# Mechanical Properties and Weathering Behavior of  Polypropylene-Hemp Shives Composites

Authors: Marcel Ionel Popa; Silvia Pernevan; Cecilia Sirghie; Iuliana Spiridon; Dorina Chambre; Dana Maria Copolovici; Niculina Popa
Journal: Journal of Chemistry
 (2013)

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## Abstract

This paper presents the obtaining and the characterization of composites with polypropylene matrix and hemp shives as filler in different ratios and containing poly(propylene)-co maleic anhydride (MAH-PP) 3% wt as compatibility agent. The weathering behavior of the composite enclosing 60% hemp shives, performed after the exposure to UV radiations at different exposure times, was evaluated. The changes in the chemical and morphological structures were investigated by FT-IR and RAMAN spectroscopies and AFM microscopy. The mechanical characteristics of the composites were determined before and after an artificial aging process, and they are within the limits of the values reported for polyolefin-based composites and materials with natural fillers. During the accelerated weathering process, the correlation between the chemical degradation of the main components of the composite and the modification of the mechanical properties after the process of aging has been observed.


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## Body

## 1. Introduction

Natural fibers such as flax, hemp, jute, kenaf, and other many types of agrowastes were investigated as reinforcement for thermoset and thermoplastic composites [1–7]. The advantages of using such natural materials as fillers are low cost, being renewable, and being biodegradable, and when they are used as fillers in composites, they give to the products better mechanical performances in comparison with synthetic fibers. They are compatible with the processing temperatures of polyolefins.The mechanical properties and the weathering behavior of composites depend on the physicochemical characteristics of the filler and the presence of compatibility agents [8–10]. Adding compatibility agents causes a significant change in mechanical parameters. Improving the mechanical characteristics and stability to weathering in the presence of compatibility agents has been explained as a covalent interaction between the surface hydroxyl group of the natural fiber and the compatibilizer. Nature, the size, and geometry of fibers mainly determine the mechanical behavior, and the content of cellulose, lignin, and hemicelluloses significantly influences the stability to natural or artificial agents.Composites based on PP as polymer matrix and natural fibers as filler in presence of various compatibilizers as coupling agents have been prepared by batch mixing and extrusion [11–13]. The addition of MAH-PP has induced a significant increase in the mechanical properties, under tensile and flexural stresses and stiffness. A review about de hemp fibers and its composites and the work that shows the general profile of the mechanical properties of natural composites based on PP are useful for obtaining new products and for predicting the mechanical properties, the stability in time under the influence of different environmental factors, and the application fields [14, 15].This paper presents the obtaining and the characterization of composites using PP as matrix, a new filler, and hemp shives in different proportions and the MAP-PP 3% wt as compatibility agent. The mechanical characteristics of the composites were determined before and after the accelerated UV weathering.


## 2. Materials and Methods

### 2.1. Materials

The PP type J700 with a melt index 9.5 g/10 min at 230°C and density 0.912 g/cm3 was purchased by Petromidia Navodari (Romania). Hemp shives (length = 13–15 μm, thichness = 7.5–9.3 μm) are used as reinforcement in composite material. The chemical composition of hemp shives is: cellulose (46.4%), hemicelluloses (29.3%), lignin (22.5), pectin (0.9%), and waxy substances (0.8%) and was determined by TAPPI test method standards. To improve the compatibility between the polymer matrix and hemp fiber as filler, the poly (propylene)-co maleic anhydride (MAH-PP) (Licocene PP MA 6452—supplied by Clariant, Swiss) with a saponification value of 41 mg KOH/g, a density at 23°C of 0.93 g/m3  was used.


### 2.2. Hemp Shives-Thermoplastic Composites Manufacturing

Three formulations noted P1 (77% PP, 3% MAH-PP, 20% hemp shives); P2 (53% PP, 3% MAH-PP, 40% hemp shives); and P3 (37% PP, 3% MAH-PP, 60% hemp shives) were obtained using Brabender LabStation (Germany) with a mixer (30/50 EHT). The three components (PP, shives, and MAH-PP) were melted and mixed at 175°C, 75 rpm for 10 minutes. Before mixing, the components were dried in a vacuum oven for 24 h at 80°C. The testing specimens were obtained by pressing using a Carver 4394 press for 14 minutes (4 minutes premelting and 10 minutes pressing).


### 2.3. Mechanical Testing

In order to evaluate the effect of filler content on the mechanical properties of maleated hardwood filled PP composites, tensile and impact strength tests were performed. Five samples for each group were obtained from the manufactured composites. For the tensile test, the stress-strain measurements were performed at 23°C and 50% relative humidity on samples (1 mm thickness), with an Instron Single Column Systems tensile testing machine (model 3345) with a series IX automated materials testing system equipped with a 5 kN load cell and activated grips, which prevented slippage of the sample before the break, operated according to SR EN ISO 527-2:1996. The cross-head speed used was 30 mm/min and gauge length of 40.0 mm. The Young’s modulus, maximum tensile strength, and elongation at break were calculated from the tensile test data. The impact tests were performed according to ISO 179 (Charpy), the unnotched samples being tested on a Ceast Impact Tester. The device has a microprocessor that allows the direct calculation of resistance and potential energy of the hammer released at different starting angles. The hammer has autocalibration and enables the collection and statistical processing of data using the Visual IMPACT software. The bending tests were conducted according to ASTM D790/2002, using a Zwick/Roell Z005 testing device.


### 2.4. Weathering Procedure

All composite samples were placed in a laboratory chamber (Angellantoni Ind., Italy), to accelerate sample weathering. The samples were exposed to the artificial light of a mercury lamp (200<λ<700 nm, incident light intensity 39 m W cm−2), at a temperature of 40°C and humidity of 65%, while the exposure time was up to 600 h. The samples were removed from the chamber at intervals after 300 and 600 h of exposure, then analyzed as to chemical changes and mechanical properties and compared with the nonirradiated sample.


### 2.5. FT-IR and Raman Spectroscopies

The FT-IR spectra of the samples, in absorbance mode, were acquired using the Bruker Vertex 70 spectrophotometer (Ettlingen, Germany), equipped with the ATR (Total Attenuated Reflectance) cell on the 600–4000 cm−1 wavelength range, using a resolution of 4–30 cm−1 and 120 coadded scans. The recorded spectra were evaluated, and the area/intensity of the characteristic bands was calculated using Opus program. The Raman spectra were recorded by using a spectrometer (inVia Raman Microscope, Renishaw, Wotton-under-Edge, Gloucestershire, United Kingdom) integrated with NTEGRA Probe NanoLaboratory AFM (NT-MDT, Moscow, Russia) at ambient temperature. The Raman laser excitation beam was operated at λ=785 nm, at 100%, 50%, or 10% laser power, in single scan measurement mode. Spectra from minimum three areas for each experiment were acquired in the range of 100 to 3200 cm−1. WiRE 3.2 (Renishaw, Wotton-under-Edge, Gloucestershire, United Kingdom) and OPUS 6.5 (Bruker, Ettlingen, Germany) were used to analyze the data.


### 2.6. AFM Microscopy

NTEGRA Probe NanoLaboratory AFM (NT-MDT, Moscow, Russia), Software Nova_1644, equipped with an M Plan Apo 100x magnification objective that has the numerical aperture of 0.70 (Mitutoyo, Kawasaki, Japan) and an RPC-TVPCI camera which helps to locate the sample position were used. For storing the optical information a CCD camera was utilized. The samples were added to two-sided tape on sapphire support, and the measurements were carried out under ambient conditions (temperature:22±1°C, relative humidity: 40±10%). Semicontact “Golden” silicon cantilevers (NSG30/Au from NT-MDT, Moscow, Russia) with a resonance frequency of 320±80 kHz were used. All samples were measured in semicontact mode (“tapping” mode) to capture simultaneously topography and phase images. To obtain an overview of the samples, these were initially measured at 30×30 μm2 with resolution of 256×256 pixels. The roughness parameters such as ten point height (Sz), root mean square (Sq), and average roughness (Ra) were obtained from the full image profiles of the samples (30×30 μm2) by using ISO 4287/1 (Nova_1644).


## 2.1. Materials

The PP type J700 with a melt index 9.5 g/10 min at 230°C and density 0.912 g/cm3 was purchased by Petromidia Navodari (Romania). Hemp shives (length = 13–15 μm, thichness = 7.5–9.3 μm) are used as reinforcement in composite material. The chemical composition of hemp shives is: cellulose (46.4%), hemicelluloses (29.3%), lignin (22.5), pectin (0.9%), and waxy substances (0.8%) and was determined by TAPPI test method standards. To improve the compatibility between the polymer matrix and hemp fiber as filler, the poly (propylene)-co maleic anhydride (MAH-PP) (Licocene PP MA 6452—supplied by Clariant, Swiss) with a saponification value of 41 mg KOH/g, a density at 23°C of 0.93 g/m3  was used.


## 2.2. Hemp Shives-Thermoplastic Composites Manufacturing

Three formulations noted P1 (77% PP, 3% MAH-PP, 20% hemp shives); P2 (53% PP, 3% MAH-PP, 40% hemp shives); and P3 (37% PP, 3% MAH-PP, 60% hemp shives) were obtained using Brabender LabStation (Germany) with a mixer (30/50 EHT). The three components (PP, shives, and MAH-PP) were melted and mixed at 175°C, 75 rpm for 10 minutes. Before mixing, the components were dried in a vacuum oven for 24 h at 80°C. The testing specimens were obtained by pressing using a Carver 4394 press for 14 minutes (4 minutes premelting and 10 minutes pressing).


## 2.3. Mechanical Testing

In order to evaluate the effect of filler content on the mechanical properties of maleated hardwood filled PP composites, tensile and impact strength tests were performed. Five samples for each group were obtained from the manufactured composites. For the tensile test, the stress-strain measurements were performed at 23°C and 50% relative humidity on samples (1 mm thickness), with an Instron Single Column Systems tensile testing machine (model 3345) with a series IX automated materials testing system equipped with a 5 kN load cell and activated grips, which prevented slippage of the sample before the break, operated according to SR EN ISO 527-2:1996. The cross-head speed used was 30 mm/min and gauge length of 40.0 mm. The Young’s modulus, maximum tensile strength, and elongation at break were calculated from the tensile test data. The impact tests were performed according to ISO 179 (Charpy), the unnotched samples being tested on a Ceast Impact Tester. The device has a microprocessor that allows the direct calculation of resistance and potential energy of the hammer released at different starting angles. The hammer has autocalibration and enables the collection and statistical processing of data using the Visual IMPACT software. The bending tests were conducted according to ASTM D790/2002, using a Zwick/Roell Z005 testing device.


## 2.4. Weathering Procedure

All composite samples were placed in a laboratory chamber (Angellantoni Ind., Italy), to accelerate sample weathering. The samples were exposed to the artificial light of a mercury lamp (200<λ<700 nm, incident light intensity 39 m W cm−2), at a temperature of 40°C and humidity of 65%, while the exposure time was up to 600 h. The samples were removed from the chamber at intervals after 300 and 600 h of exposure, then analyzed as to chemical changes and mechanical properties and compared with the nonirradiated sample.


## 2.5. FT-IR and Raman Spectroscopies

The FT-IR spectra of the samples, in absorbance mode, were acquired using the Bruker Vertex 70 spectrophotometer (Ettlingen, Germany), equipped with the ATR (Total Attenuated Reflectance) cell on the 600–4000 cm−1 wavelength range, using a resolution of 4–30 cm−1 and 120 coadded scans. The recorded spectra were evaluated, and the area/intensity of the characteristic bands was calculated using Opus program. The Raman spectra were recorded by using a spectrometer (inVia Raman Microscope, Renishaw, Wotton-under-Edge, Gloucestershire, United Kingdom) integrated with NTEGRA Probe NanoLaboratory AFM (NT-MDT, Moscow, Russia) at ambient temperature. The Raman laser excitation beam was operated at λ=785 nm, at 100%, 50%, or 10% laser power, in single scan measurement mode. Spectra from minimum three areas for each experiment were acquired in the range of 100 to 3200 cm−1. WiRE 3.2 (Renishaw, Wotton-under-Edge, Gloucestershire, United Kingdom) and OPUS 6.5 (Bruker, Ettlingen, Germany) were used to analyze the data.


## 2.6. AFM Microscopy

NTEGRA Probe NanoLaboratory AFM (NT-MDT, Moscow, Russia), Software Nova_1644, equipped with an M Plan Apo 100x magnification objective that has the numerical aperture of 0.70 (Mitutoyo, Kawasaki, Japan) and an RPC-TVPCI camera which helps to locate the sample position were used. For storing the optical information a CCD camera was utilized. The samples were added to two-sided tape on sapphire support, and the measurements were carried out under ambient conditions (temperature:22±1°C, relative humidity: 40±10%). Semicontact “Golden” silicon cantilevers (NSG30/Au from NT-MDT, Moscow, Russia) with a resonance frequency of 320±80 kHz were used. All samples were measured in semicontact mode (“tapping” mode) to capture simultaneously topography and phase images. To obtain an overview of the samples, these were initially measured at 30×30 μm2 with resolution of 256×256 pixels. The roughness parameters such as ten point height (Sz), root mean square (Sq), and average roughness (Ra) were obtained from the full image profiles of the samples (30×30 μm2) by using ISO 4287/1 (Nova_1644).


## 3. Results and Discussions

### 3.1. Mechanical Properties of Composites

The results obtained for the mechanical properties of composites (P1, P2, and P3). before the weathering are depicted in Figures 1 and 2. The Young’s modulus linearly increases with the increase of the percentage of the reinforcement (Figure 1(a)). This behavior is in accordance with the data reported for other natural filler reinforced PP composites [16–18]. For PP, the initial Young’s modulus was 1.36 GPa and 1.99 GPa for the P3 composite.Young’s modulus and flexural modulus (a) and elongation of break (b).
(a)
(b)Tensile strength and flexural strength (a) and Charpy impact strength (b).
(a)
(b)The values of the flexural modulus were found to be comparable for the samples with a content of 20 and 40% hemp shives, meanwhile the flexural modulus increases with 65% for the composites containing 60% filler. The fillers generally produce a decrease of the elongation at break [19–21]. The elongation at break depends on the adhesion between the filler and the matrix and on the stiffness of the filler in the matrix. A good adhesion between the filler and the matrix causes a decrease of the elongation;  if the adhesion is poor, this property may decrease more gradually. If the filler is rigid, the elongation decreases in all cases. Our results obtained are in good agreement with these findings [22]. The increase in the content/volume fraction of filler produces a moderate increase in the tensile strength (Figure 2(a)). This behavior can be attributed to the enhancement of the cohesion at matrix/filler interface and the positive effect of MAP-PP on the tensile strength in P1 and P2 composites. P3 exhibits a tensile strength similar to the tensile strength of PP due to the high content of hemp shives which diminishes the positive effect of MAP-PP.The flexural strength in contrast with the tensile strength increases with 23, 39, and 79% for the formulations composites containing 20, 40, and 60 wt % of hemp shives. As it is shown in Figure2(b), the Charpy impact strength for unnotched testing specimens decreases with the increase of the filler content, and in the meantime the Young Modulus and flexural modulus increase.


### 3.2. Study Regarding the Weathering Behavior of Composites

The FT-IR spectra for PP and P3 composite before and after the weathering displayed different bands, characteristic of the main components of the studied systems (Figure 3).Figure 3
FT-IR spectra recorded for PP (blue) (a); P3-no UV (green) (b); P3-UV 300 h (red) (c); and P3-UV 600 h (pink) (d).The samples P3 contain the characteristic bands of celluloses from hemp shives and PP. In the range of stretching vibrations of OH group, there is a broad band (between 3200–3600 cm−1) with a maximum peak around 3348 cm−1, which is attributed to hydroxyl group stretching vibrations belonging to the filler. Peaks around 1041 cm−1 were assigned to C–O groups (assigned for cellulose, hemicellulose, and lignin from hemp) [23, 24]. The triplet like bands from 2953 cm−1 are due to symmetrical and asymmetrical C–H stretching vibrations of CH2 and CH3 in the PP chain; the absorbance bands from 1455 and 1376 cm−1 are form C–H deformation vibrations attributable to the asymmetry stretching vibration of CH2 and the symmetry bending vibration of CH3, and the band at 1160 cm−1 is associated with rocking vibrations of CH2 and CH3, or C=C stretching vibrations from the polyolefin chain [25, 26]. After the exposure to UV radiation, the main components of composites, booth hemp shives, and PP were susceptible to weathering. The photodegradation of PP is mainly due to chain scission by oxidation which results in a decrease of the molecular weight and the change of matrix crystallinity. The lignin is the main component of hemp responsible for UV degradation because it contains choromphores [27, 28]. Similar to the photodegradation of PP, the photodegradation of lignin is a radical-based oxidative process. The spectral features assigned to hemp lignin (1595 and 1505 cm−1) decreased in intensity as a function of weathering. The band at 1718 cm−1 was attributed to the C=O stretching of oxidized chain terminals and oxidation products increased upon weathering. The structural changes produced in the matrix after weathering were investigated by observing vinyl and carbonyl groups formation in composite samples. The carbonyl index, as well as the vinyl index, has been calculated with the following formula [29] from data obtained after recording FT-IR spectra of the composite samples:
(1)carbonylindex=I1718I2912,vinylindex=I908I2912,
where I represents peak intensity. The peak intensities were normalized using the peak at 2912 cm−1, which corresponds to alkane CH stretching vibrations of the methylene groups. This peak was selected as a reference because it changed the least during weathering. The isotacticity index was calculated from the Raman spectra as the ratio between the areas located at 816 and 980 cm−1 [30] for the composite samples. The values of the carbonyl, vinyl group, and isotactic index in the studied samples during controlled weathering are presented in Table 1.Table 1
Carbonyl, vinyl and isotactic indexes of unweathered and weathered  PP-hemp shives composites.
Sample
Carbonyl index
Vinyl index
Isotactic index
P1 (no UV)
0.157
0.094
1.0
P1 (UV 300 h)
0.333
0.125
0.6
P1 (UV 600 h)
0.510
0.131
0.4FT-IR spectroscopy was used to demonstrate the occurrence of surface oxidation of the samples through the investigation of carbonyl groups change, and its index is the most used parameter to evaluate the extent of degradation of PP [31]. The increase in the carbonyl groups formation for composites after weathering is known to be proportional to the number of chain scissions occurring in PP [32]. These results indicate that chain scission may have occurred upon exposure and that the number of chain scissions and, respectively, surface oxidation for PP-based hemp composites increased at 600 h exposure time. Similarly with carbonyl groups formation, vinyl groups formation is indicative of scission of PP or hemp polymer chain. The formation of C=O groups in various oxidized products can be explained by the mechanism represented by the Norrish type I and II reactions [33]. There are three main Raman lines in the 300–500 cm−1 Raman spectral domain which were assigned to PP: 325 cm−1, 404 cm−1, and 465 cm−1. The most intense line, located at about 400 cm−1, has been appointed to the umbrella bending mode about the tertiary carbon atom. The last line has been assigned to wagging CH2 and bending CH. The Raman lines of PP from the composites after UV exposure presented a weak shift towards larger values and are more broaden, suggesting a drop of the degree of crystallinity of PP after artificial degradation [34, 35]. The degree of crystallinity of composites decreased after UV exposure for 300 h and 600 h, as it has been demonstrated by Raman spectra.


### 3.3. AFM Microscopy

AFM is recently widely used to determine the morphology of the surfaces of composite materials obtained as films (e.g., carbon nanotubes, chitosan films) or other types of materials such as composites used in aircraft industry and automotive, in medical technologies (e.g., dentines) [36]. Figure 4 exhibits representative AFM images of the composite containing hemp shives and PP recorded in a semicontact (tapping) mode. The magnitude of cantilever oscillation during scanning is shown in Figure 4 and provides additional contrast to the data analyzed from the height image profiles of the samples exhibited in Table 2.Table 2
Roughness parameters calculated from three different AFM height images from the same sample (30×30 μm2).
Sample
Ten point height, Sz (nm)
Root mean square, Sq (nm)
Average roughness, Ra (nm)
P3
4553.47 ± 282.97
1137.54 ± 151.18
913.18 ± 141.61
P3 (UV 300 h)
2988.60 ± 87.83
722.58 ± 116.23
568.97 ± 112.58
P3 (UV 600 h)
2352.06 ± 876.41
650.28 ± 170.49
516.55 ± 142.70AFM images of composites: (a) 2D, (b) 3D, (c) phase contrast images of P3, (d) 2D, (e) 3D, (f) phase contrast images of P3 after 300 h exposure at UV, (g) 2D, and (h) 3D, (i) phase contrast images of P3 after 600 h exposure at UV. Images were recorded on semicontact (tapping) mode (30×30 μm2) with resolution of  256×256 pixels.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)
(i)The phase images exhibit a rich structure and allow envisioning the fine microfibrils of cellulose and the amorphous deposits of lignin (luminous areas). The composite samples showed decrease in roughness parameters after UV degradation with 36% for the ten point height (Sz) and approximately 43% for root mean square (Sq) and average roughness (Ra), demonstrating the high deviation of the peaks and valleys from the mean line. It is clearly noted that nanofibrils from hemp shives aggregated in the polymer matrix of PP and MAP-PP and led to homogeneous composite, which became smoother and lighter in colour after aging, as can be seen by eyes also, probably due to PP degradation.The values of roughness parameters, such as root mean square, are decreasing after the aging of the composites, which is in good agreement with FT-IR and Raman data.Based on these results, we can conclude that hemp shives are suitable to be mixed with PP and to obtain homogenous composites that modestly alter with aging.


### 3.4. Mechanical Properties after Weathering

The degradation processes due to the weathering usually affect both the chemical and mechanical properties of the composites. Figures5 and 6 show the mechanical properties as a function of weathering time for P3.Charpy impact strength (a) and tensile strength (b).
(a)
(b)Young’s modulus (a) and elongation at break (b).
(a)
(b)The loss of mechanical properties was found to be due to the degradation of all main polymeric components of the composites, such as cellulose, hemicelluloses, lignin, and PP chain scission leading to the formation of sufficient amount of carboxyl and vinyl groups with the concomitant decrease in the molecular weight [37, 38]. The impact strength (Figure 5(a)) shows a decrease from 7.49 kJ/m2 to 3.74 kJ/m2, after 600 hours of exposure. The rigidity decreases with increasing of the exposure time, so that the modulus of elasticity is higher after 600 h of exposure. After UV exposure, the tensile strength decreases (Figure 5(b)) due to the effects of polymer degradation and can be attributed to the photooxidation of PP and lignin from hemp shives. Reduction of elongation at break can be a good indicator to monitor the ageing of polymers [39, 40].The elongation at break value of the PP sample is significantly higher than that of the composite samples because the composites are more brittle. The elongation at break for P3 drops to 20% of the initial value after exposure to UV for 600 h (Figure 6(b)). The decline in elongation at break with the increasing of the exposure time of P3 to UV treatment is caused by an extensive chain scission of PP in the sample.


## 3.1. Mechanical Properties of Composites

The results obtained for the mechanical properties of composites (P1, P2, and P3). before the weathering are depicted in Figures 1 and 2. The Young’s modulus linearly increases with the increase of the percentage of the reinforcement (Figure 1(a)). This behavior is in accordance with the data reported for other natural filler reinforced PP composites [16–18]. For PP, the initial Young’s modulus was 1.36 GPa and 1.99 GPa for the P3 composite.Young’s modulus and flexural modulus (a) and elongation of break (b).
(a)
(b)Tensile strength and flexural strength (a) and Charpy impact strength (b).
(a)
(b)The values of the flexural modulus were found to be comparable for the samples with a content of 20 and 40% hemp shives, meanwhile the flexural modulus increases with 65% for the composites containing 60% filler. The fillers generally produce a decrease of the elongation at break [19–21]. The elongation at break depends on the adhesion between the filler and the matrix and on the stiffness of the filler in the matrix. A good adhesion between the filler and the matrix causes a decrease of the elongation;  if the adhesion is poor, this property may decrease more gradually. If the filler is rigid, the elongation decreases in all cases. Our results obtained are in good agreement with these findings [22]. The increase in the content/volume fraction of filler produces a moderate increase in the tensile strength (Figure 2(a)). This behavior can be attributed to the enhancement of the cohesion at matrix/filler interface and the positive effect of MAP-PP on the tensile strength in P1 and P2 composites. P3 exhibits a tensile strength similar to the tensile strength of PP due to the high content of hemp shives which diminishes the positive effect of MAP-PP.The flexural strength in contrast with the tensile strength increases with 23, 39, and 79% for the formulations composites containing 20, 40, and 60 wt % of hemp shives. As it is shown in Figure2(b), the Charpy impact strength for unnotched testing specimens decreases with the increase of the filler content, and in the meantime the Young Modulus and flexural modulus increase.


## 3.2. Study Regarding the Weathering Behavior of Composites

The FT-IR spectra for PP and P3 composite before and after the weathering displayed different bands, characteristic of the main components of the studied systems (Figure 3).Figure 3
FT-IR spectra recorded for PP (blue) (a); P3-no UV (green) (b); P3-UV 300 h (red) (c); and P3-UV 600 h (pink) (d).The samples P3 contain the characteristic bands of celluloses from hemp shives and PP. In the range of stretching vibrations of OH group, there is a broad band (between 3200–3600 cm−1) with a maximum peak around 3348 cm−1, which is attributed to hydroxyl group stretching vibrations belonging to the filler. Peaks around 1041 cm−1 were assigned to C–O groups (assigned for cellulose, hemicellulose, and lignin from hemp) [23, 24]. The triplet like bands from 2953 cm−1 are due to symmetrical and asymmetrical C–H stretching vibrations of CH2 and CH3 in the PP chain; the absorbance bands from 1455 and 1376 cm−1 are form C–H deformation vibrations attributable to the asymmetry stretching vibration of CH2 and the symmetry bending vibration of CH3, and the band at 1160 cm−1 is associated with rocking vibrations of CH2 and CH3, or C=C stretching vibrations from the polyolefin chain [25, 26]. After the exposure to UV radiation, the main components of composites, booth hemp shives, and PP were susceptible to weathering. The photodegradation of PP is mainly due to chain scission by oxidation which results in a decrease of the molecular weight and the change of matrix crystallinity. The lignin is the main component of hemp responsible for UV degradation because it contains choromphores [27, 28]. Similar to the photodegradation of PP, the photodegradation of lignin is a radical-based oxidative process. The spectral features assigned to hemp lignin (1595 and 1505 cm−1) decreased in intensity as a function of weathering. The band at 1718 cm−1 was attributed to the C=O stretching of oxidized chain terminals and oxidation products increased upon weathering. The structural changes produced in the matrix after weathering were investigated by observing vinyl and carbonyl groups formation in composite samples. The carbonyl index, as well as the vinyl index, has been calculated with the following formula [29] from data obtained after recording FT-IR spectra of the composite samples:
(1)carbonylindex=I1718I2912,vinylindex=I908I2912,
where I represents peak intensity. The peak intensities were normalized using the peak at 2912 cm−1, which corresponds to alkane CH stretching vibrations of the methylene groups. This peak was selected as a reference because it changed the least during weathering. The isotacticity index was calculated from the Raman spectra as the ratio between the areas located at 816 and 980 cm−1 [30] for the composite samples. The values of the carbonyl, vinyl group, and isotactic index in the studied samples during controlled weathering are presented in Table 1.Table 1
Carbonyl, vinyl and isotactic indexes of unweathered and weathered  PP-hemp shives composites.
Sample
Carbonyl index
Vinyl index
Isotactic index
P1 (no UV)
0.157
0.094
1.0
P1 (UV 300 h)
0.333
0.125
0.6
P1 (UV 600 h)
0.510
0.131
0.4FT-IR spectroscopy was used to demonstrate the occurrence of surface oxidation of the samples through the investigation of carbonyl groups change, and its index is the most used parameter to evaluate the extent of degradation of PP [31]. The increase in the carbonyl groups formation for composites after weathering is known to be proportional to the number of chain scissions occurring in PP [32]. These results indicate that chain scission may have occurred upon exposure and that the number of chain scissions and, respectively, surface oxidation for PP-based hemp composites increased at 600 h exposure time. Similarly with carbonyl groups formation, vinyl groups formation is indicative of scission of PP or hemp polymer chain. The formation of C=O groups in various oxidized products can be explained by the mechanism represented by the Norrish type I and II reactions [33]. There are three main Raman lines in the 300–500 cm−1 Raman spectral domain which were assigned to PP: 325 cm−1, 404 cm−1, and 465 cm−1. The most intense line, located at about 400 cm−1, has been appointed to the umbrella bending mode about the tertiary carbon atom. The last line has been assigned to wagging CH2 and bending CH. The Raman lines of PP from the composites after UV exposure presented a weak shift towards larger values and are more broaden, suggesting a drop of the degree of crystallinity of PP after artificial degradation [34, 35]. The degree of crystallinity of composites decreased after UV exposure for 300 h and 600 h, as it has been demonstrated by Raman spectra.


## 3.3. AFM Microscopy

AFM is recently widely used to determine the morphology of the surfaces of composite materials obtained as films (e.g., carbon nanotubes, chitosan films) or other types of materials such as composites used in aircraft industry and automotive, in medical technologies (e.g., dentines) [36]. Figure 4 exhibits representative AFM images of the composite containing hemp shives and PP recorded in a semicontact (tapping) mode. The magnitude of cantilever oscillation during scanning is shown in Figure 4 and provides additional contrast to the data analyzed from the height image profiles of the samples exhibited in Table 2.Table 2
Roughness parameters calculated from three different AFM height images from the same sample (30×30 μm2).
Sample
Ten point height, Sz (nm)
Root mean square, Sq (nm)
Average roughness, Ra (nm)
P3
4553.47 ± 282.97
1137.54 ± 151.18
913.18 ± 141.61
P3 (UV 300 h)
2988.60 ± 87.83
722.58 ± 116.23
568.97 ± 112.58
P3 (UV 600 h)
2352.06 ± 876.41
650.28 ± 170.49
516.55 ± 142.70AFM images of composites: (a) 2D, (b) 3D, (c) phase contrast images of P3, (d) 2D, (e) 3D, (f) phase contrast images of P3 after 300 h exposure at UV, (g) 2D, and (h) 3D, (i) phase contrast images of P3 after 600 h exposure at UV. Images were recorded on semicontact (tapping) mode (30×30 μm2) with resolution of  256×256 pixels.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)
(i)The phase images exhibit a rich structure and allow envisioning the fine microfibrils of cellulose and the amorphous deposits of lignin (luminous areas). The composite samples showed decrease in roughness parameters after UV degradation with 36% for the ten point height (Sz) and approximately 43% for root mean square (Sq) and average roughness (Ra), demonstrating the high deviation of the peaks and valleys from the mean line. It is clearly noted that nanofibrils from hemp shives aggregated in the polymer matrix of PP and MAP-PP and led to homogeneous composite, which became smoother and lighter in colour after aging, as can be seen by eyes also, probably due to PP degradation.The values of roughness parameters, such as root mean square, are decreasing after the aging of the composites, which is in good agreement with FT-IR and Raman data.Based on these results, we can conclude that hemp shives are suitable to be mixed with PP and to obtain homogenous composites that modestly alter with aging.


## 3.4. Mechanical Properties after Weathering

The degradation processes due to the weathering usually affect both the chemical and mechanical properties of the composites. Figures5 and 6 show the mechanical properties as a function of weathering time for P3.Charpy impact strength (a) and tensile strength (b).
(a)
(b)Young’s modulus (a) and elongation at break (b).
(a)
(b)The loss of mechanical properties was found to be due to the degradation of all main polymeric components of the composites, such as cellulose, hemicelluloses, lignin, and PP chain scission leading to the formation of sufficient amount of carboxyl and vinyl groups with the concomitant decrease in the molecular weight [37, 38]. The impact strength (Figure 5(a)) shows a decrease from 7.49 kJ/m2 to 3.74 kJ/m2, after 600 hours of exposure. The rigidity decreases with increasing of the exposure time, so that the modulus of elasticity is higher after 600 h of exposure. After UV exposure, the tensile strength decreases (Figure 5(b)) due to the effects of polymer degradation and can be attributed to the photooxidation of PP and lignin from hemp shives. Reduction of elongation at break can be a good indicator to monitor the ageing of polymers [39, 40].The elongation at break value of the PP sample is significantly higher than that of the composite samples because the composites are more brittle. The elongation at break for P3 drops to 20% of the initial value after exposure to UV for 600 h (Figure 6(b)). The decline in elongation at break with the increasing of the exposure time of P3 to UV treatment is caused by an extensive chain scission of PP in the sample.


## 4. Conclusions

The mechanical properties are determined by the content of hemp shives in the composite materials. With the increasing of the content of hemp shives, the tensile strength increases up to an optimal value of hemp shive’s content (40%); after this value, it decreases. The decrease of the tensile strength is due to the formation of particles agglomerations after the filler exceeds the optimal filler content value. The flexural strength, flexural modulus, and Young’s modulus increase with the increasing of the content of hemp shives in the composites. The increasing of the content of hemp shives in the composites produced the decreasing of the impact strength. Also compared with the mechanical properties of the PP used as matrix, the mechanical properties of the analyzed composites are better except the impact strength and elongation at break.The artificial weathering process by exposing the composites containing 60% hemp shives to UV radiation showed structural and morphological changes which affected their the mechanical properties. The impact strength, tensile strength, and elongation at break of the composite decrease if the time of the weathering process increases. The stiffness of the composites increases with the increasing of the artificial weathering time. FT-IR and RAMAN spectroscopies revealed the increase of the carbonyl and vinyl groups content and also crystallinity modifications during the aging process. The AFM microscopy confirms that the process of accelerated photochemical degradation occurs in a first stage at the surface of the composite.Polypropylene-hemp shives composites have several advantages: light weight, low cost, reasonable strength and stiffness, recyclability, and biodegradability and can be processed using thermoplastic forming techniques. These composites may be used in processed by extrusion-forming to produce various items, such as floor boards for outdoor deck floors, railing, fencing, and garden furniture.



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*Source: 343068-2013-08-27.xml*