# Effects of MAPP Compatibilization and Acetylation Treatment Followed by Hydrothermal Aging on Polypropylene Alfa Fiber Composites

Authors: Noura Hamour; Amar Boukerrou; Hocine Djidjelli; Jean-Eudes Maigret; Johnny Beaugrand
Journal: International Journal of Polymer Science
 (2015)

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## Abstract

This work investigates the effect of hydrothermal aging on the properties of polypropylene/alfa fiber composites. Hydrothermal aging was induced in an environmental testing chamber at 65°C and 75% relative humidity (RH) over a 1000 h period. At the beginning (t=0 h), the results showed that Young’s moduli of the untreated alfa fibers and the acetylation-treated fibers increased by 21% and 36%, respectively, compared with the virgin polypropylene (PP). Additionally, Young’s moduli decreased by 7% for the compatibilized composites composed of maleic anhydride grafted polypropylene (MAPP). After 1000 h of aging, Young’s moduli decreased by 36% for untreated alfa fibers and 29% for the acetylation-treated alfa fibers and the compatibilized composites. Significant degradation was observed in the untreated alfa fiber samples. The Fourier transformed infrared (FTIR) allows us to distinguish the characteristic absorption bands of the main chemical functions present in the composite material before and after aging. The thermal properties showed that the thermal stability and the degree of crystallinity of the composites decreased after hydrothermal aging; this result was corroborated by the dynamical mechanical analysis (DMA) results.


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## Body

## 1. Introduction

In recent years, substantial attention has been focused on the development of environmentally friendly composites that combine synthetic polymers with plant-based fibers. Natural fibers such as alfa [1, 2] olive husk [3], wood [4, 5], luffa [6], coir [7], hemp [8], kenaf [9], and sisal [10] have been widely used in composites. They are used as reinforcement for the polymer matrix and have good potential to replace conventional fibers (glass, carbon, etc.) in certain applications [11]. Moreover, lignocellulosic fibers are a biodegradable material obtained from renewable and abundant sources with low extraction prices [12]. However, the hydrophilic nature of natural fibers can be a disadvantage for composite manufacturing because these fibers lack compatibility with hydrophobic polymeric matrices, which may result in poor performance. To solve this problem, chemical modification of natural fibers or the use of compatibilizer agents has been necessary. However, composites based on natural fibers present poor dimensional stability when in contact with water [13]. The possibility of using these materials in outdoor applications necessitates analyses of their mechanical behavior under the influence of hydrothermal aging [14]. Lignocellulose fibers (or plant fibers) contain many hydroxyl groups and readily interact with water molecules via hydrogen bonding. In contrast to glass fibers, in which water adsorption occurs at the surface, lignocellulosic fibers can interact with water throughout their bulk. The quantity of sorbed water depends on the relative humidity of the surrounding atmosphere and the degree of crystallinity. All of the hydroxyl groups in the amorphous phase are assumed accessible by polar solutions, which is unlike crystalline phases, in which only the surfaces are available for water sorption. Therefore, swelling by water uptake can lead to microcracking of composites and the degradation of mechanical properties [13, 15].This study aims to improve the understanding of the effect of hydrothermal aging of PP/alfa fiber composites. In addition, this study investigates the modification of interfacial adhesion forces between the alfa fibers (high hydrophilicity) and the PP matrix (strongly hydrophobic) to increase their compatibility using two different methods. The first method was based on the chemical treatment of alfa fibers through acetylation by reacting the hydroxyl groups of the lignocellulosic material with the acetyl groups of acetic anhydride (Ac). The second method consisted of using the well-known polymer maleic anhydride grafted polypropylene (MAPP) as a compatibilizer to improve the interfacial bonding between the alfa fibers and the PP matrix. These two composites were compared to a PP/untreated alfa fiber composite. The three composite materials obtained were studied using several analytical techniques, including FTIR spectroscopy, the measurement of tensile and dynamic mechanical properties (DMA) and thermal stability (TGA, DSC), and SEM observations.


## 2. Materials and Methods

### 2.1. Materials

Alfa plants were collected in western Algeria. After in-house decortication, the fraction of the material obtained after sieving through a 100μm mesh was used. The chemical composition of the alfa grass was mainly lignin (29 wt%), cellulose (45 wt%), and hemicelluloses (20 wt%). These constituents were determined using previously described chemical procedures [16]. The isotactic polypropylene (PP500P©) used in this study as the matrix was provided by SABIC (Saudi Arabia) with a melt flow index (MFI) of 3 g/10 min (230°C/2.16 kg) (ASTM D-1238) and a density of 0.9 g·cm−3 (values from supplier datasheets). Maleic anhydride (MAPP), supplied by ARKEMA (France), has a melt flow index (MFI) of 2.63 g/10 min (190°C/235 g, technical notice). Acetic anhydride (Ac, 98%), acetic acid, and sulfuric acid were provided by Sigma-Aldrich.


### 2.2. Acetylated Alfa Fibers

Dry alfa fiber (15 g) was placed in a round-bottom flask with 72.5 mL acetic acid. The reaction was performed in a thermostatic bath at 35°C for 45 min under mechanical stirring. Then, 24 mL of acetic acid was added along with 0.1 mL of concentrated H2SO4 and the bath was maintained for 1 h. After this step, the mixture was cooled to 18°C for the slow addition of acetic anhydride (40 mL) with 0.6 mL concentrated H2SO4 over 3 h with constant stirring. A temperature of 24°C was maintained for more than 15 min. Then, the temperature was slowly increased to 50–55°C and the reaction continued for 3 h. This mixture was vacuum filtered, washed with distilled water, and then dried in an oven at 50°C for 24 h [17].


### 2.3. Composite Processing

Different formulations of PP/alfa fibers were prepared using “corotating” twin-screw extrusion. In addition to neat PP, PP/untreated alfa fiber composites, PP/alfa fiber composites treated with acetic anhydride, and a compatibilized composite were prepared after twin-screw extrusion. The formulations were injected using an injection press (ERINKA mark) connected to the compounder. Tensile specimens (ISO 527-5B) were obtained as the output of the injection-molding machine. The mould temperature were kept at 180 and 30°C, respectively at different pressures (4 bar for preinjection and 5 bar for injection). Table1 shows an overview of the samples tested.Table 1
Overview of the samples tested.
Designations
Analysis
FTIR
Tensile test
ATG/DSC
DMTA
SEM
Abbreviations
Compositions
Aging Kinetic Analysis  (h)
Virgin PP
100% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20UT
Fiber 20 wt% +  80% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20AT
Acetylated fiber 20 wt% +     80% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20AMAT
Fiber 20 wt% + 5 wt% Compatibiliser + 75% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000


### 2.4. Hydrothermal Aging Treatment

The alfa fiber/polypropylene composites were placed in a Secasi Technologies (SLH41/08P, France) environmental testing chamber equipped with a relative humidity controller with a precision of ±2% to ±5%. Demineralized water was used throughout the duration of treatment to ensure the neutrality of the environment. A relative humidity (RH) of 75% and temperature of 65°C were used to conduct the aging treatments. The samples were aged for different periods: 150, 400, 600, 800, and 1000 h (approximately 6 to 41 days).


### 2.5. Fourier Transform Infrared Spectroscopy (FTIR)

FTIR spectra of the PP and PP/alfa fiber composites with and without aging were recorded using an FTIR SHIMADZU FTIR-8400S in the range of 4000–500 cm−1. The equipment was operating in absorbance mode with 4 scan, at a resolution of 4 cm−1, meaning a displacement of the mirror of 0.25 cm. Thin films, which were between 60 and 80 μm in thickness, were prepared by compression molding at 180°C for 2 min.


### 2.6. Thermogravimetric Analysis (TGA)

Thermogravimetric analysis (TGA) was performed using a Hi-Res TG 2950 (TA instruments) in an inert atmosphere at a heating rate of 10°C/min. The sample weights were in the range of 10–20 mg, and they were scanned in the temperature range of 20°C to 700°C.


### 2.7. Differential Scanning Calorimetric Analysis (DSC)

The DSC measurements were conducted using a DSC-2920 (TA instrument) differential scanning calorimeter with nitrogen as the purge gas. Samples of approximately 5–10 mg were analyzed in the temperature range of −50 to +200°C. To erase the thermal history, the first cooling and the second heating thermograms were recorded with the following scanning rate: 10°C/min in the first cooling and 10°C/min in the second heating. The melting peak (Tm) was obtained. The melting temperature (Tf), melting enthalpy (ΔHf), crystalline index (Xc), crystallization temperature (Tc), and crystallization enthalpy (ΔHc) were determined from the DSC thermograms, and the values are reported in Table 3.


### 2.8. Tensile Tests

Quasi-static tensile tests were carried out using a Macro Test Well 108-2kN testing apparatus in a climatic room where the temperature was 23°C at 65% RH according to ISO 527-5B. The speed was 50 mm/min. The tests were performed at least three times for each sample, and the results were averaged arithmetically.


### 2.9. Dynamic Mechanical Analysis (DMA)

Dry and moisture-saturated samples were subjected to dynamic mechanical analysis (DMA) using a tension cantilever system DMA Q800 (TA Instruments) at a frequency of 1 Hz and a driving force of 8 N. The dynamic storage moduli of each specimen were determined as a function of humidity from 10% to 100% (isotherm of 40°C).


### 2.10. Scanning Electron Microscopy (SEM)

Scanning electron microscopy (SEM) was used to monitor the fracture surface of the composites after the samples were frozen in liquid nitrogen. SEM analysis was performed using a TM 1000 Tabletop Microscope (Hitachi).


## 2.1. Materials

Alfa plants were collected in western Algeria. After in-house decortication, the fraction of the material obtained after sieving through a 100μm mesh was used. The chemical composition of the alfa grass was mainly lignin (29 wt%), cellulose (45 wt%), and hemicelluloses (20 wt%). These constituents were determined using previously described chemical procedures [16]. The isotactic polypropylene (PP500P©) used in this study as the matrix was provided by SABIC (Saudi Arabia) with a melt flow index (MFI) of 3 g/10 min (230°C/2.16 kg) (ASTM D-1238) and a density of 0.9 g·cm−3 (values from supplier datasheets). Maleic anhydride (MAPP), supplied by ARKEMA (France), has a melt flow index (MFI) of 2.63 g/10 min (190°C/235 g, technical notice). Acetic anhydride (Ac, 98%), acetic acid, and sulfuric acid were provided by Sigma-Aldrich.


## 2.2. Acetylated Alfa Fibers

Dry alfa fiber (15 g) was placed in a round-bottom flask with 72.5 mL acetic acid. The reaction was performed in a thermostatic bath at 35°C for 45 min under mechanical stirring. Then, 24 mL of acetic acid was added along with 0.1 mL of concentrated H2SO4 and the bath was maintained for 1 h. After this step, the mixture was cooled to 18°C for the slow addition of acetic anhydride (40 mL) with 0.6 mL concentrated H2SO4 over 3 h with constant stirring. A temperature of 24°C was maintained for more than 15 min. Then, the temperature was slowly increased to 50–55°C and the reaction continued for 3 h. This mixture was vacuum filtered, washed with distilled water, and then dried in an oven at 50°C for 24 h [17].


## 2.3. Composite Processing

Different formulations of PP/alfa fibers were prepared using “corotating” twin-screw extrusion. In addition to neat PP, PP/untreated alfa fiber composites, PP/alfa fiber composites treated with acetic anhydride, and a compatibilized composite were prepared after twin-screw extrusion. The formulations were injected using an injection press (ERINKA mark) connected to the compounder. Tensile specimens (ISO 527-5B) were obtained as the output of the injection-molding machine. The mould temperature were kept at 180 and 30°C, respectively at different pressures (4 bar for preinjection and 5 bar for injection). Table1 shows an overview of the samples tested.Table 1
Overview of the samples tested.
Designations
Analysis
FTIR
Tensile test
ATG/DSC
DMTA
SEM
Abbreviations
Compositions
Aging Kinetic Analysis  (h)
Virgin PP
100% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20UT
Fiber 20 wt% +  80% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20AT
Acetylated fiber 20 wt% +     80% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000
F20AMAT
Fiber 20 wt% + 5 wt% Compatibiliser + 75% PP
0; 1000
0; 150; 400; 600; 800; 1000
0; 1000
0; 1000
0; 1000


## 2.4. Hydrothermal Aging Treatment

The alfa fiber/polypropylene composites were placed in a Secasi Technologies (SLH41/08P, France) environmental testing chamber equipped with a relative humidity controller with a precision of ±2% to ±5%. Demineralized water was used throughout the duration of treatment to ensure the neutrality of the environment. A relative humidity (RH) of 75% and temperature of 65°C were used to conduct the aging treatments. The samples were aged for different periods: 150, 400, 600, 800, and 1000 h (approximately 6 to 41 days).


## 2.5. Fourier Transform Infrared Spectroscopy (FTIR)

FTIR spectra of the PP and PP/alfa fiber composites with and without aging were recorded using an FTIR SHIMADZU FTIR-8400S in the range of 4000–500 cm−1. The equipment was operating in absorbance mode with 4 scan, at a resolution of 4 cm−1, meaning a displacement of the mirror of 0.25 cm. Thin films, which were between 60 and 80 μm in thickness, were prepared by compression molding at 180°C for 2 min.


## 2.6. Thermogravimetric Analysis (TGA)

Thermogravimetric analysis (TGA) was performed using a Hi-Res TG 2950 (TA instruments) in an inert atmosphere at a heating rate of 10°C/min. The sample weights were in the range of 10–20 mg, and they were scanned in the temperature range of 20°C to 700°C.


## 2.7. Differential Scanning Calorimetric Analysis (DSC)

The DSC measurements were conducted using a DSC-2920 (TA instrument) differential scanning calorimeter with nitrogen as the purge gas. Samples of approximately 5–10 mg were analyzed in the temperature range of −50 to +200°C. To erase the thermal history, the first cooling and the second heating thermograms were recorded with the following scanning rate: 10°C/min in the first cooling and 10°C/min in the second heating. The melting peak (Tm) was obtained. The melting temperature (Tf), melting enthalpy (ΔHf), crystalline index (Xc), crystallization temperature (Tc), and crystallization enthalpy (ΔHc) were determined from the DSC thermograms, and the values are reported in Table 3.


## 2.8. Tensile Tests

Quasi-static tensile tests were carried out using a Macro Test Well 108-2kN testing apparatus in a climatic room where the temperature was 23°C at 65% RH according to ISO 527-5B. The speed was 50 mm/min. The tests were performed at least three times for each sample, and the results were averaged arithmetically.


## 2.9. Dynamic Mechanical Analysis (DMA)

Dry and moisture-saturated samples were subjected to dynamic mechanical analysis (DMA) using a tension cantilever system DMA Q800 (TA Instruments) at a frequency of 1 Hz and a driving force of 8 N. The dynamic storage moduli of each specimen were determined as a function of humidity from 10% to 100% (isotherm of 40°C).


## 2.10. Scanning Electron Microscopy (SEM)

Scanning electron microscopy (SEM) was used to monitor the fracture surface of the composites after the samples were frozen in liquid nitrogen. SEM analysis was performed using a TM 1000 Tabletop Microscope (Hitachi).


## 3. Results and Discussion

### 3.1. FTIR Analysis

To analyze the behavior of PP containing fibers as a function of the treatment and the applied hydrothermal aging, as well as the influence of aging on the mechanical and thermal behavior, spectroscopic techniques were employed to study the formation of radical and chemical species that affect the structure and final behavior of the composite. The technique employed was infrared (FTIR) spectroscopy. The results obtained and the FTIR spectra for the PP/untreated alfa fiber composites are shown in Figure1(a). The results presented in Figure 1(a) show the presence of aldehyde carbonyl groups (C=O) at the stretch frequency of approximately 1700 cm−1, C–H absorption within the range of 2700–2800 cm−1, and asymmetric stretching of the cis and trans C=C at approximately 1670 cm−1. Absorption bands typical of PP were also observed at frequencies between 1450 cm−1 for the –CH2 bond and 1370 cm−1 for the –CH3 bond. We also noticed the appearance of the absorption band between 3500 and 3100 cm−1, which increases in intensity after aging Figure 1(b), reflecting elongation of the hydroxyl vibration of water molecules (OH) associated with the diffusion of the liquid within the matrix and fiber interface/matrix [18, 19].Figure 1
FTIR spectra of the PP/alfa fiber composites: (a) before aging and (b) after aging.
(a)
(b)In addition, the FTIR spectra results for the F20AT (PP/treated alfa fiber by acetylation) and F20AMAT (PP/alfa fiber/MAPP) composites are shown in Figures1(a) and 1(b). As in the case of the virgin matrix and the untreated composite the spectra of F20AT F20AMAT composite present the same absorption bands. This result suggests that the presence of a compatibilizing agent and the chemical modification by acetylation of fibers have no effect on the composite during the hydrothermal aging.


### 3.2. Thermogravimetric Analysis (TGA)

Thermogravimetric analysis was used to determine the degradation temperature of the composites, as well as their components, under nitrogen atmosphere. Figure2 clearly shows that the thermal degradation profiles of the composites with and without aging are similar. One stage of polypropylene degradation was recorded, which is unlike composites, whose degradation occurs in two steps [20]. Indeed, the PP decomposes from 400°C and gives mainly propylene trimer [21]. Beyond 500°C, oligomers of other monomers are also formed, and approximately 0.8% of char is recovered at the end of its decomposition. However, the thermal degradation of the alfa fiber-filled PP composites occur in a two-step process, this result was confirmed in derivative thermogravimetric curve (DTG) (Figure 2(b)). The first thermal degradation step may correspond to lignin and polysaccharide polymers (hemicellulose and cellulose). The second step was attributed to degradation of the polymer (PP) [22].Figure 2
Thermal degradation behavior of the composites: ((a), (b)) before aging and ((c), (d)) after aging.
(a)
(b)
(c)
(d)The incorporation of the untreated alfa fiber in polypropylene led to a decrease in the onset decomposition temperature; this decrease is probably caused by the decomposition of the components of the alfa fiber (cellulose, hemicellulose, and lignin). However, the thermal stability slightly improved for the PP/alfa fiber composites with the compatibilizing agent MAPP compared with the composites modified by acetylation and untreated composites, which is explained by the improved compatibility and adhesion of the fibers to the PP matrix [3].The typical degradation temperatures of virgin PP and the PP/alfa fiber composites are summarized in Table2. Moisture plays an important role in influencing the mechanical behavior, as well as the long-term durability, of the composites. Figures 2(c) and 2(d) show the thermograms for virgin PP and PP/alfa composites after aging. The derivatives of the mass loss curves are also displayed to highlight the differences between the samples.Table 2
TGA data for neat PP and PP/alfa fiber composite materials.
Formulations
T
onset (°C)
V
max
⁡ (%/min)
Char (Wt. %)
Before   aging
Virgin PP
431
34.6
0.34
F20UT
362
30.0
2.50
F20AT
394
25.4
3.19
F20AMAT
360
21.8
3.63
After   aging
Virgin PP
393
35.0
0.23
F20UT
353
29.8
3.26
F20AT
395
24.1
3.54
F20AMAT
307
20.5
3.42Table 3
Crystallinity rates of neat PP and PP/alfa fiber composite materials.
Formulations
T
f (°C)
Δ
H
f (J/g)
T
c (°C)
Δ
H
c (J/g)
X
c (%)
Before   aging
Virgin PP
116
94.2
169
77.0
36.8
F20UT
115
87.0
170
74.4
44.5
F20AT
116
83.4
170
74.5
44.5
F20AMAT
115
80.1
170
72.4
43.3
After   aging
Virgin PP
116
85.1
170
72.0
34.4
F20UT
116
81.8
169
68.9
41.2
F20AT
116
81.4
170
67.2
40.2
F20AMAT
117
78.2
169
69.1
41.3The maximum degradation rate (Vmax⁡) decreased after aging. For the untreated composite (F20UT), the Vmax⁡ decreased from 30 to 29 (%/min). Clearly, this decrease was due to the lignin, which acts as a heat stabilizer in the PP. However, the treated composite showed the same tendencies. The Vmax⁡ decreased from 25 to 24 (%/min) and from 21 to 20 (%/min) for F20AT and F20AMAT, respectively. This decrease is due to the increase of the thermal stability.


### 3.3. Differential Scanning Calorimetry (DSC) Analysis

The percent crystallinity was obtained from DSC analysis using the following relation [23, 24]: Xc(%)=((ΔH)/(ΔHm·ω))∗100, where ΔH and ΔHm are the heat of fusion of PP and 100% crystalline PP, respectively. A value of ΔHm = 209 J/g for PP [25] was used, and ω is the reinforcement content. The crystallinity of virgin PP and the PP/alfa fiber composites decreased after aging; the crystallinity of virgin PP decreased by 6% after aging, and the crystallinity of the F20UT composite (PP/untreated alfa fiber) decreased by 7% after aging. Crystallinity reductions for the F20UT, F20AT, and F20AMAT composites were observed after hydrothermal aging (Table 3). Beg and Pickering [23] found similar results and explained that this reduction is related to the decrease of the molar mass of macromolecular chains. The other authors [26] have explained the crystallinity reduction by the decrease of the structural irregularity.


### 3.4. Effects of Hydrothermal Aging on the Mechanical Properties

Mechanical tests were performed on all of the samples before and after aging; the results are shown in Figures3(a) and 3(b). In general, the mechanical properties of these materials decreased after moisture uptake due to the effect of the water molecules, which change the structure and properties of the fibers and the matrix as well as the interface between them [27]. After the water molecule penetrates the composite materials, the fibers tend to swell. The matrix structure can also be affected by the water uptake by processes such as chain reorientation and shrinkage. Additionally, water molecules are inserted between the macromolecular chains of polypropylene weakening secondary link of Van der Waals and therefore they reduce the interactions between these chains that can move freely. For this reason we can say that the water acts as a plasticizer. Hydrothermal aging causes the degradation of fibers in a thermoplastic matrix. Water absorption and its effects contribute to the loss of compatibilization between the fibers and the matrix, which results in debonding and weakening of the interface adhesion [27].Figure 3
Evolution of the mechanical properties of the PP/alfa fiber composites: (a) tensile strength and (b) Young’s moduli.
(a)
(b)According to the obtained tensile strength results (Figure3(a)), the values at the beginning (t=0 h) are slightly increased compared with those of the PP matrix after 1000 h. A slight decrease was observed for all of the composite mixtures.At the beginning (t=0 h), Young’s moduli of the F20UT and F20AT composites were higher than that of the PP matrix, which was due to the fiber stiffness, in both of the different composites. However, the F20AMAT composite had the lowest Young modulus, which can be explained by the plasticization due to the MAPP compatibilizer. After 1000 h, the modulus decreased with exposure time to temperature and moisture, which acts as a plasticizer. Similar degradation behavior was observed by Hammiche et al. and Chen et al. [28, 29]. Finally, the changes in the mechanical properties coincided with the structural modification and chemical changes deduced from the FTIR characterization.


### 3.5. Dynamic Mechanical Analysis (DMA)

Dynamic mechanical analysis is a method for measuring the viscoelasticity of polymers. This method enables the study and characterization of the mechanical properties as the storage moduli,E′, which represents the stiffness and the elastic component of the material.E′ expresses the material’s ability to store mechanical energy and to fully transfer the energy in the form of elastic deformation. The dynamic mechanical properties of virgin PP and the PP/alfa fiber composites with and without modification were evaluated. The storage moduli,E′, as a function of humidity is depicted in Figure 4(a). In the case of the matrix, the storage moduli,E′, significantly decreased with moisture due to gradual softening of the material and increased segmental mobility. Regardless of the humidity, after the addition of fibers (F20UT), a significant increase in the storage modulus was observed, as expected. This result revealed that there is an effective stress transfer across the interface, which improves the stiffness of the composite. For the systems based on the compatibilized composites (F20AMAT), the storage moduli were slightly lower compared with those of the materials based on nonmodified fibers. This reduction can also be explained by a reduction of the stiffness. This result confirms the data obtained from the tensile measurements, which show a decrease in tensile modulus at room temperature for the compatibilized composites.Figure 4
Variation of storage moduli versus humidity (DMTA analyses): (a) before aging and (b) after aging for (blue line) virgin PP, (green line) F20UT, (light blue line) F20AT, and (black line) F20AMAT.
(a)
(b)With increasing humidity, theE′ values of the matrix PP and the composite systems decreased. However, for composites, the decreased matrix moduli are arguably compensated for by the fiber stiffness. The effects of hydrothermal aging on the dynamic mechanical behavior after aging are shown in Figure 4(b). The storage moduli of the composites containing fibers (treated or not) were slightly lower than that of the PP matrix. This decrease reflects several concurrent phenomena, which are reversible. The reversible phenomena are summarized by the plasticization caused by the presence of water. The hydrophilic nature [30] of natural fibers is considered to decrease the resistance of the composite in a humid environment. From these results, it can be deduced that a study of the behavior of the composites in a humid atmosphere is necessary not only to estimate the effects of aging but also to better understand the mechanisms involved to minimize them. Presumably, the first water molecules entering the polymer will act strongly on the matrix. These water molecules can initially spread in space (free volume and porosity) before reaching the polar sites, after which they generate swelling and, as a consequence, a change in thermomechanical properties. The mechanism of plasticization, which is generated by the diffusion of water molecules in the amorphous phase, may be responsible for such damage.


### 3.6. Scanning Electron Microscopy (SEM)

The morphology and facies rupture were observed to evaluate changes induced by fiber incorporation in the polymeric matrix because the functional properties of the resulting material are directly related to the surface features of the composite and the interfacial adhesion between its components. The results are represented in Figures5(a) and 5(b), which correspond to the fracture surface before and after hydrothermal aging, respectively. In particular, in Figure 5(a1), the facies of virgin PP before aging exhibits a very smooth relief. In contrast, in Figure 5(b1), the surface exhibits very few defects after 1000 h, likely because the surface of the virgin PP did not undergo degradation. As expected, the SEM micrographs show that the addition of F20UT to the PP matrix before aging (Figure 5(a2)) resulted in a gap or void between the fiber elements and matrix. We can also notice the presence of aggregates in the F20UT composite. The formation of these aggregates affect negatively a dispersion of the alfa fiber in the matrix inducing the debonding which increased after aging (Figure 5(b2)) between these two components. The debonding load/matrix was often accompanied by shrinkage of the polymer around the load and can be reversed after the first instance. This phenomenon is attributed to hydrolysis of the polymer matrix by water [31]. The same result was observed for the formulations F20AT and F20AMAT (Figures 5(b3) and 5(b4)). Therefore, sample degradation was caused by debonding at the load/matrix interface. As a result, hollows and wide grooves that amounted to cracks were visible [32].Figure 5
SEM micrographs of fractured surfaces (a) before aging and (b) after aging for composites: ((a1), (b1)) virgin PP, ((a2), (b2)) F20UT, ((a3), (b3)) F20AT, and ((a4), (b4)) F20AMAT.
(a)
(b)


## 3.1. FTIR Analysis

To analyze the behavior of PP containing fibers as a function of the treatment and the applied hydrothermal aging, as well as the influence of aging on the mechanical and thermal behavior, spectroscopic techniques were employed to study the formation of radical and chemical species that affect the structure and final behavior of the composite. The technique employed was infrared (FTIR) spectroscopy. The results obtained and the FTIR spectra for the PP/untreated alfa fiber composites are shown in Figure1(a). The results presented in Figure 1(a) show the presence of aldehyde carbonyl groups (C=O) at the stretch frequency of approximately 1700 cm−1, C–H absorption within the range of 2700–2800 cm−1, and asymmetric stretching of the cis and trans C=C at approximately 1670 cm−1. Absorption bands typical of PP were also observed at frequencies between 1450 cm−1 for the –CH2 bond and 1370 cm−1 for the –CH3 bond. We also noticed the appearance of the absorption band between 3500 and 3100 cm−1, which increases in intensity after aging Figure 1(b), reflecting elongation of the hydroxyl vibration of water molecules (OH) associated with the diffusion of the liquid within the matrix and fiber interface/matrix [18, 19].Figure 1
FTIR spectra of the PP/alfa fiber composites: (a) before aging and (b) after aging.
(a)
(b)In addition, the FTIR spectra results for the F20AT (PP/treated alfa fiber by acetylation) and F20AMAT (PP/alfa fiber/MAPP) composites are shown in Figures1(a) and 1(b). As in the case of the virgin matrix and the untreated composite the spectra of F20AT F20AMAT composite present the same absorption bands. This result suggests that the presence of a compatibilizing agent and the chemical modification by acetylation of fibers have no effect on the composite during the hydrothermal aging.


## 3.2. Thermogravimetric Analysis (TGA)

Thermogravimetric analysis was used to determine the degradation temperature of the composites, as well as their components, under nitrogen atmosphere. Figure2 clearly shows that the thermal degradation profiles of the composites with and without aging are similar. One stage of polypropylene degradation was recorded, which is unlike composites, whose degradation occurs in two steps [20]. Indeed, the PP decomposes from 400°C and gives mainly propylene trimer [21]. Beyond 500°C, oligomers of other monomers are also formed, and approximately 0.8% of char is recovered at the end of its decomposition. However, the thermal degradation of the alfa fiber-filled PP composites occur in a two-step process, this result was confirmed in derivative thermogravimetric curve (DTG) (Figure 2(b)). The first thermal degradation step may correspond to lignin and polysaccharide polymers (hemicellulose and cellulose). The second step was attributed to degradation of the polymer (PP) [22].Figure 2
Thermal degradation behavior of the composites: ((a), (b)) before aging and ((c), (d)) after aging.
(a)
(b)
(c)
(d)The incorporation of the untreated alfa fiber in polypropylene led to a decrease in the onset decomposition temperature; this decrease is probably caused by the decomposition of the components of the alfa fiber (cellulose, hemicellulose, and lignin). However, the thermal stability slightly improved for the PP/alfa fiber composites with the compatibilizing agent MAPP compared with the composites modified by acetylation and untreated composites, which is explained by the improved compatibility and adhesion of the fibers to the PP matrix [3].The typical degradation temperatures of virgin PP and the PP/alfa fiber composites are summarized in Table2. Moisture plays an important role in influencing the mechanical behavior, as well as the long-term durability, of the composites. Figures 2(c) and 2(d) show the thermograms for virgin PP and PP/alfa composites after aging. The derivatives of the mass loss curves are also displayed to highlight the differences between the samples.Table 2
TGA data for neat PP and PP/alfa fiber composite materials.
Formulations
T
onset (°C)
V
max
⁡ (%/min)
Char (Wt. %)
Before   aging
Virgin PP
431
34.6
0.34
F20UT
362
30.0
2.50
F20AT
394
25.4
3.19
F20AMAT
360
21.8
3.63
After   aging
Virgin PP
393
35.0
0.23
F20UT
353
29.8
3.26
F20AT
395
24.1
3.54
F20AMAT
307
20.5
3.42Table 3
Crystallinity rates of neat PP and PP/alfa fiber composite materials.
Formulations
T
f (°C)
Δ
H
f (J/g)
T
c (°C)
Δ
H
c (J/g)
X
c (%)
Before   aging
Virgin PP
116
94.2
169
77.0
36.8
F20UT
115
87.0
170
74.4
44.5
F20AT
116
83.4
170
74.5
44.5
F20AMAT
115
80.1
170
72.4
43.3
After   aging
Virgin PP
116
85.1
170
72.0
34.4
F20UT
116
81.8
169
68.9
41.2
F20AT
116
81.4
170
67.2
40.2
F20AMAT
117
78.2
169
69.1
41.3The maximum degradation rate (Vmax⁡) decreased after aging. For the untreated composite (F20UT), the Vmax⁡ decreased from 30 to 29 (%/min). Clearly, this decrease was due to the lignin, which acts as a heat stabilizer in the PP. However, the treated composite showed the same tendencies. The Vmax⁡ decreased from 25 to 24 (%/min) and from 21 to 20 (%/min) for F20AT and F20AMAT, respectively. This decrease is due to the increase of the thermal stability.


## 3.3. Differential Scanning Calorimetry (DSC) Analysis

The percent crystallinity was obtained from DSC analysis using the following relation [23, 24]: Xc(%)=((ΔH)/(ΔHm·ω))∗100, where ΔH and ΔHm are the heat of fusion of PP and 100% crystalline PP, respectively. A value of ΔHm = 209 J/g for PP [25] was used, and ω is the reinforcement content. The crystallinity of virgin PP and the PP/alfa fiber composites decreased after aging; the crystallinity of virgin PP decreased by 6% after aging, and the crystallinity of the F20UT composite (PP/untreated alfa fiber) decreased by 7% after aging. Crystallinity reductions for the F20UT, F20AT, and F20AMAT composites were observed after hydrothermal aging (Table 3). Beg and Pickering [23] found similar results and explained that this reduction is related to the decrease of the molar mass of macromolecular chains. The other authors [26] have explained the crystallinity reduction by the decrease of the structural irregularity.


## 3.4. Effects of Hydrothermal Aging on the Mechanical Properties

Mechanical tests were performed on all of the samples before and after aging; the results are shown in Figures3(a) and 3(b). In general, the mechanical properties of these materials decreased after moisture uptake due to the effect of the water molecules, which change the structure and properties of the fibers and the matrix as well as the interface between them [27]. After the water molecule penetrates the composite materials, the fibers tend to swell. The matrix structure can also be affected by the water uptake by processes such as chain reorientation and shrinkage. Additionally, water molecules are inserted between the macromolecular chains of polypropylene weakening secondary link of Van der Waals and therefore they reduce the interactions between these chains that can move freely. For this reason we can say that the water acts as a plasticizer. Hydrothermal aging causes the degradation of fibers in a thermoplastic matrix. Water absorption and its effects contribute to the loss of compatibilization between the fibers and the matrix, which results in debonding and weakening of the interface adhesion [27].Figure 3
Evolution of the mechanical properties of the PP/alfa fiber composites: (a) tensile strength and (b) Young’s moduli.
(a)
(b)According to the obtained tensile strength results (Figure3(a)), the values at the beginning (t=0 h) are slightly increased compared with those of the PP matrix after 1000 h. A slight decrease was observed for all of the composite mixtures.At the beginning (t=0 h), Young’s moduli of the F20UT and F20AT composites were higher than that of the PP matrix, which was due to the fiber stiffness, in both of the different composites. However, the F20AMAT composite had the lowest Young modulus, which can be explained by the plasticization due to the MAPP compatibilizer. After 1000 h, the modulus decreased with exposure time to temperature and moisture, which acts as a plasticizer. Similar degradation behavior was observed by Hammiche et al. and Chen et al. [28, 29]. Finally, the changes in the mechanical properties coincided with the structural modification and chemical changes deduced from the FTIR characterization.


## 3.5. Dynamic Mechanical Analysis (DMA)

Dynamic mechanical analysis is a method for measuring the viscoelasticity of polymers. This method enables the study and characterization of the mechanical properties as the storage moduli,E′, which represents the stiffness and the elastic component of the material.E′ expresses the material’s ability to store mechanical energy and to fully transfer the energy in the form of elastic deformation. The dynamic mechanical properties of virgin PP and the PP/alfa fiber composites with and without modification were evaluated. The storage moduli,E′, as a function of humidity is depicted in Figure 4(a). In the case of the matrix, the storage moduli,E′, significantly decreased with moisture due to gradual softening of the material and increased segmental mobility. Regardless of the humidity, after the addition of fibers (F20UT), a significant increase in the storage modulus was observed, as expected. This result revealed that there is an effective stress transfer across the interface, which improves the stiffness of the composite. For the systems based on the compatibilized composites (F20AMAT), the storage moduli were slightly lower compared with those of the materials based on nonmodified fibers. This reduction can also be explained by a reduction of the stiffness. This result confirms the data obtained from the tensile measurements, which show a decrease in tensile modulus at room temperature for the compatibilized composites.Figure 4
Variation of storage moduli versus humidity (DMTA analyses): (a) before aging and (b) after aging for (blue line) virgin PP, (green line) F20UT, (light blue line) F20AT, and (black line) F20AMAT.
(a)
(b)With increasing humidity, theE′ values of the matrix PP and the composite systems decreased. However, for composites, the decreased matrix moduli are arguably compensated for by the fiber stiffness. The effects of hydrothermal aging on the dynamic mechanical behavior after aging are shown in Figure 4(b). The storage moduli of the composites containing fibers (treated or not) were slightly lower than that of the PP matrix. This decrease reflects several concurrent phenomena, which are reversible. The reversible phenomena are summarized by the plasticization caused by the presence of water. The hydrophilic nature [30] of natural fibers is considered to decrease the resistance of the composite in a humid environment. From these results, it can be deduced that a study of the behavior of the composites in a humid atmosphere is necessary not only to estimate the effects of aging but also to better understand the mechanisms involved to minimize them. Presumably, the first water molecules entering the polymer will act strongly on the matrix. These water molecules can initially spread in space (free volume and porosity) before reaching the polar sites, after which they generate swelling and, as a consequence, a change in thermomechanical properties. The mechanism of plasticization, which is generated by the diffusion of water molecules in the amorphous phase, may be responsible for such damage.


## 3.6. Scanning Electron Microscopy (SEM)

The morphology and facies rupture were observed to evaluate changes induced by fiber incorporation in the polymeric matrix because the functional properties of the resulting material are directly related to the surface features of the composite and the interfacial adhesion between its components. The results are represented in Figures5(a) and 5(b), which correspond to the fracture surface before and after hydrothermal aging, respectively. In particular, in Figure 5(a1), the facies of virgin PP before aging exhibits a very smooth relief. In contrast, in Figure 5(b1), the surface exhibits very few defects after 1000 h, likely because the surface of the virgin PP did not undergo degradation. As expected, the SEM micrographs show that the addition of F20UT to the PP matrix before aging (Figure 5(a2)) resulted in a gap or void between the fiber elements and matrix. We can also notice the presence of aggregates in the F20UT composite. The formation of these aggregates affect negatively a dispersion of the alfa fiber in the matrix inducing the debonding which increased after aging (Figure 5(b2)) between these two components. The debonding load/matrix was often accompanied by shrinkage of the polymer around the load and can be reversed after the first instance. This phenomenon is attributed to hydrolysis of the polymer matrix by water [31]. The same result was observed for the formulations F20AT and F20AMAT (Figures 5(b3) and 5(b4)). Therefore, sample degradation was caused by debonding at the load/matrix interface. As a result, hollows and wide grooves that amounted to cracks were visible [32].Figure 5
SEM micrographs of fractured surfaces (a) before aging and (b) after aging for composites: ((a1), (b1)) virgin PP, ((a2), (b2)) F20UT, ((a3), (b3)) F20AT, and ((a4), (b4)) F20AMAT.
(a)
(b)


## 4. Conclusion

This study addresses the evolution of properties of untreated and treated alfa fiber-reinforced polypropylene composites during hydrothermal aging. Regardless of the type of treatment (acetylation by acetic anhydride or addition of the MAPP compatibilizing agent), the PP/alfa fiber composites showed a reduction in tensile moduli after aging. This decrease can be plausibly explained by the hydrophilic nature of the fiber that absorbs more moisture and causes swelling of the PP matrix. Rupture facies confirmed the debonding of alfa fiber elements, which in turn may participate in the decrease in mechanical properties of the composite. Concerning thermal properties, the incorporation of acetylation-treated and untreated alfa fibers before aging improved the thermal stability of the composites. In addition, the use of MAPP compatibilizer provided improved thermal stability compared with that observed with the acetylation-treated and untreated alfa fibers. After hydrothermal aging, the treated composites displayed a higher thermal stability, as evidenced by the increase in the onset temperature and the decrease of the maximum rate of degradation. This effect might be due to the stronger interactions between the fiber and matrix caused by the formation of covalent bonds at the interface in the presence of MAPP. The degrees of crystallinity of the treated and untreated samples decreased after hydrothermal aging due to the humidity; this change was corroborated by the DMA results.



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*Source: 451691-2015-10-19.xml*