# Mechanical and Thermal Properties of PLA Biocomposites Reinforced by Coir Fibers

Authors: Zhihui Sun; Li Zhang; Duoping Liang; Wei Xiao; Jing Lin
Journal: International Journal of Polymer Science
 (2017)

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## Abstract

In this work, polylactic acid (PLA) biocomposites reinforced with short coir fibers were fabricated using a corotating twin-screw extruder and injection molding machine. Short coir fibers were treated by mixed solution including hydrogen peroxide and sodium hydroxide to improve the adhesion between fibers and PLA matrix. The effects of treated coir fiber content (1, 3, 5, and 7 wt%) on tensile, impact, thermal properties, and surface morphology of PLA biocomposites were investigated. The best impact strength results were obtained for 3 wt% PLA/treated coir fiber biocomposites, where the impact strength was increased by approximately 28% compared to the neat PLA. The tensile modulus of PLA biocomposites was increased by increasing the treated coir fiber content. These results were confirmed by morphological structure analysis. Differential scanning calorimetry (DSC) results demonstrated a minor effect of the treated coir fiber on thermal behavior of PLA resin. Thermogravimetry analysis (TGA) demonstrated that the thermal stability of the PLA/treated coir fiber biocomposites was reduced by the incorporation of treated coir fiber.


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## Body

## 1. Introduction

In recent years, more and more researchers have turned their attention toward environmental pollution and limited petroleum resources. One of the solutions to reducing environmental pollution and depleting petrochemical-based plastics is to utilize degradable biomaterials [1, 2]. PLA is a kind of biocompatible and biodegradable polymer with a wide range of applications. However, its applications are limited by its slow crystallization speed and brittleness to some extent [3–6]. To overcome these disadvantages of PLA, many studies have shown that adding natural fiber such as flax, hemp, jute, and sisal is an effective, useful method to reinforce PLA [7–13].Coir fiber is selected for this study as it is nontoxic, has low cost, has low density, and is biodegradable. Coir fibers have low cellulose (40–43%) and hemicellulose (0.15–0.25%) contents and a high lignin content (41–45%) [8, 14]. In addition, coir fiber is also hydrophilic in nature. This characteristic prevents itself from interacting with most hydrophobic polymers, including PLA. Therefore, in order to improve the interfacial bonding between polymer and natural fiber, a lot of treatments are made to modify the surface of the fiber such as alkali, bleaching, acetylation, and steaming. Alkali treatment is one of most widely used methods [10, 15–19]. In this process, the lignin, hemicelluloses, pectin, and other impurities in the fiber are dissolved, and the molecular orientation is improved due to a reduction of the rotation angle of the microfibers. The fiber surface becomes rough so that the bonding ability between the fiber and polymer interface is enhanced. Bleaching with hydrogen peroxide has the same effect [16, 20–23].In this study, coir fibers were chemically pretreated with the mixed solution of hydrogen peroxide and sodium hydroxide to increase their compatibility with the PLA matrix. Then, the mechanical properties and morphology of PLA/treated coir fiber biocomposites (HPCFs) were investigated, comparing with untreated coir fiber reinforced PLA biocomposites. Furthermore, the thermal properties of HPCFs were studied.


## 2. Experimental

### 2.1. Materials and Fiber Treatments

PLA 4032D pellets with a material density of 1.24 g/cm3 were purchased from Nature Works LLC, USA. Coir fibers with a fiber diameter in the range of 100–450 μm were purchased from Tianjin Jia Add Green Products Technology Co., Ltd., China.The raw coir fibers were chopped into lengths of approximately 4–6 mm and then sieved through a 40-mesh sieve. Short coir fibers were then washed with distilled water for several times and finally dried at 60°C for 12 h. The fibers thus obtained were known as untreated coir fiber samples.Short coir fibers (250 g) were added to a 1 L mixed solution containing 160 mL (30%; w/w) of hydrogen peroxide and 0.5 g of sodium hydroxide at 85°C and magnetically stirred for 1 h. Subsequently, the soaked coir fibers were washed thoroughly with distilled water and dried in an oven at 60°C for 12 h [24, 25]. The fibers were treated as treated coir fiber samples.All neat PLA and coir fiber samples were placed in a desiccator and stored for 24 h.


### 2.2. Sample Preparation

Blends of PLA and coir fiber were melting extruded. The content of coir fibers in the PLA biocomposites varied between 1, 3, 5, and 7 wt%, respectively. This mixture was introduced into a corotating twin-screw extruder with six heating zones with temperatures set at 160, 170, 180, 190, 185, and 180°C from the feed to the die, according to Table1. The diameter of the screws was 18 mm, and the length-to-diameter ratio of the barrel was 30 : 1. The extruded material was cooled in air and then granulated in a cutting mill to produce the composite pellets with dimensions of 4-5 mm. In addition, all obtained pellets were then injected into an injection molding machine (SY-200-1, screw diameter = 22 mm, injection time = 5 s, and cooling time = 20 s) at 180°C. The PLA biocomposites presented a compact morphology with no evidence of macroscopic pores or voids. These samples were placed in a desiccator at room temperature for at least 48 h before testing.Table 1
Biocomposites compositions.
Code
PLA (wt%)
Coir fibers (wt%)
Extrusion
Temperature profile (°C)
Rotational speed (rpm)
Neat PLA
100
0
160, 170, 180; 190; 185, 180
30
1% HPCF
99
1
160, 170, 180; 190; 185, 180
30
3% HPCF
97
3
160, 170, 180; 190; 185, 180
30
5% HPCF
95
5
160, 170, 180; 190; 185, 180
30
7% HPCF
93
7
160, 170, 180; 190; 185, 180
30


### 2.3. Mechanical Testing

The tensile properties were tested using an RGM-4005 Electronic Tensile Machine (Shenzhen Instrument Co., Ltd.). The sample dimensions were150×20×4 mm, and the sample was in a dog bone shape. A tensile speed of 5 mm/min was adopted during the experiment. Tensile strength of neat PLA and PLA biocomposites was carried out in general accordance with China’s National Standard test (GB/T 1040-2006).Notched Charpy Impact Strength tests were carried out on an XCJ-40 impact tester (Chengde Jinjian Testing Instrument Co., Ltd.). The V-notch shape was prepared as shown in Figure1. The dimensions of the specimens were 80×10×4 mm. The impact strength of neat PLA and PLA biocomposites was carried out in general accordance with China’s National Standard test (GB/T 1043-2008).Figure 1
Impact sample.All the tests were performed at room temperature and over five specimens were used for each material batch to ensure good testing reproducibility.


### 2.4. Scanning Electron Microscopy (SEM)

Both the surfaces of coir fibers and the fractured surfaces of the impact specimens, subjected to sputter-coating with platinum, were characterized by Field Emission Scanning Electron Microscopy (FESEM), using Hitachi SU8020 at 15 kV.


### 2.5. Dynamic Mechanical Analysis (DMA)

The storage modulus (E′) and loss factor (tan⁡δ) of the neat PLA and biocomposite specimens were measured as a function of temperature (−50 to 150°C) using a Q800 DMA instrument equipped with a 3-point bending fixture at a frequency of 1 Hz and a constant heating rate of 3°C/min. In addition, the dimensions of the specimens were 60×10×4 mm.


### 2.6. Differential Scanning Calorimetry (DSC)

The thermal properties of the neat PLA and HPCF specimens were measured with a Mettler Toledo DSC1 Star. The heating temperature was ramped from 30 to 210°C at a rate of 10°C/min. All these experiments were carried out in a nitrogen atmosphere. The associated thermal parameters, such as the glass transition temperature (Tg), cold crystallization temperature (Tcc), melting temperature (Tm), and heat of fusion (ΔHm), were determined from the first heating cycle. The resulting degree of crystallinity (Xc) was calculated based on the following [26, 27]:(1)Xc%=ΔHmΔHm0×100%w,where ΔHm0 is the heat of fusion for a 100% crystalline PLA material (ΔHm0=93 J/g) and w is the weight fraction of the PLA matrices in the biocomposites [28]. The thermal properties of all the specimens were measured in triplicate.


### 2.7. Thermal Properties

Thermogravimetric analysis (TGA) was performed with a Mettler Toledo GmbH (TGA/SDTA851e) to detect the thermal decomposition of the neat PLA and HPCF specimens. Approximately 6–10 mg of the TGA samples was examined from 30 to 500°C at a heating ramp rate of 10°C/min under a nitrogen flow of 200 mL/min.


## 2.1. Materials and Fiber Treatments

PLA 4032D pellets with a material density of 1.24 g/cm3 were purchased from Nature Works LLC, USA. Coir fibers with a fiber diameter in the range of 100–450 μm were purchased from Tianjin Jia Add Green Products Technology Co., Ltd., China.The raw coir fibers were chopped into lengths of approximately 4–6 mm and then sieved through a 40-mesh sieve. Short coir fibers were then washed with distilled water for several times and finally dried at 60°C for 12 h. The fibers thus obtained were known as untreated coir fiber samples.Short coir fibers (250 g) were added to a 1 L mixed solution containing 160 mL (30%; w/w) of hydrogen peroxide and 0.5 g of sodium hydroxide at 85°C and magnetically stirred for 1 h. Subsequently, the soaked coir fibers were washed thoroughly with distilled water and dried in an oven at 60°C for 12 h [24, 25]. The fibers were treated as treated coir fiber samples.All neat PLA and coir fiber samples were placed in a desiccator and stored for 24 h.


## 2.2. Sample Preparation

Blends of PLA and coir fiber were melting extruded. The content of coir fibers in the PLA biocomposites varied between 1, 3, 5, and 7 wt%, respectively. This mixture was introduced into a corotating twin-screw extruder with six heating zones with temperatures set at 160, 170, 180, 190, 185, and 180°C from the feed to the die, according to Table1. The diameter of the screws was 18 mm, and the length-to-diameter ratio of the barrel was 30 : 1. The extruded material was cooled in air and then granulated in a cutting mill to produce the composite pellets with dimensions of 4-5 mm. In addition, all obtained pellets were then injected into an injection molding machine (SY-200-1, screw diameter = 22 mm, injection time = 5 s, and cooling time = 20 s) at 180°C. The PLA biocomposites presented a compact morphology with no evidence of macroscopic pores or voids. These samples were placed in a desiccator at room temperature for at least 48 h before testing.Table 1
Biocomposites compositions.
Code
PLA (wt%)
Coir fibers (wt%)
Extrusion
Temperature profile (°C)
Rotational speed (rpm)
Neat PLA
100
0
160, 170, 180; 190; 185, 180
30
1% HPCF
99
1
160, 170, 180; 190; 185, 180
30
3% HPCF
97
3
160, 170, 180; 190; 185, 180
30
5% HPCF
95
5
160, 170, 180; 190; 185, 180
30
7% HPCF
93
7
160, 170, 180; 190; 185, 180
30


## 2.3. Mechanical Testing

The tensile properties were tested using an RGM-4005 Electronic Tensile Machine (Shenzhen Instrument Co., Ltd.). The sample dimensions were150×20×4 mm, and the sample was in a dog bone shape. A tensile speed of 5 mm/min was adopted during the experiment. Tensile strength of neat PLA and PLA biocomposites was carried out in general accordance with China’s National Standard test (GB/T 1040-2006).Notched Charpy Impact Strength tests were carried out on an XCJ-40 impact tester (Chengde Jinjian Testing Instrument Co., Ltd.). The V-notch shape was prepared as shown in Figure1. The dimensions of the specimens were 80×10×4 mm. The impact strength of neat PLA and PLA biocomposites was carried out in general accordance with China’s National Standard test (GB/T 1043-2008).Figure 1
Impact sample.All the tests were performed at room temperature and over five specimens were used for each material batch to ensure good testing reproducibility.


## 2.4. Scanning Electron Microscopy (SEM)

Both the surfaces of coir fibers and the fractured surfaces of the impact specimens, subjected to sputter-coating with platinum, were characterized by Field Emission Scanning Electron Microscopy (FESEM), using Hitachi SU8020 at 15 kV.


## 2.5. Dynamic Mechanical Analysis (DMA)

The storage modulus (E′) and loss factor (tan⁡δ) of the neat PLA and biocomposite specimens were measured as a function of temperature (−50 to 150°C) using a Q800 DMA instrument equipped with a 3-point bending fixture at a frequency of 1 Hz and a constant heating rate of 3°C/min. In addition, the dimensions of the specimens were 60×10×4 mm.


## 2.6. Differential Scanning Calorimetry (DSC)

The thermal properties of the neat PLA and HPCF specimens were measured with a Mettler Toledo DSC1 Star. The heating temperature was ramped from 30 to 210°C at a rate of 10°C/min. All these experiments were carried out in a nitrogen atmosphere. The associated thermal parameters, such as the glass transition temperature (Tg), cold crystallization temperature (Tcc), melting temperature (Tm), and heat of fusion (ΔHm), were determined from the first heating cycle. The resulting degree of crystallinity (Xc) was calculated based on the following [26, 27]:(1)Xc%=ΔHmΔHm0×100%w,where ΔHm0 is the heat of fusion for a 100% crystalline PLA material (ΔHm0=93 J/g) and w is the weight fraction of the PLA matrices in the biocomposites [28]. The thermal properties of all the specimens were measured in triplicate.


## 2.7. Thermal Properties

Thermogravimetric analysis (TGA) was performed with a Mettler Toledo GmbH (TGA/SDTA851e) to detect the thermal decomposition of the neat PLA and HPCF specimens. Approximately 6–10 mg of the TGA samples was examined from 30 to 500°C at a heating ramp rate of 10°C/min under a nitrogen flow of 200 mL/min.


## 3. Results and Discussion

### 3.1. Mechanical Properties

The variation of mechanical properties of both PLA/untreated coir fiber biocomposites (PCFs) and HPCFs with different coir fiber content from 1 to 7% is shown in Figure2. Figure 2(a) shows that the tensile strength of PLA biocomposites is lower than that of neat PLA and decreases continuously with increasing fiber content regardless of fiber treatment. As it is known, coir fiber is low tensile strength compared to other fibers, which has an adverse effect on the improvement of tensile strength of PLA biocomposites due to the inherent rigidity of the coir fiber. Another possible explanation can be that tensile strength of PLA biocomposites can be predominantly influenced by the coir fiber agglomeration at higher fiber content, which results in poor stress transfer across the interface [29]. Overall, the strength levels of PCFs are inferior to their counterparts with HPCFs, which is in good agreement with the previous literature [21]. The result indicates that the weak adhesion between untreated coir fibers and the PLA matrix results in the stress not being transferred from the matrix to the stronger fiber [30]. Figure 2(b) shows that the tensile modulus of PLA biocomposites is higher than that of neat PLA due to the reducing of chain mobility in more filler content, which allows high stiffness in its composites [31]. And the tensile modulus of HPCFs is higher than that of PCFs at the same fiber content. The result indicates that alkali and hydrogen peroxide treatment promoted adequate compatibility and wettability between fiber and PLA matrix due to removing pectin and lignin from treated coir fiber [32].Figure 2
Mechanical properties of PCFs and HPCFs: (a) tensile strength, (b) tensile modulus, (c) elongation at break, and (d) impact strength.
(a)
(b)
(c)
(d)On the other hand, the PCFs and HPCFs also show a reduction in their elongation at break values in comparison to neat PLA as shown in Figure2(c). This result indicates that the biocomposites are more brittle than neat PLA mainly owing to the well-known rigid reinforcement nature of coir fiber [25]. And the elongation at break values of PCFs and HPCFs decreases with increasing fiber content. This behavior is probably associated with uneven aligning of coir fibers with PLA matrix [32]. Furthermore, the elongation at break values of HPCFs is higher than that of PCFs at the same fiber content. The mixed solution treatment often leads to the removal of the lignin and pectin from coir fibers, which results in relatively increasing the cellulose content. So the flexibility and elasticity of coir fiber are improved [25].The impact strengths of HPCFs and PCFs at different coir fiber content are shown in Figure2(d). The impact strength of coir fiber reinforced PLA biocomposites increases at all concentrations, as expected. This indicates that the addition of coir fiber is effective to increase the impact absorbance of the biocomposite materials [33]. And it is found that the impact strength of HPCFs is always higher than the value of PCFs at the same fiber content. It is known that the interfacial bonding strength between matrix and fiber affects the impact property of PLA biocomposites. The result reveals that the interfacial bonding between treated fiber and PLA matrix is better than that between untreated fiber and PLA matrix. In addition, impact energy is dissipated by debonding, fiber and/or matrix fracture and fiber pull-out [34]. The treated coir fiber at fiber content 3% by weight increases the impact strength by 27.55% compared to the neat PLA. With further increase in treated fibers content (i.e., at 5%) the impact strength of HPCFs decreases due to agglomeration of fiber.


### 3.2. Morphological Structures

Figures3(a) and 3(b) show the micromorphology of coir fiber surface. As shown in Figure 3(a), the untreated coir fibers exhibit smooth surface due to the presence of wax/pectin and other surface impurities [35]. By comparison, many holes and cracks are discovered on the treated coir fiber surface, as shown in Figure 3(b). This result proves that the mixed solution treatment of coir fiber is efficient for removing these impurities and improves the surface roughness. The increased surface roughness of treated coir fiber would likely result in more mechanical interlocking between fibers with matrix. In addition, the colour change of coir fiber from brown to yellowish brown is observed due to removal of lignin, wax, and fatty [18].Figure 3
SEM micrographs of (a) untreated coir fibers, (b) treated coir fibers, (c) 3% PCF, and (d) 3% HPCF.
(a)
(b)
(c)
(d)Figures3(c) and 3(d) show the micromorphology of impact fractured surfaces of 3% PCF and 3% HPCF, respectively. As shown in Figure 3(c), the interface between the untreated coir fiber and the PLA matrix is loose because no PLA matrix adhered to the coir fiber surface. Figure 3(d) can be obviously observed that there is smaller interstice between treated coir fiber and PLA matrix and there is more PLA matrix adhered to the surface of treated coir fiber. This shows that the interfacial adhesion is believed to be better improved by the fiber treatment, resulting in impact strength improvement of HPCFs. SEM results are in good agreement with mechanical results.


### 3.3. DMA Analysis

The plot of storage modulus (E′) against temperature for the neat PLA and HPCFs is shown in Figure 4. The values ofE′ increase with the addition of the treated coir fibers, which suggested better adhesion between the treated fibers and the PLA matrix. All the composites show a sharp decrease inE′ at approximately 66°Cdue to the glass transition and then a significant increase in the storage modulus above 93°C. This is a result of the cold crystallization of the amorphous PLA matrix [36]. Although studies have shown the effect of natural fibers as nucleating agents on the crystallization of PLA, they have emphasized the role of interfacial interactions between the treated coir fiber and the matrix. In other words, the rate of crystallization of the PLA is modified by optimizing the interfacial interaction between the fibers and PLA matrix [37].Figure 4
DMA curves of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.The peak oftan⁡δ decreases rapidly with addition of the coir fibers; this is mainly due to the existence of effective interracial bonding between fiber and matrix. Table 2 shows that Tg and Tc are slightly shifted to a lower temperature. The HPCFs induce cold crystallization earlier than the neat PLA samples.Table 2
DMA data for PLA and HPCFs.
Code
T
g (°C)
T
c
,
o
n
s
e
t (°C)
Storage modulus at 25°C (GPa)
Neat PLA
67
94
2.2
1% HPCF
66
93
2.2
3% HPCF
65
92
2.3
5% HPCF
65
92
2.4
7% HPCF
64
93
2.5


### 3.4. DSC Thermal Analysis

The DSC thermograms and associated thermal parameters for the neat PLA and HPCFs are shown in Figure5 and Table 3, respectively. With the incorporation of treated coir fibers within PLA matrix Tg decreases which indicates increased mobility and free volume of the matrix chains by loose packing of filler within the matrix due to poor interaction between the treated coir fibers and PLA matrix [38].Table 3
DSC data for PLA and HPCFs.
Sample
T
g (°C)
T
o
,
c (°C)
T
p
,
c (°C)
T
c (°C)
T
m
1 (°C)
T
m
2 (°C)
Δ
H
c
,
P
L
A
J
/
g
Δ
H
m
,
P
L
A
J
/
g
X
c
%
Neat PLA
63
101
118
110
159
177
4.21
4.97
5.35
1% HPCF
62
102
117
110
159
176
3.71
5.42
5.89
3% HPCF
61
100
116
109
159
176
4.16
4.90
5.43
5% HPCF
61
101
116
109
158
176
4.00
4.96
5.61
7% HPCF
61
97
114
107
157
175
4.09
5.17
5.98Figure 5
DSC thermograms of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.T
m of the HPCFs modest decreases compared to that of neat PLA. The degree crystallinity has a decreasing tendency with the fiber content increasing. This may be attributed to the increase in amorphosity of the HPCFs [39].In addition,Tc of the HPCFs decreases considerably from 110 to 107°C, as opposed to that of the neat PLA (Tc = 110°C). This confirms that the treated coir fibers create favorable conditions for PLA crystallization and thus increase the crystallization rate. Due to an effective nucleating effect of treated coir fibers, Xc of the HPCFs is improved with increasing the coir fibers content [39].


### 3.5. TGA Results

The TGA and DTG curves of the PLA and HPCFs are shown in Figure6 and summarized in Table 4. The peak temperature of weight loss of HPCFs shifted to the lower temperature region. The thermal stability of HPCFs decreased with increasing treated coir fiber content which can be clearly seen in Table 4. Evidently, increasing the treated coir fiber content enables the decrease in thermal stability of HPCFs due to the lower thermal stability of the coir fiber [25].Table 4
TGA data for PLA and HPCFs.
Code
T
m
a
x (°C)
Total weight loss at 500°C (%)
Neat PLA
388
99
1% HPCF
382
98
3% HPCF
382
97
5% HPCF
382
97
7% HPCF
385
97Figure 6
TGA and DTGA curves of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.


## 3.1. Mechanical Properties

The variation of mechanical properties of both PLA/untreated coir fiber biocomposites (PCFs) and HPCFs with different coir fiber content from 1 to 7% is shown in Figure2. Figure 2(a) shows that the tensile strength of PLA biocomposites is lower than that of neat PLA and decreases continuously with increasing fiber content regardless of fiber treatment. As it is known, coir fiber is low tensile strength compared to other fibers, which has an adverse effect on the improvement of tensile strength of PLA biocomposites due to the inherent rigidity of the coir fiber. Another possible explanation can be that tensile strength of PLA biocomposites can be predominantly influenced by the coir fiber agglomeration at higher fiber content, which results in poor stress transfer across the interface [29]. Overall, the strength levels of PCFs are inferior to their counterparts with HPCFs, which is in good agreement with the previous literature [21]. The result indicates that the weak adhesion between untreated coir fibers and the PLA matrix results in the stress not being transferred from the matrix to the stronger fiber [30]. Figure 2(b) shows that the tensile modulus of PLA biocomposites is higher than that of neat PLA due to the reducing of chain mobility in more filler content, which allows high stiffness in its composites [31]. And the tensile modulus of HPCFs is higher than that of PCFs at the same fiber content. The result indicates that alkali and hydrogen peroxide treatment promoted adequate compatibility and wettability between fiber and PLA matrix due to removing pectin and lignin from treated coir fiber [32].Figure 2
Mechanical properties of PCFs and HPCFs: (a) tensile strength, (b) tensile modulus, (c) elongation at break, and (d) impact strength.
(a)
(b)
(c)
(d)On the other hand, the PCFs and HPCFs also show a reduction in their elongation at break values in comparison to neat PLA as shown in Figure2(c). This result indicates that the biocomposites are more brittle than neat PLA mainly owing to the well-known rigid reinforcement nature of coir fiber [25]. And the elongation at break values of PCFs and HPCFs decreases with increasing fiber content. This behavior is probably associated with uneven aligning of coir fibers with PLA matrix [32]. Furthermore, the elongation at break values of HPCFs is higher than that of PCFs at the same fiber content. The mixed solution treatment often leads to the removal of the lignin and pectin from coir fibers, which results in relatively increasing the cellulose content. So the flexibility and elasticity of coir fiber are improved [25].The impact strengths of HPCFs and PCFs at different coir fiber content are shown in Figure2(d). The impact strength of coir fiber reinforced PLA biocomposites increases at all concentrations, as expected. This indicates that the addition of coir fiber is effective to increase the impact absorbance of the biocomposite materials [33]. And it is found that the impact strength of HPCFs is always higher than the value of PCFs at the same fiber content. It is known that the interfacial bonding strength between matrix and fiber affects the impact property of PLA biocomposites. The result reveals that the interfacial bonding between treated fiber and PLA matrix is better than that between untreated fiber and PLA matrix. In addition, impact energy is dissipated by debonding, fiber and/or matrix fracture and fiber pull-out [34]. The treated coir fiber at fiber content 3% by weight increases the impact strength by 27.55% compared to the neat PLA. With further increase in treated fibers content (i.e., at 5%) the impact strength of HPCFs decreases due to agglomeration of fiber.


## 3.2. Morphological Structures

Figures3(a) and 3(b) show the micromorphology of coir fiber surface. As shown in Figure 3(a), the untreated coir fibers exhibit smooth surface due to the presence of wax/pectin and other surface impurities [35]. By comparison, many holes and cracks are discovered on the treated coir fiber surface, as shown in Figure 3(b). This result proves that the mixed solution treatment of coir fiber is efficient for removing these impurities and improves the surface roughness. The increased surface roughness of treated coir fiber would likely result in more mechanical interlocking between fibers with matrix. In addition, the colour change of coir fiber from brown to yellowish brown is observed due to removal of lignin, wax, and fatty [18].Figure 3
SEM micrographs of (a) untreated coir fibers, (b) treated coir fibers, (c) 3% PCF, and (d) 3% HPCF.
(a)
(b)
(c)
(d)Figures3(c) and 3(d) show the micromorphology of impact fractured surfaces of 3% PCF and 3% HPCF, respectively. As shown in Figure 3(c), the interface between the untreated coir fiber and the PLA matrix is loose because no PLA matrix adhered to the coir fiber surface. Figure 3(d) can be obviously observed that there is smaller interstice between treated coir fiber and PLA matrix and there is more PLA matrix adhered to the surface of treated coir fiber. This shows that the interfacial adhesion is believed to be better improved by the fiber treatment, resulting in impact strength improvement of HPCFs. SEM results are in good agreement with mechanical results.


## 3.3. DMA Analysis

The plot of storage modulus (E′) against temperature for the neat PLA and HPCFs is shown in Figure 4. The values ofE′ increase with the addition of the treated coir fibers, which suggested better adhesion between the treated fibers and the PLA matrix. All the composites show a sharp decrease inE′ at approximately 66°Cdue to the glass transition and then a significant increase in the storage modulus above 93°C. This is a result of the cold crystallization of the amorphous PLA matrix [36]. Although studies have shown the effect of natural fibers as nucleating agents on the crystallization of PLA, they have emphasized the role of interfacial interactions between the treated coir fiber and the matrix. In other words, the rate of crystallization of the PLA is modified by optimizing the interfacial interaction between the fibers and PLA matrix [37].Figure 4
DMA curves of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.The peak oftan⁡δ decreases rapidly with addition of the coir fibers; this is mainly due to the existence of effective interracial bonding between fiber and matrix. Table 2 shows that Tg and Tc are slightly shifted to a lower temperature. The HPCFs induce cold crystallization earlier than the neat PLA samples.Table 2
DMA data for PLA and HPCFs.
Code
T
g (°C)
T
c
,
o
n
s
e
t (°C)
Storage modulus at 25°C (GPa)
Neat PLA
67
94
2.2
1% HPCF
66
93
2.2
3% HPCF
65
92
2.3
5% HPCF
65
92
2.4
7% HPCF
64
93
2.5


## 3.4. DSC Thermal Analysis

The DSC thermograms and associated thermal parameters for the neat PLA and HPCFs are shown in Figure5 and Table 3, respectively. With the incorporation of treated coir fibers within PLA matrix Tg decreases which indicates increased mobility and free volume of the matrix chains by loose packing of filler within the matrix due to poor interaction between the treated coir fibers and PLA matrix [38].Table 3
DSC data for PLA and HPCFs.
Sample
T
g (°C)
T
o
,
c (°C)
T
p
,
c (°C)
T
c (°C)
T
m
1 (°C)
T
m
2 (°C)
Δ
H
c
,
P
L
A
J
/
g
Δ
H
m
,
P
L
A
J
/
g
X
c
%
Neat PLA
63
101
118
110
159
177
4.21
4.97
5.35
1% HPCF
62
102
117
110
159
176
3.71
5.42
5.89
3% HPCF
61
100
116
109
159
176
4.16
4.90
5.43
5% HPCF
61
101
116
109
158
176
4.00
4.96
5.61
7% HPCF
61
97
114
107
157
175
4.09
5.17
5.98Figure 5
DSC thermograms of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.T
m of the HPCFs modest decreases compared to that of neat PLA. The degree crystallinity has a decreasing tendency with the fiber content increasing. This may be attributed to the increase in amorphosity of the HPCFs [39].In addition,Tc of the HPCFs decreases considerably from 110 to 107°C, as opposed to that of the neat PLA (Tc = 110°C). This confirms that the treated coir fibers create favorable conditions for PLA crystallization and thus increase the crystallization rate. Due to an effective nucleating effect of treated coir fibers, Xc of the HPCFs is improved with increasing the coir fibers content [39].


## 3.5. TGA Results

The TGA and DTG curves of the PLA and HPCFs are shown in Figure6 and summarized in Table 4. The peak temperature of weight loss of HPCFs shifted to the lower temperature region. The thermal stability of HPCFs decreased with increasing treated coir fiber content which can be clearly seen in Table 4. Evidently, increasing the treated coir fiber content enables the decrease in thermal stability of HPCFs due to the lower thermal stability of the coir fiber [25].Table 4
TGA data for PLA and HPCFs.
Code
T
m
a
x (°C)
Total weight loss at 500°C (%)
Neat PLA
388
99
1% HPCF
382
98
3% HPCF
382
97
5% HPCF
382
97
7% HPCF
385
97Figure 6
TGA and DTGA curves of (a) neat PLA, (b) 1% HPCF, (c) 3% HPCF, (d) 5% HPCF, and (e) 7% HPCF.


## 4. Conclusions

The mechanical and thermal properties of neat PLA and HPCFs were investigated. The tensile strength and elongation at break of HPCFs decreased with the increasing of treated coir fiber content. However the tensile modulus and impact strength of HPCFs increased with fiber content. Thus the interfacial adhesion between PLA and treated coir fiber was believed to be improved by the pretreatment of fiber. This result was supported by SEM analyses. The DMA results showed that the treated coir fiber reinforced biocomposites have higher storage modulus resulting in significantly improved stiffness. Crystallinity of HPCFs increased by introduction of treated coir fibers. The total weight loss of HPCFs reduced at 500°C.



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*Source: 2178329-2017-07-10.xml*