Jumpei
Kawada
*a,
Masayuki
Kitou
b,
Makoto
Mouri
a,
Yuichi
Kato
a,
Yoshihide
Katagiri
a,
Mitsumasa
Matsushita
a,
Toshiyuki
Ario
b,
Osamu
Kitou
b and
Arimitsu
Usuki
a
aToyota Central R&D laboratories, Inc., 41-1 Yokomichi, Nagakute, Aichi 480-1192, Japan. E-mail: jumpei-kawada@mosk.tytlabs.co.jp
bToyota Boshoku Corporation, 88 Kanayama, Kamekubi, Toyota, Aichi 470-0395, Japan
First published on 11th August 2017
Injection molded bio-alloys based on polyamide 11 (PA11), 100% bio-based plastics from inedible plants, and polypropylene (PP) mixed with the maleic anhydride-modified ethylene-butene rubber copolymer (m-EBR) were prepared using a twin-screw extruder. The mechanical properties and morphologies of the bio-alloys were investigated using flexural tests, Charpy notched impact tests, field emission-scanning electron microscopy (FE-SEM), Raman spectroscopy, and transmission electron microscopy (TEM). The bio-alloy had a flexural modulus of 1090 ± 20 MPa and a Charpy notched impact strength of 98 ± 5 kJ m−2, which is superior to that of polycarbonates. The FE-SEM observations revealed that the bio-alloy has a unique “salami-like structure in a co-continuous phase”, and the TEM observations showed that some m-EBR formed 10 to 20 nm wide continuous interphases between the PP and PA11 matrices. Continuous rubber interphases played an important role in enhancing the impact strength. The bio-alloys exhibited good rigidity and excellent impact strength, making them feasible for applications in automobiles and other industries.
Although some bio-based plastics such as poly(lactic acid)9 and poly(hydroxy alkanoate)s10,11 are already on the market due to significant progress and tremendous achievements, the share of bio-based or renewable plastics in the plastics market is low (<5%),12 and these plastics are not employed to a significant extent in the automobile or electric industries. Recently, cellulose nanofibers (CNF), another promising material, have been studied intensively.13–16 CNF can be used as nanosize fillers in a polymer matrix since they have excellent modulus and tensile strength,17,18 but they cannot be utilized as a thermoplastic. Polymer alloys have added different characteristics to the original polymers, and improved the mechanical and physical properties of polymers.19,20 Numerous studies on synthetic polymer alloys and blends have been reported,19–25 which have led to an understanding of the polymer toughening mechanism, including crazing, cavitation, and shear yielding.22,26–33 Nevertheless, there are still few bio-based plastics or bio-alloys in the automobile and electrical industries.
Vegetable oils are historically and presently one of the most important renewable feedstocks. The annual global production of vegetable oils amounted to approximately 140 million tons in 2009 and 2010, and the production of castor oil increased by 38% from 1999 to 2008.34 Castor beans are a non-food resource because they contain the highly toxic ricin. Polyamide 11 (PA11) was used in this study because it is a completely bio-based plastic made from the castor bean plant which thus absorbs CO2 during cultivation. Therefore, the use of PA11 is advantageous because the amount of CO2 emission is not increased, whereas the production of other polyamides (PA) from petroleum resources does increase CO2 emissions. The total energy consumption required to produce PA11 is less than that required to produce petroleum-based PA. For bio-alloys, polypropylene (PP) was selected as the counterpart of PA11 because Braskem expects a 30 kton per year of green polypropylene plant to go onstream as soon as bio-based propylene is available from bioethanol8 and PP is one of the most abundant plastics in the world. Although the PP/PA11 bio-alloy is currently produced as a partially bio-based plastic, it is possible to be produced as a 100% bio-alloy in the near future.
Recently, bio-based alloys have been studied as green materials35–37 because the processing method, so-called melt blending, is an organic solvent-free process. The research to date on the PP/PA11 bio-alloy by Wang et al. has revealed that the PP/PA11 bio-alloy has a dispersed phase morphology and that the dispersed phase size of PA11 is dependent on the amount of maleated ethylene-propylene-diene rubber.38,39 Fu et al. simulated a PP/PA11 blend by atomistic molecular dynamics and mesoscopic dynamics simulations and predicted that the PP/PA11 blend had a phase separation structure or a co-continuous structure, depending on the PP/PA11 ratio40 as well as the PP/PA6 alloy.41 We have reported “salami” and finer “nano-salami” structures of PP/PA11 bio-alloys that have significantly enhanced the Charpy notched impact strength without a large reduction in the stiffness of the bio-alloys.42 Nanotechnology has played an extremely important role in the design of polymer alloys. Therefore, the purpose of this research is to create bio-alloys with good stiffness and high toughness by controlling the bio-alloy morphology at the nanometre scale, especially considering applications in the automobile or electrical industries.
Sample | Proportion (wt%) | Mechanical properties | |||
---|---|---|---|---|---|
PP | PA11 | m-EBRa | Flexural modulus (MPa) | Charpy notched impact strength (kJ m−2) | |
a Maleic anhydride-modified ethylene-butene rubber copolymer. | |||||
#1 | 100 | 0 | 0 | 1480 ± 30 | 2.5 ± 0.2 |
#2 | 0 | 100 | 0 | 1310 ± 30 | 11 ± 2 |
#3 | 90 | 0 | 10 | 1200 ± 10 | 3.5 ± 0.5 |
#4 | 80 | 10 | 10 | 1050 ± 10 | 8.0 ± 0.3 |
#5 | 65 | 25 | 10 | 1120 ± 20 | 9.1 ± 0.6 |
#6 | 50 | 40 | 10 | 1150 ± 10 | 10 ± 0.3 |
#7 | 35 | 55 | 10 | 1000 ± 10 | 21 ± 0.3 |
#8 | 30 | 60 | 10 | 950 ± 10 | 62 ± 2 |
#9 | 25 | 65 | 10 | 940 ± 20 | 24 ± 1 |
#10 | 10 | 80 | 10 | 870 ± 10 | 72 ± 1 |
#11 | 0 | 90 | 10 | 870 ± 30 | 72 ± 1 |
The flexural moduli of these bio-alloy samples decreased from 1200 MPa to 870 MPa when the amount of PA11 was increased because the flexural modulus of PA11 with the reactive compatibilizer is low. However, the trend of the Charpy notched impact strength for these PP/PA11 bio-alloys was quite different from that of the flexural moduli, as shown in Fig. 1, when the PA11 content was increased. It should be noted that the Charpy notched impact strength with a PA11 content of 60 wt% was extremely high.
To understand the unusual trend of the Charpy notched impact strength with respect to the PP/PA11 ratio, the morphologies of the bio-alloys were observed using field emission-scanning electron microscopy (FE-SEM), and the results are shown in Fig. 2. The FE-SEM image of sample #5 in Fig. 2 shows a typical salami structure where PP was a matrix and PA11 was a dispersed phase including dispersed subdomains of m-EBR.42 As the proportion of PA11 was increased, the size of the salami structure was enlarged, as represented by sample #6. On the other hand, when PA was added at 60 wt%, such as in sample #8, PP and PA11 both formed independent matrices to generate a co-continuous phase in which the PP matrix had PA11 salami structures with m-EBR or PP dispersed subdomains, and the PA11 matrix had PP salami structures with m-EBR or PA11 dispersed subdomains. This is a novel structure that has salami structures in each continuous phase. Since Ide and Hasegawa reported a versatile route to enhance the physical properties of PA,21 extensive studies have been conducted for the purpose of toughening PA. The relationship between the morphology and the mechanical properties has since been studied in the blends of PP and PA.40,41,43–47 Nonetheless, the unique phenomenon observed here in PP/PA has not yet been reported and not predicted by computer simulation.40,41 As the proportion of PA11 was increased to more than 60 wt%, the morphology was altered to be a PA11 matrix, i.e., a phase inversion occurred, as shown in sample #9. In sample #11, PA11 and m-EBR were mixed finely at the nanometre scale. These results suggest that salami structures in a co-continuous phase lead to significant improvements in the mechanical properties of PP/PA11 bio-alloys.
Fig. 2 FE-SEM images of freeze-fracture surfaces of the injection molded test pieces subjected to oxygen plasma treatment for 60 s. The sample numbers correspond to those in Table 1. The scale bars represent 2 μm. |
Transmission electron microscopy (TEM) and atomic force microscopy measurements have provided evidence that the interphase between a matrix and dispersed phases in a salami structure is m-EBR.42 Sample #8 was investigated using a TEM technique with a stain for rubbers as shown in Fig. 3, and the interphases were observed as dark layers between the PP and PA11 matrices. These results indicate that m-EBR was located in the interphases, and Fig. 3 shows that m-EBR formed continuous phases with widths of approximately 10 to 20 nm.
These continuous rubber interphases account for the significant improvement in the impact resistance and are the reason why bio-alloys with 70% PA11 did not have high Charpy notched impact strength, because the bio-alloy did not have these continuous interphases due to the phase inversion.
To confirm that the co-continuous phase was present in all three dimensions, sample #8 was examined using Raman spectroscopy. Fig. 4(a) shows the Raman spectra of PP and PA11. The PP spectrum shows a characteristic peak at 840 cm−1, indicative of ρ(CH2) vibrations, while the PA11 spectrum has a characteristic peak at 1640 cm−1, which is attributed to the amide I band and is indicative of CO stretching. Consequently, the presence of both components can be distinguished by assessing these two peaks. A three-dimensional analysis of sample #8 based on its Raman spectrum is presented in Fig. 4(b–h), where the PP and PA11 regions are coloured blue and green, respectively. The arrow in Fig. 4(b) indicates a PP region, and there was PA11 at the same position except for the z position in Fig. 4(c) shown by the broken arrow when the sample was measured just above 2.4 μm in the z axis direction of Fig. 4(b). PP appeared again in Fig. 4(d), (e) and (f), as indicated by the arrow, when the sample was observed from the positive z direction, at z = 5.1, 7.5, and 9.9 μm, respectively. When sample #8 was observed from different faces, as in Fig. 4(g) and (h), continuous PP matrices at the arrows and continuous PA11 matrices at the broken arrows were detected.
The Raman data revealed that PP and PA11 form an independent continuous matrix. In this analysis, the spatial resolution was on the order of 1 μm, such that the salami structures, which are usually less than 1 μm, could not be detected in the co-continuous phase structure.
The fracture surface of sample #8 was quite unique. The surface occasionally left evidence of ductile behaviour, as shown in Fig. 6. The materials were stretched well at the interface, vertical to the fracture surface, which indicates plastic deformation, and is evidence that a significant amount of impact energy was absorbed during the stretching of the material.
Fig. 6 FE-SEM image of the sample #8 fracture surface after the Charpy notched impact test. The scale bar represents 5 μm. |
The morphologically controlled bio-alloy with salami structures in a co-continuous phase structure has superior mechanical properties, i.e. excellent impact resistance with a good flexural modulus. Such properties are challenging to achieve, especially both high rigidity and high impact resistance, because these properties are mutually exclusive. This enhancement of the mechanical properties is most certainly due to the structure. PP regions retain a good flexural modulus and PA11, which has end-groups bonded to m-EBR,42 is attributed to the improvement of the Charpy notched impact strength through mechanisms such as the formation of cavitations and shearing deformation. In addition, continuous rubber interphases between the PP and PA11 matrices, whose width is only 10 to 20 nm, play a key role in enhancing the Charpy notched impact strength because the rubber interphase can absorb the impact energy.
Footnote |
† Electronic supplementary information (ESI) available. See DOI: 10.1039/c7gc01842h |
This journal is © The Royal Society of Chemistry 2017 |