SciELO - Scientific Electronic Library Online

vol.29 número2The influence of fiber size on the behavior of the araucaria pine nut shell/PU compositeThermal radical polymerization of Bis(methacrylamide)s índice de autoresíndice de assuntospesquisa de artigos
Home Pagelista alfabética de periódicos  

Serviços Personalizados




Links relacionados



versão impressa ISSN 0104-1428versão On-line ISSN 1678-5169

Polímeros vol.29 no.2 São Carlos  2019  Epub 10-Jun-2019 


Compatibility and characterization of Bio-PE/PCL blends

Elieber Barros Bezerra1 

Danyelle Campos de França1 

Dayanne Diniz de Souza Morais1 

Ingridy Dayane dos Santo Silva2 

Danilo Diniz Siqueira1 

Edcleide Maria Araújo1  *

Renate Maria Ramos Wellen2 

1Departamento de Engenharia de Materiais, Universidade Federal de Campina Grande – UFCG, Campina Grande, PB, Brasil

2Departamento de Engenharia de Materiais, Universidade Federal da Paraíba – UFPB, João Pessoa, PB, Brasil


In this work, blends based on environmentally friend polymers such as Biopolyethylene (Bio-PE), Polycaprolactone (PCL) and Polyethylene graft maleic anhydride (PEgMA) added as compatibilizer agent were produced by conventional extrusion, aiming to produce bio-blends with synergic properties at low processing cost, being at same time non-polluting and therefore contributing to the environment preservation. Differential scanning calorimetry (DSC) showed that blending does not significantly interfere on the melting and crystallization behaviors of neat polymers, suggesting being low miscibility compounds. Mechanical properties were observed changing with blend composition as the impact strength significantly increased reaching values higher than 130% when compared to neat Bio-PE. Scanning electron microscopy (SEM) images showed honeycomb morphology in Bio-PE/PCL blends, and the addition of PEgMA decreased the coalescence contributing to obtain more stable and synergic compounds. Bio-PE/PCL/PEgMA at 80/20/10 contents presented the best properties and may be used for packaging materials (food containers, film wrapping), and hygiene products.

Keywords:  Bio-PE; PCL; thermal behavior; mechanical properties; morphology

1. Introduction

Currently petroleum-based polymer products are still dominant in the world market due to their excellent mechanical and thermal properties, as well as to their great versatility in several applications, providing an amount of approximately 300 million tons of plastic products produced by the end of this year. However, given the characteristic of nonbiodegradability and durability of some polymers as polyolefins, polyamides, polyesters and so on, a serious environmental problem follows the contemporary man with potential damage to nature, especially in the populous urban centers[1-4].

Therefore, the society has been asking the industrial sector for adopting “ecologically acceptable” policies, such as the rational use of natural resources, mainly in the production of materials for the productive sectors. Focused on this subject polymer scientists have suggested as an alternative to the use of polymers derived from fossil sources the production of biopolymers (polymers produced from renewable sources) and biodegradable (polymers able to naturally degrade in the environment) ones[5-7].

The use of biodegradable polymers appear as a possible and fast solution to reduce environmental pollution, they can be produced from renewable resources such as maize, sugar cane, cellulose and chitin, for instance, additionally they present shorter life cycle compared to the non-biodegradable ones (as polypropylene (PP), poly(ethylene terephthalate) (PET), nylons and so on) and when discarded they produce compounds not harmefull to the environment, as the case of poly(hydroxibutyrate) (PHB), PCL, poly(butylene adipate‐co‐terephthalate) (PBAT) for instance[7].

Additionally, the use of “green” polymers, such as biopolyethylene (Bio-PE), produced from ethanol (from sugarcane), although not biodegradable, maintains the neutral balance of carbon dioxide (CO2) in the natural environment. The CO2 captured from the atmosphere by the biomass, when later released to the atmosphere by the combustion, is captured again by the sugarcane trough the photosynthesis process in the next harvest[7-10].

Another alternative to this scenario would be the use of environmentally degradable polymers, which have the advantage of being stable over their useful life and being degraded in a short time after disposal in the environment; PCL is one of these polymers that has aroused interest in the substitution of conventional polymers since it is a fully biodegradable hydroxycarbonic acid based on polyester. Moreover, it has good properties and also compatibility with other materials[11-17].

Research in polymer blends involving these two classes of polymers appears as a viable alternative to the process of developing ecologically friend materials. In addition, studies of polymer blends are an alternative to obtain materials with properties that, in general, are not found in a neat resin[18,19].

Therefore, the objective of this work is to develop polymer blends based on environmentally friend polymers (Bio-PE and PCL) with different compositions; Bio-PE/PCL/PEgMA blends were also produced aiming the tenacification and compatibilization of Bio-PE upon addition of PEgMA, which has PE and MA segments,which are able to react with Bio-PE and PCL end groups. These blends were characterized by differential scanning calorimetry (DSC), heat deflection temperature (HDT), mechanical tensile and impact strength tests, scanning electron microscopy (SEM) and contact angle measurement.

2. Materials and Methods

2.1 Materials

High Density Polyethylene (Bio-PE), I'm green® SHC7260, Braskem. Polymer produced from sugarcane. Minimum carbon content from renewable source of 94%. Density 0.959 g/cm3, MIF = 7.2 g/10 min (190°C/2.16 kg). Polycaprolactone (PCL), Capa® 6500, MIF = 28 g/10min (160°C/2.16 kg) and elongation up to 800%, purchased from Perstorp Winning Formulas. Polyethylene grafted with 1.5-1.7% Maleic Anhydride (PEgMA) Polybond 3029, purchased from Addivant. Density 0.95 g/cm3, MIF = 4.0 g/10min (190°C/2.16 kg) and melt temperature (Tm) = 130°C. These parameters were collected from the resin datasheets, which are inserted in Appendix 1 with HDPE, PCL and PE-gMA Datasheets, respectively.

2.2 Methods

Polymer blending carried out in a modular, interpenetrating, twin screw extruder with L/D ratio of 40, model ZSK 18 mm, Werner-Pfleiderer, Coperion (Wesseling, Rhein-Erft-Kreis, Germany). Prior to extrusion, the raw materials were manually mixed to promote further homogenization. For all blends, the following extrusion parameters were used: feed rate of 5 kg/h; screw speed of 250 rpm; temperature profile in the extruder zones 200°C in all zones. The output material was granulated and oven dried under vacuum at 40°C for 24h.

The compositions of the extruded blends and their codes are shown in Table 1.

Table 1 Compositions of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. 

Compounds Bio-PE (%) PCL (%) PEgMA (phr)
Bio-PE 100 - -
Bio-PE/PCL 90 10 -
Bio-PE/PCL/PEgMA 90 10 10
Bio-PE/PCL 80 20 -
Bio-PE/PCL/PEgMA 80 20 10
Bio-PE/PCL 70 30 -
Bio-PE/PCL/PEgMA 70 30 10
PCL - 100 -

Figure 1 shows the screw used during the extrusion. The screw configuration has mixing sections with dispersive and distributive elements. The main feed zone of premixed materials is indicated in Figure 1 with the down arrow. The upward-facing arrows are degassing points (vents).

Figure 1 Schematic representation of the screw configuration used during the extrusion. 

After extrusion, injected specimens were molded according to ASTM standards D 638, D256 and D648, for tensile, impact and HDT experiments, respectively. An Arburg Injector, Model Allrounder 270C Golden Edition (Loßburg, Baden-Württemberg, Germany), was used, operating at 180°C, with mold at 20°C. Blends, neat Bio-PE and PCL were subjected to the same injection parameters. An average of 10 specimens was used for each investigated composition.

2.3 Characterizations

2.3.1 Differential Scanning Calorimetry (DSC)

DSC analyzes were performed using a TA Instrument DSC-Q20 (New Castle, Delawere, EUA). The temperature program used was: heating from 20°C to 250°C, cooling to 10°C, reheating to 250°C, at a heating/cooling rate of 10°C/min, under inert environment with nitrogen flow of 50 mL/min. The samples tested weighed approximately 3.5 mg.

2.3.2 Heat Deflection Temperature (HDT)

HDT was determined according to ASTM D 648, in a Ceast equipment (Norwood, Massachusetts, EUA), model HDT 6 VICAT/N 6921.000, with a tension of 455 kPa, heating rate of 120°C/h (method A). The temperature was determined after the sample deflecting 0.25 mm. Series of five injected samples were tested and the HDT, with its respective standard deviation, is reported.

2.3.3 Mechanical test

The tensile tests were performed according to ASTM D 638. Properties as elastic modulus, tensile strength and elongation at break were measured. The tests were performed in a universal EMIC equipment (Curitiba, Paraná, Brazil), model DL10000, using a 100 kgf load cell, with deformation rate of 50 mm/min, operating at room temperature (~23°C). The results presented are an average of 10 specimens tested.

2.3.4 Mechanical impact strength test

The IZOD impact strength tests were performed on notched specimens, using a Resil 5.5 equipment from Ceast (Norwood, Massachusetts, EUA) and a pendulum of 2.75 J, according to ASTM D 256, at room temperature (~23oC). The results reported were obtained from an average of 10 specimens.

2.3.5 Scanning Electron Microscopy (SEM)

SEM analyzes were obtained on the Tescan Vega 3 equipment (South Moravia, Brno, Czech Republic) with a voltage of 30 kV under high vacuum, images were captured on the fracture surface of the fractured impact specimen. The fracture surfaces of the samples were gold-covered (Shimadzu Metallic-IC-50, using a current of 4mA for a period of 3 minutes) in order to avoid negative charge accumulation. The average diameters of dispersed phases were computed using the Tesca See 3 software.

2.3.6 Contact angle measurement

The contact angle analysis to determine the hydrophilicity of the blends was performed by distilled water drop method through a Phoenix-i model of the Electro Optics - SEO Surface (Saneop-ro, Namwon, South Korea). This analysis was done on the surface of the injection molded specimens. An analysis was performed from 20 photos, using an interval of 10 seconds, totaling 200s.

3. Results and Discussions

3.1 Differential Scanning Calorimetry (DSC)

Understanding how the addition of PCL and PEgMA affect the morphology of Bio-PE is especially important because the resulting crystalline structure will influence the chemical as well as physical properties of the blends; to reach this aim DSC was employed, these scans are presented in Figure 2, and parameters determined from them are presented in Tables A1 -A4 of Appendix 2 .

Figure 2 Top: DSC scans of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA compounds acquired during cooling. Bottom: DSC scans of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA compounds acquired during the second heating. 

DSC scans of Figure 2 (Top) present the exothermic peaks relative to melt crystallization of Bio-PE and PCL. The addition of PCL slightly changed the crystallization of Bio-PE, which has a crystallization range between 106.04°C and 119.19°C; the exothermic crystallization peak of PCL in the blends was observed between 32.91 and 42.48°C. Bio-PE has a degree of crystallinity ΔXc ~ 14.50% and PCL between 4.75-8.65%; these data are in the literature range as published by Fel et al.[20] for (high density polyethylene) HDPE and by Antunes & Felisberti[21] for PCL. The crystallization rates and τ1/2 (time to reach 50% of crystallinity) of Bio-PE and PCL were subtly modified in the blends, as shown in 45. These behaviors suggest the low miscibility of Bio-PE/PCL system, with respective crystalline phases, i.e. Bio-PE and PCL, crystallizing as separate phases, nevertheless phase segregation was not verified as further on presented in SEM images (Figure 3) where Bio-PE is the matrix and PCL the dispersed phase, nevertheless upon addition of PEgMA the particle sizes decreased as an indication of chemical interactions between Bio-PE/PCL and PEgMA, conducting to the blends compatibilization[22].

Figure 3 SEM images of fractured surface of: Bio-PE (a, b); PCL (c, d); Bio-PE/PCL (90/10) (e, f); Bio-PE/PCL (80/20) (g, h); Bio-PE/PCL (70/30) (i, j); Bio-PE/PCL/PEgMA (90/10/10 phr) (k, l); PE/PCL/PEgMA (80/20/10 phr) (m, n); PE/PCL/PEgMA (70/30/10 phr) (o, p). 

DSC scans acquired during the second heating are presented in Figure 2 (bottom), two endothermic peaks are observed, in the lower temperature region 47.57-62.05°C and in higher temperatures 106.41-138.46°C, associate with the fusion of PCL and Bio-PE, respectively. Similarly to that observed during the melt crystallization, the melting behavior of Bio-PE was not altered in the blends, with the degree of crystallinity ΔXc: 13.27-18.28%. The parameters computed from these scans are found in Tables A1 -A4 and in Figures A6 A7 of Appendix 2 and 3.

The Molten Fraction plots presented a sigmoidal shape characteristic of phase transformation in polymers without discontinuities, behavior similar to that observed during crystallization from the melt (Relative Crystallinity); these curves are presented in Appendix 3, 811. The melting rates of PCL and Bio-PE increased in the blends with values between 30-50% higher than in the neat resins, which can be understood as a facilitated melting process, thus providing a processing with less energy consuming and possibly cheaper[23,24].

3.2 Heat Deflection Temperature (HDT)

Table 2 shows HDT of Bio-PE, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. Addition of PCL to Bio-PE promoted a slight decrease in the HDT of Bio-PE/PCL blends, being a reduction of approximately 3.9% for Bio-PE/PCL blend (90/10); 9.3% for 80/20 and 12.6% for 70/30 blend. This decrease is most like due to the high flexibility, low melting temperature (≈ 60°C) and low glass transition (≈ -60°C) of PCL[25]. These results are in agreement with the data obtained by DSC.

Table 2 Heat deflection temperature (HDT) of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. 

Composition HDT (°C)
Bio-PE 66.8±1.5
Bio-PE/PCL (90/10) 64.2±0.7
Bio-PE/PCL/PEgMA (90/10/10 phr) 64.5±0.4
Bio-PE/PCL (80/20) 60.6±1.0
Bio-PE/PCL/PEgMA (80/20/10 phr) 69.1±0.2
Bio-PE/PCL (70/30) 58.4±0.5
Bio-PE/PCL/PEgMA (70/30/10 phr) 58.9±0.8
PCL 51.3±0.7

The addition of PEgMA to Bio-PE/PCL provided distinct results for the different concentrations of PCL. It is verified for Bio-PE/PCL/PEgMA (90/10/10 phr and 70/30/10 phr) a similar behavior to that presented by their respective binary blends. For the compound 80/20/10 phr, an increase in HDT compared to Bio-PE is observed, this increase being approximately 3.4%, results suggest in this concentration the effect of PEgMA is optimized in terms of higher heat deflexion temperature stability.

In general, the individual contribution of each component and the morphology generated by the phases in polymer blends are the most important characteristics concerned with its performance. Generally, the continuous phase provides greater contribution to the HDT of the blends, as also reported by Ferreira et al.[26] and Luna et al.[27]. Subsequently, the morphology of blends will be examined by SEM, where these results can be better elucidated.

3.3 Mechanical tests – tensile strength

Table 3 presents the results for Elastic Modulus, Tensile Strength and Elongation at Break of the investigated compounds in this work.

Table 3 Tensile properties of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. 

Composition Elastic modulus (MPa) Tensile
strength (MPa)
Elongation at break (%)
Bio-PE 445.2±20.3 22.9±0.4 531.3±26.6
Bio-PE/PCL (90/10) 467.6±15.9 23.6±0.3 252.5±20.6
Bio-PE/PCL/PEgMA (90/10/10 phr) 412.8±11.9 23.2±0.4 425.9±34.6
Bio-PE/PCL (80/20) 465.4±6.9 23.7±0.3 Not determined*
Bio-PE/PCL/PEgMA (80/20/10 phr) 430.8±10.1 23.0±0.5 475.1±15.4
Bio-PE/PCL (70/30) 426.2±6.6 23.3±0.2 13.8±0.9
Bio-PE/PCL/PEgMA (70/30/10 phr) 365.3±10.1 21.5±0.2 Not determined*
PCL 238.5±16.5 18.8 ± 0.3 > 580**

*After cold drawing and neck propagation, the specimens showed formation of fibrils and the equipment was unable to record the rupture;

**Specimen did not break during the test.

From the data shown in Table 3, it is possible to infer that Bio-PE and PCL have high elongation at break, that is, both are able of undergoing large deformations[28,29].

Analyzing the effect of PCL addition on Bio-PE/PCL blends, it was observed that increasing PCL content did not promote a significant change in the Elastic Modulus nor in the Tensile Strength data. In general, the stiffness of immiscible blends may be related with the competitive effect between the performance of the interface and the stiff polymer content that presents higher stiffness (modulus), as reported by Machado et al.[30], Rosa et al.[31], Moura et al.[32] and Silva[33]. In the present work, despite the fact the Bio-PE/PCL blends are immiscible, their mechanical behavior was not negatively affected, by the contrary, the Elastic Modulus of Bio-PE/PCL was observed being ~5% higher than neat Bio-PE, producing a synergic performance.

In relation to the addition of PEgMA, it did not result in higher changes in the Elastic Modulus with observed decreases between 8-15%, on the other hand, the Elongation at Break of Bio-PE/PCL/PEgMA blends showed increases higher than 70% in relation to Bio-PE/PCL blends. These results are linked to the morphological effect among the phases, despite the immiscible character (as observed by DSC scans Figure 2, SEM images Figure 3, Table A1 -A4 and 67 of Appendix 2 and 3), in the amorphous phases of both polymers, secondary interactions are possible to occur, additionally PEgMA contributes to better mechanical performance. SEM images captured with the aim of a better enlightenment, and shown further on[30,33,34], suggest the Elongation at Break of Bio-PE/PCL blends, being the ternary systems with addition of the functionalized copolymer PEgMA improved (higher), which can be resulted from the reaction between maleic anhydride with the hydroxyl (OH) end groups of PCL that may be taken place providing an interface with higher performance, behaviors which can be inferred from decreases in dispersed phase as showed in Figure 3 and Table 4 by dispersed phase’s average diameter measurements[24,25,35-40].

Table 4 Average diameter for the dispersed phase of Bio-PE/PCL blends. 

Composition Average Diameter (µm)
Bio-PE/PCL (90/10) 1.2±0.1
Bio-PE/PCL (80/20) 2.0±0.1
Bio-PE/PCL (70/30) 2.8±0.2

3.4 Impact strength

Table 5 shows the Impact Strength results of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. It is verified that addition of 10% PCL did not promote a significant variation in the impact strength of Bio-PE. On the other hand, blends with 20% and 30% PCL showed higher impact strength with increases of 88.2% for Bio-PE/PCL (80/20) and 83.2% for Bio-PE/PCL (70/30). This increase may be related to the PCL effect that presents elastomeric characteristics, being able to act as a properly impact modifier, thus promoting a significant improvement in the energy absorption mechanisms of the produced blends in this work[33,38,41]. The addition of PEgMA also contributed to increase the impact strength, where increases of 133.2% for Bio-PE/PCL/PEgMA (80/20/10 phr) and 100.3% for Bio-PE/PCL/PEgMA (70/30/10 phr) were reached. This behavior can be attributed to the higher amount of linkages between Bio-PE/PCL phases promoted by the reaction trough maleic anhydride and hydroxyl groups of PCL, as well as the compatibility of PEgMA with Bio-PE, which efficiently drives the tension transfer mechanisms between the phases (Bio-PE matrix and PCL dispersed phase, see SEM images)[24,33,38].

Table 5 Impact Strength of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. 

Composition Impact strength (J/m)
Bio-PE 34.0±1.0
Bio-PE/PCL (90/10) 36.5±3.1
Bio-PE/PCL/PEgMA (90/10/10 phr) 36.0±1.9
Bio-PE/PCL (80/20) 64.0±2.9
Bio-PE/PCL/PEgMA (80/20/10 phr) 79.3±2.8
Bio-PE/PCL (70/30) 62.3±3.8
Bio-PE/PCL/PEgMA (70/30/10 phr) 68.1±5.0
PCL 178.5±4.4

3.5 Scanning Electron Microscopy (SEM)

Figure 3 presents SEM images of Bio-PE, PCL and Bio-PE/PCL and Bio-PE/PCL/PEgMA blends, these images were captured on the fractured surface of the specimens after impact experiments.

In Figure 3ad is observed the surfaces of Bio-PE and PCL with characteristics of ductile fracture evidencing the elastic deformation followed by the plastic one, these images corroborate the previous results obtained with mechanical tests where deformations higher than 500% were reached for the neat polymers.

SEM images of 90/10, 80/20 and 70/30 Bio-PE/PCL blends, respectively, are shown in Figure 3ej. These SEMs present a honeycomb morphology[42], and suggest low interfacial adhesion.

The increase of PCL content into Bio-PE/PCL blends conducted to an increase in the mean diameter of the dispersed phase, (see results in Table 4), leading to the coalescence between PCL domains, which are indicated by the red arrows in Figure 3. In addition, a larger number of PCL domains in Bio-PE/PCL 70/30 were pull out from Bio-PE matrix[43,44], these results agree with those shown in the DSC analyzes and with mechanical properties, where low miscibility was observed.

The effect of PEgMA on the phase behavior of Bio-PE/PCL blends is also shown in Figure 3kp. For Bio-PE/PCL/PEgMA 90/10/10 and 80/20/10 blends is verified a very similar morphology to that of Bio-PE. These images show a homogeneous morphology, and it is difficult to make distinction between the dispersed PCL phase from the Bio-PE matrix. This effect may occur due to the interaction and ability of the compatibillizer (PEgMA) to remain at the interface, promoting a reduction of the interfacial energy and avoiding the domain coalescence, this would be the driving force for the improvement in the impact strength as well as for the increase in the elongation at break as previously presented in mechanical results[45,46].

For the Bio-PE/PCL/PEgMa 70/30/10 blend, Figure 3o, p is observed a morphology similar to that of Bio-PE/PCL 70/30 blend. However, a smaller amount of domains are verified on the fracture surface in relation to the binary blend. At this concentration, the compatibillizer was shown to be less effective compared to the compositions Bio-PE/PCL/PEgMA 90/10/10 and 80/20/10. As also presented in Table 4 the dispersed phase’s average dimater increases with PCL content in binary blends and decreases upon addition of PEgMA, trend observed for Bio-PE/PCL 90/10/10 and 80/20/10, for the blend 70/30/10 the trend change and coalescence increases, suggesting solubility limit barrier was reached.

Summing up, the incorporation of PEgMA provided a better adhesion between the phases, contributing to the homogeneity of the blends in relation to the non-compatibillized ones, i.e., PEgMA led to the morphology stabilization of the blends[32,44,46,47]. It is suggested the addition of PEgMA increases interfacial adhesion due to the chemical interaction between the hydroxyl group of PCL and the maleic anhydride groups, as previously reported by Bezerra et al.[24].

3.6 Contact angle

The contact angle measurement allows evaluating the hydrophilicity and hydrophobicity of the polymer blend surfaces, where this means the interaction energy between the surface and the used liquid. The collected data for the contact angle demonstrates the increased degree of blend surface interaction with water, indicating an increase in its hydrophilic character with the increase of PCL content, which is expected since PCL is the most hydrophilic polymer[48-50].

Figure 4 shows the data of contact angle for Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends, at different times, and Table A5 (Appendix 4) presents the average data with the standard deviation included. For the Bio-PE/PCL blends with 10% and 20% of PCL the contact angle is observed reducing 15.7% and 15%, respectively. For Bio-PE/PCL blend (70/30) the contact angle increased 5.5% related to Bio-PE, as previously observed in Figure 3 and Table 4 at this composition coalescence of PCL dispersed particles took place decreasing the contact area of PCL phase and possibly providing a lower contact angle as presented in Figure 4.

Figure 4 Contact angle of Bio-PE, PCL, Bio-PE/PCL and Bio-PE/PCL/PEgMA blends. 

For Bio-PE/PCL/PEgMA blends, i.e., 90/10/10 and 80/20/10, it was observed that addition of PEgMA promoted stabilization of the contact angle; meanwhile an increase of this parameter was verified for the composition 70/30/10. As previously reported, this is probably due to the occurrence of reactions between the maleic anhydride group and hydroxyl groups of PCL, decreasing the disperse particle size and improving the the system compatilization[24].

4. Conclusions

Processing of Bio-PE/PCL and Bio-PE/PCL/PEgMA blends does lightly interfere in the crystallization and melting events of neat polymers suggesting being mixtures with low miscibility. From HDT data reduced values were observed for the binary blends, meanwhile PEgMA provided subtle increase. Contact angle measurements indicate an increase in the blend’s hydrophilic character increasing PCL content. Addition of PCL to Bio-PE reduced the elastic modulus, increased the elongation at break and impact strength, allowing a control of these properties by changing the blend composition. Impact Strength of compatibilized blends significantly increased when compared to neat Bio-PE being 113.2% higher for Bio-PE/PCL/PEgMA. Addition of PEgMA decreases the phase coalescence conducting to a more stable compounds as evidenced by SEM images. Summing up Bio-PE/PCL/PEgMA (80/20/10) is thermally stable presenting better homogeneity with higher HDT and Impact strength.

Appendix 1


Figure A1 Datasheets – HDPE. 

Figure A2 Datasheets – PCL. 

Figure A3 Datasheets – PEgMA. 

Appendix 2

. DSC Results - Tables.

Table A1 DSC data for Bio-PE collected during the cooling – Melt Crystallization Event. 

First Peak–BioPE
Bio-PE 119.19 115.31 106.04 115.37- 1.7756 0.49 37.88 12.93
PCL - - - -- - - - -
Bio-PE/PCL (70/30) 119.70 116.66 107.52 116.90 2.5037 0.39 42.49 14.50
Bio-PE/PCL (80/20) 119.46 115.91 107.46 116.03 2.1497 0.45 38.24 13.05
Bio-PE/PCL (90/10) 119.38 116.07 107.12 116.15 2.2896 0.43 49.55 16.91
Bio-PE/PCL/PEgMA (70/30/10Pcr) 119.35 116.13 107.52 116.42 2.3361 0.41 43.27 14.77
Bio-PE/PCL/PEgMA (80/20/10Pcr) 119.39 116.59 107.34 116.84 2.2740 0.37 43.86 14.97
Bio-PE/PCL/PEgMA (90/10/10Pcr) 119.36 116.03 105.39 116.49 1.7684 0.42 46.38 15.83

Table A2 DSC data for PCL collected during the cooling – Melt Crystallization Event. 

Second Peak –PCL
Bio-PE - - - - - - - -
PCL 34.42 29.79 23.79 29.77 2.1030 0.49 21.58 15.47
Bio-PE/PCL (70/30) 42.48 37.22 32.91 36.85 2.2325 0.54 11.02 7.90
Bio-PE/PCL (80/20) 43.79 38.80 34.48 - 1.8600 0.50 8.05 5.77
Bio-PE/PCL (90/10) 42.61 38.75 35.18 37.96 2.0444 0.39 6.62 4.75
Bio-PE/PCL/PEgMA (70/30/10Pcr) 44.42 39.47 34.16 39.86 1.6427 0.50 8.95 6.42
Bio-PE/PCL/PEgMA (80/20/10Pcr) 45.17 41.27 37.24 41.39 2.1896 0.39 6.99 5.01
Bio-PE/PCL/PEgMA (90/10/10Pcr) 44.80 41.64 38.47 41.79 2.5397 0.32 5.33 3.82

Table A3 DSC data for PCL collected during the second heating – Fusion Event. 

FirstPeak –PCL
Bio-PE - - - - - - - -
PCL 46.57 56.78 62.05 57.19 1.7776 1.04 19.74 14.15
Bio-PE/PCL (70/30) 47.87 55.08 57.93 55.65 2.9497 0.73 11.03 7.90
Bio-PE/PCL (80/20) 48.32 55.39 58.47 56.05 2.6811 0.71 9.81 7.03
Bio-PE/PCL (90/10) 51.75 55.63 58.11 56.03 3.1103 0.39 9.26 6.63
Bio-PE/PCL/PEgMA (70/30/10Pcr) 46.36 55.14 59.13 56.02 2.4021 0.89 11.62 8.33
Bio-PE/PCL/PEgMA (80/20/10Pcr) 48.63 55.33 58.52 56.19 2.5409 0.67 10.32 7.40
Bio-PE/PCL/PEgMA (90/10/10Pcr) 51.14 55.61 58.02 56.26 2.8503 0.45 7.08 5.07

Table A4 DSC data for Bio-PE collected during the second heating – Fusion Event. 

Second Peak –BioPE
Bio-PE 106.41 131.18 138.46 133.47 1.0994 2.53 41.46 14.15
PCL - - - - - - - -
Bio-PE/PCL (70/30) 110.55 129.88 135.55 131.76 1.5131 1.97 47.05 16.06
Bio-PE/PCL (80/20) 110.98 130.54 136.80 132.46 1.2590 2.00 41.28 14.09
Bio-PE/PCL (90/10) 110.06 130.96 137.04 133.05 1.4486 2.13 53.58 18.29
Bio-PE/PCL/PEgMA (70/30/10Pcr) 110.25 129.82 135.87 131.86 1.4086 1.99 47.68 16.27
Bio-PE/PCL/PEgMA (80/20/10Pcr) 106.97 129.75 136.01 131.77 1.2183 2.32 48.33 16.50
Bio-PE/PCL/PEgMA (90/10/10Pcr) 106.98 130.72 137.58 132.88 1.0978 2.41 49.52 16.90

Appendix 3

DSC parameters 411.

Figure A4 Crystallization Rate of Bio-PE in the investigated compounds. 

Figure A5 Crystallization Rate of PCL in the investigated compounds. 

Figure A6 Melting Rate of Bio-PE in the investigated compounds. 

Figure A7 Melting Rate of PCL in the investigated compounds. 

Figure A8 Relative Crystallinity of Bio-PE in the investigated compounds. 

Figure A9 Relative Crystallinity of PCL in the investigated compounds. 

Figure A10 Molten Fraction of Bio-PE in the investigated compounds. 

Figure A11 Molten Fraction of PCL in the investigated compounds. 

Appendix 4

Contact angle average data with the standard deviation.

Table A5 Average contact angle with its respective standard deviation. 

Composition Contact angle
Bio-PE (100) 71.5±0.7
Bio-PE/PCL (90/10) 60.3±0.7
Bio-PE/PCL (80/20) 60.7±1.1
Bio-PE/PCL (70/30) 75.3±1.9
Bio-PE/PCL/PEgMA (90/10/10) 68.8±1.2
Bio-PE/PCL/PEgMA (80/20/10) 69.8±0.8
Bio-PE/PCL/PEgMA (70/30/10) 77.8±2.0
PCL (100) 61.2±1.1

5. Acknowledgements

The authors thank Addivant for the functionalized copolymers; Labmat (Laboratory of Materials Engineering/CCT/UFCG) for experiments, to MCTI/CNPq, CAPES/PNPD and CAPES, for the financial support.

How to cite: Bezerra, E. B., França, D. C., Morais, D. D. S., Silva, I. D. S., Siqueira, D. D., Araújo, E. M., & Wellen, R. M. R. (2019). Compatibility and characterization of Bio-PE/PCL blends. Polímeros: Ciência e Tecnologia, 29(2), e2019022.

6. References

1 Hemais, C. A., Rosa, E. O. R., & Barros, H. M. (2000). Observações sobre o desenvolvimento tecnológico e os ciclos da indústria de polímeros no Brasil. Polímeros: Ciência e Tecnologia, 10(3), 149-154. [ Links ]

2 Rosa, D. S., Franco, B. L. M., & Calil, M. R. (2001). Biodegradabilidade e propriedades mecânicas de novas misturas poliméricas. Polímeros: Ciência e Tecnologia, 11(2), 82-88. [ Links ]

3 Rosa, D. S., Chui, Q. S. H., Pantano, R., Fo., & Agnelli, J. A. M. (2002). Avaliação da biodegradação de Poli-β-(Hidroxibutirato), Poli-β-(Hidroxibutirato-co-valerato) e Poli-ε-(caprolactona) em solo compostado. Polímeros: Ciência e Tecnologia, 12(4), 311-317. [ Links ]

4 Le Guern, C. (2018). When the mermaids cry: the great plastic tide. Natural Care. Retrieved in 2018, October 20, from http://plastic-pollution.orgLinks ]

5 Ray, S. S., & Bousmina, M. (2005). Biodegradable polymers and their layered silicate nanocomposites: in greening the 21st century materials world. Progress in Materials Science, 50(8), 962-1079. [ Links ]

6 Brito, G. F., Agrawal, P., Araújo, E. M., & Mélo, T. J. A. (2012). Tenacificação do Poli(Ácido Lático) pela adição do terpolímero (Etileno/Acrilato de Metila/Metacrilato de Glicidila). Polímeros: Ciência e Tecnologia, 22(2), 164-169. [ Links ]

7 Bastioli, C. (2005). Handbook of biodegradable polymers. Shrewsbury: Rapra Technology. [ Links ]

8 Associação Brasileira de Normas Técnicas. (2008). NBR 15448-1: embalagens plásticas degradáveis e/ou de fontes renováveis - parte 1: Terminologia. Rio de Janeiro: ABNT. [ Links ]

9 Brito, G. F., Agrawal, P., Araújo, E. M., & Mélo, T. J. A. (2012). Polylactide/Biopolyethylene bioblends. Polímeros: Ciência e Tecnologia, 22(5), 427-429. [ Links ]

10 Braskem Produtos Verdes. Retrieved in 2018, March 19, from ]

11 Swift, G. (1998). Requirements for biodegradable water-soluble polymers. Polymer Degradation & Stability, 59(1-3), 19-24. [ Links ]

12 Braunegg, G., Lefebvre, G., & Genser, K. F. (1998). Polyhydroxyalkanoates, biopolyesters from renewable resources: physiological and engineering aspects. Journal of Biotechnology, 65(2-3), 27-61. PMid:9828458. [ Links ]

13 Zuchowska, O., Hlavata, D., Steller, R., Adamiak, W., & Meissner, W. (1999). Physical structure of polyolefin-starch blends after ageing. Polymer Degradation & Stability, 64(2), 339-346. [ Links ]

14 Pelicano, M., Pachekoski, W., & Agnelli, J. A. M. (2009). Influência da adição de amido de mandioca na biodegradação da blenda polimérica PHBV/Ecoflex. Polímeros: Ciência e Tecnologia, 19(3), 212-217. [ Links ]

15 American Society For Testing and Materials. (2017). ASTM D883: terminology relating to plastics. West Conshohocken: Philadelphia. [ Links ]

16 Amini, M., Mobli, M., Khalili, M., & Ebadi-Dehaghani, H. (2018). Assessment of compatibility in Polypropylene/Poly(lactic acid)/Ethylene vinyl alcohol ternary blends: relating experiments and molecular dynamics simulation results. Journal of Macromolecular Science, Part B: Physics, 57(4), 1-18. [ Links ]

17 Boronat, T., Fombuena, V., Garcia-Sanoguera, D., Sanchez-Nacher, L., & Balart, R. (2015). Development of a biocomposite based on green polyethylene biopolymer and eggshell. Materials & Design, 68, 177-185. [ Links ]

18 Utracki, L. A. (2002). Polymer blends handbook (Vol. 1). Netherlands: Kluwer Academic Publishers. [ Links ]

19 Matta, A. K., Rao, R. U., Suman, K. N. S., & Rambabu, V. (2014). Preparation and characterization of biodegradable PLA/PCL polymeric blends. Procedia Materials Science, 6, 1266-1270. [ Links ]

20 Fel, E., Khrouz, L., Massardier, V., Cassagnau, P., & Bonneviot, L. (2016). Comparative study of gamma-irradiated PP and PE polyolefins part 2: Properties of PP/PE blends obtained by reactive processing with radicals obtained by high shear or gamma-irradiation. Polymer, 82, 217-227. [ Links ]

21 Antunes, M. C. M., & Felisberti, M. I. (2005). Blends of Poly(hydroxybutyrate) and Poly (ε-caprolactone) Obtained from Melting Mixture. Polímeros: Ciência e Tecnologia, 15(2), 134-138. [ Links ]

22 Faker, M., Razavi Aghjeh, M. K., Ghaffari, M., & Seyyedi, S. A. (2008). Rheology, morphology and mechanical properties of polyethylene/ethylene vinyl acetate copolymer (PE/EVA) blends. European Polymer Journal, 44(6), 1834-1842. [ Links ]

23 Greco, R., Mancarella, C., Martuscelli, E., Ragosta, G., & Yin, J. (1987). Polyolefin blends: 1. Effect of EPR composition on structure, morphology and mechanical properties of HDPE/EPR alloys. Polymer, 28(11), 1922-1928. [ Links ]

24 Bezerra, E. B., França, D. C., Morais, D. D. S., Ferreira, E. S. B., Araújo, E. M., & Wellen, R. M. R. (2017). Comportamento reológico do Bio-PE e do PCL na presença do PEgAA e PEgMA. Revista Matéria, 22(1), 1-12. [ Links ]

25 Morais, D. D. S. (2016). Desenvolvimento de blendas de Poliestireno/Poli(ɛ-caprolactona) (Tese de doutorado). Universidade Federal de Campina Grande, Campina Grande. [ Links ]

26 Ferreira, L. A. S., Pessan, L. A., & Hage, E., Jr. (1997). Comportamento mecânico e termo-mecânico de blendas poliméricas PBT/ABS. Polímeros: Ciência e Tecnologia, 7(1), 67-72. [ Links ]

27 Luna, C. B. B., Silva, D. F., & Araújo, E. M. (2014). Estudo do comportamento de blendas de poliamida 6/resíduo de borracha da indústria de calçados. Revista Univap, 20(36), 98-110. [ Links ]

28 Boronat, T., Fombuena, V., Garcia-Sanoguera, D., Sanchez-Nacher, L., & Balart, R. (2015). Development of a biocomposite based on green polyethylene biopolymer and eggshell. Materials & Design, 68, 177-185. [ Links ]

29 Escocio, V. A., Visconte, L. L. Y., Cavalcante, A. P., Furatado, A. M. S., & Pacheco, E. B. A. V. (2015) Study of mechanical and morphological properties of biobased polyethylene (HDPE) and sponge-gourds (Luffa-Cylindrica) agroresidue composites. In Proceedings of the AIP Conference Proceedings 1664 (p. 1-5). USA: AIP Publishing LLC. [ Links ]

30 Machado, A. V., Moura, I., Duarte, F. M., Botelho, G., Nogueira, R., & Brito, A. G. (2007). Evaluation of properties and biodeterioration potential of polyethylene and aliphatic polyester blends. International Polymer Processing, 22(5), 512-518. [ Links ]

31 Rosa, D. C., Guedes, C. G. F., & Bardi, M. A. G. (2007). Evaluation of thermal, mechanical and morphological properties of PCL/CA and PCL/CA/PE-g-GMA blends. Polymer Testing, 26(2), 209-215. [ Links ]

32 Moura, I., Machado, A. V., Duarte, F. M., Botelho, G., & Nogueira, R. (2008). Preparation of biodegradable materials by reactive extrusion. Materials Science Forum, 587-588, 520-524. [ Links ]

33 Silva, T. R. G. (2014). Influência da poli (ε-caprolactona) e de copolímeros funcionalizados no desempenho de blendas com matriz de poli (Ácido-Lático) [Tese de doutorado). Universidade Federal de Campina Grande, Campina Grande. [ Links ]

34 Semba, T., Kitagawa, K., Ishiaku, U. S., Kotaki, M., & Hamada, H. (2007). Effect of compounding procedure on mechanical properties and dispersed phase morphology of poly(lactic acid)/polycaprolactone blends containing peroxide. Journal of Applied Polymer Science, 103(2), 1066-1074. [ Links ]

35 Takasu, A., Oishi, Y., Lio, Y., Inai, Y., & Hirabayashi, T. (2003). Synthesis of aliphatic polyesters by direct polyesterification of dicarboxylic acids with diols under mild conditions catalyzed by reusable rare-earth triflate. Macromolecules, 36(6), 1772-1774. [ Links ]

36 Chevallier, C., Becquart, F., Majeste, J.-C., & Taha, M. (2013). Solvent-free preparation, characterization, and properties of SEBS–g–polycarbonate copolymers. Designed Monomers and Polymers, 6(16), 564-577. [ Links ]

37 Araújo, J. P., Agrawal, P. A., & Mélo, T. J. A. (2015). Blendas PLA/PEgAA: avaliação da reatividade entre os polímeros e da concentração de PEgAA nas propriedades e na morfologia. Revista Eletrônica de Materiais e Processos, 10(3), 118-127. Retrieved in 2018, March 15, from ]

38 Deblieck, R. A. C., Van Beek, D. J. M., Remerie, K., & Ward, I. M. (2011). Failure mechanisms in polyolefines: the role of crazing, shear yielding and the entanglement network. Polymer, 52(14), 2979-2990. [ Links ]

39 Botlhoko, O. J., Ramontja, J., & Ray, S. S. (2018). A new insight into morphological, thermal, and mechanical properties of melt-processed polylactide/poly(ε-caprolactone) blends. Polymer Degradation & Stability, 154, 84-95. [ Links ]

40 França, D. C., Morais, D. D., Bezerra, E. B., Araújo, E. M., & Wellen, R. M. R. (2018). Photodegradation mechanisms on poly(ε-caprolactone) (PCL). Materials Research, 21(5), 1-8. [ Links ]

41 Guimarães, M. J. O. C., Rocha, M. C. G., & Coutinho, F. M. B. (2002). Polietileno de alta densidade tenacificado com elastômero metalocênico: 1. Propriedades mecânicas e características morfológicas. Polímeros: Ciência e Tecnologia, 12(2), 76-84. [ Links ]

42 Roeder, J., Oliveira, R. V. B., Gonçalves, M. C., Soldi, V., & Pires, A. T. N. (2002). Polypropylene/polyamide-6 blends: influence of compatibilizing agent on interface domains. Polymer Testing, 21(7), 815-821. [ Links ]

43 Bucknall, C. B., & Paul, D. R. (2009). Notched impact behavior of polymer blends: Part 1: new model for particle size dependence. Polymer, 50(23), 5539-5548. [ Links ]

44 Liu, H., Song, W., Chen, F., Guo, L., & Zhang, J. (2011). Interaction of microstructure and interfacial adhesion on Impact Performance of Polylactide (PLA) ternary blends. Macromolecules, 44(6), 1513-1522. [ Links ]

45 Plochocki, A. P., Dagli, S. S., & Andrews, R. D. (1990). The interface in binary mixtures of polymers containing a corresponding block copolymer: Effects of industrial mixing processes and of coalescence. Polymer Engineering and Science, 30(12), 741-752. [ Links ]

46 Pracella, M. (2016). Modification of polymer properties. Oxford: Elsevier Science. [ Links ]

47 Sánchez, A., Rosales, C., Laredo, E., Müller, A. J., & Pracella, M. (2001). Compatibility studies in binary blends of PA6 and ULDPE-graft-DEM. Macromolecular Chemistry and Physics, 202(11), 2461-2478.<2461::AID-MACP2461>3.0.CO;2-1. [ Links ]

48 Barcellos, I. O. (1998). Estudo de blendas poliméricas e hidrogéis com aplicações na área biomédica [Tese de doutorado). Universidade Federal de Santa Catarina, Florianópolis. [ Links ]

49 Zinadini, S., Zinatizadeh, A. A., Rahimi, M., Vatanpour, V., & Zangeneh, H. (2014). Preparation of a novel antifouling mixed matrix PES membrane by embedding graphene oxide nanoplates. Journal of Membrane Science, 453(1), 292-301. [ Links ]

50 Rahimi, M., Zinadini, S., Zinatizadeh, A. A., Vatanpour, V., Rajabi, L., Rahimi, Z. (2016). Hydrophilic goethite nanoparticle as a novel antifouling agent in fabrication of nanocomposite polyethersulfone membrane. Journal of Applied Polymer Science, 133(26), 1-13. [ Links ]

Received: March 20, 2018; Revised: January 06, 2019; Accepted: February 20, 2019

Creative Commons License This is an Open Access article distributed under the terms of the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.