Recycling of Pretreated Polyolefin-Based Ocean-Bound Plastic Recycling of Pretreated Polyolefin-Based Ocean-Bound Plastic Waste by Incorporating Clay and Rubber Waste by Incorporating Clay and Rubber

: Plastic waste found in oceans has become a major concern because of its impact on marine organisms and human health. There is signiﬁcant global interest in recycling these materials, but their reclamation, sorting, cleaning, and reprocessing, along with the degradation that occurs in the natural environment, all make it difﬁcult to achieve high quality recycled resins from ocean plastic waste. To mitigate these limitations, various additives including clay and rubber were explored. In this study, we compounded different types of ocean-bound (o-HDPE and o-PP) and virgin polymers (v-LDPE and v-PS) with various additives including a functionalized clay, styrene-multi-block-copolymer (SMB), and ethylene-propylene-based rubber (EPR). Physical observation showed that all blends containing PS were brittle due to the weak interfaces between the polyoleﬁn regions and the PS domains within the polymer blend matrix. Blends containing clay showed rough surfaces and brittleness because of the non-uniform distribution of clay particles in the polymer matrix. To evaluate the properties and compatibility of the blends, characterizations using differential scanning calorimetry (DSC), scanning electron microscopy (SEM), and small-amplitude oscillatory shear (SAOS) rheology were carried out. The polymer blend (v-LDPE, o-HDPE, o-PP) containing EPR showed improved elasticity. Incorporating additives such as rubber could improve the mechanical properties of polymer blends for recycling purposes.


Introduction
Most plastic waste streams contain a mixture of different polymers.For example, an estimated amount of 182,085 metric tons of plastics is discarded into Brazil's Amazon river and enters the Atlantic ocean [1,2].These plastics are ingested by living things including fish, turtles, etc. [1,3,4].In particular, polyolefins including high-density polyethylene (HDPE), low-density polyethylene (LDPE), and polypropylene (PP) account for 82% of the ingested plastics [5].
Sorting different polymers to a high degree of purity is technically challenging and adds a costly step for recycling.Blending of polymers is thus considered as a cost-effective method to recycle comingled plastic waste [6].However, polymers do not blend well.The small entropic gain during mixing makes most polymers immiscible [7].In melt blending, mechanical, thermal, optical, chemical, or rheological properties of recycled polymers could be weakened due to immiscibility of polymers.These inferior properties result from the poor interaction between the phases of the constituent polymers in the blend.Improvement of adhesion between the polymer phases can help attain satisfactory performance of the blend [8,9].To improve compatibility of immiscible blends, additives are commonly used.One of the most used additives is compatibilizers [10].Compatibilizers are added to enhance the interaction between polymer phases.Compatibilizers such as block or graft copolymers serve as surfactants or covalent linkages at the interface, lowering interfacial tension and improving adhesion between phases [11].Compatibilization is mostly achieved by reactive means.This strategy includes trans-reactions, reactive formation of copolymers, formation of ionically bonded structures, and the breaking and recombination of chains via mechanochemical blending [12][13][14].In reactive processing, bonds are formed between dissimilar polymers during blending, and this helps in compatibilizing the immiscible phases of the blend and provides a stable morphology.Improper compatibilization of blends may lead to early mechanical failure due to weakness at the interfaces between phases [15,16].
Studies have been conducted to improve polymer properties by blending.Rivas et al., (2001) studied the possible increase in tensile strength and heat deflection temperature (HDT) of ABS in PET/ABS blend.It was reported that a blend with up to 10 wt% waste PET in ABS showed a higher tensile strength and higher heat deflection temperature when compared to virgin ABS [17].This is just one example of how polymer properties have been improved by blending.
Another method to improve the mechanical/thermal properties of recycled plastics is the addition of additives such as fillers, which could be natural (e.g., biomass), inorganic (e.g., clay), or elastomers (e.g., rubber) [10].Additives have been used as processing aids (to improve polymer processability), antioxidants (to delay degradative processes), fillers (to decrease cost and enhance performance), impact modifiers (to increase impact strength), and compatibilizers (to improve blend morphology and interfacial adhesion) [18].
Clays have been used to improve many different aspects of the performance of polymers.These clays are added to the polymer matrix of thermoplastics to improve their flame retardancy [19,20], barrier properties [19,21], mechanical properties [19], thermal expansion coefficients [22], and gas barrier properties [23].These property improvements depend on the structural configuration and interfacial interaction between the polymer and the clay [24].Some studies have shown that to include exfoliated clay in polymer blends can compatibilize the phases [25,26].Particle shape (spheres, rods), particle radius relative to the radius of gyration of polymer, surface chemistry, and processing method are a few factors that influence the dispersion of clay into nano-size particles and the final properties (e.g., mechanical and thermal properties) of the blends [27].Exfoliation of clay is desired in polymer blends, since properly exfoliated clay can migrate to the blend interface, enhancing the compatibility between the two phases by altering the viscosity of the matrix and preventing droplet coalescence during mixing [28][29][30].If exfoliation is not achieved, the micron-scale clay particles will instead serve as filler particles that can reinforce the blend, but without enhancement of phase compatibility [31].Blending of rubbers such as ethylene-propylene-diene monomer (EPDM) with polymers is an alternative method for improving properties of the blend.An EPDM/PP blend using maleated PP as a compatibilizer with surface-oxidized rubber has shown an improvement in mechanical properties of the blend [32].
Waste polymers tend to have inferior properties due to degradation; thus, the inclusion of virgin polymers in the blend has the tendency to improve the lower properties of the waste polymers.From an economic and environmental point of view, inclusion of virgin polymers in waste blend may improve the quality of the blend and also reduce the waste disposal problem [6].Therefore, blending virgin and waste polymers could be a good strategy to handle waste polymers.
A large number of blending/compatibility studies have been made using virgin polymers and incorporating compatibilizers.To the best of our knowledge, similar studies have not been conducted using plastic waste recovered from the marine environment (e.g., ocean-bound plastic waste), which could be harmful not only to the marine ecosystem but also to human beings [33][34][35].In addition, ocean-bound plastic waste usually has inferior properties (as compared to virgin plastics) due to environmental degradation.In light of this, this paper aims to evaluate the effects of rubber and clay on the performance of polymer blends composed of polyolefin-based ocean-bound plastic waste (which is primarily made of HDPE and PP) [36] In addition, HDPE and PP based ocean-bound plastic waste (o-HDPE and o-PP) were also blended with another two commodity plastics (virgin LDPE, v-LDPE and virgin PS, v-PS) to understand the polymer blend systems composed of polyolefins (o-HDPE, o-PP and v-LDPE) and polyolefins/PS mixture.
Melt mixing was carried out using a micro-compounder.The thermal, mechanical, and rheological properties of the blends were compared to individual waste plastics for recycling purposes.The compatibilizer efficacy using clay, rubber, and compatibilizer was also evaluated.The results obtained from this study are expected to help optimize blend composition and recycling ocean-bound plastic waste.

General Observations of Polymer Blends
As Table 1 shows, polymer blends were created with virgin LDPE (v-LDPE) and PS (v-PS), ocean-bound HDPE (o-HDPE) and PP (o-PP), as well as additives (clay, SMB, and EPR).The compounded filaments were visually evaluated first.Figure S1 (Supplementary Materials) shows images of blended filaments.In general, all blends containing v-PS showed a rough surface and were brittle (Table 1).Owing to great structural differences and the minimal entropic gain from mixing polymers, PS did not blend well with the polyethylene and polypropylene components [37].Blends containing clay typically remained as aggregates in the filament.Filaments containing 30% of clay were very brittle and had clay particles visible on the surface, while the filament with 10% clay was flexible but still showed visible clay particles.The filament with 25% EPR was very flexible due to the elastic properties of EPR.A similar characteristic was observed by Bertin et al. when EPR was used as compatibilizer in the study of virgin and recycled LDPE/PP blends [38].DSC was used to identify any increased compatibility behavior of the blends.Table 2 and Figure 1 show the DSC data obtained from the second heating cycle of polymer blends from −50 • C to 300 • C. The thermogram shows two endothermic peaks of the crystalline portions of the constituent polymers of the blends.Ocean PP (o-PP) shows two endothermic peaks at 130 • C and 162 • C.This may be due to the presence of PE contamination in the recycled PP [39].Another possibility could be that the PP is actually a copolymer with some ethylene to enhance the impact strength [40] PE showed a larger enthalpy of fusion due to a higher composition of both HDPE and LDPE in all the blends.For the blends, only two distinct peaks were observed although the blends contained three polymers.This is attributed to the nearly identical melting temperatures of the PE grades; thus, the two materials could not be resolved separately [41].However, a slight shoulder is observed around 120 • C which is likely from the o-LDPE phase.It is not clear from DSC analysis whether perfect miscibility occurred between HDPE and LDPE.A similar phenomenon is seen in other studies, and it was speculated that some miscibility is possible between the LDPE and HDPE.Although branching extent was not known in this study, other works show that lower branching contents of LDPE improve miscibility of HDPE and LDPE [42][43][44][45].
Table 2. Thermal transition properties (including melting temperature, enthalpy of melting and crystallinity) of polymer blends composed of o-HDPE, v-LDPE and o-PP (from the second heating curve of DSC). of fusion due to a higher composition of both HDPE and LDPE in all the blends.For the blends, only two distinct peaks were observed although the blends contained three polymers.This is attributed to the nearly identical melting temperatures of the PE grades; thus, the two materials could not be resolved separately [41].However, a slight shoulder is observed around 120 °C which is likely from the o-LDPE phase.It is not clear from DSC analysis whether perfect miscibility occurred between HDPE and LDPE.A similar phenomenon is seen in other studies, and it was speculated that some miscibility is possible between the LDPE and HDPE.Although branching extent was not known in this study, other works show that lower branching contents of LDPE improve miscibility of HDPE and LDPE [42][43][44][45].

Scanning Electron Microscopy (SEM)
To evaluate the effects of clay and EPR on the morphology of the ternary blends, three ternary polymer blends (o-HDPE (30%)_o-PP (30%)_v-LDPE (30%), o-HDPE (30%)_o-PP (30%)_v-LDPE 30%)_clay (10%), and o-HDPE (25%)_o-PP (25%)_v-LDPE (25%)_EPR (25%)) were observed under SEM.The study of the morphological characteristics of the selected blends was essential to determine the phase interactions and miscibility of the constituent polymers.The fractured surface was investigated for the blends (Figure 2).The results indicate that the blend without any additive showed large voids, and this could be associated with the incompatibility of the phases.However, results from blends containing clay and EPR showed smaller voids with the exception of a large chunk of EPR appearing.This large chunk may be as a result of poor shearing of the EPR during micro-compounding at low speed.In addition, the EPR used was not received in the form of pellets, but the particle size was manually reduced before compounding.This result also indicates that the particle size of EPR is an important factor to consider when including EPR in a blend.Apart from the large chunks observed in the blend with EPR, there was generally a reduction of the void size in the blend.Increasing the speed of the micro-compounder may reduce the particle size of the EPR due to an increase in shear stress.
ing EPR in a blend.Apart from the large chunks observed in the blend with EPR, there was generally a reduction of the void size in the blend.Increasing the speed of the microcompounder may reduce the particle size of the EPR due to an increase in shear stress.
Theories show the possibility of determining the interfacial energy at the boundary of two polymers [46,47].The miscibility of polymers is associated with the changes in the free surface energy of the polymer blends.This can be studied using surface-sensitive techniques such as contact angle goniometry, atomic force microscopy and X-ray photoelectron spectroscopy [48,49].This could be studied in future research work to advance the fundamental understanding of the polymer blend system.For example, the miscibility of styrene-acrylonitrile/ethylene-propylene-diene blend was estimated through changes of the surface free energy between the interfaces by Sirocic et al. [50].The surface energy also shed some light regarding the governing mechanism of fiber-matrix adhesion in a polypropylene/polyamide carbon fiber reinforced blend [51].Although beyond the scope of this study, we predict that the interfacial energy between polyolefins could be lowered by clay that is properly exfoliated and segregated to the interfaces.

Rheology
A strain sweep was run to determine a strain amplitude in the linear viscoelastic regime for the frequency sweep.A 10% strain was selected and used for further testing (Figure S2). Figure 3a shows the plot of complex viscosity versus angular frequency.The individual o-PP and o-HDPE both show a Newtonian plateau at low frequency, whereas the v-LDPE is more shear thinning in character over the whole frequency range.There is an increase in viscosity at low frequencies in all the blends, reflecting the influence of the v-LDPE in the blends.As Figure 3a shows, no plateau was observed for all the polymer blends tested and thus no Newtonian behavior was found for all the blends.Overall, o-PP and v-LDPE had the lowest magnitude of the viscosity.However, the viscosities of the Theories show the possibility of determining the interfacial energy at the boundary of two polymers [46,47].The miscibility of polymers is associated with the changes in the free surface energy of the polymer blends.This can be studied using surface-sensitive techniques such as contact angle goniometry, atomic force microscopy and X-ray photoelectron spectroscopy [48,49].This could be studied in future research work to advance the fundamental understanding of the polymer blend system.For example, the miscibility of styrene-acrylonitrile/ethylene-propylene-diene blend was estimated through changes of the surface free energy between the interfaces by Sirocic et al. [50].The surface energy also shed some light regarding the governing mechanism of fiber-matrix adhesion in a polypropylene/polyamide carbon fiber reinforced blend [51].Although beyond the scope of this study, we predict that the interfacial energy between polyolefins could be lowered by clay that is properly exfoliated and segregated to the interfaces.

Rheology
A strain sweep was run to determine a strain amplitude in the linear viscoelastic regime for the frequency sweep.A 10% strain was selected and used for further testing (Figure S2). Figure 3a shows the plot of complex viscosity versus angular frequency.The individual o-PP and o-HDPE both show a Newtonian plateau at low frequency, whereas the v-LDPE is more shear thinning in character over the whole frequency range.There is an increase in viscosity at low frequencies in all the blends, reflecting the influence of the v-LDPE in the blends.As Figure 3a shows, no plateau was observed for all the polymer blends tested and thus no Newtonian behavior was found for all the blends.Overall, o-PP and v-LDPE had the lowest magnitude of the viscosity.However, the viscosities of the o-PP and v-LDPE polymer blend increased when they were blended with o-HDPE, EPR, and clay.The clay and EPR may have acted like solid fillers, immobilizing chains at the interfaces and increasing the viscosities of the blend.
Figure 3b shows the storage modulus of the blends versus the angular frequency.Storage modulus describes the elasticity of the polymers.At lower frequency, the blends with LDPE show slight terminal plateauing behavior associated with a high degree of molecular entanglement [52].In the high angular frequency regime, not much difference is seen in the storage modulus of the blends.This suggests that segmental motions of the polymer backbones were unaffected by the clay and EPR.
o-PP and v-LDPE polymer blend increased when they were blended with o-HDPE, EPR, and clay.The clay and EPR may have acted like solid fillers, immobilizing chains at the interfaces and increasing the viscosities of the blend.
Figure 3b shows the storage modulus of the blends versus the angular frequency.Storage modulus describes the elasticity of the polymers.At lower frequency, the blends with LDPE show slight terminal plateauing behavior associated with a high degree of molecular entanglement [52].In the high angular frequency regime, not much difference is seen in the storage modulus of the blends.This suggests that segmental motions of the polymer backbones were unaffected by the clay and EPR.

Tensile Testing
Single virgin and ocean plastic resins (unmixed) were compression molded to understand their processibility and mechanical properties using a traditional molding technique.Compression molded virgin plastics (unmixed) showed a slightly higher flexibility and strength compared to their OPW counterparts.These same single resins (virgin and OPW) were also processed into filaments using a 3-Devo 350 Composer and 3D printed on the Creality 3-D printer.Tensile properties of the 3D printed specimens (unmixed) were similar to those of virgin plastics; however, there were noticeable improvement in the modulus and overall toughness of the 3D printed OPWs compared to their 3D printed virgin plastic counterparts and, in some cases, the compression molded virgin plastic material.When blending both virgin, OPW, and virgin/OPW materials (various types of resin), the 3D printed tensile specimens consistently outperformed the compression molded parts in terms of toughness, indicating that unique properties can be provided by 3D printing of these thermoplastics.In compression molded plastics blends, there was significant phase separation.This effect was likely due to slow cooling and a longer time scale for the resins to phase separate due to immiscibility between the polymers.The extruded and 3D printed plastic blends showed reduced phase separation and improved properties relative to their compression molded counterparts due to rapid cooling on the 3D printer bed, which shortened the time scale for phase separation to occur.These drastically different time scales allowed for improved miscibility of blends and their mechanical properties and were the primary motivation for utilizing 3D printing in this paper.However, it is acknowledged that one may find applications for the compression molded

Tensile Testing
Single virgin and ocean plastic resins (unmixed) were compression molded to understand their processibility and mechanical properties using a traditional molding technique.Compression molded virgin plastics (unmixed) showed a slightly higher flexibility and strength compared to their OPW counterparts.These same single resins (virgin and OPW) were also processed into filaments using a 3-Devo 350 Composer and 3D printed on the Creality 3-D printer.Tensile properties of the 3D printed specimens (unmixed) were similar to those of virgin plastics; however, there were noticeable improvement in the modulus and overall toughness of the 3D printed OPWs compared to their 3D printed virgin plastic counterparts and, in some cases, the compression molded virgin plastic material.When blending both virgin, OPW, and virgin/OPW materials (various types of resin), the 3D printed tensile specimens consistently outperformed the compression molded parts in terms of toughness, indicating that unique properties can be provided by 3D printing of these thermoplastics.In compression molded plastics blends, there was significant phase separation.This effect was likely due to slow cooling and a longer time scale for the resins to phase separate due to immiscibility between the polymers.The extruded and 3D printed plastic blends showed reduced phase separation and improved properties relative to their compression molded counterparts due to rapid cooling on the 3D printer bed, which shortened the time scale for phase separation to occur.These drastically different time scales allowed for improved miscibility of blends and their mechanical properties and were the primary motivation for utilizing 3D printing in this paper.However, it is acknowledged that one may find applications for the compression molded parts that could still bring significant value, such as fencing posts, playground surfacing, and other low flexibility applications.Additional research to compare different processing methods using this formulation of material is therefore recommended.For 3D printed filaments, based on the flexibility and ease of processing, these materials could be used for making toys, tents, mats, and other recreational applications.Table 3 and Figure 4 shows the mechanical properties of the individual polymers and the blends.The addition of clay improved the toughness of polymer blend (as shown in Figure 4), and the addition of EPR largely did the same.EPR improved the elongation of the blend due to its elastic nature, but the ultimate tensile strength of the blend decreased.Notably, the addition of clays led to 3-D printer nozzle clogging, and the addition of EPR led to softening of the polymer to such an extent that the feedgear of the printer cut the polymer stripping material and disabled feeding.Interestingly, the o-HDPE and v-LDPE were the only polymers that were able to undergo strain hardening as printed polymers.parts that could still bring significant value, such as fencing posts, playground surfacing, and other low flexibility applications.Additional research to compare different processing methods using this formulation of material is therefore recommended.For 3D printed filaments, based on the flexibility and ease of processing, these materials could be used for making toys, tents, mats, and other recreational applications.Table 3 and Figure 4 shows the mechanical properties of the individual polymers and the blends.The addition of clay improved the toughness of polymer blend (as shown in Figure 4), and the addition of EPR largely did the same.EPR improved the elongation of the blend due to its elastic nature, but the ultimate tensile strength of the blend decreased.Notably, the addition of clays led to 3-D printer nozzle clogging, and the addition of EPR led to softening of the polymer to such an extent that the feedgear of the printer cut the polymer stripping material and disabled feeding.Interestingly, the o-HDPE and v-LDPE were the only polymers that were able to undergo strain hardening as printed polymers.

Materials and Methods
Table 4 summarizes the properties of polymers used in this study.The polymer types used in this work were virgin high-density polyethylene (v-HDPE) from ExxonMobil

Materials and Methods
Table 4 summarizes the properties of polymers used in this study.The polymer types used in this work were virgin high-density polyethylene (v-HDPE) from ExxonMobil (BA50-100), virgin low-density polyethylene (v-LDPE) from ExxonMobil (LD123.LN), virgin polystyrene (v-PS) from Certene (SGM-140), ocean-bound high-density polyethylene (o-HDPE) (OR.190222), and ocean-bound polypropylene (o-PP) (OR.190252) samples were graciously provided by Oceanworks.Additives used in this study included a styrenemulti-block-copolymer (SMB), a functionalized clay developed by Luna Innovations, and ethylene-propylene-based copolymer rubber (EPR) from ExxonMoobil (Vistalon TM 404) with ethylene content of 44.5 wt% and a low Mooney viscosity of 28 MU [53].The EPR received was not in pellet form (i.e., was in irregular shapes of chunks) and the size of EPR was manually reduced by chopping it into smaller pieces.

Compounding of Materials
Recycled blends were prepared by mixing virgin LDPE, virgin PS, recycled ocean HDPE, recycled ocean PP, EPR SMB, and clay in various ratios.The blends were formulated with nearly equal fractions of each included polymer and a minimal proportion of additives.Blends with virgin polymer are labeled with V (e.g., v-LDPE) while those with recycled ocean plastic are labeled with O (e.g., o-HDPE).Compounding was done in a conical twin screw micro compounder (Xplore TM HT-15, Sittard, The Netherlands) at a screw speed of 15 rpm and a temperature of 200-240 • C [53].Samples were extruded as filaments with a diameter of about 0.5 cm.

Extruding Printer Filament
A 3-Devo 350 Composer (3devo, Claymont, DE, United States) is a filament making machine with automatic spooling.It requires roughly 150-200 g of material.For virgin or recycled pure filament (e.g., 100% o-HDPE, 100% v-LDPE) pellets were added to the hopper directly.Filaments of compounded materials from the DSM Xplore TM were pelletized using tin snips and put into the 3-Devo hopper.Materials were purged between runs with v-HDPE.Contamination was prevented by extruding filament until the color of the filament became consistent and this filament was used for 3-D printing.Between different samples and prior to purging the 3Devo, the contents of the hopper were removed from the feed screw with a vacuum.It requires roughly 150-200 g of material.In using the 3-Devo Composer the material was put into the hopper and the material, when the color became consistent, was used for printing applications.Before adding new materials to the 3Devo the contents of the hopper were removed from the feed screw with a vacuum.In using this machine, the processing conditions for the highest melting point component were used.The processing temperatures for the polymers were set by first setting the feed and nozzle temperature to about 30% above the melting temperature of that class of polymer.The other two temperatures, the mixing temperatures, were set to 10-20 • C greater than the nozzle and feed temperatures.If necessary, to obtain a more consistent filament diameter the nozzle and mixing temperatures were altered.

Printing Tensile Speciments (i.e., Dogbones)
A Creality 3-D printer (nozzle diameter of 0.4 mm) with the Cura software (Ultimaker, Utrecht, the Netherlands) was used to print dogbone specimens.For most samples, the printer was set to 270 • C and the bed temperature was set to 60 • C. The printer was able to extrude all specimens at this temperature.These conditions were chosen to observe how these polymers would behave at temperatures intended for higher processing temperature polymers such as PET.The low bed temperature allows these polymers to be compared to print conditions for acrylonitrile-butadiene-styrene (ABS) print filament.The samples were printed with 100% infill with a crosshatch pattern on the dogbones and a linear pattern through the gauge area of the dogbones.ASTM D638 coupons were printed in all cases.The thickness of the printed dogbones ranged between 0.05-0.13inches and the width ranged between 0.129-0.165inches.Compression molded samples had a thickness of 0.54-0.59inches and a width of 0.16 inches.

Differential Scanning Calorimetry
The melting and crystallization behavior of the polymer blends were determined using differential scanning calorimeter (Discovery RES-02-002-B, TA Instruments, New Castle, DE, USA).Aluminum hermetic pans were used for both reference and blended samples.A heat/cool/heat cycle was used for this experiment.Samples (3-6 mg) were heated at a rate of 10 • C/min to 300 • C and cooled at 10 • C/min to −50 • C. The same heating procedure was repeated.The percent crystallinity of the blended samples was determined using the second heating curve.The percent crystallinity was estimated as the ratio of the enthalpy of the heat of fusion of the sample, ∆H f , to the mass fraction f of the heat of fusion of 100% crystalline of the polymer, ∆H f o , (Equation ( 1)).

Scanning Electron Microscopy
The phase interactions between individual polymers in the blends were investigated using a scanning electron microscope (SEM, JEOL JSM 6390, Tokyo, Japan).Filaments were immersed in liquid nitrogen for 10 min and fractured after they became brittle.Fractured samples were coated with gold for 120 s using a vacuum sputter coater (Denton vacuum desk IV, Denton Vacuum, LLC, Moorestown, NJ, USA).The morphology of the blend was observed under the microscope at a beam energy of 5 kV.

Rheology
The rheological behavior of the blends in the second stage was determined using an ARES-G2 rotational rheometer (ARES 401001.901,TA instrument, New Castle, DE, USA).Sample disks of 25 mm diameter were molded using a micro injection molding machine (Xplore Instruments BV, Sittard, The Netherlands) at 190 • C. A strain sweep was performed at 200 • C to select a strain percentage in the linear viscoelastic region (LVR) for the frequency sweep.A frequency sweep was also performed at 200 • C and at a strain amplitude of 10% (determined to be in the LVR from the strain sweep) over an angular frequency of 100 rad/s to 0.1 rad/s with a constant plate gap of 1.5 mm [59] Click or tap here to enter text.

Tensile Testing
Single virgin and ocean plastic resins (unmixed) were compression molded to understand their processibility and mechanical properties using a traditional molding technique.Tensile testing was conducted on an ADMET tensile tester equipped with serrated clamps at a crosshead sped of 2 in•min −1 .The tensile specimens were ASTM D638 Type V dogbones, and the thickness of each sample was measured prior to testing.The tensile data was taken without an extensometer, and the outputs from the tensile testing were elongated at break and peak yield strength.The only samples that had a greater ultimate tensile stress than yield stress were the v-HDPE and v-LDPE samples.

Conclusions
Polymer blending could be an effective and environmentally conscious means for recycling of plastics materials.Blending of polymers can improve the properties of individual polymers.The incorporation of additives such as compatibilizers, clay, and rubber also has an influence on the properties of the polymer materials.There was no evidence of improvement of miscibility from the differential scanning calorimetry results since the glass transition temperatures of the individual polymers could not be resolved in the blends.Scanning electron microscopy confirmed the immiscibility of the blends without any additive.However, aggregated particles were seen in the blend containing clay.Based on previous literature findings, clay could well have improved the compatibility of the blends

Figure 4 .
Figure 4. Mechanical properties of polymer blends made of ocean-bound plastic waste with a strain of (a) 0-1 mm/mm and (b) 0-10 mm/mm.

Figure 4 .
Figure 4. Mechanical properties of polymer blends made of ocean-bound plastic waste with a strain of (a) 0-1 mm/mm and (b) 0-10 mm/mm.

Table 2 .
Thermal transition properties (including melting temperature, enthalpy of melting, and crystallinity) of polymer blends composed of o-HDPE, v-LDPE, and o-PP (from the second heating curve of DSC).

Table 3 .
Mechanical properties (including ultimate tensile strength and elongation at peak load) of polymer blends composed of o-HDPE, v-LDPE, and o-PP (from the printing tensile bars, n = 3).
* The sample clogged the nozzle so only one sample was printed for these two samples.

Table 3 .
Mechanical properties (including ultimate tensile strength and elongation at peak load) of polymer blends composed of o-HDPE, v-LDPE, and o-PP (from the printing tensile bars, n = 3).

Table 4 .
Properties of polymers used in this study.