# Enhancement of Mechanical and Dynamic Mechanical Properties of Hydrophilic Nanoclay Reinforced Polylactic Acid/Polycaprolactone/Oil Palm Mesocarp Fiber Hybrid Composites

Authors: Chern Chiet Eng; Nor Azowa Ibrahim; Norhazlin Zainuddin; Hidayah Ariffin; Wan Md. Zin Wan Yunus; Yoon Yee Then
Journal: International Journal of Polymer Science
 (2014)

---

## Abstract

In previous studies, the effect of the addition of 1 wt% hydrophilic nanoclay on polylactic acid (PLA)/polycaprolactone (PCL)/oil palm mesocarp fiber (OPMF) biocomposites was investigated by tensile properties, thermogravimetric analysis (TGA), and scanning electron microscopy (SEM). The current studies focus on the effect of addition of 1 wt% hydrophilic nanoclay on mechanical (flexural and impact properties) and dynamic mechanical properties of composites. The composites were characterized by the Fourier transform infrared spectroscopy (FTIR) and dynamic mechanical analysis (DMA). FTIR spectra show that peak shifting occurs when 1 wt% hydrophilic nanoclay was added to composites. The addition of 1 wt% hydrophilic nanoclay successfully improves the flexural properties and impact resistance of the biocomposites. The storage modulus of biocomposites was decreased when nanoclay was added which indicates that the stiffness of biocomposites was reduced. The loss modulus curve shows that the addition of nanoclay shift twotg in composites become closer to each other which indicates that the incorporation of nanoclay slightly compatibilizes the biocomposites. Tan δ indicated that hybrid composites dissipate less energy compared to biocomposites indicate that addition of clay to biocomposites improves fiber/matrix adhesion. Water sorption test shows that the addition of nanoclay enhances water resistance of composites.


---

## Body

## 1. Introduction

In our preliminary studies [1], we reported that the incorporation 1 wt% of hydrophilic nanoclay in polylactic Acid (PLA)/polycaprolactone (PCL) blends successfully enhance the morphology, mechanical and thermal properties of the blends. Therefore, we choose incorporation of 1 wt% of hydrophilic nanoclay into PLA/PCL/oil palm mesocarp fiber (OPMF) biocomposites to study the effect of nanoclay on biocomposites.In our previous paper [2], we reported that the addition of 1 wt% hydrophilic nanoclay to PLA/PCL/OPMF biocomposites increases the tensile strength and elongation at break of biocomposites around 8.48% and 32.14%, respectively, at 10% fiber loading. Besides, thermogravimetric analysis (TGA) results show that the presence of clay increases the thermal stability of the biocomposites. Scanning electron microscopy (SEM) micrographs revealed that PLA/PCL/OPMF biocomposites consist of cavity which indicated poor fiber/matrix adhesion while micrographs of PLA/PCL/OPMF/clay hybrid composites show better fiber/matrix adhesion as no cavity is present at facture surfaces.Natural fiber as reinforcement filler in polymer composites has received increasing attention from researchers as natural fibers have many significant advantages over synthetic fibers. They are environmentally friendly, fully biodegradable, abundantly available, renewable, and cheap and have low density [3]. However, there are some disadvantages such as poor wetability, incompatibility with some polymeric matrices, and high moisture adsorption which restrict their usage in polymer composites [4].The oil palm (Elaeis guineensis) originates from South Africa which grows well in all tropical areas of the world and it has become one of the main industrial crops. Malaysian palm oil industry has grown tremendously over the last 25 years and has become the world’s leading producer and exporter of palm oil [5]. For every kg of palm oil produced, approximately 4 kg of dry biomass is produced, excluding palm oil mill effluent (POME). In 2010, the amount of mesocarp fiber available was 10.80 Mt/year [6]. Therefore, there is huge amount of fiber that can be utilized instead of being discarded as waste. Traditionally, the mesocarp fiber is mixed with kernel shell and is being utilized as solid fuel to generate electricity for the mill.Polylactic acid (PLA) is biodegradable polymer with good mechanical properties, thermal plasticity, and biocompatibility. However, PLA is a comparatively brittle and stiff polymer with low deformation at break. Therefore, modification of PLA is needed in order to compete with other flexible polymers such as polypropylene or polyethylene [7]. Polycaprolactone (PCL) is flexible semicrystalline biodegradable polymer with low melting point and exceptional blend compatibility. High flexibility of PCL can be considered as a good plasticizer for PLA compared to low molecular weight plasticizers as it does not migrate to the surface of the blended samples and the physical properties cannot be debased [8].Recently, many studies have been conducted by academic or industrial researcher on biodegradable polymer in order to replace conventional nonbiodegradable polymer which causes major drawback to the environment. However, the cost of biodegradable polymer is comparatively higher than petrochemical based nonbiodegradable polymer which limits its application. The incorporation of cheap natural fibers as reinforcement filler into biodegradable polymer is an alternative to reduce its cost.Hybrid composites are materials made by combining two or more different types of fillers in a single matrix. Although several fillers can be incorporated into the hybrid system, a combination of only two types of fillers would be more beneficial. By careful selection of the reinforcing fillers/fibers, the performance properties of the resulting composite can be significantly improved while the material cost can be substantially reduced [9]. The properties of hybrid composites depend on the individual components in which there is a more favourable balance between the inherent advantages and disadvantages. Besides, the advantages of one type of filler could complement the other filler in hybrid composite that contains two or more types of fillers. Through proper material design, a hybrid composite with balance in cost and performance could be obtained [10].Kord [11] investigates the effect of nanoclay on polypropylene (PP)/hemp fiber composites. The increment of nanoclay loading is up to 3% increase in tensile modulus, tensile strength, and elongation at break of composites. However, the increment of nanoclay loading decreases the impact strength. Besides, the increment of nanoclay loading significantly decreases water absorption and swelling thickness of composites. The dynamic mechanical behaviour and fire properties of composites were improved by the addition of nanoclay. X-ray diffraction (XRD) shows that the dispersion of nanoclay in the hemp fiber/PP samples is not exfoliated.The aim of incorporation of cheap natural fiber (OPMF) into expensive biodegradable polymer (PLA and PCL) was to reduce its cost. The addition of hydrophilic fiber to hydrophobic matrix will reduce the mechanical strength as incompatibility between fiber and matrix; therefore the objective of this paper is to investigate the effect of addition of 1 wt% of hydrophilic nanoclay on mechanical, dynamic mechanical, morphology, and water absorption properties of PLA/PCL/OPMF/nanoclay hybrid composites by melt intercalation. Various characterization techniques such as the Fourier transform infrared spectroscopy (FTIR) and dynamic mechanical analysis (DMA) were used to study the effect of addition of nanoclay on the properties of PLA/PCL/OPMF/nanoclay hybrid composites.


## 2. Experimental

### 2.1. Materials

All reactions were carried out by using reagent grade chemicals (>98% purity) without further purification. The hydrophilic nanoclay (Nanomer PGV) was purchased from Sigma-Aldrich and used as received. Polylactide Resin 4060D was supplied by NatureWorks while polycaprolactone (CAPA 650) was supplied by the Solvay caprolactone. Oil palm mesocarp fibers were obtained from Felda Palm Ind. Sdn Bhd., Serting Hilir.


### 2.2. Preparation of Hybrid Composites

The composites were prepared by melt blending technique where the composition of PLA and PCL was kept constant at 85 wt% and 15 wt%, respectively, in blend, while the clay content was constant at 1 wt%. Only the content of OPMF varies from 0% to 30%. PLA, PCL, nanoclay, and OPMF were manually premixed in a container and fed into Brabender Plastograph EC at 170°C with rotor speed of 50 rpm for 10 minutes. The products were then compression moulded into sheets of 1 mm thickness by an electrically heated hydraulic press with a force of 1500 kN at 160°C for 10 minutes. The sample sheets were then used for further characterization.


### 2.3. The Fourier Transform Infrared Spectroscopy (FTIR)

Perkin Elmer Spectrum 100 series spectrometer equipped with attenuated total reflectance (ATR) was used to determine the functional groups and types of the bonding of the samples with the infrared spectra recorded in the range of frequency of 280 to 4000 cm−1 with the resolution of 4 cm−1 and number of scan being 16 scans.


### 2.4. Tensile Properties

Tensile properties measurement was performed by Instron machine model 4301, with grip attachment distance of 45 mm. Load of 1.0 kN was applied at constant crosshead speed of 5 mm min−1. Computerized Instron (Software series 9, national instruments GPIB PC2/2a, and NI-488.2) was used to process data. Test specimens were prepared and stamped in compliance with ASTM D638 dumbbell parameters. Sample thickness was measured with Mitutoyo Digimatic Indicator, type IDF-112, having measuring accuracy of ±0.001 mm.


### 2.5. Flexural Properties

The flexural strength and modulus were measured with Instron Universal Testing Machine 4301 according to ASTM D790. The size of the samples testing is 127 mm × 12.7 mm × 3 mm. The crosshead speed is 1.3 mm/min and the support span length is 48 mm. Data was processed with computerized Instron (Software series 9, national instruments GPIB PC2/2a, and NI-488.2).


### 2.6. The Izod Impact Strength

The Izod impact test was carried out according to ASTM D256 standard using an impact tester (The IZOD Impact Tester). The sample size is 63.5 × 12.7 × 3 mm, while the notch length is 2.54 mm. The energy required to break the samples was divided by unit area of residual cross section of sample to obtain impact resistance value. The impact strength (J/m) was calculated by dividing the energy obtained (J) with the thickness of specimen (m).


### 2.7. Thermogravimetric Analysis (TGA)

TGA testing was conducted in accordance with ASTM E1131. Perkin Elmer TGA7 was used for thermogravimetric analysis of samples where about 15 mg of the samples was heated from 35°C to 800°C with the heating rate of 10°C/min. Nitrogen gas was pumped with the flow rate of 20 mL/min in order to let the analysis be carried out in nitrogen atmosphere.


### 2.8. Dynamic Mechanical Analysis (DMA)

DMA testing was conducted in accordance with ASTM D5023-07. The Perkin Elmer Model Pyris Diamond DMA was used. Samples were tested under the condition of static force 10 N and dynamic force 8 N with 1 Hz frequencies. Scan was done from −100°C to 130°C at 2°C/min rate with sample dimensions being 1 mm in thickness and 30 mm in length by using bending mode.


### 2.9. Scanning Electron Microscopy (SEM)

The surface morphology of fracture surface was observed with SEM JEOL JSM-6400. The fracture surface was obtained from plain strain fracture tensile tested specimens and was sputter coated with gold using biorad coating system before viewing.


### 2.10. Water Sorption Test

Water absorption studies were performed following the ASTM D638, type M3 standard. The films were cut into dumbbell shapes and dried at room temperature overnight to reach the constant weight. Then, the samples were immersed at 25°C of distilled water for up to 30 days. Mass uptakes of the samples were measured periodically by removing them from the water bath. The samples were wiped with the tissue paper to remove the surface water. The moisture uptake expressed in percent weight gain,ΔM, is
(1)
Δ
M
=
M
t
-
M
o
M
o
×
100
%
,
whereM
t = mass of sample after immersion andM
o = mass of sample before immersion.


## 2.1. Materials

All reactions were carried out by using reagent grade chemicals (>98% purity) without further purification. The hydrophilic nanoclay (Nanomer PGV) was purchased from Sigma-Aldrich and used as received. Polylactide Resin 4060D was supplied by NatureWorks while polycaprolactone (CAPA 650) was supplied by the Solvay caprolactone. Oil palm mesocarp fibers were obtained from Felda Palm Ind. Sdn Bhd., Serting Hilir.


## 2.2. Preparation of Hybrid Composites

The composites were prepared by melt blending technique where the composition of PLA and PCL was kept constant at 85 wt% and 15 wt%, respectively, in blend, while the clay content was constant at 1 wt%. Only the content of OPMF varies from 0% to 30%. PLA, PCL, nanoclay, and OPMF were manually premixed in a container and fed into Brabender Plastograph EC at 170°C with rotor speed of 50 rpm for 10 minutes. The products were then compression moulded into sheets of 1 mm thickness by an electrically heated hydraulic press with a force of 1500 kN at 160°C for 10 minutes. The sample sheets were then used for further characterization.


## 2.3. The Fourier Transform Infrared Spectroscopy (FTIR)

Perkin Elmer Spectrum 100 series spectrometer equipped with attenuated total reflectance (ATR) was used to determine the functional groups and types of the bonding of the samples with the infrared spectra recorded in the range of frequency of 280 to 4000 cm−1 with the resolution of 4 cm−1 and number of scan being 16 scans.


## 2.4. Tensile Properties

Tensile properties measurement was performed by Instron machine model 4301, with grip attachment distance of 45 mm. Load of 1.0 kN was applied at constant crosshead speed of 5 mm min−1. Computerized Instron (Software series 9, national instruments GPIB PC2/2a, and NI-488.2) was used to process data. Test specimens were prepared and stamped in compliance with ASTM D638 dumbbell parameters. Sample thickness was measured with Mitutoyo Digimatic Indicator, type IDF-112, having measuring accuracy of ±0.001 mm.


## 2.5. Flexural Properties

The flexural strength and modulus were measured with Instron Universal Testing Machine 4301 according to ASTM D790. The size of the samples testing is 127 mm × 12.7 mm × 3 mm. The crosshead speed is 1.3 mm/min and the support span length is 48 mm. Data was processed with computerized Instron (Software series 9, national instruments GPIB PC2/2a, and NI-488.2).


## 2.6. The Izod Impact Strength

The Izod impact test was carried out according to ASTM D256 standard using an impact tester (The IZOD Impact Tester). The sample size is 63.5 × 12.7 × 3 mm, while the notch length is 2.54 mm. The energy required to break the samples was divided by unit area of residual cross section of sample to obtain impact resistance value. The impact strength (J/m) was calculated by dividing the energy obtained (J) with the thickness of specimen (m).


## 2.7. Thermogravimetric Analysis (TGA)

TGA testing was conducted in accordance with ASTM E1131. Perkin Elmer TGA7 was used for thermogravimetric analysis of samples where about 15 mg of the samples was heated from 35°C to 800°C with the heating rate of 10°C/min. Nitrogen gas was pumped with the flow rate of 20 mL/min in order to let the analysis be carried out in nitrogen atmosphere.


## 2.8. Dynamic Mechanical Analysis (DMA)

DMA testing was conducted in accordance with ASTM D5023-07. The Perkin Elmer Model Pyris Diamond DMA was used. Samples were tested under the condition of static force 10 N and dynamic force 8 N with 1 Hz frequencies. Scan was done from −100°C to 130°C at 2°C/min rate with sample dimensions being 1 mm in thickness and 30 mm in length by using bending mode.


## 2.9. Scanning Electron Microscopy (SEM)

The surface morphology of fracture surface was observed with SEM JEOL JSM-6400. The fracture surface was obtained from plain strain fracture tensile tested specimens and was sputter coated with gold using biorad coating system before viewing.


## 2.10. Water Sorption Test

Water absorption studies were performed following the ASTM D638, type M3 standard. The films were cut into dumbbell shapes and dried at room temperature overnight to reach the constant weight. Then, the samples were immersed at 25°C of distilled water for up to 30 days. Mass uptakes of the samples were measured periodically by removing them from the water bath. The samples were wiped with the tissue paper to remove the surface water. The moisture uptake expressed in percent weight gain,ΔM, is
(1)
Δ
M
=
M
t
-
M
o
M
o
×
100
%
,
whereM
t = mass of sample after immersion andM
o = mass of sample before immersion.


## 3. Results and Discussion

### 3.1. The Fourier Transform Infrared Spectroscopy (FTIR)

FTIR spectra of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites are shown in Figure1. Both composites exhibit strong absorbance peak at 1748.90 cm−1and 1745 cm−1, respectively, indicating the presence of C=O stretching. Besides, C–H stretching is present in both composites but the intensity of the peak for PLA/PCL/1 wt% clay/OPMF hybrid composites is higher than PLA/PCL/OPMF biocomposites with the peak at 2939 cm−1 and 2947 cm−1, respectively. Shifting of peaks in IR spectra is observed when there is strong interaction in polymer blends [12]. Therefore, peak shifting is observed when 1 wt% of clay was incorporated into biocomposites which indicated that there might be some physical interaction between PLA, PCL, clay, and OPMF in composites.Figure 1
FTIR spectra of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


### 3.2. Tensile Properties

In our previous studies [2], we reported that the addition of 1 wt% of nanoclay successfully increases the tensile strength and elongation at break but decreases the tensile modulus of PLA/PCL/OPMF biocomposites which is summarized in Table 1. PLA/PCL/OPMF biocomposites show the highest tensile strength at 10 wt% of the fiber loading and decrease with the increasing of fiber loading which results from poor dispersion of fibers which leads to agglomeration of fillers. Besides, fiber acts as included filler in the resin matrix, which weakens the composite due to poor interfacial adhesion and obstructs the stress propagation, which leads to reduction of tensile strength as the filler loading increases. The presence of hydrophilic nanoclay increases the overall tensile strength of hybrid composites which suggests that the presence of hydrophilic nanoclay acts as physical compatibilizing agents between hydrophilic fiber and hydrophobic matrix and thus improves the fiber/matrix adhesion of hybrid composites. This might be due to the addition of nanoclay which successfully improves the miscibility of PLA/PLA in blends [1], while at the same time the presence of hydrophilic nanoclay is more compatible with hydrophilic fiber which enhances better physical interaction between fiber and matrix resulting in better mechanical properties of hybrid composites.Table 1
Tensile properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.
Sample
Tensile strength (MPa)
Elongation at break (mm)
Tensile modulus (MPa)
PLA85/PCL15
45.94
±
1.75
1.68
±
0.30
902.92
±
50.69
PLA85/PCL15/10 wt% OPMF
33.48
±
2.44
0.56
±
0.04
884.80
±
44.16
PLA85/PCL15/20 wt% OPMF
27.99
±
1.34
0.40
±
0.02
878.73
±
44.79
PLA85/PCL15/30 wt% OPMF
22.43
±
1.37
0.35
±
0.02
723.37
±
31.37
PLA85/PCL15/1 wt% clay/10 wt% OPMF
36.32
±
1.22
0.74
±
0.02
685.80
±
71.32
PLA85/PCL15/1 wt% clay/20 wt% OPMF
32.32
±
0.55
0.64
±
0.10
661.17
±
46.36
PLA85/PCL15/1 wt% clay/30 wt% OPMF
29.46
±
1.58
0.61
±
0.02
577.18
±
27.04The addition of fiber decreases the elongation at break of composites from 1.68 mm to 0.56 mm (PLA/PCL/OPMF biocomposites) and 0.74 mm (PLA/PCL/OPMF/1 wt% clay hybrid composites), respectively, at 10 wt% fiber loading. The addition of fiber into matrix causes composites to become stiffer and harder as the segment mobility of the composites is reduced which leads to low elongation. On the other hand, the addition of hydrophilic nanoclay improves the fiber/matrix adhesion of hybrid composites and also stress transfer within hybrid composites which enhance the flexibility of the composites. Therefore, PLA/PCL/OPMF/1 wt% clay hybrid composites show better elongation at break than PLA/PCL/OPMF biocomposites.Tensile modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/OPMF/1 wt% clay hybrid composites indicates that the overall tensile modulus of biocomposites is higher than hybrid composites. Therefore, this implies that the addition of hydrophilic nanoclay decreases the stiffness of the composites as the flexibility of composites increase which leads to lower tensile modulus.


### 3.3. Flexural Properties

Flexural strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure2. The addition of 1% clay in hybrid compositesshows better flexural strength (36.53 MPa) compared to biocomposites (21.45 MPa) at 10 wt% fiber loading. Therefore, the addition of clay has positive effect on flexural strength of hybrid composites due to better interfacial adhesion between matrix and filler which will improve stress transfer from matrix to filler resulting in higher values of flexural strength. Weak fiber/matrix interfacial bonding results in poor flexural properties [13]. When higher amount of fiber is incorporated into the composites, flexural strength decreases. This is due to the increment of population of fiber defects and fiber ends with increased fiber content. The fiber defects could act as source of stress concentration in composites [14].Figure 2
Flexural strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure3 shows flexural modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. The biocomposites show increment in flexural modulus from 2437.80 MPa to 2797.00 MPa, while hybrid composites do not show changes in flexural modulus (2433.20 MPa) when 10 wt% of fiber was added. When the amount of fiber increases, the flexural modulus of hybrid composites increases and flexural modulus of biocomposites decreases. The increasing trend in flexural modulus with the increment amount of fiber for hybrid composites due to the addition of fillers with higher stiffness than matrix is mentioned by [15]. However, biocomposites show decrement of flexural modulus with increment of fiber loading due to poor interfacial adhesion between fiber and matrix which leads to low flexural modulus.Figure 3
Flexural modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


### 3.4. The Izod Impact Strength

Impact strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure4. The impact strength decreases from 188.70 J/m (PLA85/PCL15) to 82.37 J/m and 95.44 J/m for biocomposites and hybrid composites, respectively, at 10 wt% fiber loading. When fiber is incorporated into matrix, poor energy absorbing capability of fiber inhibit deformation and ductile mobility of polymer molecules which lower the ability of composites to absorb energy during crack propagation. Besides, less energy is required to initiate a crack as fiber creates high stress concentration regions [16]. However, the impact strength of hybrid composites is higher than biocomposites as the addition of clay improves impact strength of hybrid composites due to better fiber/matrix adhesion in hybrid composites compared to biocomposites.Figure 4
Impact strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


### 3.5. Thermogravimetric Analysis (TGA)

Previously we reported that incorporation of nanoclay improves the thermal stability of PLA/PCL/OPMF biocomposites [2]. The PLA/PCL/OPMF biocomposites show onset temperature of 196.01°C, which increases to 221.12°C when clay is added to the biocomposites. Table 2 shows the thermal properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. The increment of thermal stability of hybrid composites due to clay can hinder the permeability of volatile degradation products out of the materials. The dispersed clay forms a barrier which delays the release of thermal degradation products compared to the neat polymer [17].Table 2
Thermal properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.
Sample
Onset temperature (°C)
Offset temperature (°C)
% of degradation
PLA/PCL/OPMF
196.01
473.84
72.78
PLA/PCL/1 wt% clay/OPMF
221.12
458.36
71.08


### 3.6. Dynamic Mechanical Analysis (DMA)

The storage modulus (G
′) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure 5. All the fiber loading in composites for DMA testing is 10 wt%. Increment of G
′ after addition of fibers is due to incorporation of high modulus fibers in the matrix. The value of storage modulus decreases at higher temperature due to loss in stiffness of the fibers [18]. The G
′ results show agreement with the flexural modulus results as biocomposites show higher tensile modulus than hybrid composites. The addition of clay shows considerable effect on the elastic properties of hybrid composites by reducing the stiffness of the hybrid composites.Figure 5
Storage modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure6 shows the loss modulus (G
′
′) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. All the fiber loading in composites for DMA testing is 10 wt%. Loss modulus indicates the material’s ability to dissipate energy in the form of heat or molecular rearrangements during the deformation [19]. The loss modulus accounts for the viscous component of the complex modulus or the out of phase component with the applied strain which normally increases with the addition of filler [20]. The addition of fiber increases the G
′
′ of biocomposites and hybrid composites at the temperature around −68°C and then decreases at 48°C. The addition of clay to biocomposites slightly shiftsT
g of biocomposites from −67.7°C to −67.0°C at PCL region and also from 47.6°C to 46.5°C at PLA region which suggests that the incorporation of clay slightly compatibilizes the biocomposites resulting in better mechanical properties of hybrid composites than biocomposites.Figure 6
Loss modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure7 illustrated the loss factor (tan
δ) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. All the fiber loading in composites for DMA testing is 10 wt%. The addition of fiber decreases tan
δ in the glass transition region because molecular mobility of the composites decreased and the mechanical loss to overcome interfriction between molecular chains is reduced. Normally, damping of the polymer is much greater than fibers. Therefore, the addition of fibers to polymer matrix will increase the elasticity and decrease the viscosity and hence less energy will be used to overcome the frictional forces between molecular chains as to decrease mechanical loss [21]. The higher the damping at the interface, the poorer the interfacial adhesion between fiber and matrix [22]. Besides, composites with poor interfacial bonding tend to dissipate more energy compared with composites with good interfacial bonding. Therefore, addition of clay to biocomposites improves fiber/matrix adhesion as hybrid composites show lower tan
δ than biocomposites.Figure 7
Tan
δ of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


### 3.7. Scanning Electron Microscopy (SEM)

In our previous paper [2], we reported that PLA/PCL/OPMF biocomposites consist of cavity as fiber has been pulled out from matrix which indicated poor fiber/matrix adhesion as fiber could not provide an efficient stress transfer from the matrix to the filler causing them to have lower mechanical properties in response to stress. On the other hand, PLA/PCL/OPMF/1 wt% clay hybrid composites show better fiber/matrix adhesion as no cavity is present and fiber breakage could be seen on facture surfaces indicating better fiber/matrix adhesion. Therefore, the SEM results support the tensile properties results as the biocomposites show low strength due to poor stress transfer between matrix and fiber in composites which cause the composites to become brittle. On the other hand, SEM results also support the tensile properties results that hybrid composites show better mechanical properties than biocomposites.


### 3.8. Water Sorption Test

Water absorption of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is shown in Figure8. The fiber absorbs water due to the presence of hydroxyl groups which absorb water through the formation of hydrogen bonding [23]. All composites show a sharp increment in water absorption at the beginning and then remain constant around 10 days with the maximum water absorption being 5.81% and 5.29% for biocomposites and hybrid composites, respectively. Water absorption of all composites is typical type of the Fickian diffusion behaviour. In Fick’s law, the concentration gradient is the driving force for diffusion and amount of the component diffused in a function of time. Generally, moisture absorption process follows the prediction of Fick’s law as the mass of water absorbed increases linearly with square root of time until reach equilibrium plateau [24]. Biocomposites show higher water absorption than hybrid composites which might be due to the weak fiber/matrix adhesion leads to more void in composites which can act as pathways for water diffusion into the composites. Therefore, addition of clay improves fiber/matrix adhesion while enhancing water resistance of composites at the same time.Figure 8
Water absorption of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 3.1. The Fourier Transform Infrared Spectroscopy (FTIR)

FTIR spectra of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites are shown in Figure1. Both composites exhibit strong absorbance peak at 1748.90 cm−1and 1745 cm−1, respectively, indicating the presence of C=O stretching. Besides, C–H stretching is present in both composites but the intensity of the peak for PLA/PCL/1 wt% clay/OPMF hybrid composites is higher than PLA/PCL/OPMF biocomposites with the peak at 2939 cm−1 and 2947 cm−1, respectively. Shifting of peaks in IR spectra is observed when there is strong interaction in polymer blends [12]. Therefore, peak shifting is observed when 1 wt% of clay was incorporated into biocomposites which indicated that there might be some physical interaction between PLA, PCL, clay, and OPMF in composites.Figure 1
FTIR spectra of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 3.2. Tensile Properties

In our previous studies [2], we reported that the addition of 1 wt% of nanoclay successfully increases the tensile strength and elongation at break but decreases the tensile modulus of PLA/PCL/OPMF biocomposites which is summarized in Table 1. PLA/PCL/OPMF biocomposites show the highest tensile strength at 10 wt% of the fiber loading and decrease with the increasing of fiber loading which results from poor dispersion of fibers which leads to agglomeration of fillers. Besides, fiber acts as included filler in the resin matrix, which weakens the composite due to poor interfacial adhesion and obstructs the stress propagation, which leads to reduction of tensile strength as the filler loading increases. The presence of hydrophilic nanoclay increases the overall tensile strength of hybrid composites which suggests that the presence of hydrophilic nanoclay acts as physical compatibilizing agents between hydrophilic fiber and hydrophobic matrix and thus improves the fiber/matrix adhesion of hybrid composites. This might be due to the addition of nanoclay which successfully improves the miscibility of PLA/PLA in blends [1], while at the same time the presence of hydrophilic nanoclay is more compatible with hydrophilic fiber which enhances better physical interaction between fiber and matrix resulting in better mechanical properties of hybrid composites.Table 1
Tensile properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.
Sample
Tensile strength (MPa)
Elongation at break (mm)
Tensile modulus (MPa)
PLA85/PCL15
45.94
±
1.75
1.68
±
0.30
902.92
±
50.69
PLA85/PCL15/10 wt% OPMF
33.48
±
2.44
0.56
±
0.04
884.80
±
44.16
PLA85/PCL15/20 wt% OPMF
27.99
±
1.34
0.40
±
0.02
878.73
±
44.79
PLA85/PCL15/30 wt% OPMF
22.43
±
1.37
0.35
±
0.02
723.37
±
31.37
PLA85/PCL15/1 wt% clay/10 wt% OPMF
36.32
±
1.22
0.74
±
0.02
685.80
±
71.32
PLA85/PCL15/1 wt% clay/20 wt% OPMF
32.32
±
0.55
0.64
±
0.10
661.17
±
46.36
PLA85/PCL15/1 wt% clay/30 wt% OPMF
29.46
±
1.58
0.61
±
0.02
577.18
±
27.04The addition of fiber decreases the elongation at break of composites from 1.68 mm to 0.56 mm (PLA/PCL/OPMF biocomposites) and 0.74 mm (PLA/PCL/OPMF/1 wt% clay hybrid composites), respectively, at 10 wt% fiber loading. The addition of fiber into matrix causes composites to become stiffer and harder as the segment mobility of the composites is reduced which leads to low elongation. On the other hand, the addition of hydrophilic nanoclay improves the fiber/matrix adhesion of hybrid composites and also stress transfer within hybrid composites which enhance the flexibility of the composites. Therefore, PLA/PCL/OPMF/1 wt% clay hybrid composites show better elongation at break than PLA/PCL/OPMF biocomposites.Tensile modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/OPMF/1 wt% clay hybrid composites indicates that the overall tensile modulus of biocomposites is higher than hybrid composites. Therefore, this implies that the addition of hydrophilic nanoclay decreases the stiffness of the composites as the flexibility of composites increase which leads to lower tensile modulus.


## 3.3. Flexural Properties

Flexural strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure2. The addition of 1% clay in hybrid compositesshows better flexural strength (36.53 MPa) compared to biocomposites (21.45 MPa) at 10 wt% fiber loading. Therefore, the addition of clay has positive effect on flexural strength of hybrid composites due to better interfacial adhesion between matrix and filler which will improve stress transfer from matrix to filler resulting in higher values of flexural strength. Weak fiber/matrix interfacial bonding results in poor flexural properties [13]. When higher amount of fiber is incorporated into the composites, flexural strength decreases. This is due to the increment of population of fiber defects and fiber ends with increased fiber content. The fiber defects could act as source of stress concentration in composites [14].Figure 2
Flexural strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure3 shows flexural modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. The biocomposites show increment in flexural modulus from 2437.80 MPa to 2797.00 MPa, while hybrid composites do not show changes in flexural modulus (2433.20 MPa) when 10 wt% of fiber was added. When the amount of fiber increases, the flexural modulus of hybrid composites increases and flexural modulus of biocomposites decreases. The increasing trend in flexural modulus with the increment amount of fiber for hybrid composites due to the addition of fillers with higher stiffness than matrix is mentioned by [15]. However, biocomposites show decrement of flexural modulus with increment of fiber loading due to poor interfacial adhesion between fiber and matrix which leads to low flexural modulus.Figure 3
Flexural modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 3.4. The Izod Impact Strength

Impact strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure4. The impact strength decreases from 188.70 J/m (PLA85/PCL15) to 82.37 J/m and 95.44 J/m for biocomposites and hybrid composites, respectively, at 10 wt% fiber loading. When fiber is incorporated into matrix, poor energy absorbing capability of fiber inhibit deformation and ductile mobility of polymer molecules which lower the ability of composites to absorb energy during crack propagation. Besides, less energy is required to initiate a crack as fiber creates high stress concentration regions [16]. However, the impact strength of hybrid composites is higher than biocomposites as the addition of clay improves impact strength of hybrid composites due to better fiber/matrix adhesion in hybrid composites compared to biocomposites.Figure 4
Impact strength of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 3.5. Thermogravimetric Analysis (TGA)

Previously we reported that incorporation of nanoclay improves the thermal stability of PLA/PCL/OPMF biocomposites [2]. The PLA/PCL/OPMF biocomposites show onset temperature of 196.01°C, which increases to 221.12°C when clay is added to the biocomposites. Table 2 shows the thermal properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. The increment of thermal stability of hybrid composites due to clay can hinder the permeability of volatile degradation products out of the materials. The dispersed clay forms a barrier which delays the release of thermal degradation products compared to the neat polymer [17].Table 2
Thermal properties of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.
Sample
Onset temperature (°C)
Offset temperature (°C)
% of degradation
PLA/PCL/OPMF
196.01
473.84
72.78
PLA/PCL/1 wt% clay/OPMF
221.12
458.36
71.08


## 3.6. Dynamic Mechanical Analysis (DMA)

The storage modulus (G
′) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is illustrated in Figure 5. All the fiber loading in composites for DMA testing is 10 wt%. Increment of G
′ after addition of fibers is due to incorporation of high modulus fibers in the matrix. The value of storage modulus decreases at higher temperature due to loss in stiffness of the fibers [18]. The G
′ results show agreement with the flexural modulus results as biocomposites show higher tensile modulus than hybrid composites. The addition of clay shows considerable effect on the elastic properties of hybrid composites by reducing the stiffness of the hybrid composites.Figure 5
Storage modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure6 shows the loss modulus (G
′
′) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. All the fiber loading in composites for DMA testing is 10 wt%. Loss modulus indicates the material’s ability to dissipate energy in the form of heat or molecular rearrangements during the deformation [19]. The loss modulus accounts for the viscous component of the complex modulus or the out of phase component with the applied strain which normally increases with the addition of filler [20]. The addition of fiber increases the G
′
′ of biocomposites and hybrid composites at the temperature around −68°C and then decreases at 48°C. The addition of clay to biocomposites slightly shiftsT
g of biocomposites from −67.7°C to −67.0°C at PCL region and also from 47.6°C to 46.5°C at PLA region which suggests that the incorporation of clay slightly compatibilizes the biocomposites resulting in better mechanical properties of hybrid composites than biocomposites.Figure 6
Loss modulus of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.Figure7 illustrated the loss factor (tan
δ) of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites. All the fiber loading in composites for DMA testing is 10 wt%. The addition of fiber decreases tan
δ in the glass transition region because molecular mobility of the composites decreased and the mechanical loss to overcome interfriction between molecular chains is reduced. Normally, damping of the polymer is much greater than fibers. Therefore, the addition of fibers to polymer matrix will increase the elasticity and decrease the viscosity and hence less energy will be used to overcome the frictional forces between molecular chains as to decrease mechanical loss [21]. The higher the damping at the interface, the poorer the interfacial adhesion between fiber and matrix [22]. Besides, composites with poor interfacial bonding tend to dissipate more energy compared with composites with good interfacial bonding. Therefore, addition of clay to biocomposites improves fiber/matrix adhesion as hybrid composites show lower tan
δ than biocomposites.Figure 7
Tan
δ of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 3.7. Scanning Electron Microscopy (SEM)

In our previous paper [2], we reported that PLA/PCL/OPMF biocomposites consist of cavity as fiber has been pulled out from matrix which indicated poor fiber/matrix adhesion as fiber could not provide an efficient stress transfer from the matrix to the filler causing them to have lower mechanical properties in response to stress. On the other hand, PLA/PCL/OPMF/1 wt% clay hybrid composites show better fiber/matrix adhesion as no cavity is present and fiber breakage could be seen on facture surfaces indicating better fiber/matrix adhesion. Therefore, the SEM results support the tensile properties results as the biocomposites show low strength due to poor stress transfer between matrix and fiber in composites which cause the composites to become brittle. On the other hand, SEM results also support the tensile properties results that hybrid composites show better mechanical properties than biocomposites.


## 3.8. Water Sorption Test

Water absorption of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites is shown in Figure8. The fiber absorbs water due to the presence of hydroxyl groups which absorb water through the formation of hydrogen bonding [23]. All composites show a sharp increment in water absorption at the beginning and then remain constant around 10 days with the maximum water absorption being 5.81% and 5.29% for biocomposites and hybrid composites, respectively. Water absorption of all composites is typical type of the Fickian diffusion behaviour. In Fick’s law, the concentration gradient is the driving force for diffusion and amount of the component diffused in a function of time. Generally, moisture absorption process follows the prediction of Fick’s law as the mass of water absorbed increases linearly with square root of time until reach equilibrium plateau [24]. Biocomposites show higher water absorption than hybrid composites which might be due to the weak fiber/matrix adhesion leads to more void in composites which can act as pathways for water diffusion into the composites. Therefore, addition of clay improves fiber/matrix adhesion while enhancing water resistance of composites at the same time.Figure 8
Water absorption of PLA/PCL/OPMF biocomposites and PLA/PCL/1 wt% clay/OPMF hybrid composites.


## 4. Conclusion

In these studies, the addition of 1 wt% hydrophilic nanoclay successfully improves the overall flexural strength and impact strength of PLA/PCL/OPMF biocomposites. DMA analysis shows decrement in storage modulus when nanoclay was added indicating that addition of nanoclay has considerable effect on the elastic properties of hybrid composites by reducing the stiffness of the hybrid composites. Loss modulus shows that the addition of nanoclay to biocomposites slightly shiftsT
g of biocomposites from −67.7°C to −67.0°C at PCL region and also from 47.6°C to 46.5°C at PLA region which suggests that the incorporation of nanoclay slightly compatibilizes the biocomposites resulting in better mechanical properties of PLA/PCL/1 wt% clay/OPMF hybrid composites than biocomposites. Tan
δ indicated that hybrid composites dissipate less energy compared to biocomposites indicating that addition of clay to biocomposites improves fiber/matrix adhesion. Water sorption test shows that the addition of nanoclay improves fiber/matrix adhesion while enhancing water resistance of composites at the same time. Therefore, the addition of nanoclay in hybrid composites makes hybrid composites possess good strength and properties which is comparable with some conventional plastics. Besides, the incorporation of natural fibers in hybrid composites lowering the cost of biodegradable polymer which wider the application of biodegradable polymer based composites. The applications of the hybrid composites might be more suitable for single-use materials that do not require very high strength, while at the same time biodegradability and environment friendly are one of the concerns of selection of materials.



---

*Source: 715801-2014-04-27.xml*