved the interface compatibility of the two phases. Therefore, in the crystallization process of the sample, MCC promoted the crystallization of rPP and acted as a nucleating agent.

Owing to the unique three-dimensional structure of T-ZnOw in T-ZnOw/MCC/ PP-g-MA/rPP composite, the needles of T-ZnOw could be embedded in rPP matrix. A large steric hindrance of T-ZnOw could promote the interaction with MCC and form a greater resistance to the activity of rPP molecular chains. T-ZnOw also played a role in rPP as a nucleating agent to promote rPP to form crystallization around fillers. (113.0-123.5°C) of T-ZnOw/MCC/PP-g-MA/rPP composite was higher than that of the other two types of composites and close to that of pure rPP. Hence, the presence of T-ZnOw could promote PP molecular chains to have a faster crystallization rate at a relatively high temperature. With only a small amount of T-ZnOw, the crystallization process was promoted, thereby preventing oversizing of the crystal size. Relatively high mechanical properties of T-ZnOw/MCC/PP-g-MA/rPP composite in the mechanical properties analysis confirmed this result.

Nonisothermal crystallization could be analyzed according to the cooling rate dT/dt. The improved Irvar equation of the isothermal crystallization kinetics can be applied to determine the nonisothermal crystallization kinetic constant K and the Avrami exponent n. The Avrami equation is given by (5).

The kinetic constant is a key factor for the simulation of nonisothermal crystallization processes. In order to obtain results, the modified Avrami equation is adopted and the physical dimensions of the kinetic constants are set to [54, 55]. The change of the above equation to a linear form is given as

where is the relative crystallinity; K is the crystallization rate constant; and n is the Avrami index.

The relationship between X(t) and the crystallization time of rPP based composites at different cooling rates along with curves of vs. is shown in Figure 7. It can be observed from Figures 7(a) and 7(d) that the curves of relative X(t) and crystallization time both had an “S” shape, which became smooth with a drop of rate. The shape of curves became sharp when temperature was dropped, which indicated that the crystallization time decreased with a fast drop in the temperature. The parameter of t1/2 in Table 5 represented the time for the composite to complete 50% crystallization. The faster cooling rate worsened the activity of the polymer molecular chains, and the degree of crystal perfection was significantly reduced, which resulted in a shortened crystallization time.

It can be seen from Figures 7(a1)–7(d1) that rPP and its composites both had a good linear relationship between and at different cooling rates. The value of depended on the nucleation mechanism and the crystal growth mode, as well as the rate constant K containing the nucleation and growth parameters. Results indicate that after improving the parameters of Avrami equation, it could be applied to rPP and its composites for nonisothermal crystallization kinetics analysis.

4. Conclusion

In this study, T-ZnOw was filled into the MCC/PP-g-MA/rPP composite in order to improve the properties of the composite. Optimized composition of the composite for the best performance was T-ZnOw: MCC: PP-g-MA: rPP = 5:55:5:35. PP-g-MA improved the compatibility between fillers and matrix. Synergistic effect of T-ZnOw and MCC led to an enhancement of the mechanical performances. Thermal analysis and thermal degradation activation energy suggest that T-ZnOw improved the initial degradation temperature and maximum weight loss temperature of the composite. Effect of T-ZnOw on the crystallization behavior of the composite could be clearly observed from the nonisothermal crystallization kinetics. The presence of T-ZnOw promoted the crystallization of the matrix at a relatively high temperature and MCC acted as a nucleating agent during the crystallization, which resulted in the increase of the crystallization rate of the composite.

Data Availability

The data used to support the findings of this study are available from the corresponding author upon request.

Conflicts of Interest

The authors declare that they have no conflicts of interest.