# High-Density Polyethylene Composites Filled with Nanosilica Containing Immobilized Nanosilver or Nanocopper: Thermal, Mechanical, and Bactericidal Properties and Morphology and Interphase Characterization

Authors: Regina Jeziórska; Maria Zielecka; Beata Gutarowska; Zofia Żakowska
Journal: International Journal of Polymer Science
 (2014)

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## Abstract

Silica containing immobilized nanosilver (Ag-SiO2) or nanocopper (Cu-SiO2) was used as a filler for high-density polyethylene (HDPE). The HDPE/Ag-SiO2 and HDPE/Cu-SiO2 composites were prepared by melt blending and injection molding. The microstructure of the composites was examined using transmission electron microscopy (TEM). The crystallization behavior and thermal properties were studied using differential scanning calorimetry (DSC) and thermogravimetry (TGA). The mechanical properties were characterized by tensile, flexural, and impact tests as well as dynamic mechanical thermal analysis (DMTA). The ability of silica to give antimicrobial activity to HDPE was also investigated and discussed. The TEM images indicate that Ag-SiO2 show lower degree of agglomeration than Cu-SiO2 nanoparticles. The crystallization temperature increased, whereas crystallinity decreased in the composites. The thermal stability of the composites was significantly better compared to HDPE. Improved stiffness indicating very good interfacial adhesion was observed. Excellent activity against different kinds of bacteria was found.


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## Body

## 1. Introduction

There are numerous ways by which bactericidal properties can be given to a polymer matrix: incorporation of volatile or nonvolatile bactericidal agents directly into polymers [1, 2], coating or adsorbing agents onto polymer surfaces [3], immobilization of them to polymers by ion or covalent linkages [4], and the use of polymers that are inherently bactericidal [5]. The antimicrobial activity of silver and copper is well established, especially when metals are applied in the form of nanoparticles (NPs). Silver and copper NPs have strong inhibiting and antimicrobial effects as well as broad spectrum of biocidal activities [6–8]. However, the mechanism of antibacterial effect of silver or copper is still not fully understood. It is generally believed that interactions of silver or copper with thiol groups play the essential role in deterioration of bacteria [9, 10]. Nanoparticles of these metals are a new group of bactericidal materials due to the different physicochemical properties as compared to the bulk materials of the same composition. The bactericidal efficiency of these metals increases with decreasing their particle size due to their larger specific area. Based on the results of TEM analysis and bactericidal effects of silver and copper nanoparticles it can be stated that nanoparticles of these metals interact with the elements of bacterial membrane resulting in the structural changes leading to the cell death. Moreover, when silver or copper nanoparticles are small enough to disrupt the bacterial cell membranes they can gain entry in order to disrupt the enzyme function [11, 12]. The agglomeration of silver or copper NPs or colloids can result in the decrease in their bactericidal and fungicidal properties.The problem of NPs stability was solved by the development of silica nanospheres containing immobilized silver or copper NPs [13]. Because of these unique properties, their incorporation into different materials often leads to the generation of materials showing activity against a broad spectrum of microbes. Besides polyolefins [2], many other polymers, for example, polyamides [4, 14], polyurethanes [14], silicone rubber [15], and methacrylate copolymers [16], were filled or coated with silver nanoparticles. In all cases a good activity against different kinds of bacteria was found.In the previous work [17], it was found that silica containing immobilized nanosilver (Ag-SiO2) in the presence of maleated high-density polyethylene improved adhesion between the HDPE and wood fiber. Moreover, silica nanoparticles increased tensile and flexural moduli of wood-filled HDPE composites, pointing to a synergetic effect arising from the presence of the reinforced HDPE phase, containing high amounts of the finely dispersed wood fiber. Improved bactericidal properties againstEscherichia coli,Staphylococcus aureus, orSalmonella typhimurium of the wood-filled HDPE composites modified by silica containing immobilized nanosilver were observed.In the first part of the paper, sol-gel process for manufacturing of nanosilica containing immobilized nanosilver or nanocopper is described. Photon correlation spectroscopy (PCS) analysis, as well as scanning electron microscopy (SEM) and powder X-ray diffraction (XRD), was used to verify the silica size and its surface modification by the added nanosilver or nanocopper. Then, the manufacturing of silica-filled HDPE composites is presented. In the second part of the work, the phase behavior, microstructure, and mechanical properties of silica-filled high-density polyethylene composites were studied using transmission electron microscopy (TEM), differential scanning calorimetry (DSC), thermogravimetry (TGA), and dynamic mechanical analysis (DMTA). Finally, the ability of spherical silica containing immobilized nanosilver or nanocopper to give bactericidal properties to HDPE composites was investigated by the adenosine-5′-triphosphate (ATP) method and discussed. The purpose of the development of these HDPE composite materials is to make the use of them for a variety of applications possible, which include food packaging, medical devices (e.g., tracheotomy tubes, vascular or urinary catheters, hip prosthetics), healthcare (including disposables), personal care products, fishing nets, vials, and shower mats. The use of spherical silica containing immobilized nanosilver or nanocopper assures long-term bactericidal activity as well as enhanced mechanical properties.


## 2. Experimental

### 2.1. Materials

The high-density polyethylene (HDPE, Hostalen GC 7260) with the melt flow rate (MFR) of 8 g/10 min (ISO 1133) was supplied by Orlen Polyolefins (Poland) and used as a base polymeric matrix. Tetraethoxysilane (TEOS)—technical grade, commercial product TES 28 supplied by Wacker Chemie (Germany), ethyl alcohol—reagent grade, aqueous ammonia—reagent grade, silver nitrate, copper acetate all supplied by POCh S.A. (Poland), were used as received.


### 2.2. Synthesis of Spherical Silica Containing Immobilized Nanosilver (Ag-SiO2) or Nanocopper (Cu-SiO2) via Sol-Gel Method

Spherical silica containing immobilized nanosilver (Ag-SiO2) or nanocopper (Cu-SiO2) was synthesized according to the developed sol-gel process [18, 19]. Ethyl alcohol, aqueous ammonia, and distilled water were mixed to obtain the reaction mixture. The initial pH of the reaction mixture was measured using pH-meter Schott Instruments LAB 850. All syntheses were carried out at room temperature (293 K). Tetraethoxysilane, distilled immediately before use in the preparation of nanoparticles, used as alkoxysilane precursor was added to the reaction mixture stirred with constant speed during 2 hours. The reaction mixture containing TEOS/EtOH/H2O in the molar ratios 0.023/0.500/0.477 was used in the synthesis with the initial pH range from 10.4 to 11.3 and the final pH range was 7.5–10.8, with furtherin situ modification with silver or copper nanoparticles using silver nitrate or copper acetate. The product obtained, nanosilica containing immobilized nanosilver or nanocopper, was dried in an oven dryer for 2 hours at 50–90°C or in a spray dryer.


### 2.3. Nanosilica Characterization

Photon correlation spectroscopy (PCS) was used to evaluate particle size and particle size distribution of resulting sols. The measurements were performed using a Malvern apparatus (Zetasizer Nano ZS). The results were registered in the form of the particle size distribution curve. The resulting peak was analyzed using the averaged number method. In Figure1 the particle size distribution curves of the nanosilica containing immobilized nanosilver or nanocoper are shown. The developed synthesis method allows obtaining silica nanoparticles characterized by an almost uniform particle size, which is relating to the selection of the sol-gel process parameters. The monomodal particle size distribution and very low dispersion of particle size were observed for homogeneous sols obtained by sol-gel process. The characteristics of nanosilver or nanocopper immobilized on nanosilica fillers are presented in Table 1. The specific surface area of silica nanoparticles was measured by BET-N2 sorption method using Gemini 2370 V3.02 apparatus. The results are reported in Table 1. The size of specific surface area decreased with increasing pH value of reaction mixture in the sol-gel process. Very good correlation among the specific surface area of silica nanospheres, particle size of sol particles, and the pH value of the reaction mixture in the sol-gel process was demonstrated [20]. Silver or copper content was determined by absorption atomic spectroscopy (AAS), using an AAS Spectrometer 5100 PC, Perkin Elmer. The measured silver or copper contents are presented in Table 1. Scanning electron microscopy (SEM) was performed using a JEOL JSM-6490LV operating in the high vacuum mode at accelerating voltage of 15 kV to compare morphology of silica nanoparticles containing immobilized nanosilver (Ag-SiO2) or nanocopper (Cu-SiO2). The micrographs reported in Figure 2 highlight structural similarity of both nanosilica types containing immobilized nanosilver or nanocopper. As can be expected the spherical shape of silica particles is kept and nanoparticles of silver or copper permanently embedded on the nanosilica surface can be observed. The presence of silver or copper at different oxidation levels was confirmed by powder X-ray diffraction using X-ray powder diffractometer Siemens D500 with high-resolution solid-state detector Si[Li], copper lamp (operating parameters U = 40 kV, I = 30 mA), and radiation CuK (λ = 0.1541837 nm). Selected XRD curves of silica nanoparticles containing immobilized nanosilver or nanocopper are shown in Figures 3(a) and 3(b), respectively. The layout of the diffraction peaks 110, 200, 220, and 311 is characteristic for the type F cubic structure formed by metallic silver Ag0 or copper Cu0. The angular positions of characteristic reflexes from Ag0 and Cu0 are presented in Table 2. Strongly defined sharp peaks suggest the presence of metallic silver or metallic copper nanoparticles.Table 1
Characteristics of nanosilica containing immobilized nanosilver or nanocopper.
Property
Ag-SiO2
Cu-SiO2
Size (nm)
30
30
Specific surface area (m2/g)
274.4
274.4
Polydispersity (%)
0.16
0.16
Silver content (ppm)
70 000
78 000
Silver size (nm)
7.5–8.0
7.5–8.0Table 2
XRD results: the angular position of characteristic reflexes for silica containing immobilized nanosilver or nanocopper.
Characteristic reflex
The angular position (eV)
Ag
Cu
111
38.15
43.33
200
44.32
50.48
220
64.49
74.20
311
77.55
90.03Particle size distribution curves of Ag-SiO2 (a) and Cu-SiO2 (b); average particle size 30 nm.
(a)
(b)SEM images of the silica containing immobilized: nanosilver (a) and nanocopper (b).
(a)
(b)XRD curves of silica containing immobilized nanosilver (a) and nanocopper (b).
(a)
(b)


### 2.4. Nanocomposite Preparation

High-density polyethylene and nanosilica were melt mixed using a Berstorff ZE 25A × 51D twin screw corotating extruder (D = 25 mm, L/D = 51) according to the process published elsewhere [21]. All the materials were fed into the throat of the extruder using separate gravimetric feeders. Different screw elements along the screw worked in order to induce polymer melting and achieve a finer dispersion of the nanoparticles in the polymer melt [22]. The three mixing sections enhanced the compounding and also increased the residence time of the mixture in the barrel. The extruder also had a vacuum degassing port to remove any moisture traces or other volatile products formed during compounding. Melt mixing was carried out using a screw speed of 600 rpm and also a temperature profile of 30, 175, 175, 180, 180, 180, 180, 180, 180, 180, 180, 180, and 180°C for the sequential heating zones, from the hopper to the die. The melt temperature and pressure were continuously recorded during compounding. After compounding, the material was extruded from the die, which had two cylindrical nozzles of 4 mm diameter, and then cooled rapidly in the air and pelletized with an adjustable rotating knife into 4 mm pellets.


### 2.5. Structural Properties of Composites

Cross-fracture surfaces of the composites were studied by means of scanning-transmission electron microscope STEM Hitachi S-5500 equipped with a dark-field detector and a bright-field detector.


### 2.6. Thermal Properties

A Perkin Elmer differential scanning calorimeter (DSC-7) was used for thermal analyses. All experiments were run at the heating rate of 10°C/min under a nitrogen atmosphere. A thermogravimetric analyzer (TGA/SDTA 851e Mettler Toledo) was used to investigate the thermooxidative stability of neat HDPE and the composites. The samples were heated from room temperature to 600°C at the heating rate of 10°C/min in the atmosphere.


### 2.7. Dynamic Mechanical Analysis (DMTA)

The dynamic mechanical properties of samples were tested using a dynamic mechanical analyzer, model Rheometrics RDS 2. The torsion method was used with a frequency of 1 Hz, a strain level of 0.1% in the temperature range of −150 to 100°C. The heating rate was 3°C/min. The testing was performed using rectangular bars measuring approximately 38 × 10 × 2 mm, prepared by injection molding.


### 2.8. Mechanical Properties

Samples were prepared by injection molding using an Arburg 420 M single screw injection machine (Allrounder 1000–250) containing five different heating zones. The temperatures of these were 180/190/195/195/200°C, from the feeding zone to the die, while the mold was cooled with water at 25°C. A minimum of 5 specimens for each composite were tested in order to estimate the precision of the reported data. An Instron Series 4505 tensile tester, which operated at a crosshead speed of 5 mm/min at room temperature, was used to measure the tensile and flexural properties of the composites according to ISO 527 and ISO 178, respectively.


### 2.9. Bactericidal Properties

Escherichia coli strain ATCC 8739,Staphylococcus aureus strain ATCC 6538,Salmonella typhimurium strain ATCC 14028,Pseudomonas fluorescens, andBurkholderia cepacia strains isolated from a fridge’s sink were used as test organisms to check bactericidal properties of HDPE and its composites filled with nanosilica containing immobilized nanosilver or nanocopper. The bacteria were grown over 24 h in trypton-soya medium (TSB, Merck) at 37 ± 1°C. The resulting suspension of bacteria was diluted to a concentration of about 1 × 106 CFU/mL, where CFU is a colony forming unit (this being the measure of viable bacteria). The exact initial concentration of bacteria was determined using the microscopy method. The vitality of bacteria on polymer surface was determined using the adenosine-5′-triphosphate (ATP) method. The HY-LiTE (Merck) system based on the bioluminescent method was applied to measure the ATP content on polymer surface. Measurement of ATP indicates the current amount of biological material by measuring the emission of light quanta during ATP hydrolysis and the numeric value is called relative light unit (RLU). The polymers, after being taken out from the nutrient medium, were washed three times with deionized distilled water to remove nonadhered cells. Then the samples (in the form of smear) were taken using HY-LiTE test-tube according to producer procedure. They were placed in luminometer (Merck) and RLU values were read. The results were given in RLU/cm2. The ATP contents on the surfaces of neat polymers placed formerly in the nutrient medium (without bacteria culture) were also determined, as control samples, according to the same procedure. The level of ATP in control samples was 20–39 RLU and it was taken into account in calculations.


## 2.1. Materials

The high-density polyethylene (HDPE, Hostalen GC 7260) with the melt flow rate (MFR) of 8 g/10 min (ISO 1133) was supplied by Orlen Polyolefins (Poland) and used as a base polymeric matrix. Tetraethoxysilane (TEOS)—technical grade, commercial product TES 28 supplied by Wacker Chemie (Germany), ethyl alcohol—reagent grade, aqueous ammonia—reagent grade, silver nitrate, copper acetate all supplied by POCh S.A. (Poland), were used as received.


## 2.2. Synthesis of Spherical Silica Containing Immobilized Nanosilver (Ag-SiO2) or Nanocopper (Cu-SiO2) via Sol-Gel Method

Spherical silica containing immobilized nanosilver (Ag-SiO2) or nanocopper (Cu-SiO2) was synthesized according to the developed sol-gel process [18, 19]. Ethyl alcohol, aqueous ammonia, and distilled water were mixed to obtain the reaction mixture. The initial pH of the reaction mixture was measured using pH-meter Schott Instruments LAB 850. All syntheses were carried out at room temperature (293 K). Tetraethoxysilane, distilled immediately before use in the preparation of nanoparticles, used as alkoxysilane precursor was added to the reaction mixture stirred with constant speed during 2 hours. The reaction mixture containing TEOS/EtOH/H2O in the molar ratios 0.023/0.500/0.477 was used in the synthesis with the initial pH range from 10.4 to 11.3 and the final pH range was 7.5–10.8, with furtherin situ modification with silver or copper nanoparticles using silver nitrate or copper acetate. The product obtained, nanosilica containing immobilized nanosilver or nanocopper, was dried in an oven dryer for 2 hours at 50–90°C or in a spray dryer.


## 2.3. Nanosilica Characterization

Photon correlation spectroscopy (PCS) was used to evaluate particle size and particle size distribution of resulting sols. The measurements were performed using a Malvern apparatus (Zetasizer Nano ZS). The results were registered in the form of the particle size distribution curve. The resulting peak was analyzed using the averaged number method. In Figure1 the particle size distribution curves of the nanosilica containing immobilized nanosilver or nanocoper are shown. The developed synthesis method allows obtaining silica nanoparticles characterized by an almost uniform particle size, which is relating to the selection of the sol-gel process parameters. The monomodal particle size distribution and very low dispersion of particle size were observed for homogeneous sols obtained by sol-gel process. The characteristics of nanosilver or nanocopper immobilized on nanosilica fillers are presented in Table 1. The specific surface area of silica nanoparticles was measured by BET-N2 sorption method using Gemini 2370 V3.02 apparatus. The results are reported in Table 1. The size of specific surface area decreased with increasing pH value of reaction mixture in the sol-gel process. Very good correlation among the specific surface area of silica nanospheres, particle size of sol particles, and the pH value of the reaction mixture in the sol-gel process was demonstrated [20]. Silver or copper content was determined by absorption atomic spectroscopy (AAS), using an AAS Spectrometer 5100 PC, Perkin Elmer. The measured silver or copper contents are presented in Table 1. Scanning electron microscopy (SEM) was performed using a JEOL JSM-6490LV operating in the high vacuum mode at accelerating voltage of 15 kV to compare morphology of silica nanoparticles containing immobilized nanosilver (Ag-SiO2) or nanocopper (Cu-SiO2). The micrographs reported in Figure 2 highlight structural similarity of both nanosilica types containing immobilized nanosilver or nanocopper. As can be expected the spherical shape of silica particles is kept and nanoparticles of silver or copper permanently embedded on the nanosilica surface can be observed. The presence of silver or copper at different oxidation levels was confirmed by powder X-ray diffraction using X-ray powder diffractometer Siemens D500 with high-resolution solid-state detector Si[Li], copper lamp (operating parameters U = 40 kV, I = 30 mA), and radiation CuK (λ = 0.1541837 nm). Selected XRD curves of silica nanoparticles containing immobilized nanosilver or nanocopper are shown in Figures 3(a) and 3(b), respectively. The layout of the diffraction peaks 110, 200, 220, and 311 is characteristic for the type F cubic structure formed by metallic silver Ag0 or copper Cu0. The angular positions of characteristic reflexes from Ag0 and Cu0 are presented in Table 2. Strongly defined sharp peaks suggest the presence of metallic silver or metallic copper nanoparticles.Table 1
Characteristics of nanosilica containing immobilized nanosilver or nanocopper.
Property
Ag-SiO2
Cu-SiO2
Size (nm)
30
30
Specific surface area (m2/g)
274.4
274.4
Polydispersity (%)
0.16
0.16
Silver content (ppm)
70 000
78 000
Silver size (nm)
7.5–8.0
7.5–8.0Table 2
XRD results: the angular position of characteristic reflexes for silica containing immobilized nanosilver or nanocopper.
Characteristic reflex
The angular position (eV)
Ag
Cu
111
38.15
43.33
200
44.32
50.48
220
64.49
74.20
311
77.55
90.03Particle size distribution curves of Ag-SiO2 (a) and Cu-SiO2 (b); average particle size 30 nm.
(a)
(b)SEM images of the silica containing immobilized: nanosilver (a) and nanocopper (b).
(a)
(b)XRD curves of silica containing immobilized nanosilver (a) and nanocopper (b).
(a)
(b)


## 2.4. Nanocomposite Preparation

High-density polyethylene and nanosilica were melt mixed using a Berstorff ZE 25A × 51D twin screw corotating extruder (D = 25 mm, L/D = 51) according to the process published elsewhere [21]. All the materials were fed into the throat of the extruder using separate gravimetric feeders. Different screw elements along the screw worked in order to induce polymer melting and achieve a finer dispersion of the nanoparticles in the polymer melt [22]. The three mixing sections enhanced the compounding and also increased the residence time of the mixture in the barrel. The extruder also had a vacuum degassing port to remove any moisture traces or other volatile products formed during compounding. Melt mixing was carried out using a screw speed of 600 rpm and also a temperature profile of 30, 175, 175, 180, 180, 180, 180, 180, 180, 180, 180, 180, and 180°C for the sequential heating zones, from the hopper to the die. The melt temperature and pressure were continuously recorded during compounding. After compounding, the material was extruded from the die, which had two cylindrical nozzles of 4 mm diameter, and then cooled rapidly in the air and pelletized with an adjustable rotating knife into 4 mm pellets.


## 2.5. Structural Properties of Composites

Cross-fracture surfaces of the composites were studied by means of scanning-transmission electron microscope STEM Hitachi S-5500 equipped with a dark-field detector and a bright-field detector.


## 2.6. Thermal Properties

A Perkin Elmer differential scanning calorimeter (DSC-7) was used for thermal analyses. All experiments were run at the heating rate of 10°C/min under a nitrogen atmosphere. A thermogravimetric analyzer (TGA/SDTA 851e Mettler Toledo) was used to investigate the thermooxidative stability of neat HDPE and the composites. The samples were heated from room temperature to 600°C at the heating rate of 10°C/min in the atmosphere.


## 2.7. Dynamic Mechanical Analysis (DMTA)

The dynamic mechanical properties of samples were tested using a dynamic mechanical analyzer, model Rheometrics RDS 2. The torsion method was used with a frequency of 1 Hz, a strain level of 0.1% in the temperature range of −150 to 100°C. The heating rate was 3°C/min. The testing was performed using rectangular bars measuring approximately 38 × 10 × 2 mm, prepared by injection molding.


## 2.8. Mechanical Properties

Samples were prepared by injection molding using an Arburg 420 M single screw injection machine (Allrounder 1000–250) containing five different heating zones. The temperatures of these were 180/190/195/195/200°C, from the feeding zone to the die, while the mold was cooled with water at 25°C. A minimum of 5 specimens for each composite were tested in order to estimate the precision of the reported data. An Instron Series 4505 tensile tester, which operated at a crosshead speed of 5 mm/min at room temperature, was used to measure the tensile and flexural properties of the composites according to ISO 527 and ISO 178, respectively.


## 2.9. Bactericidal Properties

Escherichia coli strain ATCC 8739,Staphylococcus aureus strain ATCC 6538,Salmonella typhimurium strain ATCC 14028,Pseudomonas fluorescens, andBurkholderia cepacia strains isolated from a fridge’s sink were used as test organisms to check bactericidal properties of HDPE and its composites filled with nanosilica containing immobilized nanosilver or nanocopper. The bacteria were grown over 24 h in trypton-soya medium (TSB, Merck) at 37 ± 1°C. The resulting suspension of bacteria was diluted to a concentration of about 1 × 106 CFU/mL, where CFU is a colony forming unit (this being the measure of viable bacteria). The exact initial concentration of bacteria was determined using the microscopy method. The vitality of bacteria on polymer surface was determined using the adenosine-5′-triphosphate (ATP) method. The HY-LiTE (Merck) system based on the bioluminescent method was applied to measure the ATP content on polymer surface. Measurement of ATP indicates the current amount of biological material by measuring the emission of light quanta during ATP hydrolysis and the numeric value is called relative light unit (RLU). The polymers, after being taken out from the nutrient medium, were washed three times with deionized distilled water to remove nonadhered cells. Then the samples (in the form of smear) were taken using HY-LiTE test-tube according to producer procedure. They were placed in luminometer (Merck) and RLU values were read. The results were given in RLU/cm2. The ATP contents on the surfaces of neat polymers placed formerly in the nutrient medium (without bacteria culture) were also determined, as control samples, according to the same procedure. The level of ATP in control samples was 20–39 RLU and it was taken into account in calculations.


## 3. Results and Discussion

### 3.1. Microstructure of the Silica-Filled HDPE Composites

Filler dispersion and adhesion to the polymer matrix are of great importance for improving the mechanical properties of composites. Good control of the interface morphology of composites is one of the most critical parameters to impart the desired mechanical properties to such materials.In general, good dispersion of inorganic nanofillers in polymer matrices is especially hard to achieve by melt compounding at high filler content [23]. It is well known that the neat silica nanoparticles tend to form agglomerates because of the formation of hydrogen bonds among the abundant hydroxyl groups and adsorbed water on their surface. This effect is more pronounced for higher concentrations of nanosilica [24, 25]. After modification by silver or copper, majority of hydroxyl groups have reacted and silver or copper nanoparticles covered the silica surface. This produces a better dispersion of the silica particles in the polymer matrix, and as a consequence the composite properties improved [17]. Therefore, silica containing immobilized nanosilver or nanocopper presents lower tendency to form agglomerates than neat silica so it can be used at higher concentrations (≥10 wt.%) to give bactericidal properties to the polymer modified. However, the surface activity of the silica is extremely high and the particles consequently have a tendency to aggregate tightly creating micron-sized silica-cluster [23].Transmission electron microscopy was performed to explain the behavior of the silica-filled HDPE composites. Figures4 and 5 show the dispersion state of silica-filled HDPE composites. Comparing composites containing different concentrations of silica, the dispersion of individual silica nanoparticles in the HDPE matrix is finer at lower silica content (10 wt.%). However, the two concentrations of silica are relatively high for such fillers. From the TEM images it is clear that Cu-SiO2 shows bigger tendency to form agglomerates than Ag-SiO2. One possible explanation of this fact could be that the hydrodynamic force induced in the polymer melt during melt compounding exceeds the cohesive force acting between the silica particles forming the agglomerates, resulting in the dispersion of the isolated large silica particles in the HDPE matrix. Moreover, the shear stress induced in the kneaded HDPE melt is not sufficient to provide nanometric dispersion of silica nanoparticles. However, isolated silica nanoparticles were observed inside agglomerates (see Figures 4 and 5).TEM images of HDPE/Ag-SiO2 composites: 10 wt.% Ag-SiO2 ((a), (b)), 15 wt.% Ag-SiO2 ((c), (d)).
(a)
(b)
(c)
(d)TEM images of HDPE/Cu-SiO2 composites: 10 wt.% Cu-SiO2 ((a), (b)), 15 wt.% Ag-SiO2 ((c), (d)).
(a)
(b)
(c)
(d)


### 3.2. Crystallization Behavior of the Silica-Filled HDPE Composites

The effect of nanosilica containing immobilized silver or copper nanoparticles on crystallization behavior of HDPE was determined by DSC measurements. Figures6 and 7 show the second heating and cooling DSC curves of HDPE and investigated silica-filled HDPE composites. The important data obtained are listed in Table 3. It is clear from the results that the addition of silica nanoparticles shows no effect on the melting temperature (Tm) of HDPE matrix. Moreover, there is no effect on the crystallinity of the matrix although the crystallization process starts at a higher temperature. The crystallinity values of HDPE matrix in silica-filled composites are decreased to a maximum 3% achieved by HDPE/Ag-SiO2 composite containing 15% of Ag-SiO2. The crystallization temperatures (Tc) of HDPE in the composites are slightly increased as a function of silica content with a maximum improvement of 3°C. Based on these results, it can be concluded that the crystalline features of HDPE have not been influenced greatly by addition of both silver and copper modified silica nanoparticles. Probably, the presence of nanoparticles prevents the growth of HDPE crystals due to small interparticle distances [26].Table 3
DSC test: thermal transition properties (second run) of HDPE-based composites filled with different contents of Ag-SiO2 or Cu-SiO2.
Sample
T
m (°C)
T
c (°C)
X
c
a (%)
HDPE
134
118
68
HDPE/Ag-SiO2 (90/10)
133
120
66
HDPE/Ag-SiO2 (85/15)
133
121
65
HDPE/Cu-SiO2 (90/10)
133
120
68
HDPE/Cu-SiO2 (85/15)
133
121
67
aAssessed by integrating the normalized area of the melting endothermic peak and rationing the heat involved to the reference value of 100% crystalline HDPE (293 J/g).DSC curves of HDPE and nanosilica containing immobilized nanosilver filled HDPE composites: second heating (a) and cooling run (b).
(a)
(b)DSC curves of HDPE and nanosilica containing immobilized nanocopper filled HDPE composites: second heating (a) and cooling run (b).
(a)
(b)


### 3.3. Thermogravimetric Analysis

The TGA curves of the neat HDPE and silica-filled composites in an air atmosphere are displayed in Figure8. The onset (Ton⁡), maximum (Tmax⁡), and thermooxidative decomposition temperatures at 10% (T10) and 50% weight loss (T50) are evaluated from the TGA curves, as listed in Table 4. It was found that the presence of silica significantly altered the degradation mechanism of HDPE. Ton⁡, T10, T50, and Tmax⁡ of neat HDPE are about 359, 374, 424, and 440°C, respectively. It was observed that silica containing immobilized silver or copper significantly improved thermal properties of HDPE composites due to the 13–41°C higher thermooxidative decomposition temperatures. The onset, maximum, and thermooxidative decomposition temperatures at 50% weight loss of the HDPE/Ag-SiO2 composites are higher than of neat HDPE and tend to increase at higher silica content. Although T10 of the composite filled with silica containing immobilized nanosilver is higher in comparison with neat HDPE, it unfortunately slightly decreases with increasing silica content.Table 4
TGA test: thermooxidative decomposition temperatures of HDPE-based composites filled by different weight percentages of Ag-SiO2or Cu-SiO2.
Sample
T
on
⁡ (°C)
T
10 (°C)
T
50 (°C)
T
max
⁡ (°C)
Residue weight (%)
HDPE
359
374
424
440
0
HDPE/Ag-SiO2 (90/10)
400
396
455
462
8.6
HDPE/Ag-SiO2 (85/15)
404
390
463
464
13.1
HDPE/Cu-SiO2 (90/10)
400
393
457
467
7.5
HDPE/Cu-SiO2 (85/15)
400
400
437
458
11.4TGA curves of HDPE and HDPE composites with nanosilica containing immobilized nanosilver (a) and nanocopper (b).
(a)
(b)In the case of HDPE/Cu-SiO2 composites T50 and Tmax⁡ values are higher compared to neat HDPE but decrease with increasing silica content. The decrease in thermooxidative stability at higher silica content could be attributed to nanoparticles agglomeration [24, 27]. This is in a good agreement with TEM micrographs discussed above (see Figures 4 and 5).An increase in the thermal stability of silica-filled HDPE composites may be explained by the formation of the HDPE-silica nanoparticles network by the physical crosslinking of HDPE via silica nanoparticles; this causes the whole system to be stabilized due to the thermal motions of the HDPE chains being restricted.


### 3.4. Dynamic Mechanical Properties

In order to evaluate the effect of Ag-SiO2 as well as Cu-SiO2 nanoparticles on the HDPE matrix, thermomechanical properties were measured. Due to the very high surface area of the nanoparticles in the HDPE composites, the applied stress is expected to be easily transferred from the matrix onto the silica particles resulting in an enhancement of the mechanical properties. Figures 9 and 10 compare the variation of storage modulus (G′), loss modulus (G′′), and loss tangent (tan δ) as a function of temperature, measured at frequency 1 Hz, for HDPE and the silica-filled HDPE composites studied. These samples present two well-expressed relaxations, α and γ, and a very weak β relaxation. Table 5 summarizes the results for storage modulus at room temperature and temperatures of α, β, and γ relaxations.Table 5
DMTA results for HDPE and the HDPE composites containing Ag-SiO2 or Cu-SiO2.
Sample
Storage modulus (MPa) at 23°C
Loss modulus (peak position) (°C)
Loss modulus (peak high) (MPa)
T
γ
T
β
T
α
T
γ
T
β
T
α
HDPE
1140
−120.2
−36.3
41.9
169
35.7
105
HDPE/Ag-SiO2 (90/10)
1250
−119.6
−47.1
44.1
143
43.6
112
HDPE/Ag-SiO2 (85/15)
1320
−119.9
−51.3
44.6
157
49.7
116
HDPE/Cu-SiO2 (90/10)
1240
−122.0
−41.8
45.7
157
36.3
113
HDPE/Cu-SiO2 (85/15)
1270
−121.8
−47.1
44.5
163
40.5
116Dynamic mechanical relaxation behavior versus temperature of HDPE and silica containing immobilized nanosilver filled HDPE composites at frequency of 1 Hz:G′ (a), G′′ (b), and tan δ (c).
(a)
(b)
(c)Dynamic mechanical relaxation behavior versus temperature of HDPE and silica containing immobilized nanocopper filled HDPE composites at frequency of 1 Hz:G′ (a), G′′ (b), and tan δ (c).
(a)
(b)
(c)The storage modulus of the HDPE/Ag-SiO2 and HDPE/Cu-SiO2 composites was significantly higher than corresponding HDPE in the β and α relaxations regions, due to the stiffening effect of the silica. As showed in Table 5, the addition of Ag-SiO2 to HDPE improved G′ at 23°C by about 10–15%. Silica could hinder the chain motion of HDPE, which would improve the modulus. As a result of these changes, the storage modulus of the interface is higher than that of the free part. An increase in the Ag-SiO2 content enlarges the interfacial area and results in increased volume of interphase.Theα relaxation is well expressed as a maximum in loss modulus and as a small hump before the melting process in the temperature dependence of tan δ. This relaxation appears centered at 42°C for HDPE. The addition of silica containing immobilized nanosilver or nanocopper increases α relaxation to about 46°C. However, the value of the α relaxation strongly depends on the type and content of silica. Moreover, it can be seen that the composites show higher α peak intensity compared to neat HDPE indicating higher stiffness of the material. The α relaxation has been defined as the reorientation of molecules within the crystal [28]. It was reported [29] that there is a relation between crystallites’ thickness and intensity of the α relaxation and that this process is affected by the chain mobility of the crystallites. Therefore, chain mobility occurs at higher temperature as crystallite thickness increases. The position and intensity of the α relaxation maximum is usually connected with crystallites’ thickness and crystallinity level, respectively [30].Theγ relaxation occurs as a maximum at −118°C for the HDPE, from −118°C to −122°C for the composites in loss modulus, and at slightly higher temperatures in tan δ, with corresponding decrease in storage modulus, compare Table 5 and Table 6. This is a clear effect of silica containing immobilized nanosilver or nanocopper loading on the breadth and location of the relaxation; this process is shifted to lower temperatures in the presence of silica, as a consequence of slightly lower crystallinity as compared to HDPE. The γ relaxation has been associated with a single relaxation process, predominantly of amorphous origin. This relaxation is typical for the joint movements of chains containing three or more methylene groups (units) in the main chain [29, 30]. The intensity of the γ relaxation is usually associated with the amorphous region of semicrystalline polymers. Therefore, the decrease in the intensity of γ relaxation of the silica-filled composites can be attributed to the decrease in the quantity of the amorphous phase. It was reported that the position of γ loss modulus peak can change between −125°C and −105°C depending on the type of polyethylene (LDPE, LLDPE, or HDPE) and therefore on crystallinity degree (between 20% and 70%) [31–33].Table 6
DMTA results for HDPE and the HDPE composites containing Ag-SiO2 or Cu-SiO2.
Sample
Loss tangent (peak position) (°C)
Loss tangent (peak high)
T
γ
T
γ
HDPE
−116.4
0.0630
HDPE/Ag-SiO2 (90/10)
−116.8
0.0605
HDPE/Ag-SiO2 (85/15)
−117.6
0.0584
HDPE/Cu-SiO2 (90/10)
−117.5
0.0567
HDPE/Cu-SiO2 (85/15)
−117.6
0.0567At temperatures below theγ relaxation storage modulus G′ of the HDPE/Ag-SiO2 composites becomes smaller than of HDPE as well as the HDPE/Cu-SiO2 composites. One possible explanation of this fact could be that below that relaxation the modulus of elasticity of the amorphous phase is higher than that of the crystal one. These samples have the lowest quantity of amorphous phase (see Figures 9(b) and 10(b)) and moreover the physical cross-linking now could not contribute to the increasing of the storage modulus.Theβ relaxation can be observed as a weak maximum in loss modulus (Figures 9(b) and 10(b)) for HDPE and silica-filled HDPE composites. It was found that β relaxation occurs between −5°C and −50°C depending upon the type of polyethylene [30, 33, 34]. Some authors have concluded that the β relaxation results from motion of chain units in the interfacial region [34], whereas others attributed this process to the glass transition [31]. Nitta and Tanaka have suggested a different molecular origin of the β relaxation in linear polyethylene with high molecular weights quite dissimilar to those aforementioned for branched polyethylene [30]. Because of the formation of loose tie and loop molecules in the amorphous layers in polyethylene with high molecular weights, the β relaxation seems to be a consequence of the motion of the loose tie molecules in this type of polyethylene. The absence of the β relaxation in typical linear polyethylene having a thinner amorphous layer, which is considered to promote taut tie molecules, can be directly attributed to the lack of loose tie molecules [35].Theβ-relaxation appears as a maximum at −36°C for HDPE and 5–15°C lower temperature for the HDPE composites. Evidently, the HDPE/Ag-SiO2 composite containing 15 wt.% Ag-SiO2 shows the highest intensity of β transition peak amongst all the samples. This is related to increased interfacial interactions between HDPE matrix and Ag-SiO2 or Cu-SiO2 nanoparticles.


### 3.5. Mechanical Properties

The mechanical properties of polymer composites depend crucially upon the efficiency of stress transfer from the polymer matrix to the fillers, which will be influenced by the interphase. The interphase in composites is the boundary layer between filler surface and polymer matrix, which exhibits local properties different from those of the bulk matrix.The effect of silica containing immobilized nanosilver or nanocopper on the mechanical properties of HDPE composites is summarized in Table7. The incorporation of both types of silica nanoparticles reinforces HDPE but reduces the ductility of the matrix. Moreover, the addition of silica containing immobilized nanosilver as well as nanocopper significantly increases the material stiffness indicated by overall increased tensile and flexural moduli. Besides, this effect increases with increasing silica content. However, the greater improvement in flexural than in tensile modulus was observed. The maximum improvement in flexural modulus is almost 50% achieved for both types of silica. Since the crystallinity of matrix in the HDPE/Ag-SiO2 and HDPE/Cu-SiO2 composites is lower compared to neat HDPE, the increase in tensile and flexural moduli should be attributed to the rigid particles themselves. It is well known that the improvement in the modulus depends on the morphology of nanocomposites [24, 27, 36]. Reinforcing efficiency of the nanofiller is balanced by two opposite phenomena. The negative effect can be attributed to migration of nanoparticles into the interphase of particle-matrix causing worse performance. Dispersion of nanosilica as positive effect could enhance the modulus.Table 7
Tensile, flexural and impact properties of HDPE and the HDPE composites containing Ag-SiO2or Cu-SiO2; tensile and flexural testing speed 5 mm/min.
Property
HDPE
Ag-SiO2 (wt.%)
Cu-SiO2 (wt.%)
10
15
10
15
Tensile strength (MPa)
23
±
0.2
26
±
0.1
27
±
0.3
26
±
0.3
27
±
0.3
Elongation at break (%)
438
±
20
149
±
12
42
±
11
145
±
18
32
±
3
Tensile modulus (MPa)
1390
±
12
1520
±
10
1600
±
14
1570
±
16
1690
±
18
Flexural strength (MPa)
18
±
0.2
24
±
0.3
25
±
0.2
23
±
0.4
25
±
0.5
Flexural modulus (MPa)
640
±
10
898
±
14
950
±
12
893
±
28
949
±
15
Charpy impact strength (kJ/m2)
4.0
±
0.2
4.0
±
0.6
4.1
±
0.3
3.6
±
0.3
3.2
±
0.4As can be seen silica improved tensile and flexural strength of HDPE matrix. However, the greater improvement (35%) in flexural than tensile strength was observed. Generally, the tensile and flexural strength mainly depends on the interfacial interactions between polymer matrix and a filler. This could suggest very good interfacial adhesion between HDPE matrix and silica containing immobilized nanosilver or nanocopper.Correlating the crystalline behavior and mechanical properties of Ag-SiO2 or Cu-SiO2 HDPE composites, one can conclude that the improvements in tensile and flexural properties of composites are mainly caused by the change of the stress state around the nanoparticles, because decreased crystallinity and spherulite size can only lead to decreased stiffness and strength [37]. Of course, the effect of crystalline behavior of matrix on the fracture toughness of a crystalline polymer is very complicated and needs to be further investigated.Moreover, impact strength of the composites strongly depends on the type as well as concentration of silica nanoparticles. However, the addition of silica containing immobilized nanosilver shows no effect on the impact strength. Unlike, the composites filled with Cu-SiO2 exhibit lower impact strength compared to the neat HDPE. Additionally, impact strength decreases as a function of Cu-SiO2 content, due to the growing degree of nanoparticles agglomeration. These results are in good agreement with TEM studies.


### 3.6. Bactericidal Activity

Bactericidal properties of HDPE composites containing the silica with immobilized nanosilver or nanocopper were examined againstE. coli,St. aureus,Salmonella typhimurium,Pseudomonas fluorescens, andBulkolderia cepacia following the ATP test method and the results are shown in Tables 8 and 9. The active nanosilver and nanocopper present in the HDPE composites containing 10 wt.% of nanosilica have a significant influence on the material bactericidal activity. Unlikely, the huge growth of ATP content forSt. aureus onto the composites surface for higher silica content (15 wt.%) was observed. It could be due to the agglomeration of silica nanoparticles. Therefore, this negative effect was much more pronounced for Cu-SiO2 than Ag-SiO2 nanoparticles. Two processes may be considered to explain this finding.(i)
The bacteria were killed by silver or copper nanoparticles immobilized on the silica surface (bactericidal effect).(ii)
The bacteria survived but could not grow to colonies on the polymer surface. The silver or cooper nanoparticles immobilized on the silica surface inhibited the growth of bacterial cells (bacteriostatic effect).Table 8
Vitality ofE. coli and St. aureus onto HDPE and the HDPE/Ag-SiO2and HDPE/Cu-SiO2composites surface determined using ATP method.
Sample
ATP (RLU/cm2)
E. coli
St. aureus
HDPE
2800
603
HDPE/Ag-SiO2 (90/10)
1007
170
HDPE/Ag-SiO2 (85/15)
2133
1273
HDPE/Cu-SiO2 (90/10)
1050
240
HDPE/Cu-SiO2 (85/15)
2600
1800Table 9
Vitality ofSalmonella typhimurium,  Pseudomonas fluorescens and Burkholderia cepacia onto HDPE and the HDPE/Ag-SiO2(90/10) and HDPE/Cu-SiO2(90/10) composites surface determined using ATP method.
Sample
ATP (RLU/cm2)
Salmonella typhimurium
Pseudomonas fluorescens
Burkholderia cepacia
HDPE
5675
2037
2150
HDPE/Ag-SiO2 (90/10)
1606
740
1400
HDPE/Cu-SiO2 (90/10)
683
880
1125From the results shown in Tables8 and 9 it can be concluded that 10 wt.% of Ag-SiO2 or Cu-SiO2 would be sufficient for the HDPE composites to provide good activity against different kinds of bacteria (E. coli,St. aureus,Salmonella typhimurium,Pseudomonas fluorescens, andBurkholderia cepacia), due to the significant ATP reduction (between 50 and 90%). The highest efficacy of the composites containing 10 wt.% of Cu-SiO2 againstSalmonella was observed. Correlating the mechanical and bactericidal properties of the Ag-SiO2 or Cu-SiO2 HDPE composites, one can conclude that the agglomeration of nanoparticles within polymer matrix has stronger effect for bactericidal activity than mechanical properties. It can be explained by very good interfacial adhesion between nanoparticles surface and polymer matrix.


## 3.1. Microstructure of the Silica-Filled HDPE Composites

Filler dispersion and adhesion to the polymer matrix are of great importance for improving the mechanical properties of composites. Good control of the interface morphology of composites is one of the most critical parameters to impart the desired mechanical properties to such materials.In general, good dispersion of inorganic nanofillers in polymer matrices is especially hard to achieve by melt compounding at high filler content [23]. It is well known that the neat silica nanoparticles tend to form agglomerates because of the formation of hydrogen bonds among the abundant hydroxyl groups and adsorbed water on their surface. This effect is more pronounced for higher concentrations of nanosilica [24, 25]. After modification by silver or copper, majority of hydroxyl groups have reacted and silver or copper nanoparticles covered the silica surface. This produces a better dispersion of the silica particles in the polymer matrix, and as a consequence the composite properties improved [17]. Therefore, silica containing immobilized nanosilver or nanocopper presents lower tendency to form agglomerates than neat silica so it can be used at higher concentrations (≥10 wt.%) to give bactericidal properties to the polymer modified. However, the surface activity of the silica is extremely high and the particles consequently have a tendency to aggregate tightly creating micron-sized silica-cluster [23].Transmission electron microscopy was performed to explain the behavior of the silica-filled HDPE composites. Figures4 and 5 show the dispersion state of silica-filled HDPE composites. Comparing composites containing different concentrations of silica, the dispersion of individual silica nanoparticles in the HDPE matrix is finer at lower silica content (10 wt.%). However, the two concentrations of silica are relatively high for such fillers. From the TEM images it is clear that Cu-SiO2 shows bigger tendency to form agglomerates than Ag-SiO2. One possible explanation of this fact could be that the hydrodynamic force induced in the polymer melt during melt compounding exceeds the cohesive force acting between the silica particles forming the agglomerates, resulting in the dispersion of the isolated large silica particles in the HDPE matrix. Moreover, the shear stress induced in the kneaded HDPE melt is not sufficient to provide nanometric dispersion of silica nanoparticles. However, isolated silica nanoparticles were observed inside agglomerates (see Figures 4 and 5).TEM images of HDPE/Ag-SiO2 composites: 10 wt.% Ag-SiO2 ((a), (b)), 15 wt.% Ag-SiO2 ((c), (d)).
(a)
(b)
(c)
(d)TEM images of HDPE/Cu-SiO2 composites: 10 wt.% Cu-SiO2 ((a), (b)), 15 wt.% Ag-SiO2 ((c), (d)).
(a)
(b)
(c)
(d)


## 3.2. Crystallization Behavior of the Silica-Filled HDPE Composites

The effect of nanosilica containing immobilized silver or copper nanoparticles on crystallization behavior of HDPE was determined by DSC measurements. Figures6 and 7 show the second heating and cooling DSC curves of HDPE and investigated silica-filled HDPE composites. The important data obtained are listed in Table 3. It is clear from the results that the addition of silica nanoparticles shows no effect on the melting temperature (Tm) of HDPE matrix. Moreover, there is no effect on the crystallinity of the matrix although the crystallization process starts at a higher temperature. The crystallinity values of HDPE matrix in silica-filled composites are decreased to a maximum 3% achieved by HDPE/Ag-SiO2 composite containing 15% of Ag-SiO2. The crystallization temperatures (Tc) of HDPE in the composites are slightly increased as a function of silica content with a maximum improvement of 3°C. Based on these results, it can be concluded that the crystalline features of HDPE have not been influenced greatly by addition of both silver and copper modified silica nanoparticles. Probably, the presence of nanoparticles prevents the growth of HDPE crystals due to small interparticle distances [26].Table 3
DSC test: thermal transition properties (second run) of HDPE-based composites filled with different contents of Ag-SiO2 or Cu-SiO2.
Sample
T
m (°C)
T
c (°C)
X
c
a (%)
HDPE
134
118
68
HDPE/Ag-SiO2 (90/10)
133
120
66
HDPE/Ag-SiO2 (85/15)
133
121
65
HDPE/Cu-SiO2 (90/10)
133
120
68
HDPE/Cu-SiO2 (85/15)
133
121
67
aAssessed by integrating the normalized area of the melting endothermic peak and rationing the heat involved to the reference value of 100% crystalline HDPE (293 J/g).DSC curves of HDPE and nanosilica containing immobilized nanosilver filled HDPE composites: second heating (a) and cooling run (b).
(a)
(b)DSC curves of HDPE and nanosilica containing immobilized nanocopper filled HDPE composites: second heating (a) and cooling run (b).
(a)
(b)


## 3.3. Thermogravimetric Analysis

The TGA curves of the neat HDPE and silica-filled composites in an air atmosphere are displayed in Figure8. The onset (Ton⁡), maximum (Tmax⁡), and thermooxidative decomposition temperatures at 10% (T10) and 50% weight loss (T50) are evaluated from the TGA curves, as listed in Table 4. It was found that the presence of silica significantly altered the degradation mechanism of HDPE. Ton⁡, T10, T50, and Tmax⁡ of neat HDPE are about 359, 374, 424, and 440°C, respectively. It was observed that silica containing immobilized silver or copper significantly improved thermal properties of HDPE composites due to the 13–41°C higher thermooxidative decomposition temperatures. The onset, maximum, and thermooxidative decomposition temperatures at 50% weight loss of the HDPE/Ag-SiO2 composites are higher than of neat HDPE and tend to increase at higher silica content. Although T10 of the composite filled with silica containing immobilized nanosilver is higher in comparison with neat HDPE, it unfortunately slightly decreases with increasing silica content.Table 4
TGA test: thermooxidative decomposition temperatures of HDPE-based composites filled by different weight percentages of Ag-SiO2or Cu-SiO2.
Sample
T
on
⁡ (°C)
T
10 (°C)
T
50 (°C)
T
max
⁡ (°C)
Residue weight (%)
HDPE
359
374
424
440
0
HDPE/Ag-SiO2 (90/10)
400
396
455
462
8.6
HDPE/Ag-SiO2 (85/15)
404
390
463
464
13.1
HDPE/Cu-SiO2 (90/10)
400
393
457
467
7.5
HDPE/Cu-SiO2 (85/15)
400
400
437
458
11.4TGA curves of HDPE and HDPE composites with nanosilica containing immobilized nanosilver (a) and nanocopper (b).
(a)
(b)In the case of HDPE/Cu-SiO2 composites T50 and Tmax⁡ values are higher compared to neat HDPE but decrease with increasing silica content. The decrease in thermooxidative stability at higher silica content could be attributed to nanoparticles agglomeration [24, 27]. This is in a good agreement with TEM micrographs discussed above (see Figures 4 and 5).An increase in the thermal stability of silica-filled HDPE composites may be explained by the formation of the HDPE-silica nanoparticles network by the physical crosslinking of HDPE via silica nanoparticles; this causes the whole system to be stabilized due to the thermal motions of the HDPE chains being restricted.


## 3.4. Dynamic Mechanical Properties

In order to evaluate the effect of Ag-SiO2 as well as Cu-SiO2 nanoparticles on the HDPE matrix, thermomechanical properties were measured. Due to the very high surface area of the nanoparticles in the HDPE composites, the applied stress is expected to be easily transferred from the matrix onto the silica particles resulting in an enhancement of the mechanical properties. Figures 9 and 10 compare the variation of storage modulus (G′), loss modulus (G′′), and loss tangent (tan δ) as a function of temperature, measured at frequency 1 Hz, for HDPE and the silica-filled HDPE composites studied. These samples present two well-expressed relaxations, α and γ, and a very weak β relaxation. Table 5 summarizes the results for storage modulus at room temperature and temperatures of α, β, and γ relaxations.Table 5
DMTA results for HDPE and the HDPE composites containing Ag-SiO2 or Cu-SiO2.
Sample
Storage modulus (MPa) at 23°C
Loss modulus (peak position) (°C)
Loss modulus (peak high) (MPa)
T
γ
T
β
T
α
T
γ
T
β
T
α
HDPE
1140
−120.2
−36.3
41.9
169
35.7
105
HDPE/Ag-SiO2 (90/10)
1250
−119.6
−47.1
44.1
143
43.6
112
HDPE/Ag-SiO2 (85/15)
1320
−119.9
−51.3
44.6
157
49.7
116
HDPE/Cu-SiO2 (90/10)
1240
−122.0
−41.8
45.7
157
36.3
113
HDPE/Cu-SiO2 (85/15)
1270
−121.8
−47.1
44.5
163
40.5
116Dynamic mechanical relaxation behavior versus temperature of HDPE and silica containing immobilized nanosilver filled HDPE composites at frequency of 1 Hz:G′ (a), G′′ (b), and tan δ (c).
(a)
(b)
(c)Dynamic mechanical relaxation behavior versus temperature of HDPE and silica containing immobilized nanocopper filled HDPE composites at frequency of 1 Hz:G′ (a), G′′ (b), and tan δ (c).
(a)
(b)
(c)The storage modulus of the HDPE/Ag-SiO2 and HDPE/Cu-SiO2 composites was significantly higher than corresponding HDPE in the β and α relaxations regions, due to the stiffening effect of the silica. As showed in Table 5, the addition of Ag-SiO2 to HDPE improved G′ at 23°C by about 10–15%. Silica could hinder the chain motion of HDPE, which would improve the modulus. As a result of these changes, the storage modulus of the interface is higher than that of the free part. An increase in the Ag-SiO2 content enlarges the interfacial area and results in increased volume of interphase.Theα relaxation is well expressed as a maximum in loss modulus and as a small hump before the melting process in the temperature dependence of tan δ. This relaxation appears centered at 42°C for HDPE. The addition of silica containing immobilized nanosilver or nanocopper increases α relaxation to about 46°C. However, the value of the α relaxation strongly depends on the type and content of silica. Moreover, it can be seen that the composites show higher α peak intensity compared to neat HDPE indicating higher stiffness of the material. The α relaxation has been defined as the reorientation of molecules within the crystal [28]. It was reported [29] that there is a relation between crystallites’ thickness and intensity of the α relaxation and that this process is affected by the chain mobility of the crystallites. Therefore, chain mobility occurs at higher temperature as crystallite thickness increases. The position and intensity of the α relaxation maximum is usually connected with crystallites’ thickness and crystallinity level, respectively [30].Theγ relaxation occurs as a maximum at −118°C for the HDPE, from −118°C to −122°C for the composites in loss modulus, and at slightly higher temperatures in tan δ, with corresponding decrease in storage modulus, compare Table 5 and Table 6. This is a clear effect of silica containing immobilized nanosilver or nanocopper loading on the breadth and location of the relaxation; this process is shifted to lower temperatures in the presence of silica, as a consequence of slightly lower crystallinity as compared to HDPE. The γ relaxation has been associated with a single relaxation process, predominantly of amorphous origin. This relaxation is typical for the joint movements of chains containing three or more methylene groups (units) in the main chain [29, 30]. The intensity of the γ relaxation is usually associated with the amorphous region of semicrystalline polymers. Therefore, the decrease in the intensity of γ relaxation of the silica-filled composites can be attributed to the decrease in the quantity of the amorphous phase. It was reported that the position of γ loss modulus peak can change between −125°C and −105°C depending on the type of polyethylene (LDPE, LLDPE, or HDPE) and therefore on crystallinity degree (between 20% and 70%) [31–33].Table 6
DMTA results for HDPE and the HDPE composites containing Ag-SiO2 or Cu-SiO2.
Sample
Loss tangent (peak position) (°C)
Loss tangent (peak high)
T
γ
T
γ
HDPE
−116.4
0.0630
HDPE/Ag-SiO2 (90/10)
−116.8
0.0605
HDPE/Ag-SiO2 (85/15)
−117.6
0.0584
HDPE/Cu-SiO2 (90/10)
−117.5
0.0567
HDPE/Cu-SiO2 (85/15)
−117.6
0.0567At temperatures below theγ relaxation storage modulus G′ of the HDPE/Ag-SiO2 composites becomes smaller than of HDPE as well as the HDPE/Cu-SiO2 composites. One possible explanation of this fact could be that below that relaxation the modulus of elasticity of the amorphous phase is higher than that of the crystal one. These samples have the lowest quantity of amorphous phase (see Figures 9(b) and 10(b)) and moreover the physical cross-linking now could not contribute to the increasing of the storage modulus.Theβ relaxation can be observed as a weak maximum in loss modulus (Figures 9(b) and 10(b)) for HDPE and silica-filled HDPE composites. It was found that β relaxation occurs between −5°C and −50°C depending upon the type of polyethylene [30, 33, 34]. Some authors have concluded that the β relaxation results from motion of chain units in the interfacial region [34], whereas others attributed this process to the glass transition [31]. Nitta and Tanaka have suggested a different molecular origin of the β relaxation in linear polyethylene with high molecular weights quite dissimilar to those aforementioned for branched polyethylene [30]. Because of the formation of loose tie and loop molecules in the amorphous layers in polyethylene with high molecular weights, the β relaxation seems to be a consequence of the motion of the loose tie molecules in this type of polyethylene. The absence of the β relaxation in typical linear polyethylene having a thinner amorphous layer, which is considered to promote taut tie molecules, can be directly attributed to the lack of loose tie molecules [35].Theβ-relaxation appears as a maximum at −36°C for HDPE and 5–15°C lower temperature for the HDPE composites. Evidently, the HDPE/Ag-SiO2 composite containing 15 wt.% Ag-SiO2 shows the highest intensity of β transition peak amongst all the samples. This is related to increased interfacial interactions between HDPE matrix and Ag-SiO2 or Cu-SiO2 nanoparticles.


## 3.5. Mechanical Properties

The mechanical properties of polymer composites depend crucially upon the efficiency of stress transfer from the polymer matrix to the fillers, which will be influenced by the interphase. The interphase in composites is the boundary layer between filler surface and polymer matrix, which exhibits local properties different from those of the bulk matrix.The effect of silica containing immobilized nanosilver or nanocopper on the mechanical properties of HDPE composites is summarized in Table7. The incorporation of both types of silica nanoparticles reinforces HDPE but reduces the ductility of the matrix. Moreover, the addition of silica containing immobilized nanosilver as well as nanocopper significantly increases the material stiffness indicated by overall increased tensile and flexural moduli. Besides, this effect increases with increasing silica content. However, the greater improvement in flexural than in tensile modulus was observed. The maximum improvement in flexural modulus is almost 50% achieved for both types of silica. Since the crystallinity of matrix in the HDPE/Ag-SiO2 and HDPE/Cu-SiO2 composites is lower compared to neat HDPE, the increase in tensile and flexural moduli should be attributed to the rigid particles themselves. It is well known that the improvement in the modulus depends on the morphology of nanocomposites [24, 27, 36]. Reinforcing efficiency of the nanofiller is balanced by two opposite phenomena. The negative effect can be attributed to migration of nanoparticles into the interphase of particle-matrix causing worse performance. Dispersion of nanosilica as positive effect could enhance the modulus.Table 7
Tensile, flexural and impact properties of HDPE and the HDPE composites containing Ag-SiO2or Cu-SiO2; tensile and flexural testing speed 5 mm/min.
Property
HDPE
Ag-SiO2 (wt.%)
Cu-SiO2 (wt.%)
10
15
10
15
Tensile strength (MPa)
23
±
0.2
26
±
0.1
27
±
0.3
26
±
0.3
27
±
0.3
Elongation at break (%)
438
±
20
149
±
12
42
±
11
145
±
18
32
±
3
Tensile modulus (MPa)
1390
±
12
1520
±
10
1600
±
14
1570
±
16
1690
±
18
Flexural strength (MPa)
18
±
0.2
24
±
0.3
25
±
0.2
23
±
0.4
25
±
0.5
Flexural modulus (MPa)
640
±
10
898
±
14
950
±
12
893
±
28
949
±
15
Charpy impact strength (kJ/m2)
4.0
±
0.2
4.0
±
0.6
4.1
±
0.3
3.6
±
0.3
3.2
±
0.4As can be seen silica improved tensile and flexural strength of HDPE matrix. However, the greater improvement (35%) in flexural than tensile strength was observed. Generally, the tensile and flexural strength mainly depends on the interfacial interactions between polymer matrix and a filler. This could suggest very good interfacial adhesion between HDPE matrix and silica containing immobilized nanosilver or nanocopper.Correlating the crystalline behavior and mechanical properties of Ag-SiO2 or Cu-SiO2 HDPE composites, one can conclude that the improvements in tensile and flexural properties of composites are mainly caused by the change of the stress state around the nanoparticles, because decreased crystallinity and spherulite size can only lead to decreased stiffness and strength [37]. Of course, the effect of crystalline behavior of matrix on the fracture toughness of a crystalline polymer is very complicated and needs to be further investigated.Moreover, impact strength of the composites strongly depends on the type as well as concentration of silica nanoparticles. However, the addition of silica containing immobilized nanosilver shows no effect on the impact strength. Unlike, the composites filled with Cu-SiO2 exhibit lower impact strength compared to the neat HDPE. Additionally, impact strength decreases as a function of Cu-SiO2 content, due to the growing degree of nanoparticles agglomeration. These results are in good agreement with TEM studies.


## 3.6. Bactericidal Activity

Bactericidal properties of HDPE composites containing the silica with immobilized nanosilver or nanocopper were examined againstE. coli,St. aureus,Salmonella typhimurium,Pseudomonas fluorescens, andBulkolderia cepacia following the ATP test method and the results are shown in Tables 8 and 9. The active nanosilver and nanocopper present in the HDPE composites containing 10 wt.% of nanosilica have a significant influence on the material bactericidal activity. Unlikely, the huge growth of ATP content forSt. aureus onto the composites surface for higher silica content (15 wt.%) was observed. It could be due to the agglomeration of silica nanoparticles. Therefore, this negative effect was much more pronounced for Cu-SiO2 than Ag-SiO2 nanoparticles. Two processes may be considered to explain this finding.(i)
The bacteria were killed by silver or copper nanoparticles immobilized on the silica surface (bactericidal effect).(ii)
The bacteria survived but could not grow to colonies on the polymer surface. The silver or cooper nanoparticles immobilized on the silica surface inhibited the growth of bacterial cells (bacteriostatic effect).Table 8
Vitality ofE. coli and St. aureus onto HDPE and the HDPE/Ag-SiO2and HDPE/Cu-SiO2composites surface determined using ATP method.
Sample
ATP (RLU/cm2)
E. coli
St. aureus
HDPE
2800
603
HDPE/Ag-SiO2 (90/10)
1007
170
HDPE/Ag-SiO2 (85/15)
2133
1273
HDPE/Cu-SiO2 (90/10)
1050
240
HDPE/Cu-SiO2 (85/15)
2600
1800Table 9
Vitality ofSalmonella typhimurium,  Pseudomonas fluorescens and Burkholderia cepacia onto HDPE and the HDPE/Ag-SiO2(90/10) and HDPE/Cu-SiO2(90/10) composites surface determined using ATP method.
Sample
ATP (RLU/cm2)
Salmonella typhimurium
Pseudomonas fluorescens
Burkholderia cepacia
HDPE
5675
2037
2150
HDPE/Ag-SiO2 (90/10)
1606
740
1400
HDPE/Cu-SiO2 (90/10)
683
880
1125From the results shown in Tables8 and 9 it can be concluded that 10 wt.% of Ag-SiO2 or Cu-SiO2 would be sufficient for the HDPE composites to provide good activity against different kinds of bacteria (E. coli,St. aureus,Salmonella typhimurium,Pseudomonas fluorescens, andBurkholderia cepacia), due to the significant ATP reduction (between 50 and 90%). The highest efficacy of the composites containing 10 wt.% of Cu-SiO2 againstSalmonella was observed. Correlating the mechanical and bactericidal properties of the Ag-SiO2 or Cu-SiO2 HDPE composites, one can conclude that the agglomeration of nanoparticles within polymer matrix has stronger effect for bactericidal activity than mechanical properties. It can be explained by very good interfacial adhesion between nanoparticles surface and polymer matrix.


## 4. Conclusions

In this study, the silica nanoparticles containing immobilized nanosilver or nanocopper were compounded in HDPE by melt blending. From the TEM images it is clear that Cu-SiO2 shows bigger tendency to form agglomerates than Ag-SiO2. However, individual silica nanoparticles separated by the polymer matrix could be seen inside agglomerates. Based on DSC results, it can be concluded that the crystalline features of HDPE have not been influenced greatly by addition of both silver and copper modified silica nanoparticles. Probably, the presence of nanoparticles prevents the growth of HDPE crystals due to small interparticle distances. The thermal stability of the composites containing Ag-SiO2 as well as Cu-SiO2 nanoparticles was extremely better compared to neat HDPE. From DMTA measurements, both storage modulus and loss modulus of all HDPE/silica composites are increased in β and α relaxation regions indicating that the material became stiffer. Moreover, the gradual enhancement in tensile and flexural strength of the HDPE composites was observed. The addition of silica nanoparticles to the HDPE increased tensile modulus and flexural modulus, pointing to a synergetic effect arising from the presence of the reinforced HDPE phase and very good interfacial interactions between nanoparticles surface and polymer matrix. Maximum improvement in flexural modulus is about 50% achieved by the HDPE composite containing 15 wt.% of Ag-SiO2 as well as Cu-SiO2 nanoparticles. HDPE composites modified with nanosilica containing immobilized nanosilver or nanocopper were found to be active againstE. coli,St. aureus,Salmonella typhimurium,Pseudomonas fluorescens, andBurkholderia cepacia whereas unmodified (without Ag-SiO2 or Cu-SiO2) did not show this efficacy. Thus silica-filled HDPE composites containing active nanosilver or nanocopper are effective bactericidal materials.



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*Source: 183724-2014-05-07.xml*