Comparative Study on Polyamide 6 Toughness using Multiple Melt-Kneading Techniques

In the present work, we tried to toughen polyamide 6 (PA6) by blending a small amount of low molecular-weight polyethylene (LMWPE). We obtained the PA6/LMWPE blends with different morphologies using multiple melt-kneading methods such as the uniaxial melt-kneading, the eight-axial screw melt-kneading, and the high shearing method. As a result, it was elucidated that the LMWPE was homogeneously and finely dispersed by using the eight-axial melt-kneading method. On the other hand, we found that for high shearing method the LMWPE was finely dispersed to a degree close to the compatible system. The result of the three-point bending test showed that the PA6 was brittle fractured, but it changed to ductile fracture when a small amount of LMWPE was blended. Also, the fracture displacement was extensively improved. The results of the comparison by the melt-kneading methods revealed that the toughness of the PA6 was improved even by adding a small amount of LMWPE (about 2%) when they were blended using the eight-axial screw melt-kneading machine. The cross-sectional observation in the bending test showed that voids were produced from the LMWPE. We elucidated that the production of voids was induced with low stress by adding fragile LMWPE, resulting in the improvement of the bending toughness. Moreover, we found that the LMWPE needs to be finely dispersed with an appropriate particle size in order to exhibit ductile properties.


Introduction
In recent years, due to the rise in environmental consciousness, weight reduction aimed at reducing the fuel consumption of automobiles is proceeding. Under these circumstances, the proportion of using light polymer in automobiles is increasing. However, extremely high mechanical properties are required for materials loaded in automobiles. For that reason, the number of cases has been increasing where a single type of polymer material cannot meet requirements in automobiles. One of the methods to solve this problem is to use polymer blend, a mixture of different kinds of polymer materials. Up to now, the research and development on polymer blend method have been extensively conducted as a method that exhibits various properties and functions. As a result, many polymer alloy materials with various characteristics have been proposed [1,2]. In particular, for polymer materials showing brittle fracture behavior, it is tried to change them to be ductile by blending elastomer and gum. However, with these methods, the rigidity of the polymer materials is generally reduced while increasing ductility [3,4].
A crystalline polymer, polyamide 6 (PA6), is an engineering plastic that has extremely high mechanical property because of the strong molecular-molecular interaction of hydrogen bonds in amide group. Although PA6 has strong rigidity, it causes brittle fracture when imposed with a large displacement. Hence it is very important to change the property of PA6 to be ductile while maintaining its high rigidity [5].
In the present study, we tried to improve the toughness of PA6 by blending a small amount of low molecular-weight polyethylene (LMWPE). The purpose of the work is to clarify the relation between the inner structure and the mechanical property of the polymer blends with different morphologies produced by three different kinds of melt-kneading methods.

Academic Journal of Polymer science
(Tm) of PA6 were 50 °C and 218 °C, respectively. The melt flow rate (MFR) was 26g/10min at 230 °C. As a modifier of PA6, LMWPE (Hi wax 1105A, Mitsubishi Chemical Co.) was used. The LMWPE was denatured by maleic anhydride. The Tg was 104 °C, and the average molecular weight (Mw) of the LMWPE was 1,900. The molded film of LMWPE is an extremely brittle and low-strength material exhibiting a tensile strength of 1.4MPa and a breaking strain of 0.006 in a tensile test. The blend ratio of the samples were PA6/LMWPE=98:2 and 95:5 wt%, and the kneading temperature was 250 °C.

Melt-kneading methods
The blend ratio, the details of the melt-kneading machines, and the kneading conditions for the present samples are shown in Table 1. The melt-kneading machines used were Single screw extruder (SSE) (CER40, Hoshi Plastic Co., Ltd.), Octa screw kneading extruder (OSE) (Technobell Co., Ltd.), and High-shear process kneader (HSP) (Niigata Machine Techno CO., Ltd). The OSE was used for low-shear kneading. Therefore, it is expected that we obtain the products with relatively large domain diameter. The OSE is a machine where all eight screws engage and rotate in the same direction. Since the resin stays among eight screws in the OSE, the long-time kneading is possible compared with the SSE. The HSP is a batch-type kneading machine and has a special screw with a small hole in the center (return hole). Hence, it is possible to knead a certain amount of resin at arbitrary rotation speed and time [6][7][8][9].  The samples after kneading were pelletized, and then molded to three-point bending test pieces and flat plate test pieces using the injection molding machine.

SEM observation
The samples after kneading were frozen and fractured in liquid nitrogen, and the fracture surface was observed by a scanning electron microscopy (SEM).

Mechanical properties and observation of plastic deformation region
Three-point bending tests were conducted for specimens with notches. The Poisson contraction at the tip of the notch is suppressed due to the constraint of the distortion. Hence the pure uniaxial stretching test becomes possible. This test method is known to be effective for the evaluation of toughness (ductile or brittle) for polymer blend materials [10]. As additional experiments, the bending test was stopped at the displacement just before the fracture or at the maximum displacement (10mm), and the sample was fixed by embedding with epoxy resin. The plane of the sample perpendicular to the tip of the notch was then scraped to 20μm thick thin film using a microtome. The void-producing region in the plane was observed with a polarization microscope.

Impact resistance evaluation
For evaluating the impact strength at the time of rapid deformation, a high-speed impact test (punching) was conducted. The sample molded to a plane shape was punched by a test rod of 10mm diameter, and the stress was measured. The speed of the impact test was 10m･s -1 . Figure 1 shows the cross-sectional SEM images for PA6/ LMWPE kneaded by SSE (a) and OSE (b). For the SSE-kneaded sample, LMWPE aggregates with a maximum particle size of 3μm were observed. The size of the aggregates was not homogeneous. For the OSE-kneaded sample, we confirmed the LMWPE aggregates with a particle size from 1μm to 2μm. The size of the aggregates was relatively homogeneous compared with that of the SSE-kneaded sample. For the HSP-kneaded sample, LMWPE aggregates were not observed. The reason would be that the LMWPE was extremely finely dispersed in this case.  Figure 2 displays the results of the three-point bending test for pure PA6 and PA6/LMWPE blends produced by respective kneading methods. Only OSE kneaded-samples were prepared with LMWPE addition amount of 2 and 5wt%. For the pure PA6, SSE-kneaded sample, and HPS-kneaded sample, they were finally brittle fractured. In particular, for the HSP-kneaded blend, the fracture behavior was same as that of the pure PA6, thus the effect of the LMWPE blending could not be confirmed. On the other hand, the OSE-kneaded sample showed plastic deformation, and it was not fractured even at the maximum displacement (10mm) resulting in the general yield. The OSE kneaded sample (LMWPE: 5wt%) showed better breaking elongation than the system in which LMWPE(added 2wt%), but the maximum bending strength greatly decreased. This result seems to be due to excessive addition of brittle LMWPE. Figure 3 presents the polarization microscope image of the plastic deformation region produced at the tip of the notch in the bending test. For the pure PA6 (a), voids were not produced even at 3.2mm deformation, just before the fracture. While for SSE-kneaded blend (b), the plastic deformation region originating from the voids formation was confirmed for the sample just before the fracture (displacement: 6mm). In this case, the blending of LMWPE induced the void formation, and the Poisson contraction among the voids became possible, which led to the ductile behavior of the sample compared with the pure PA6. However, the stress was locally concentrated because of the inhomogeneous size of the dispersed LMWPE. Therefore, it is considered that the sample finally resulted in the brittle fracture.  For the OSE-kneaded sample (c), we confirmed the plastic deformation regions that are wider than those for the SSEkneaded one at the same displacement (6mm). Compared with the SSE-kneaded sample, the OSE-kneaded one exhibited morphology where the size of the LMWPE aggregates was small and homogeneous. Therefore, the distance among the LMWPE aggregates was homogeneous, so the sample was homogeneously deformed due to the dispersion of the stress. As a result, it is considered that the sample resulted in the general yield without the brittle fracture even at the maximum displacement.

Three point bending test and observation of plastic deformation region
For the HSP-kneaded sample (d), we observed a fine plastic deformation region at the displacement (3.2mm), just before the fracture. By the high shearing kneading, the LMWPE showed the dispersion condition that is close to the homogeneous compatibility system. As a result, voids expansion did not proceed because the size of the produced voids was extremely small. Thus, the stress constraint was not relaxed because the Poisson contraction was not sufficient. This would be the reason that the HSP-kneaded sample finally resulted in the brittle fracture. Based on the above results, we controlled fragile LMWPE to exhibit fine (about 1μm size) and homogeneous higher-order structure. By doing so, the void formation was induced, and the stress was relaxed. As a result, we succeeded in improving the toughness of PA6. On the other hand, the HSP-knead blended sample with excessively finely dispersed LMWPE did not have a higher-order structure. We consider that the blending of LMWPE did not lead to improve the toughness of PA6 in this case because the stress relaxation function did not work. Figure 4 shows the load-displacement curve in the highspeed impact test at 10m.s-1. At this speed, both the PA6 and the HSP-kneaded samples were brittle fractured. The reason is that in both samples the cracks were developed because the stress was not relaxed in the deformation at the high speed. On the other hand, the SSE-and OSE-kneaded samples showed ductile fracture. For these samples, the LMWPE that is easy to be fractured existed as domains with 1-3μm diameter. The stress relaxation effect expressed even at high speed of 10m･s -1 because the LMWPE became the origin of voids. Based on these results, we succeeded in leading the SSE-and OSE-kneaded blends to the ductile fracture. On the other hand, the effect of the stress relaxation effect in the HSP-kneaded sample that has extremely fine dispersed structure of the LMWPE was not sufficient. We consider this is the reason why the HSP-kneaded sample led to the brittle fracture.

Conclusion
In the present work, we tried to toughen PA6 by blending a small amount of LMWPE. We obtained the PA6/LMWPE blends with different morphologies using multiple melt-kneading methods such as the uniaxial melt-kneading, the eight-axial screw melt-kneading, and the high shearing method. As a result, it was Your next submission with Juniper Publishers will reach you the below assets possible to lead to ductile fracture while maintaining rigidity by adding a small amount of LMWPE to PA6. Kneading by OSE was effective for finely dispersing LMWPE and equalizing dispersed particle size, and the properties of the blended material were also the most stable. This result seems to be because Poisson contraction was possible even at high speed deformation, and PA6 could lead to ductile fracture, since LMWPE which breaks easily is the starting point of void formation. However, when LMWPE was dispersed in a region close to the nano order and homogeneous system, the effect of adding LMWPE did not appear. It has been found that it was important to form a higher order structure having an island phase size larger than a certain level for toughening by polymer blending.