# Tailored sPP/Silica Nanocomposite for Ecofriendly Insulation of Extruded HVDC Cable

Authors: Bin Dang; Jinliang He; Jun Hu; Yao Zhou
Journal: Journal of Nanomaterials
 (2015)

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## Abstract

Cross-linked polyethylene (XLPE) is a thermosetting material that cannot be recycled at the end of its lifetime. This study investigated the potential of syndiotactic polypropylene (sPP)/silica as an ecofriendly extruded insulation system for HVDC cables. We investigated the morphology, Fourier transform infrared, and thermal, thermomechanical, and electrical behaviors of sPP modified with 0.5–3% nanosilica. We found that the silica/sPP nanocomposite without cross-linking offered a suitable mechanical modulus at room temperature and sufficient intensity at high temperatures, and adding nanosilica modified by a silane coupling agent to the sPP resulted in significant DC resistivity and space charge improvement. The optimal nanosilica content in the sPP was determined by balancing the mechanical and thermomechanical characteristics and the DC resistivity. The sPP/silica nanocomposite reported here shows great potential as a candidate insulation material for future ecofriendly extruded HVDC cables.


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## Body

## 1. Introduction

Extruded cables with cross-linked polyethylene (XLPE) insulation have been successfully applied for high-voltage direct current transmission in power systems because of their favorable combination of superior mechanical, thermomechanical, and electrical properties. However, it is difficult to recycle the XLPE when the cable reaches the end of its life, because of the thermosetting properties of XPLE; it must therefore be burnt, resulting in great damage to the environment. Minimizing the detrimental environmental effects that result from the disposal of XLPE is important. The difficulty in producing recyclable power cable insulation lies in combining good mechanical properties at room temperature with good thermomechanical properties at the operating temperature.Recent studies have investigated novel thermoplastic alternatives for the electrical insulation of extruded cables [1–5]. The potential replacements for XLPE for next-generation extruded cables can be divided into ethylene and propylene systems. For ethylene systems, low-density polyethylene (LDPE) and its blends [1], high-density polyethylene (HDPE) and its blends [2], and LDPE/HDPE blends [3] have been investigated. It was found that LDPE and HDPE have a lower operating temperature than polypropylene and that HDPE is too rigid to be used with cables and must be blended with elastomer. Another candidate material for cables is polypropylene; polypropylene has a higher melting temperature than polyethylene. However, a series of experiments on isotactic polypropylene (iPP) showed that iPP was a stiff material that lacked the requisite flexibility at room temperature that would allow it to be incorporated into cables. Researchers have studied propylene-based copolymers [4] and alloys [5]. Unfortunately, studies [5] revealed that none of the iPP-based systems satisfied all of the requirements of an ideal thermoplastic insulation system, namely, low-temperature flexibility, high-temperature integrity, and high breakdown strength.Syndiotactic polypropylene (sPP), which has a potentially sufficient flexibility, in contrast with iPP, and low dielectric loss and high breakdown strength [6], is a promising candidate for new insulation materials. The disadvantage of sPP is its slow crystallization rate, which will limit its commercial application [7]. The addition of nanoparticles can enhance the crystallization rate, thus reducing the processing time. Polymer nanocomposites have attracted much attention for the insulation of HVDC, based on polyethylene copolymers, because of their improved electrical properties [7]. Nanoparticles have a larger interfacial area than microcomposites and can thus determine the properties of nanofillers, even at low volume fractions in such fillers [8]. However, the nanoparticles have a strong tendency to aggregate, which may degrade the performance of the nanocomposites. Such nanoparticles are therefore typically functionalized, to avoid agglomeration and maintain the stability of the nanoparticles within the polymer matrix [9].In this study, by analyzing the morphology, Fourier transform infrared spectra, thermal and thermomechanical characteristics, tensile testing, DC resistivity, and space charge characteristics of sPP/silica nanocomposites, the most suitable candidate materials to meet the ever-growing demand for ecofriendly, highly efficient HVDC cables were identified.


## 2. Experiments

### 2.1. Materials

Commercial syndiotactic polypropylene 1471 (Total Fina, France) with a melt flow index of 4 g/10 min, a density of 0.88 g/cm3, and a melting point of 130°C was used. Syndiotactic polypropylene 1471 is a low-crystallinity, syndiotactic form of copolymer polypropylene. Nanosilica (Sigma-Aldrich, USA) with an average diameter of approximately 5–15 nm was used as the nanoparticles. Dimethyldichlorosilane (hereafter chl) (Sinopharm Chemical Reagent Beijing Co., Ltd., China) was used as a surface modification agent.


### 2.2. Functionalization of the Silica Nanoparticles

The surface modification of the original silica nanoparticles was performed as follows [10]: The silica was vacuum dried for 24 h immediately prior to compounding. Then, 10 g of silica and 100 mL of xylene were mixed in a beaker. After sonication for 30 min, the mixture was transferred to a three-necked, round-bottom flask, and 5 g chl was added to the flask. This mixture was heated to 130°C in an oil bath and refluxed for 12 h under magnetic stirring. The nanoparticles were washed with deionized water and separated from the reaction mixture via centrifugation performed at 4000 rpm for 30 min; they were then dried under vacuum at 100°C for 24 h.


### 2.3. Preparation of sPP/Silica Nanocomposite Films

Four propylene-based systems were studied, as shown in Table1. The systems were manually premixed, and the mixture was melt blended in a HAKKE minilab II at 200°C for 5 min. All samples were manufactured using hot pressing. 150 μm films were prepared via premelting performed using a curing press operated at 200°C for 10 min, followed by pressing under a pressure of ~20 MPa for 10 min and pressing at 25°C under a pressure of ~5 MPa for a further 10 min.Table 1
Materials used in this investigation.
Abbreviation
Composition (weight ratio)
PP
chl-silica
sPP
100
0
0.5 phr
100
0.5
1 phr
100
1
3 phr
100
3All samples were sandwiched between two pieces of cover steel plate under a short-circuit state and annealed at 100°C for 2 h in the vacuum chamber, to estimate the residual stress.


### 2.4. Characterization

To investigate the dispersibility of the chl-silica nanoparticles in the sPP matrix and the morphology, cross-sectional scanning electron microscopy (SEM) images were obtained using an ultrahigh-resolution HITACHI S-5500 instrument operated at 5 kV. The samples were fractured in liquid nitrogen and then coated with carbon prior to examination under the electron beam. Fourier transform infrared (FTIR) spectra were measured over the range of 4000–500 cm−1, using a Nicolet 6700 FTIR instrument. Differential scanning calorimetry (DSC) measurements on ~5 mg samples were performed under a nitrogen atmosphere, using a heating/cooling rate of 10°C min−1 between 20°C and 150°C, using a TA Q2000 instrument. The thermal stability of ~10 mg samples was determined using a TGA Q5000 series thermogravimetric analyzer (TA Instruments, USA), using a heating rate of 10°C min−1 in an ambient air environment. Dynamic mechanical thermal analysis (DMTA) was performed using a TA Q800 instrument. The investigated samples (with dimensions of 20 mm × 5 mm) were cooled to −30°C and heated to 120°C under nitrogen flow, using a heating rate of 3°C min−1, under a strain-controlled sinusoidal tensile loaded at a frequency of 1 Hz and a strain of 0.01%. Tensile testing was undertaken at different temperature using a TA Q800 instrument at a fixed speed of 250 μm min−1. Rectangle specimens with a cross section of 5 mm × 2 mm were prepared for the measurements. DC resistivity measurements were performed using a three-terminal-cell system, according to ASTM D257-14. The applied DC electrical field was 6 kV mm−1, and the measurements were performed for 60 min, long enough for the polarization current to reach a steady state. The DC electrical field of 60 kV/mm was applied to the plate samples for 1800 seconds, using an electric pulse with an amplitude of 800 V and duration of 7 ns. The space charge measurements were carried out using a pulsed electroacoustic method (PEA) system equipped with a Lecroy WaveRunner 610Zi (1 GHz, 20 GS/s digital oscilloscope).


## 2.1. Materials

Commercial syndiotactic polypropylene 1471 (Total Fina, France) with a melt flow index of 4 g/10 min, a density of 0.88 g/cm3, and a melting point of 130°C was used. Syndiotactic polypropylene 1471 is a low-crystallinity, syndiotactic form of copolymer polypropylene. Nanosilica (Sigma-Aldrich, USA) with an average diameter of approximately 5–15 nm was used as the nanoparticles. Dimethyldichlorosilane (hereafter chl) (Sinopharm Chemical Reagent Beijing Co., Ltd., China) was used as a surface modification agent.


## 2.2. Functionalization of the Silica Nanoparticles

The surface modification of the original silica nanoparticles was performed as follows [10]: The silica was vacuum dried for 24 h immediately prior to compounding. Then, 10 g of silica and 100 mL of xylene were mixed in a beaker. After sonication for 30 min, the mixture was transferred to a three-necked, round-bottom flask, and 5 g chl was added to the flask. This mixture was heated to 130°C in an oil bath and refluxed for 12 h under magnetic stirring. The nanoparticles were washed with deionized water and separated from the reaction mixture via centrifugation performed at 4000 rpm for 30 min; they were then dried under vacuum at 100°C for 24 h.


## 2.3. Preparation of sPP/Silica Nanocomposite Films

Four propylene-based systems were studied, as shown in Table1. The systems were manually premixed, and the mixture was melt blended in a HAKKE minilab II at 200°C for 5 min. All samples were manufactured using hot pressing. 150 μm films were prepared via premelting performed using a curing press operated at 200°C for 10 min, followed by pressing under a pressure of ~20 MPa for 10 min and pressing at 25°C under a pressure of ~5 MPa for a further 10 min.Table 1
Materials used in this investigation.
Abbreviation
Composition (weight ratio)
PP
chl-silica
sPP
100
0
0.5 phr
100
0.5
1 phr
100
1
3 phr
100
3All samples were sandwiched between two pieces of cover steel plate under a short-circuit state and annealed at 100°C for 2 h in the vacuum chamber, to estimate the residual stress.


## 2.4. Characterization

To investigate the dispersibility of the chl-silica nanoparticles in the sPP matrix and the morphology, cross-sectional scanning electron microscopy (SEM) images were obtained using an ultrahigh-resolution HITACHI S-5500 instrument operated at 5 kV. The samples were fractured in liquid nitrogen and then coated with carbon prior to examination under the electron beam. Fourier transform infrared (FTIR) spectra were measured over the range of 4000–500 cm−1, using a Nicolet 6700 FTIR instrument. Differential scanning calorimetry (DSC) measurements on ~5 mg samples were performed under a nitrogen atmosphere, using a heating/cooling rate of 10°C min−1 between 20°C and 150°C, using a TA Q2000 instrument. The thermal stability of ~10 mg samples was determined using a TGA Q5000 series thermogravimetric analyzer (TA Instruments, USA), using a heating rate of 10°C min−1 in an ambient air environment. Dynamic mechanical thermal analysis (DMTA) was performed using a TA Q800 instrument. The investigated samples (with dimensions of 20 mm × 5 mm) were cooled to −30°C and heated to 120°C under nitrogen flow, using a heating rate of 3°C min−1, under a strain-controlled sinusoidal tensile loaded at a frequency of 1 Hz and a strain of 0.01%. Tensile testing was undertaken at different temperature using a TA Q800 instrument at a fixed speed of 250 μm min−1. Rectangle specimens with a cross section of 5 mm × 2 mm were prepared for the measurements. DC resistivity measurements were performed using a three-terminal-cell system, according to ASTM D257-14. The applied DC electrical field was 6 kV mm−1, and the measurements were performed for 60 min, long enough for the polarization current to reach a steady state. The DC electrical field of 60 kV/mm was applied to the plate samples for 1800 seconds, using an electric pulse with an amplitude of 800 V and duration of 7 ns. The space charge measurements were carried out using a pulsed electroacoustic method (PEA) system equipped with a Lecroy WaveRunner 610Zi (1 GHz, 20 GS/s digital oscilloscope).


## 3. Results and Discussion

### 3.1. FTIR Characterization

The surface modification of inorganic nanoparticles enlarges the interface between the matrix and the nanoparticles, leading to improvements in the performance of the nanocomposites. The silica nanoparticles, which were functionalized via surface modification, were characterized using FTIR, as shown in Figure1. The silica, which had O-H groups, showed an absorption peak at 3427 cm−1 [16]. The FTIR spectra clearly illustrated the presence of fewer silicon hydroxyls in the chl-silica, indicating the enhancement of the surface hydrophobicity of the silica nanoparticles after the surface modification. Another change in the FTIR spectra was related to the wavenumbers at 2966 cm−1 and 2870 cm−1, which represented carbon hydrogen bonds. Compared with the lack of absorption at these two wavenumbers for the silica nanoparticles, the presence of absorption signals for the chl coupling agent indicated that the chl had been successfully grafted to the surface of the silica nanoparticles.Figure 1
FTIR spectra for silica nanoparticles.


### 3.2. Dispersion and Morphology

Particle dispersion is the key factor in controlling the properties of nanocomposites. Figure2 shows SEM images illustrating the dispersion of the nanoparticles in the nanocomposites with 3 phr chl-silica. Similar images were obtained for the other samples. The images suggested that the silica nanoparticles with a polymer shell were well dispersed in the sPP matrix, with good compatibility. It is likely that the excellent compatibility of the silica nanoparticles and the sPP matrix originated from the surface modification with the silane coupling agent.Figure 2
SEM images demonstrating the dispersibility of the silica nanoparticles and showing the cross-sectional microstructure of the sample; (b) is a partial enlargement of the frame shown in (a).
(a)
(b)


### 3.3. Thermal Analysis

Figure3 presents the melting and crystallization behaviors of the sPP/chl-silica nanocomposites as a function of the chl-silica content. Figure 3(a) shows that the sPP nanocomposites had two distinct melting transitions, in accordance with results from a previous study [17]. The melting temperature of the neat sPP was higher than that of LDPE or LLDPE, and that melting temperature shifted to a higher temperature when the chl-silica was incorporated into the sPP matrix. The sPP nanocomposites therefore all appear to be good candidates for HVDC cable applications, at least from the point of view of their melting behavior.Figure 3
Melting (a) and crystallization (b) curves for the sPP/silica nanocomposites.
(a)
(b)The nonisothermal crystallization curves for the pure sPP and its nanocomposites shown in Figure3(b) indicate that the crystallization temperature moved to a higher temperature when the chl-silica was added to the sPP matrix, proving that incorporating the chl-silica had a great effect on the nucleation of the nanocomposites. The higher the crystallization temperature, the shorter the cooling time. Hence, the sPP nanocomposites had a shorter processing cycle compared with sPP.Thermogravimetric analysis was performed in an attempt to understand the degradation characteristics of the samples, which are important for the processing of the power cable. The thermogravimetry (TG) and derivative thermogravimetry (DTG) results are shown in Figure4. The temperatures at which the maximum rate of heat consumption occurred for this degradation process are listed in Table 2 for the various nanocomposites. Table 2 shows that sPP with 1 phr and 3 phr chl-silica had a maximum decomposition temperature of 347.6°C and 352.8°C, respectively.Table 2
Degradation temperatures for the sPP/chl-silica samples, obtained from TGA results.
Sample
T
degrad
(°C)
sPP
333.5
0.5 phr
331.5
1 phr
347.6
3 phr
352.8Figure 4
TG and DTG curves for the sPP/chl-silica nanocomposites.


### 3.4. Dynamic Mechanical and Thermal Characteristics

HVDC cables are typically installed at room temperature and operate at high temperatures. It is therefore necessary to focus on the mechanical properties at room temperature and at high temperatures. Figure5(a) shows a plot of the storage modulus as a function of temperature. The results indicated that all samples had a storage modulus of ~500 MPa at room temperature, lower than that of isotactic polypropylene (~1000 MPa). All of the samples showed a storage modulus of ~100 MPa at high temperatures, higher than that of LDPE or LLDPE.Figure 5
Storage modulus (a) andtan⁡δ (b) for the sPP/chl-silica nanocomposites.
(a)
(b)We determined from thetan⁡δ curves in Figure 5(b) that the characteristic peak for polypropylene was at ~12°C. The peak in the tan⁡δ curve was due to the glass transition characteristic of sPP [18]. The presence of the nanosilica did not change the glass transition temperature of the composites.


### 3.5. Tensile Testing

Figure6 shows the typical tensile stress-strain curves of sPP nanocomposites at different temperatures. Furthermore, elastic modulus and tensile yield strength of the samples at different temperatures are presented in Figure 7. It can be seen from Figure 6 that all four materials at different temperature displayed a characteristic necking behavior after imposed strain and had high breaking elongation (more than 200%). The high breaking elongation at room temperature indicates that the nanocomposites have sufficiently high mechanical flexibility for cable installation. From Figure 7, the elastic modulus increased and the tensile yield strength decreased at different temperatures when the chl-silica was added to the sPP matrix. In addition, an elastic modulus at room temperature of ~110 MPa and sufficient elastic modulus at high temperature for sPP nanocomposites indicate that the nanocomposites are suitable for cable applications [11].Figure 6
Tensile tests results at different temperatures (a) sPP, (b) 0.5 phr, (c) 1 phr, and (d) 3 phr.
(a)
(b)
(c)
(d)Figure 7
Elastic modulus (a) and tensile yield strength (b) for sPP nanocomposites at different temperatures.
(a)
(b)


### 3.6. DC Resistivity

The dielectric loss from HVDC cables results mainly from the leakage current. Figure8 shows the leakage current density and DC resistivity of the samples at room temperature. The pure sPP showed a higher leakage current and took less time to reach stability, compared with the other samples. The electric field distribution within the insulation of an HVDC cable depends on the DC resistivity. The volume resistivity was evaluated from the leakage current value noted 60 minutes after the application of the DC voltage shown in Figure 8(b). Under the applied field, the volume resistivity of the films with silica nanofillers was higher than that of the pure sPP; in particular, the sPP with 1% chl-silica exhibited a volume resistivity that was one order of magnitude higher than that shown by the base polymer. A possible reason for this was the good dispersion of the chl-silica in the sPP matrix. For polymer nanocomposites, the nanoparticle-polymer interactions play an important role in determining the materials’ performance [19]. More specifically, this phenomenon was related to the introduction of deeper carrier traps by the incorporation of the nanosilica [20]. The nanocomposite with 1 phr chl-silica had the lowest leakage current density, showing that this sample had more deep traps than the other samples. These deep traps likely had a significant effect on the space charge distribution in the samples. This effect will be discussed later.Figure 8
Leakage current density (a) and DC resistivity (b) of sPP and its nanocomposites subjected to an electric field of 6 kV/mm at room temperature.
(a)
(b)


### 3.7. Space Charge Characteristics

Apart from the mechanical properties and the DC resistivity, an outstanding space charge distribution is another important requirement for HVDC cables, because the accumulation of space charge in HVDC cables results in the failure of cable insulation [13, 21]. Figure 9 shows the space charge distribution in the samples during polarization, under a DC electric field of 60 kV mm−1 applied for 1800 s. Figures 9(a) and 9(d) show that a large number of homocharges formed around the cathode of the neat sPP and the nanocomposite with 3 phr chl-silica; this was a result of electron injection at the cathode. Figures 9(b) and 9(c) illustrate the improved space charge distribution in the nanocomposites with 0.5 phr and 1 phr chl-silica. Only a small number of homospace charges were observed near the cathode of these samples. The suppression of space charges is considered to be closely related to the presence of carrier traps. The deep traps in the sPP samples with 0.5 phr or 1 phr chl-silica blocked the electrons injected from the cathode, and the blocked electrons increased the potential barrier for charge injection, thus suppressing the formation of space charges to a significant degree. The sPP with 3 phr chl-silica showed fewer deep traps than the sPP with 0.5 phr chl-silica or that with 1 phr chl-silica, as shown by the leakage current density curves in Figure 8(a). Hence, a small number of electrons could still be injected into the sample with 3 phr chl-silica.Figure 9
Space charge distribution during polarization in (a) sPP, (b) 0.5 phr, (c) 1 phr, and (d) 3 phr subjected to a DC electric field of 60 kV/mm for 1800 s.
(a)
(b)
(c)
(d)


### 3.8. Comparison between sPP Nanocomposites and XLPE

In order to better illustrate the properties of sPP nanocomposites, a comparison of the various performances considered in this investigation between sPP nanocomposites and typical XLPE is given in Table3. The operating temperature of 1 phr is the same as XLPE from the view of thermal and mechanical properties. The electrical properties of 1 phr are more superior to XLPE (i.e., increased volume resistivity and no space charge accumulation).Table 3
Comparison between sPP/chl-silica nanocomposites and XLPE.
Properties
sPP/chl-silica nanocomposites
XLPE
Operating temperature
70°C
70°C [11, 12]
Breaking elongation
≥200%
≥200% [13]
Tensile yield strength (25°C)
≥10 MPa
22 MPa [14]
DC volume resistivity
≥1017 Ω·cm (6 kV/mm)
0.92 × 1017 Ω·cm (10 kV/mm) [15]
Space charge characteristics
No space charge accumulation in sPP with 0.5 phr and 1 phr chl-silica
Small amount of heterospace charge near anode and slight charge injection near cathode (−50 kV/mm) [15]


## 3.1. FTIR Characterization

The surface modification of inorganic nanoparticles enlarges the interface between the matrix and the nanoparticles, leading to improvements in the performance of the nanocomposites. The silica nanoparticles, which were functionalized via surface modification, were characterized using FTIR, as shown in Figure1. The silica, which had O-H groups, showed an absorption peak at 3427 cm−1 [16]. The FTIR spectra clearly illustrated the presence of fewer silicon hydroxyls in the chl-silica, indicating the enhancement of the surface hydrophobicity of the silica nanoparticles after the surface modification. Another change in the FTIR spectra was related to the wavenumbers at 2966 cm−1 and 2870 cm−1, which represented carbon hydrogen bonds. Compared with the lack of absorption at these two wavenumbers for the silica nanoparticles, the presence of absorption signals for the chl coupling agent indicated that the chl had been successfully grafted to the surface of the silica nanoparticles.Figure 1
FTIR spectra for silica nanoparticles.


## 3.2. Dispersion and Morphology

Particle dispersion is the key factor in controlling the properties of nanocomposites. Figure2 shows SEM images illustrating the dispersion of the nanoparticles in the nanocomposites with 3 phr chl-silica. Similar images were obtained for the other samples. The images suggested that the silica nanoparticles with a polymer shell were well dispersed in the sPP matrix, with good compatibility. It is likely that the excellent compatibility of the silica nanoparticles and the sPP matrix originated from the surface modification with the silane coupling agent.Figure 2
SEM images demonstrating the dispersibility of the silica nanoparticles and showing the cross-sectional microstructure of the sample; (b) is a partial enlargement of the frame shown in (a).
(a)
(b)


## 3.3. Thermal Analysis

Figure3 presents the melting and crystallization behaviors of the sPP/chl-silica nanocomposites as a function of the chl-silica content. Figure 3(a) shows that the sPP nanocomposites had two distinct melting transitions, in accordance with results from a previous study [17]. The melting temperature of the neat sPP was higher than that of LDPE or LLDPE, and that melting temperature shifted to a higher temperature when the chl-silica was incorporated into the sPP matrix. The sPP nanocomposites therefore all appear to be good candidates for HVDC cable applications, at least from the point of view of their melting behavior.Figure 3
Melting (a) and crystallization (b) curves for the sPP/silica nanocomposites.
(a)
(b)The nonisothermal crystallization curves for the pure sPP and its nanocomposites shown in Figure3(b) indicate that the crystallization temperature moved to a higher temperature when the chl-silica was added to the sPP matrix, proving that incorporating the chl-silica had a great effect on the nucleation of the nanocomposites. The higher the crystallization temperature, the shorter the cooling time. Hence, the sPP nanocomposites had a shorter processing cycle compared with sPP.Thermogravimetric analysis was performed in an attempt to understand the degradation characteristics of the samples, which are important for the processing of the power cable. The thermogravimetry (TG) and derivative thermogravimetry (DTG) results are shown in Figure4. The temperatures at which the maximum rate of heat consumption occurred for this degradation process are listed in Table 2 for the various nanocomposites. Table 2 shows that sPP with 1 phr and 3 phr chl-silica had a maximum decomposition temperature of 347.6°C and 352.8°C, respectively.Table 2
Degradation temperatures for the sPP/chl-silica samples, obtained from TGA results.
Sample
T
degrad
(°C)
sPP
333.5
0.5 phr
331.5
1 phr
347.6
3 phr
352.8Figure 4
TG and DTG curves for the sPP/chl-silica nanocomposites.


## 3.4. Dynamic Mechanical and Thermal Characteristics

HVDC cables are typically installed at room temperature and operate at high temperatures. It is therefore necessary to focus on the mechanical properties at room temperature and at high temperatures. Figure5(a) shows a plot of the storage modulus as a function of temperature. The results indicated that all samples had a storage modulus of ~500 MPa at room temperature, lower than that of isotactic polypropylene (~1000 MPa). All of the samples showed a storage modulus of ~100 MPa at high temperatures, higher than that of LDPE or LLDPE.Figure 5
Storage modulus (a) andtan⁡δ (b) for the sPP/chl-silica nanocomposites.
(a)
(b)We determined from thetan⁡δ curves in Figure 5(b) that the characteristic peak for polypropylene was at ~12°C. The peak in the tan⁡δ curve was due to the glass transition characteristic of sPP [18]. The presence of the nanosilica did not change the glass transition temperature of the composites.


## 3.5. Tensile Testing

Figure6 shows the typical tensile stress-strain curves of sPP nanocomposites at different temperatures. Furthermore, elastic modulus and tensile yield strength of the samples at different temperatures are presented in Figure 7. It can be seen from Figure 6 that all four materials at different temperature displayed a characteristic necking behavior after imposed strain and had high breaking elongation (more than 200%). The high breaking elongation at room temperature indicates that the nanocomposites have sufficiently high mechanical flexibility for cable installation. From Figure 7, the elastic modulus increased and the tensile yield strength decreased at different temperatures when the chl-silica was added to the sPP matrix. In addition, an elastic modulus at room temperature of ~110 MPa and sufficient elastic modulus at high temperature for sPP nanocomposites indicate that the nanocomposites are suitable for cable applications [11].Figure 6
Tensile tests results at different temperatures (a) sPP, (b) 0.5 phr, (c) 1 phr, and (d) 3 phr.
(a)
(b)
(c)
(d)Figure 7
Elastic modulus (a) and tensile yield strength (b) for sPP nanocomposites at different temperatures.
(a)
(b)


## 3.6. DC Resistivity

The dielectric loss from HVDC cables results mainly from the leakage current. Figure8 shows the leakage current density and DC resistivity of the samples at room temperature. The pure sPP showed a higher leakage current and took less time to reach stability, compared with the other samples. The electric field distribution within the insulation of an HVDC cable depends on the DC resistivity. The volume resistivity was evaluated from the leakage current value noted 60 minutes after the application of the DC voltage shown in Figure 8(b). Under the applied field, the volume resistivity of the films with silica nanofillers was higher than that of the pure sPP; in particular, the sPP with 1% chl-silica exhibited a volume resistivity that was one order of magnitude higher than that shown by the base polymer. A possible reason for this was the good dispersion of the chl-silica in the sPP matrix. For polymer nanocomposites, the nanoparticle-polymer interactions play an important role in determining the materials’ performance [19]. More specifically, this phenomenon was related to the introduction of deeper carrier traps by the incorporation of the nanosilica [20]. The nanocomposite with 1 phr chl-silica had the lowest leakage current density, showing that this sample had more deep traps than the other samples. These deep traps likely had a significant effect on the space charge distribution in the samples. This effect will be discussed later.Figure 8
Leakage current density (a) and DC resistivity (b) of sPP and its nanocomposites subjected to an electric field of 6 kV/mm at room temperature.
(a)
(b)


## 3.7. Space Charge Characteristics

Apart from the mechanical properties and the DC resistivity, an outstanding space charge distribution is another important requirement for HVDC cables, because the accumulation of space charge in HVDC cables results in the failure of cable insulation [13, 21]. Figure 9 shows the space charge distribution in the samples during polarization, under a DC electric field of 60 kV mm−1 applied for 1800 s. Figures 9(a) and 9(d) show that a large number of homocharges formed around the cathode of the neat sPP and the nanocomposite with 3 phr chl-silica; this was a result of electron injection at the cathode. Figures 9(b) and 9(c) illustrate the improved space charge distribution in the nanocomposites with 0.5 phr and 1 phr chl-silica. Only a small number of homospace charges were observed near the cathode of these samples. The suppression of space charges is considered to be closely related to the presence of carrier traps. The deep traps in the sPP samples with 0.5 phr or 1 phr chl-silica blocked the electrons injected from the cathode, and the blocked electrons increased the potential barrier for charge injection, thus suppressing the formation of space charges to a significant degree. The sPP with 3 phr chl-silica showed fewer deep traps than the sPP with 0.5 phr chl-silica or that with 1 phr chl-silica, as shown by the leakage current density curves in Figure 8(a). Hence, a small number of electrons could still be injected into the sample with 3 phr chl-silica.Figure 9
Space charge distribution during polarization in (a) sPP, (b) 0.5 phr, (c) 1 phr, and (d) 3 phr subjected to a DC electric field of 60 kV/mm for 1800 s.
(a)
(b)
(c)
(d)


## 3.8. Comparison between sPP Nanocomposites and XLPE

In order to better illustrate the properties of sPP nanocomposites, a comparison of the various performances considered in this investigation between sPP nanocomposites and typical XLPE is given in Table3. The operating temperature of 1 phr is the same as XLPE from the view of thermal and mechanical properties. The electrical properties of 1 phr are more superior to XLPE (i.e., increased volume resistivity and no space charge accumulation).Table 3
Comparison between sPP/chl-silica nanocomposites and XLPE.
Properties
sPP/chl-silica nanocomposites
XLPE
Operating temperature
70°C
70°C [11, 12]
Breaking elongation
≥200%
≥200% [13]
Tensile yield strength (25°C)
≥10 MPa
22 MPa [14]
DC volume resistivity
≥1017 Ω·cm (6 kV/mm)
0.92 × 1017 Ω·cm (10 kV/mm) [15]
Space charge characteristics
No space charge accumulation in sPP with 0.5 phr and 1 phr chl-silica
Small amount of heterospace charge near anode and slight charge injection near cathode (−50 kV/mm) [15]


## 4. Conclusion

In this study, the properties of nanosilica-modified sPP were investigated, and the main conclusions are summarized below:(1)
The silica nanoparticles used for the modification showed excellent dispersion, because of the improvement of the hydrophobicity of silica nanoparticles that resulted from their functionalization, as characterized using FTIR spectroscopy.(2)
The materials without cross-linking provided a suitable mechanical modulus at room temperature and sufficient intensity at high temperatures. The manufactured materials therefore had a sufficient ability to maintain their integrity in a cable under operating conditions.(3)
The melting temperature and crystallization temperature of the sPP/chl-silica nanocomposites were higher, compared with the values for neat polypropylene.(4)
The addition of chl-silica to the sPP resulted in significant improvement of the DC resistivity. The enhancement in the DC resistivity was related to the introduction of the deep carrier traps by the nanosilica.Out of the nanocomposites considered here, the nanocomposite containing 1% nanosilica in sPP provided the optimum mechanical and thermomechanical properties and significant improvements in the DC resistivity and space charge distribution. This nanocomposite holds potential as a candidate insulation material for future ecofriendly extruded HVDC cables.



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*Source: 686248-2015-12-15.xml*