# Enhanced Thermal Performance and Impact Strength of UHMWPE/Recycled-PA6 Blends Synthesized via a Melting Extrusion Route

Authors: Xiuying Yang; Junye Cheng; Guangping Zheng; Deqing Zhang
Journal: Advances in Materials Science and Engineering
 (2016)

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## Abstract

The blends of ultra-high molecular weight polyethylene (UHMWPE) and recycled-polyamide 6 (R-PA6) were prepared via a melting extrusion route using high-density polyethylene-graft-maleic anhydride (HDPE-g-MAH) as the compatibilizer. The morphologies and distributions of the chemical components of the blends were characterized by scanning electron microscopy and synchrotron Fourier transform infrared microspectroscopy. The effects of R-PA6 content on the Vicat softening temperature (VST), heat distortion temperature (HDT), and impact strength of the blends were studied. Remarkably, in comparison with those of UHMWPE, the VST and HDT of UHMWPE/R-PA6 blends with 44 wt% R-PA6 were increased to 165.1 and 98.4°C, respectively, and the Charpy impact strength and Izod impact strength of the blends were enhanced to 33.9 and 16.2 kJ/m2, respectively. In addition, it was found that the blending system containing 44 wt% R-PA6 and 48 wt% UHMWPE exhibited the best compatibility when it was prepared using 8 wt% HDPE-g-MAH. The distribution of the phases of UHMWPE and R-PA6 was uniform, and no obvious phase separation was observed in the blends.


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## Body

## 1. Introduction

Ultra-high molecular weight polyethylene (UHMWPE) has a relative molecular weight ranging from 1.5 to 8 million, a dense crystal structure, and excellent chemical inertia. As a consequence, the strength of UHMWPE is not much affected by strong acids and base solutions as well as organic solvents. Besides its chemical stability, UHMWPE possesses the properties of low water absorption, excellent resistances to low temperature, aging, wear, and fatigue, and outstanding toughness for the resistance of impact and cutting. The impact strength of UHMWPE can reach >1070 J/m of the notch and the wear resistance was reported to be ~0.25% of wear rate per cycle. Therefore, UHMWPE has been widely used in various fields such as textile, paper, machinery, and mining [1–4]. In particular, because of their low friction coefficient, high wear, and corrosion resistances, UHMWPE-lined pipes are widely used in oilfields to extend the wax cleaning cycle of oilfield and reduce the swabbing loads as well as the energy consumption during the manufacturing processes of oilfields. Furthermore, UHMWPE is also utilized to repair the old oil pipes to extend their service life time and reduce the production cost of the oilfield [5]. In the oilfields, the actual operating temperature of lined pipes can reach 125°C, whereas the Vicat softening temperature (VST) of the UHMWPE-lined pipes is only 127°C due to the effects of molding process on VST (the VST of UHMWPE resin is 131°C). The low VST reduces the ability of UHMWPE-lined pipes to withstand external loads and increases their damage rate. It is thus an urgent need to increase the softening temperature of UHMWPE-lined pipes of oil wells.Polyamide 6 (PA6) has been widely used in the fields of electricity, machinery, and automobile because of its excellent mechanical properties, abrasion resistance, and workability [6–8]. In spite of high strength, wear and heat resistance, and ease of fabrication and processing for PA6, however, its impact strength, dimensional stability, and barrier properties to moisture are very poor, which limits its application in many fields. The above shortcomings of PA6 can be compensated by blending it with UHMWPE, which has high strength and modulus, high barrier properties to moisture, good wear resistance, and excellent impact strength at low temperature previously mentioned. Unfortunately, UHMWPE is immiscible with PA6. By simple blending of these polymers, we obtained a coarse-phase structure with low interfacial adhesion, leading to poor mechanical properties of the blend. Therefore, it is necessary to incorporate into the blended system a compatibilizer which forms bonds at the interface and imparts to the blend good mechanical properties. In the previous work on the blending modification of UHMWPE and PA6, the major goals were to improve the tensile and impact performances of PA6 by adding a small amount of UHMWPE, and to investigate the effects of compatibilizer [9]. Using HDPE-g-MAH as a compatibilizer for the blends of PA6/UHMWPE (80/20), it was found that the dimensions of UHMWPE domains in the PA6 matrix decreased dramatically as compared with those of the uncompatibilized blending systems [10]. The tensile strength and Izod impact strength of PA6/UHMWPE/HDPE-g-MAH (80/20/20) were about 1.5~1.6 times as high as those of PA6/UHMWPE (80/20) [10]. The UHMWPE-g-acrylic acid was also used as a compatibilizer to prepare the PA6/UHMWPE blends. Investigations on the mechanical property, impact property, crystallization behavior, and frictional property of PA6/UHMWPE suggested that these properties depended mostly on the interfacial structures and the compatibility between UHMWPE and polyamide [11].In this study, we fully take advantage of the high VST of recycled-PA6 (R-PA6) which can reach up to 210°C and prepare the UHMWPE/R-PA6 blends using HDPE-g-MAH as the compatibilizer. The effects of the blending compositions on the VST, heat distortion temperature (HDT), impact resistance, and blending morphologies are investigated. This study could lay a solid foundation for the industrial applications of UHMWPE-lined pipes in oilfield with low cost and high VST.


## 2. Experimental

### 2.1. Materials

UHMWPE (M-III) of a weight-average molecular weight of 3.5 million was purchased from Beijing Chemical Agent Second Factory. R-PA6 with a relative viscosity larger than 2.5 and HDPE-g-MAH with a grafting ratio of 0.8 wt% were prepared in our lab based on reported methods [10, 12].


### 2.2. Preparation Process

R-PA6 was first dried at 80°C for 12 h in vacuum. Then HDPE-g-MAH, UHMWPE, and dried R-PA6 were mixed in certain proportion. The blends were prepared by reactive blending of the components in a homemade twin-screw extruder (ϕ
=
30 mm and L
/
D
=
44) at a constant speed of 160 r/min. The processing temperature was at about 235–250°C. In the next step, the extruded material was granulated and dried. Subsequently the obtained material was molded into specimens using an injection molding machine. Finally the specimens were annealed at 80°C for 3 h to reduce the internal stresses.


### 2.3. Characterization

The Charpy impact strength, Izod impact strength, VST, and HDT were measured according to the ISO 179-1: 2000, ISO 180: 2000, ISO 306: 1994, and ISO 75-1: 2003 protocols, respectively. Thermal analyses were performed by differential scanning calorimetry (DSC, Netzsch 204 F1, Germany) in air at a heating rate of 10°C/min. A scanning electron microscope (SEM, HITACHI S-4300, HITACHI, Japan) was used to observe the morphologies of the blends. Before observation, the examined sections were coated with gold in a vacuum. Synchrotron FTIR microspectroscopy and mapping technology (FTIR/NIR Spectrometer Frontier and FTIR Microscope Spotlight 400, PE, USA) were used to characterize the compositions and distributions of the blending materials.


## 2.1. Materials

UHMWPE (M-III) of a weight-average molecular weight of 3.5 million was purchased from Beijing Chemical Agent Second Factory. R-PA6 with a relative viscosity larger than 2.5 and HDPE-g-MAH with a grafting ratio of 0.8 wt% were prepared in our lab based on reported methods [10, 12].


## 2.2. Preparation Process

R-PA6 was first dried at 80°C for 12 h in vacuum. Then HDPE-g-MAH, UHMWPE, and dried R-PA6 were mixed in certain proportion. The blends were prepared by reactive blending of the components in a homemade twin-screw extruder (ϕ
=
30 mm and L
/
D
=
44) at a constant speed of 160 r/min. The processing temperature was at about 235–250°C. In the next step, the extruded material was granulated and dried. Subsequently the obtained material was molded into specimens using an injection molding machine. Finally the specimens were annealed at 80°C for 3 h to reduce the internal stresses.


## 2.3. Characterization

The Charpy impact strength, Izod impact strength, VST, and HDT were measured according to the ISO 179-1: 2000, ISO 180: 2000, ISO 306: 1994, and ISO 75-1: 2003 protocols, respectively. Thermal analyses were performed by differential scanning calorimetry (DSC, Netzsch 204 F1, Germany) in air at a heating rate of 10°C/min. A scanning electron microscope (SEM, HITACHI S-4300, HITACHI, Japan) was used to observe the morphologies of the blends. Before observation, the examined sections were coated with gold in a vacuum. Synchrotron FTIR microspectroscopy and mapping technology (FTIR/NIR Spectrometer Frontier and FTIR Microscope Spotlight 400, PE, USA) were used to characterize the compositions and distributions of the blending materials.


## 3. Result and Discussion

It is known that the VST and HDT of UHMWPE are 127°C and 95°C, respectively, whereas the VST and HDT of R-PA6 are 213°C and 177°C, respectively [13, 14]. Figure 1 shows the effects of R-PA6 additions on the VST and HDT of UHMWPE/PA blends prepared by using 8 wt% HDPE-g-MAH compatibilizer. The VST and HDT increase gradually with increasing content of R-PA6. When the contents of R-PA6 are 44 wt% and 52 wt%, the VST of the UHMWPE/PA blends reach 165.1°C and 197.9°C, respectively, and the HDT are as high as 98.4°C and 96.3°C, respectively. The results demonstrate that the addition of R-PA6 significantly improves the thermal performance of UHMWPE/PA.Figure 1
The effect of R-PA6 content on the thermal performance of UHMWPE/R-PA6/HDPE-g-MAH.Figure2 shows the effects of R-PA6 addition on the impact strength of UHMWPE/R-PA6/HDPE-g-MAH. As the R-PA6 content increases, both the Charpy impact strength and Izod impact strength of UHMWPE/R-PA6/HDPE-g-MAH tend to decrease, which are mainly attributed to the low impact strength of the R-PA6 component [15]. The impact performance is also associated with the effects of HDPE-g-MAH on the compatibility and the distribution of blending components [16]. When the HDPE-g-MAH is dispersed on the interface between UHMWPE and R-PA6, the MAH segments of HDPE-g-MAH could react with the terminal amines or carboxyl groups of R-PA6, resulting in the reduced interfacial tension, the improved interfacial wetting, and the enhanced interfacial bonding strength for more convenient load transfer and better dispersion of the components. As a consequence, the impact strength of UHMWPE/R-PA6 can be improved. However, the HDPE-g-MAH only enhances the compatibility between R-PA6 and UHMWPE with appropriate contents and the excessive or too less R-PA6 content would reduce the compatibility, resulting in the reduced impact strength of UHMWPE/R-PA6. As shown in Figure 2, when the content of R-PA6 is 44 wt%, the impact strength of UHMWPE/R-PA6 reaches a local maximum. For example, the Charpy impact strength and Izod impact strength of UHMWPE/R-PA6 with 44 wt% R-PA6 are 33.9 and 16.2 kJ/m2, respectively, which could meet the impact strength requirement for oil exploitation equipment.Figure 2
The effect of R-PA6 content on the impact strength of UHMWPE/R-PA6/HDPE-g-MAH.Figure3 shows the DSC curves of UHMWPE/R-PA6/HDPE-g-MAH blending materials with different chemical compositions. As shown in Figure 3, distinct melting and decomposition peaks in the DSC curves for the blends can be observed at 0~600°C, and the peak temperatures are almost independent of the R-PA6 content. These observations suggest that UHMWPE and R-PA6 are thermodynamically incompatible. Hence, the blending process seems to have no obvious effects on their crystal morphologies, melting points, and thermal decompositions. In addition, it is noted that the melting points of neat R-PA6 and UHMWPE are both higher than other UHMWPE/R-PA6/HDPE-g-MAH blends. This may be attributed to the lower crystallinity for blending materials after melt blending of different components.Figure 3
DSC curves of UHMWPE/R-PA6/HDPE-g-MAH with different amounts of R-PA6 and neat UHMWPE.Figure4 shows the SEM images of the fracture surfaces of the UHMWPE/R-PA6/HDPE-g-MAH blending materials with different chemical compositions. The two components, UHMWPE and R-PA6, can not be distinguished in these images. When the content of R-PA6 is 40 wt%, large cracks and wiredrawing-like HDPE-g-MAH are found on the fracture surface of the UHMWPE/R-PA6/HDPE-g-MAH blending materials. When the content of R-PA6 is 44 wt%, instead, less cracks and dramatically reduced wiredrawing-like HDPE-g-MAH are observed on the fracture surface which is relatively uniform and smooth compared to that of the blend with a R-PA6 content of 40 wt%. As a contrast, Figure 4(c) shows the SEM image of the fracture surfaces of the UHMWPE/R-PA6 blending materials without compatibilizer. From this image, it is found that there is obvious separation of the two phases and R-PA6 takes on sphere-like shape. These results indicate that when the R-PA6 content is 44 wt%, with 8 wt% HDPE-g-MAH as the compatibilizer, the compatibility between UHMWPE and R-PA6 is the best. Because the dispersion of HDPE-g-MAH molecules at the interface between the two incompatible phases could reduce the interfacial tension, improve the viscosity between phases, and promote the integration of these two phases, therefore the HDPE-g-MAH improves the compatibility between UHMWPE and R-PA6 and their phase interface becomes indistinct and the number of cracks can be decreased on the fracture surface.Figure 4
SEM images of UHMWPE/R-PA6/HDPE-g-MAH blending material with different R-PA6 compositions: (a) 40 wt% and (b) 44 wt%; (c) SEM image of UHMWPE/R-PA6 blending material.
(a)
(b)
(c)Synchrotron FTIR microspectroscopy and mapping technology have been employed to better characterize the phase separation of UHMWPE and R-PA6 in the blends. As shown in Figure6, the peak at 1637.8 cm−1 is attributed to the typical absorption peak of the carbonyl group in the amide, indicating that the chemical component at point A in Figure 5 could be R-PA6 [17]. Single-peak comparison mode for the peak at 1637.8 cm−1 is shown in Figure 7 where the upward convex portion results from the peak at 1637.8 cm−1, that is, the R-PA6 component. As shown in Figure 7, with 8 wt% HDPE-g-MAH as the compatibilizer, the distribution of R-PA6 in UHMWPE/R-PA6 with 44 wt% R-PA6 is more uniform than that in UHMWPE/R-PA6 with 40 wt% R-PA6. The result is in good agreement with the observation that the UHMWPE/R-PA6 with 44 wt% R-PA6 has a better impact strength, as shown in Figure 2.Figure 5
Intensity distribution map of UHMWPE/R-PA6/HDPE-g-MAH sample with 40 wt% R-PA6.Figure 6
FTIR spectrum at point A in Figure5. The peak at 1637.8 cm−1 is indicated.Figure 7
Intensity distribution 3D-maps of synchrotron FTIR microspectroscopy at 1637.8 cm−1 and mapping for the fracture surface of UHMWPE/R-PA6/HDPE-g-MAH blends with different R-PA6 compositions: (a) 40 wt% and (b) 44 wt%.
(a)
(b)


## 4. Conclusion

The VST and HDT of the UHMWPE/R-PA6/HDPE-g-MAH blends containing 8 wt% of HDPE-g-MAH compatibilizer and 44 wt% R-PA6 are as high as 165.1°C and 98.4°C, respectively, and the Charpy strength and Izod impact strength are 33.9 and 16.2 kJ/m2, respectively. The results of DSC, SEM, and synchrotron FTIR microspectroscopy and mapping technology demonstrate that the UHMWPE and R-PA6 are thermodynamically incompatible. Remarkably, the addition of R-PA6 is found to effectively increase the VST and HDT of UHMWPE material systems and reduce the cost of materials for UHMWPE-lined pipes.



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*Source: 8089525-2016-04-26.xml*