Poly(Acrylonitrile–Butadiene–Styrene) as a Special β-Nucleating Agent on the Toughness of Isotactic Polypropylene

The influence of poly(acrylonitrile–butadiene–styrene) (ABS) as a special β-nucleating agent on the impact and tensile properties of isotactic polypropylene (iPP) were investigated by dynamic rheological measurements, wide-angle X-ray diffraction (WAXD), differential scanning calorimetry (DSC), scanning electron microscopy (SEM), and mechanical properties tests. It is found that the β nucleation efficiency of ABS is closely related to its concentration, dispersibility, and molding method for the iPP/ABS blends. The content of β-crystal (Kβ) rises with the incorporation of ABS and shows a maximum with the introduction of 1% ABS for compression-molded blends and 2% ABS for injection-molded blends, respectively, which is followed by a decrease in Kβ. The addition of a small amount of ABS has a significant reinforcing and toughening effect on iPP. Compared with the compression-molded samples, the ABS dispersed phase in injection-molded samples has a smaller particle size and a larger specific surface area, which are favorable for stress transmission and higher β nucleation efficiency, and therefore, better tensile and impact properties can be expected.


Dynamic Rheological Properties
Dynamic rheological measurements were conducted in a rotational rheometer (MCR 102, Anton-Paar, Graz, Austria), using 25 mm parallel-plate fixtures with a constant gap setting of 0.9 mm. A nitrogen atmosphere was utilized to avoid thermal degradation. The storage modulus and complex viscosity were measured at 190 °C with respect to angular frequency, which was varied from 0.0398 to 628 rad/s in the linear viscoelastic region.

Differential Scanning Calorimetry (DSC)
Samples of about 8 mg were analyzed under nitrogen atmosphere by a differential scanning calorimeter (DSC 6000, Perkin Elmer, Boston, USA). Each sample was first heated to 210 °C and maintained for 3 min to ensure an identical thermal history, following by cooling at a rate of 10 °C/min. As soon as the temperature reached 100 °C, it was reheated to 210 °C at the same rate. The reason for cooling to 100 °C is to avoid β-to-α recrystallization [38,39].

Wide-Angle X-Ray Diffraction (WAXD)
The preparation of specimens for WAXD is illustrated in Figure 1. WAXD measurements of the core zone of the specimens were performed using a wide-angle X-ray diffractometer (D8 ADVANCE, BRUKER, Mannheim, Germany) with a Cu Ka radiation (λ=1.54 Å ). The data were collected from 5 to 35° (2θ) at a scan speed of 2°/min.

Dynamic Rheological Properties
Dynamic rheological measurements were conducted in a rotational rheometer (MCR 102, Anton-Paar, Graz, Austria), using 25 mm parallel-plate fixtures with a constant gap setting of 0.9 mm. A nitrogen atmosphere was utilized to avoid thermal degradation. The storage modulus and complex viscosity were measured at 190 • C with respect to angular frequency, which was varied from 0.0398 to 628 rad/s in the linear viscoelastic region.

Differential Scanning Calorimetry (DSC)
Samples of about 8 mg were analyzed under nitrogen atmosphere by a differential scanning calorimeter (DSC 6000, Perkin Elmer, Boston, USA). Each sample was first heated to 210 • C and maintained for 3 min to ensure an identical thermal history, following by cooling at a rate of 10 • C/min. As soon as the temperature reached 100 • C, it was reheated to 210 • C at the same rate. The reason for cooling to 100 • C is to avoid β-to-α recrystallization [38,39].

Wide-Angle X-Ray Diffraction (WAXD)
The preparation of specimens for WAXD is illustrated in Figure 1. WAXD measurements of the core zone of the specimens were performed using a wide-angle X-ray diffractometer (D8 ADVANCE, BRUKER, Mannheim, Germany) with a Cu Ka radiation (λ = 1.54 Å). The data were collected from 5 to 35 • (2θ) at a scan speed of 2 • /min.

Scanning Electron Microscopy (SEM)
Microscopic observation was realized using a field emission scanning electron microscope (SUPRA 55, Zeiss, Karlsruhe, Germany) with an accelerating voltage of 5 kV. The samples were cryofractured parallel to the molding direction. All the specimens were gold sputtered before observation. Calculation of diameter of ABS dispersed phase was fully described in reference [42].

Mechanical Properties Measurements
Tensile testing was performed using a universal testing machine (4302, Instron, Norfolk, USA) according to GB/T 1040-2006. The Izod notched impact strength was measured by using an impact tester (XJU-22, Chengde Testing Machine Co. Ltd., Chengde, China) according to GB/T 1843-2008. Figure 2 presents the results of storage modulus (G') and complex viscosity (η*) obtained for pure iPP and ABS with respect to angular frequency (ω) at 190 • C. Obviously, for iPP, the slope of G'-ω curve at the low-frequency region is close to 2, exhibiting typical terminal behavior. However, ABS shows a deviation from the terminal behavior, indicating the presence of a longer relaxation time. This kind of non-terminal behavior could be attributed to the two-phase structure of ABS. In contrast to iPP, the used ABS has higher complex viscosity in the tested angular frequency range. This is beneficial to the dispersion of ABS in iPP matrix.  (5) where Hα(111) and Hα(-131) express the heights of α-form diffraction peaks at (111) and (-131) crystal planes, respectively.

Scanning Electron Microscopy (SEM)
Microscopic observation was realized using a field emission scanning electron microscope (SUPRA 55, Zeiss, Karlsruhe, Germany) with an accelerating voltage of 5 kV. The samples were cryofractured parallel to the molding direction. All the specimens were gold sputtered before observation. Calculation of diameter of ABS dispersed phase was fully described in reference [42].

Mechanical Properties Measurements
Tensile testing was performed using a universal testing machine (4302, Instron, Norfolk, USA) according to GB/T 1040-2006. The Izod notched impact strength was measured by using an impact tester (XJU-22, Chengde Testing Machine Co. Ltd., Chengde, China) according to GB/T 1843-2008. Figure 2 presents the results of storage modulus (G') and complex viscosity (η*) obtained for pure iPP and ABS with respect to angular frequency (ω) at 190 °C. Obviously, for iPP, the slope of G'-ω curve at the low-frequency region is close to 2, exhibiting typical terminal behavior. However, ABS shows a deviation from the terminal behavior, indicating the presence of a longer relaxation time. This kind of non-terminal behavior could be attributed to the two-phase structure of ABS. In contrast to iPP, the used ABS has higher complex viscosity in the tested angular frequency range. This is beneficial to the dispersion of ABS in iPP matrix.  polymers with different viscosity, the viscosity of the blend should be lower than that of the two pure components due to the mutual repulsion of the macromolecular chains in the melts. However, the complex viscosity of the blends displayed an intermediate behavior between the pure components, implying that there was chain entanglement between iPP and ABS melts, which can be seen more clearly from the weighted relaxation spectra of the blends, as shown in Figure 4. With the increase in the ABS concentration, weighted relaxation spectrum presented an increasing trend in width, indicating more difficult relaxation for iPP resulting from the entanglement between iPP and ABS chains. Figure 2. Storage modulus (G') and complex viscosity (η * ) with respect to angular frequency (ω) for pure iPP and ABS. Figure 3 shows the results of complex viscosity with respect to angular frequency for the blends. It could be seen that the complex viscosity of all the blends fell off with the increasing angular frequency, similar to that of pure components. In general, if the blend consists of two completely immiscible polymers with different viscosity, the viscosity of the blend should be lower than that of the two pure components due to the mutual repulsion of the macromolecular chains in the melts. However, the complex viscosity of the blends displayed an intermediate behavior between the pure components, implying that there was chain entanglement between iPP and ABS melts, which can be seen more clearly from the weighted relaxation spectra of the blends, as shown in Figure 4. With the increase in the ABS concentration, weighted relaxation spectrum presented an increasing trend in width, indicating more difficult relaxation for iPP resulting from the entanglement between iPP and ABS chains.     Figure 5 presents the DSC curves of pure iPP and iPP/ABS blends on the first cooling (a) and the second heating scan (b), and the detailed crystallization and melting parameters are summarized in Table 1. It can be seen from the DSC curves that pure iPP shows one exothermic peak at 111.9 °C and one endothermic peak at 164.2 °C . For the iPP/ABS blends, the crystallization temperature of iPP increases from 111.9 to 116.1 °C with increasing ABS concentration on the first cooling scans, implying that ABS could perform the function of heterogeneous nucleation. On the second heating scans, the blends show two or three melting peaks. The first one appears at around 150 °C,  Storage modulus (G') and complex viscosity (η * ) with respect to angular frequency (ω) for pure iPP and ABS. Figure 3 shows the results of complex viscosity with respect to angular frequency for the blends. It could be seen that the complex viscosity of all the blends fell off with the increasing angular frequency, similar to that of pure components. In general, if the blend consists of two completely immiscible polymers with different viscosity, the viscosity of the blend should be lower than that of the two pure components due to the mutual repulsion of the macromolecular chains in the melts. However, the complex viscosity of the blends displayed an intermediate behavior between the pure components, implying that there was chain entanglement between iPP and ABS melts, which can be seen more clearly from the weighted relaxation spectra of the blends, as shown in Figure 4. With the increase in the ABS concentration, weighted relaxation spectrum presented an increasing trend in width, indicating more difficult relaxation for iPP resulting from the entanglement between iPP and ABS chains.     Figure 5 presents the DSC curves of pure iPP and iPP/ABS blends on the first cooling (a) and the second heating scan (b), and the detailed crystallization and melting parameters are summarized in Table 1. It can be seen from the DSC curves that pure iPP shows one exothermic peak at 111.9 °C and one endothermic peak at 164.2 °C . For the iPP/ABS blends, the crystallization temperature of iPP increases from 111.9 to 116.1 °C with increasing ABS concentration on the first cooling scans, implying that ABS could perform the function of heterogeneous nucleation. On the second heating scans, the blends show two or three melting peaks. The first one appears at around 150 °C,  Figure 5 presents the DSC curves of pure iPP and iPP/ABS blends on the first cooling (a) and the second heating scan (b), and the detailed crystallization and melting parameters are summarized in Table 1. It can be seen from the DSC curves that pure iPP shows one exothermic peak at 111.9 • C and one endothermic peak at 164.2 • C. For the iPP/ABS blends, the crystallization temperature of iPP increases from 111.9 to 116.1 • C with increasing ABS concentration on the first cooling scans, implying that ABS could perform the function of heterogeneous nucleation. On the second heating scans, the blends show two or three melting peaks. The first one appears at around 150 • C, corresponding to the melting of β-crystal of iPP, indicating that ABS owns a remarkable β nucleation activity on iPP. The second melting peak appears at around 163 • C, attributed to the melting peak of α-crystal for iPP. However, with a further increase in the ABS content, α'-crystal melting peak could be observed at around 169 • C as a result of melting and recrystallization of partial β-crystals. The crystallinity of the α-form (X α ) and β-form (X β ) and the relative content of β-crystal (ϕ β ) are also listed in Table 1, which were calculated according to the standard procedures described in the literature [17]. Obviously, the blends reach the highest X β and ϕ β values with the addition of 2% ABS. corresponding to the melting of β-crystal of iPP, indicating that ABS owns a remarkable β nucleation activity on iPP. The second melting peak appears at around 163 °C, attributed to the melting peak of α-crystal for iPP. However, with a further increase in the ABS content, α'-crystal melting peak could be observed at around 169 °C as a result of melting and recrystallization of partial β-crystals. The crystallinity of the α-form (Xα) and β-form (Xβ) and the relative content of β-crystal (φβ) are also listed in Table 1, which were calculated according to the standard procedures described in the literature [17]. Obviously, the blends reach the highest Xβ and φβ values with the addition of 2% ABS.    Figure 6a,b shows the WAXD patterns of pure iPP and iPP/ABS blends prepared by compression molding and injection molding, respectively. It can be found that only α-crystals exist in the pure iPP, and its characteristic peaks (2θ) are located at 14.1°, 16.9°, 18.5°, 21.1°, and 21.8°, corresponding to the (110), (040), (130) reflections and overlapping (111) and (-131) reflections, respectively. With introducing ABS into iPP, a new crystal structure, β-phase appears, with the characteristic peak (300) located at 15.9°. This is consistent with the DSC results. According to the Turner-Jones equation [40], Kβ values calculated from the WAXD patterns in Figure 6, are displayed in Figure 7. It could be found that the Kβ value increased with addition of ABS and reached a maximum when incorporating 1% ABS for compression-molded blends and 2% ABS for injection-molded blends, respectively. With a further increase in ABS content, a decrease in Kβ could be found. The maximum Kβ values of these two systems were 8.4% and 36.2%, respectively.

First Cooling Scan
Second Heating Scan 3.3. Crystalline Structure and Phase Morphology Figure 6a,b shows the WAXD patterns of pure iPP and iPP/ABS blends prepared by compression molding and injection molding, respectively. It can be found that only α-crystals exist in the pure iPP, and its characteristic peaks (2θ) are located at 14.1 • , 16.9 • , 18.5 • , 21.1 • , and 21.8 • , corresponding to the (110), (040), (130) reflections and overlapping (111) and (-131) reflections, respectively. With introducing ABS into iPP, a new crystal structure, β-phase appears, with the characteristic peak (300) located at 15.9 • . This is consistent with the DSC results. According to the Turner-Jones equation [40], K β values calculated from the WAXD patterns in Figure 6, are displayed in Figure 7. It could be found that the K β value increased with addition of ABS and reached a maximum when incorporating 1% ABS for compression-molded blends and 2% ABS for injection-molded blends, respectively. With a further increase in ABS content, a decrease in K β could be found. The maximum K β values of these two systems were 8.4% and 36.2%, respectively.  Generally speaking, the increase in the concentration of β-nucleating agent is in favor of the rise in the relative content of β-crystal. However, the results presented in Figure 7 indicate that the Kβ values of iPP/ABS blends do not increase monotonously with respects to the ABS content. There are several different explanations for this phenomenon. Fujiyama et al. considered that when the content of β-nucleating agent exceeds a certain value, a large number of nuclei will cause the polypropylene chains to have difficulty in adjusting conformation to satisfy the chirality requirement of β-crystal, reducing the order of β-iPP in the direction of the C-axis, followed by a decrease in nucleation efficiency [41]. However, Su et al. found that further increase in the concentration of the nucleating agent deteriorated its dispersibility in the iPP matrix, leading to nonlinear change in Kβ values [19,20]. Table 2 lists the corresponding WAXD parameters. Compared to the values of the orientation parameters, including A110, A130, and C for different blends, it could be found that with the increase in ABS concentration, all the parameters showed a trend of decreasing first and then rising. This is consistent with the results of styrene-butadiene-styrene block copolymer (SBS) induced crystallization in the iPP/SBS blends reported by Fujiyama et al. [43] He found that a further rise in content of β-nucleating agent will increase the ordering of α-iPP and reduce the ordering of β-iPP in C-axis direction, resulting in the difficult formation of β-crystal followed by a reduction in β-crystal content. A careful examination reveals that the iPP spherulite sizes, including L110 and L040, are barely affected by the introduction of ABS, indicating that the formed β-crystals did not have a significant influence on the size of α-crystals. In addition, as shown in Table 2, the iPP/ABS blends obtained by  Generally speaking, the increase in the concentration of β-nucleating agent is in favor of the rise in the relative content of β-crystal. However, the results presented in Figure 7 indicate that the Kβ values of iPP/ABS blends do not increase monotonously with respects to the ABS content. There are several different explanations for this phenomenon. Fujiyama et al. considered that when the content of β-nucleating agent exceeds a certain value, a large number of nuclei will cause the polypropylene chains to have difficulty in adjusting conformation to satisfy the chirality requirement of β-crystal, reducing the order of β-iPP in the direction of the C-axis, followed by a decrease in nucleation efficiency [41]. However, Su et al. found that further increase in the concentration of the nucleating agent deteriorated its dispersibility in the iPP matrix, leading to nonlinear change in Kβ values [19,20]. Table 2 lists the corresponding WAXD parameters. Compared to the values of the orientation parameters, including A110, A130, and C for different blends, it could be found that with the increase in ABS concentration, all the parameters showed a trend of decreasing first and then rising. This is consistent with the results of styrene-butadiene-styrene block copolymer (SBS) induced crystallization in the iPP/SBS blends reported by Fujiyama et al. [43] He found that a further rise in content of β-nucleating agent will increase the ordering of α-iPP and reduce the ordering of β-iPP in C-axis direction, resulting in the difficult formation of β-crystal followed by a reduction in β-crystal content. A careful examination reveals that the iPP spherulite sizes, including L110 and L040, are barely affected by the introduction of ABS, indicating that the formed β-crystals did not have a significant influence on the size of α-crystals. In addition, as shown in Table 2, the iPP/ABS blends obtained by Generally speaking, the increase in the concentration of β-nucleating agent is in favor of the rise in the relative content of β-crystal. However, the results presented in Figure 7 indicate that the K β values of iPP/ABS blends do not increase monotonously with respects to the ABS content. There are several different explanations for this phenomenon. Fujiyama et al. considered that when the content of β-nucleating agent exceeds a certain value, a large number of nuclei will cause the polypropylene chains to have difficulty in adjusting conformation to satisfy the chirality requirement of β-crystal, reducing the order of β-iPP in the direction of the C-axis, followed by a decrease in nucleation efficiency [41]. However, Su et al. found that further increase in the concentration of the nucleating agent deteriorated its dispersibility in the iPP matrix, leading to nonlinear change in K β values [19,20]. Table 2 lists the corresponding WAXD parameters. Compared to the values of the orientation parameters, including A 110 , A 130 , and C for different blends, it could be found that with the increase in ABS concentration, all the parameters showed a trend of decreasing first and then rising. This is consistent with the results of styrene-butadiene-styrene block copolymer (SBS) induced crystallization in the iPP/SBS blends reported by Fujiyama et al. [43] He found that a further rise in content of β-nucleating agent will increase the ordering of α-iPP and reduce the ordering of β-iPP in C-axis direction, resulting in the difficult formation of β-crystal followed by a reduction in β-crystal content. A careful examination reveals that the iPP spherulite sizes, including L 110 and L 040 , are barely affected by the introduction of ABS, indicating that the formed β-crystals did not have a significant influence on the size of α-crystals. In addition, as shown in Table 2, the iPP/ABS blends obtained by two different molding methods had higher values of crystallinity (X c ) in contrast to pure iPP, owing to the heterogeneous nucleating effect of ABS. When the concentration of ABS exceeds a critical value, excessive amorphous ABS will hinder the crystallization of PP, followed by a decrease in crystallinity. To inspect the effect of ABS concentration on its morphology and dispersibility in the iPP/ABS blends prepared by compression molding and injection molding, SEM was used to observe the phase morphology, as displayed in Figure 8a1-e1 and Figure 8a2-e3, respectively. Especially, a skin region and a core region can form in the process of injection molding [20]. It is clear that ABS disperses as microspheres in the iPP matrix, indicating the immiscibility between the iPP and ABS. The size and polydispersity of ABS particles for different blends are listed in Table 3. Obviously, with the rise in ABS content, the size and polydispersity of ABS particles increased gradually. This could be attributed to the change of its dispersibility in the iPP matrix.
Compression molding is one of the traditional processing technologies and is mainly used for the production of thermosetting plastics. In the process of compression molding, pressure on plastics is relatively uniform, resulting in short flow distance and small deformation, and hence, a product with low internal stress will be obtained. The morphology investigation showed a spherical droplet structure of micron-scale for the ABS dispersed phase, as displayed in Figure 8a1-e1.
In the process of injection molding, the polymer melt is subjected to the dual effects of the temperature field and shear field, leading to its morphology being different from the result obtained under the compressing molding. In general, a typical skin-core structure exists along the thickness direction. It can be seen from Figure 8a2-e2,a3-e3 that, when the ABS mass fraction was lower than 2%, the ABS dispersed phase was microsphere-shaped in both the skin and core regions. These microspheres dispersed uniformly in the iPP matrix, and the size did not change significantly (about 1 µm), implying that the shear flowing has no influence on the morphology of the small-sized ABS microspheres in the process of injection molding. However, when the ABS content was up to 4%, the ABS particles in the skin and core regions were stretched into ellipsoids. In contrast to the ABS dispersed phase in the core region, the ABS in the skin region suffered more shear, resulting in smaller microspheres in the iPP matrix. Compared with compression molding, the ABS dispersed phase is more easily sheared in the process of injection molding. Therefore, the ABS microspheres showed a smaller size and polydispersity, regardless of the skin region or the core region, as listed in Table 3.
It is important to mention that shearing or stretching could also restrain the formation of β-iPP [24]. However, it can be found from Figure 6 that the shear effect has little impact on the crystal form of the used iPP. In contrast to the compression-molded iPP, the α-crystal diffraction peak intensity at (040) crystal plane for the iPP sample prepared by injection molding was significantly increased, indicating that the shear makes the iPP present preferential growth in (040) crystal plane. Furthermore, the K β values for the blends prepared by injection molding were relatively higher, which is mainly due to the smaller size and better dispersibility of the ABS dispersed phase.     Figure 9 presents the influence of ABS content on the tensile strength, elongation at break, and impact strength of the iPP/ABS blends. Obviously, incorporating a small amount of ABS leads to a remarkable improvement in both rigidity (tensile strength) and toughness (elongation at break, impact strength) of iPP. In contrast to pure iPP, the maximum values of tensile strength, elongation at break, and impact strength of the blends were 44.6 MPa, 1402.1%, and 7.6 kJ/m 2 , enhanced by 37.3%, 69.7%, and 128.4%, respectively. As mentioned earlier, there are certain chain entanglement and interfacial interaction between the iPP and ABS, as shown in Figure 10. During the stretching process, rigid ABS domains could play a role in stress transfer and reinforcement, and ultimately lead to higher tensile strength of the iPP/ABS blends in comparison with pure iPP. When the ABS content was 1%, the tensile strength reached its maximum. However, further increase in ABS content led to the decrease in the tensile strength. This could be explained by the interfacial debonding arising from the immiscibility between iPP and ABS.  Figure 9 presents the influence of ABS content on the tensile strength, elongation at break, and impact strength of the iPP/ABS blends. Obviously, incorporating a small amount of ABS leads to a remarkable improvement in both rigidity (tensile strength) and toughness (elongation at break, impact strength) of iPP. In contrast to pure iPP, the maximum values of tensile strength, elongation at break, and impact strength of the blends were 44.6 MPa, 1402.1%, and 7.6 kJ/m 2 , enhanced by 37.3%, 69.7%, and 128.4%, respectively. As mentioned earlier, there are certain chain entanglement and interfacial interaction between the iPP and ABS, as shown in Figure 10. During the stretching process, rigid ABS domains could play a role in stress transfer and reinforcement, and ultimately lead to higher tensile strength of the iPP/ABS blends in comparison with pure iPP. When the ABS content was 1%, the tensile strength reached its maximum. However, further increase in ABS content led to the decrease in the tensile strength. This could be explained by the interfacial debonding arising from the immiscibility between iPP and ABS.

Mechanical Properties
When the sample is subjected to tensile or impact loading, debonding of the rigid organic particles of ABS occurs, followed by cavitation at the interface between the iPP and ABS. The cavitation and subsequent plastic deformation process could dissipate plenty of energy [42]. Moreover, ABS is an effective β-nucleating agent, and can induce the formation of β-crystal for iPP. Therefore, the  When the sample is subjected to tensile or impact loading, debonding of the rigid organic particles of ABS occurs, followed by cavitation at the interface between the iPP and ABS. The cavitation and subsequent plastic deformation process could dissipate plenty of energy [42]. Moreover, ABS is an effective β-nucleating agent, and can induce the formation of β-crystal for iPP. Therefore, the iPP/ABS blends have superior fracture and impact toughness. ABS shows a remarkable β nucleation activity, which contributes to the improvement in iPP impact strength. It should be mentioned that a further increase in ABS content will reduce the order of β-iPP in the C-axis direction and deteriorate its dispersibility. Moreover, introducing excess ABS brings about the formation of defects in the blends.
As a result, the values of elongation at break and impact strength fell off with a further increase in ABS content.

Conclusions
Poly(acrylonitrile-butadiene-styrene) (ABS) could generally serve as a modifier for isotactic polypropylene (iPP). In the traditional processing modification method, the iPP/ABS blends show unfavorable mechanical performance as a result of the incompatibility between ABS and iPP, as well as a high concentration of ABS. In this experiment, the mass fraction of ABS was controlled within 4%. The results show that a small amount of ABS can disperse uniformly in the iPP matrix. ABS shows a remarkable β nucleation activity on iPP. Its β nucleation efficiency is closely related to its concentration, dispersibility, and molding method for the blends. The Kβ value increases by the introduction of ABS and reaches a maximum with the addition of 1% ABS for compression-molded blends and 2% ABS for injection-molded blends, respectively. The maximum Kβ values of these two systems were 8.4% and 36.2%, respectively. Furthermore, there are certain chain entanglement and interfacial interaction between the iPP and ABS. During the stretching process, rigid ABS domains could play a role in stress transfer and reinforcement. As a result, the addition of a small amount of ABS has a significant reinforcing and toughening effect on iPP. In contrast to pure iPP, the maximum values of tensile strength, elongation at break, and impact strength of the blends were 44.6 MPa, 1402.1%, and 7.6 kJ/m 2 , enhanced by 37.3%, 69.7%, and 128.4%, respectively. Compared with the compression-molded samples, the ABS dispersed phase in injection-molded samples had a smaller particle size and a larger specific surface area, which is favorable for stress transmission and higher β nucleation efficiency, and therefore, better tensile and impact properties can be expected.  Compared with the compression-molded samples, the ABS dispersed phase in the injection-molded samples had a smaller particle size and a larger specific surface area, which is favorable for stress transmission and higher β nucleation efficiency, and therefore, better tensile and impact properties were obtained.

Conclusions
Poly(acrylonitrile-butadiene-styrene) (ABS) could generally serve as a modifier for isotactic polypropylene (iPP). In the traditional processing modification method, the iPP/ABS blends show unfavorable mechanical performance as a result of the incompatibility between ABS and iPP, as well as a high concentration of ABS. In this experiment, the mass fraction of ABS was controlled within 4%. The results show that a small amount of ABS can disperse uniformly in the iPP matrix. ABS shows a remarkable β nucleation activity on iPP. Its β nucleation efficiency is closely related to its concentration, dispersibility, and molding method for the blends. The K β value increases by the introduction of ABS and reaches a maximum with the addition of 1% ABS for compression-molded blends and 2% ABS for injection-molded blends, respectively. The maximum K β values of these two systems were 8.4% and 36.2%, respectively. Furthermore, there are certain chain entanglement and interfacial interaction between the iPP and ABS. During the stretching process, rigid ABS domains could play a role in stress transfer and reinforcement. As a result, the addition of a small amount of ABS has a significant reinforcing and toughening effect on iPP. In contrast to pure iPP, the maximum values of tensile strength, elongation at break, and impact strength of the blends were 44.6 MPa, 1402.1%, and 7.6 kJ/m 2 , enhanced by 37.3%, 69.7%, and 128.4%, respectively. Compared with the compression-molded samples, the ABS dispersed phase in injection-molded samples had a smaller particle size and a larger specific surface area, which is favorable for stress transmission and higher β nucleation efficiency, and therefore, better tensile and impact properties can be expected.