# Plasma Treatment ofAgave Fiber Powder and Its Effect on the Mechanical and Thermal Properties of Composites Based on Polyethylene

Authors: Florentino Soriano Corral; Luis Antonio Calva Nava; Ernesto Hernández Hernández; José Francisco Hernández Gámez; María Guadalupe Neira Velázquez; María Isabel Montalvo Sierra; Pablo González Morones; Ramón Enrique Díaz De León Gómez
Journal: International Journal of Polymer Science
 (2016)

---

## Abstract

Composites based on low-density polyethylene (LDPE) were prepared withAgave fiber powder (AFP) that was coated by plasma polymerization process using ethylene gas. Treated and pristine AFP were analyzed by infrared spectroscopy, scanning electron microscopy, and contact water angle for the assessment of surface properties. The polymer composites were prepared by melt mixing using 0, 5, 10, and 20 wt% of AFP and their mechanical and thermal properties were measured. Dispersion evaluation in water confirmed that the AFP treated changed from hydrophilic to hydrophobic behavior and it was also corroborated with water contact angle tests. The addition of treated and untreated AFP (200 mesh) at 20 wt% promotes an increase of Young’s modulus of the composites of up to 60% and 32%, respectively, in relation to the neat matrix. Also, an increase of crystallinity of LDPE was observed by the addition of treated and untreated AFP; however no significant effect on the crystallization temperature was observed in LDPE containing AFP.


---

## Body

## 1. Introduction

Natural fibers are suitable materials to reinforce synthetic polymers, such as thermosets and thermoplastics, because they exhibit a relatively high strength, high stiffness, and low density [1]. These fibers are biodegradable and are available from a renewable source and have special advantages in comparison with other synthetic fibers. A large variety of natural fibers are available around the world, but they are not compatible with most polymers and as a consequence they require a chemical or physical treatment in order to promote interfacial interactions with the polymer matrices.Agave tequilanaWeberazul is an economically important specie cultivated in Mexico and is the only one of the species ofAgavaceae that is appropriate for the production of tequila. After the juice extraction process is carried out, fibers fromAgave are disposed and they become a serious waste problem. From the total wet weight of the agave plant, 54% represents the agave head, which is the raw material for tequila production; the rest of the wet plant (46%) is not used and typically it is left in the fields and became a potential source of mosquito breeding [2]. In the year 2013 the production ofAgave to extract tequila was 756,900 tons [3] and approximately 60% of this amount was discarded.Several researchers have been studying the use of agave fibers (AF) as reinforcement in some polymeric matrices. For example, Aranda and coworkers studied the behavior of composites based on thermoplastic starch with different contents of agave bagasse fibers (0–15 wt%) and polylactic acid (PLA). The results showed that thermoplastic starch hygroscopicity decreased as PLA and fiber content increased. Storage, stress-strain, and flexural modulus increased with PLA and/or agave bagasse fibers content, while the impact resistance decreased [4]. In another study conducted by Singha and coworkers, they modified AF and mixed it with a polystyrene matrix. The effect of different fiber dimensions (particles, short and long fibers) on the mechanical properties of the composites was also investigated herein. Particles of fibers give better mechanical properties than short and long fibers [5]. In other work, AF were modified by maleic anhydride grafted polyethylene and mixed with LDPE. It was found that tensile and flexural modulus increased with treated AF concentration, while the impact strength of the composites decreased [6]. Guzmán and coworkers also prepared composites based on LDPE with AF at contents of 5, 10, and 20 wt% and processed the composites at several temperature profiles; their results showed that Young’s modulus of the composites increased with fiber content but decreased linearly with the increment of processing temperatures due to the fiber degradation [7].The application of natural fillers can be seen as an approach to adjust material performance of polymer composites assuming that filler/matrix interactions will be optimized and a hygroscopicity of natural fillers will be hindered. Plasma technology has demonstrated its potential to modify the surface properties of polymers, nanoparticles, and natural fibers among others [8–10]. Previously, different authors had reported the advantages of plasma treatment in natural fibers to improve their interfacial adhesion with different polymers [11]. For example, argon and air plasma treatment improve the compatibility between wood fibers (20 wt%) and polypropylene increasing the tensile strength and Young’s modulus in 13% and 150%, respectively, due to oxygen groups deposited on the surface of wood fibers during plasma treatment [12]. Other authors used oxygen plasma treatment to modify the surface of jute fiber and they found a direct dependence of the plasma power conditions on the interfacial adhesion of the fiber with high density polyethylene (HDPE). For example, when the jute fabric was treated at a plasma power of 30 W, the flexural strength increased up to a value of 39.7 MPa. Increasing the plasma power to 60 W resulted in greatest flexural strength (45.6 MPa) value, in relation to the value of HDPE/untreated jute composites (31.4 MPa) [13]. When a monomer like styrene was used to plasma-treat the surface of cellulose fibers for 4 minutes, Young’s modulus of the composites increased in about 44% and the treatment promoted the compatibility with polystyrene due to the plasma coating of styrene monomer deposited at the surface of cellulose fibers [14]. In the same way, in our previous work [15] we obtained an increase in Young’s modulus up to 60% in composites based polyethylene as a result of the surface modification of agave fibers by ethylene plasma; a good dispersion and compatibility were observed in the composites. The treatment of natural fibers by plasma polymerization process also could reduce the humidity absorption of the fibers, and this is an important issue to use the natural fibers for different applications.The aim of the present work is to study systematically the effect of treatment of AFP by ethylene plasma on the mechanical and thermal properties in polymer composites based on low-density polyethylene.


## 2. Experimental

### 2.1. Materials

LDPE (PX 20020 P) with a density of 0.92 g/cm3 and a melt flow index of 0.2 g/10 min was supplied by Petroleos Mexicanos (PEMEX).Agave fiber (AF) was provided by Solyagave S. A. de C. V, and to obtainAgave fiber powder (AFP), AF was grinded and separated in sieves of 200 and 325 mesh by Ro-tap test sieve shaker. The contents ofAgave fiber powder used in the polymer composites were 5, 10, and 20 wt%. The ethylene gas monomer used for the plasma polymerization process was kindly supplied by Infra (Mexico).


### 2.2. Plasma Treatment

The plasma treatment of the AFP was carried out in a round bottom flask (500 mL) with a copper wire coiled around the wall of the flask, acting as an inductive electrode. One of the ends of the copper wire was connected to a radio frequency generator (Advanced Energy RFX600). The plasma treatment of AFP was carried out as follows: 7 g of AFP and a magnetic stirrer were introduced into the round bottom flask, which was then connected to the vacuum system. The initial internal pressure in the flask was 28 Pa. During the plasma treatment, the ethylene gas flow rate was fixed at 0.16 cm3 min−1 while the internal pressure was increased to 50 Pa. The plasma process conditions were 40 W of input plasma power and 60 min of treatment time. More details of this plasma reactor can be found in [16].


### 2.3. Formulation of Polymer Blends

The composites were prepared in a Brabender plasticorder mixing chamber (75 cm3) with a CAM type rotor, and the blends were prepared at 60 rpm and 160°C for 15 min. First, LDPE was placed in the heated chamber; then the AFP were added and mixed for 15 min.


### 2.4. Specimen Preparation

For the mechanical tests, samples with a thickness of 2 mm were prepared by compression molding in a PHI thermal hot platens model Q230H-X4A at 160°C and a load of 20 ton and were cooled under the same pressure conditions by circulating water through the platens.The mechanical tests were carried out in accordance with ASTM D-638, in a SMF-120 tensile apparatus, using a strain rate of 50 mm/min at 25°C. Six specimens per experiment were previously conditioned at 23 ± 2°C for 40 h, at 50 ± 5% of relative humidity.The grinded AF with and without plasma treatment was analyzed by infrared spectroscopy using a PerkinElmer FTIR spectrometer, coupled to an attenuated total reflectance unit (ATR-IR). The infrared analyses were performed with a resolution of 4 cm−1 and 20 scans.Differential scanning calorimetry (DSC) analyses of composites were carried out in an equipment (Discovery Series) from TA instruments, at a heating rate of 10°C min−1 in a temperature interval from 0 to 200°C, in a nitrogen atmosphere with a flow rate of 50 mL/min. The degree of crystallinity (in percentage) of the LDPE was determined using(1)
X
c
=
Δ
H
m
∗
Δ
H
m
1
-
∅
×
100
,where Δ
H
m
∗ is the fusion enthalpy of the composite determined by DSC, Δ
H
m is the enthalpy of the PE with a crystallinity of 100% that is reported as 293 J g−1 [17], and “∅” is the weight fraction of the dispersed phase in the composite.The morphology of the composites was determined using a Topcon SM510 scanning electron microscope (SEM). The samples were cryogenically fractured, and previous to the analysis, samples were coated with Au-Pd to reduce the charge effect.


## 2.1. Materials

LDPE (PX 20020 P) with a density of 0.92 g/cm3 and a melt flow index of 0.2 g/10 min was supplied by Petroleos Mexicanos (PEMEX).Agave fiber (AF) was provided by Solyagave S. A. de C. V, and to obtainAgave fiber powder (AFP), AF was grinded and separated in sieves of 200 and 325 mesh by Ro-tap test sieve shaker. The contents ofAgave fiber powder used in the polymer composites were 5, 10, and 20 wt%. The ethylene gas monomer used for the plasma polymerization process was kindly supplied by Infra (Mexico).


## 2.2. Plasma Treatment

The plasma treatment of the AFP was carried out in a round bottom flask (500 mL) with a copper wire coiled around the wall of the flask, acting as an inductive electrode. One of the ends of the copper wire was connected to a radio frequency generator (Advanced Energy RFX600). The plasma treatment of AFP was carried out as follows: 7 g of AFP and a magnetic stirrer were introduced into the round bottom flask, which was then connected to the vacuum system. The initial internal pressure in the flask was 28 Pa. During the plasma treatment, the ethylene gas flow rate was fixed at 0.16 cm3 min−1 while the internal pressure was increased to 50 Pa. The plasma process conditions were 40 W of input plasma power and 60 min of treatment time. More details of this plasma reactor can be found in [16].


## 2.3. Formulation of Polymer Blends

The composites were prepared in a Brabender plasticorder mixing chamber (75 cm3) with a CAM type rotor, and the blends were prepared at 60 rpm and 160°C for 15 min. First, LDPE was placed in the heated chamber; then the AFP were added and mixed for 15 min.


## 2.4. Specimen Preparation

For the mechanical tests, samples with a thickness of 2 mm were prepared by compression molding in a PHI thermal hot platens model Q230H-X4A at 160°C and a load of 20 ton and were cooled under the same pressure conditions by circulating water through the platens.The mechanical tests were carried out in accordance with ASTM D-638, in a SMF-120 tensile apparatus, using a strain rate of 50 mm/min at 25°C. Six specimens per experiment were previously conditioned at 23 ± 2°C for 40 h, at 50 ± 5% of relative humidity.The grinded AF with and without plasma treatment was analyzed by infrared spectroscopy using a PerkinElmer FTIR spectrometer, coupled to an attenuated total reflectance unit (ATR-IR). The infrared analyses were performed with a resolution of 4 cm−1 and 20 scans.Differential scanning calorimetry (DSC) analyses of composites were carried out in an equipment (Discovery Series) from TA instruments, at a heating rate of 10°C min−1 in a temperature interval from 0 to 200°C, in a nitrogen atmosphere with a flow rate of 50 mL/min. The degree of crystallinity (in percentage) of the LDPE was determined using(1)
X
c
=
Δ
H
m
∗
Δ
H
m
1
-
∅
×
100
,where Δ
H
m
∗ is the fusion enthalpy of the composite determined by DSC, Δ
H
m is the enthalpy of the PE with a crystallinity of 100% that is reported as 293 J g−1 [17], and “∅” is the weight fraction of the dispersed phase in the composite.The morphology of the composites was determined using a Topcon SM510 scanning electron microscope (SEM). The samples were cryogenically fractured, and previous to the analysis, samples were coated with Au-Pd to reduce the charge effect.


## 3. Results and Discussion

### 3.1. Infrared Spectroscopy Analysis of AFP

Figure1 shows the ATR-IR spectrum of the AFP unmodified (Figure 1(A)) as well as the ATR-IR spectrum of AFP modified by plasma (Figure 1(B)). The first broad band located at 3400 cm−1 is due to the stretching vibrations of hydroxyl groups from the cellulose present in the AFP; the band located at 2920 cm−1 is related to C-H stretching of the aliphatic methylene groups [18]. The weak peak at 1730 cm−1 is attributed to hemicellulose, associated with the C=O stretching in nonconjugated ketones, ester groups, and carbonyls [19]. The band located at 1640 cm−1 is attributed to the C=O stretching vibration and the C=C stretching vibration from alkenes groups and aromatic compounds [20]. Aromatic structure vibration from lignin and lignocellulose presents a band between 1510 and 1520 cm−1 [21]. Peaks at 1250 and 1000 cm−1 are related to C-O-C and C-O stretching vibrations on the cellulose chain bone [22]. Finally, the band at 1080 cm−1 associated with the stretch vibration of C-O is attributed to polysaccharides and hemicelluloses as reported previously by Grube and Bodirlau, respectively [23, 24].Figure 1
FTIR spectra of (A) pristine AFP and (B) AFP modified by plasma.In relation to the plasma treated AFP, the same infrared signals were observed in both fibers (pristine and coated). Typically, the amount of these plasma films on the surface of materials is lower than 5 wt% in relation to the substrate, and therefore it is difficult to observe infrared signals of the deposit, since it is beyond the limit of detection of FTIR. Another reason is that the films synthesized by plasma polymerization present a low relation H/C (aprox 1.49) against monomer (2) as has been shown previously by other authors [25], and this fact suggests that the polymeric nanofilm has a highly crosslinked structure and therefore a difference between two spectral signals cannot be seen.In literature, it has been reported that the plasma treatment polymer or plasma coating suffers a partial oxidation due to a reaction with atmospheric oxygen or water vapor after removal of the treated substrate from the vacuum chamber or even with oxygen dissolved in the monomers [25, 26]. These signals associated with the oxidation of polymer films deposited on the surface of the fiber powder by plasma were not detected by infrared due to possible overlap with bands of the AFP.The change on the surface characteristics of AFP after the plasma treatment was measured qualitatively through water dispersion tests in water. The untreated AFP are very well dispersed in water (see Figure2, left) and this behavior is due to the polar groups present in cellulose, which promotes the hydrophilic character of AFP. Meanwhile, plasma treated AFP remains on the water surface up to 2 months indicating that the fibers have a hydrophobic behavior (Figure 2, right). The above can be explained by the presence of a plasma polyethylene thin film coating located at the AFP surface, which inhibits the interaction between the surface of treated AFP and water. This kind of polymeric layer had been reported by several researchers, who have demonstrated that the presence of the plasma polymer at the surface of a substrate reduces the moisture and oxygen permeability, both of which are related to the density and structure of the plasma polymer thin film coatings [27, 28]. The cross-linked structure of polyethylene synthesized by plasma and its low concentration of oxygen in their structure could explain the long time stability of the hydrophobic behavior of treated AFP.Figure 2
Dispersion test of AFP in water. Left: untreated AFP; right: plasma treated AFP (hydrophobic behavior of the plasma treated samples remains upon two months).Another evidence that corroborated the hydrophobic character of the plasma treated AFP was the contact angle measurement and it was 75° approximately. In case of the untreated AFP no contact angle was formed due to the fast absorption of water drop by the agave fibers indicating thus their hydrophilic behavior. It is well known that plasma treatments can change the polarity of several types of fibers and improve their compatibility towards different polymer matrix [29]; this indicates that plasma treatment with ethylene reduces the surface energy, and thus the treated fibers present lower wettability than pristine fibers; also the film coating deposited on the fibers presents low polarity.


### 3.2. Mixing Torque

The torque-time curves during the preparation of the composites in melt state are presented in Figure3; at LDPE feeding, an increase in the torque value of up to 20 Nm can be identified; then it diminished to 10 Nm at 2 min, and it lastly is associated with the melting of LDPE pellets. In the interval from 4 to 6 min there was some increase of the values of torque associated with the addition of the AFP. This means that the presence of AFP increases the melt viscosity of the mixture. After 6 min, the intermolecular forces and physical entanglement between the adjacent molecules decrease, and an equilibrium value (obtained at 12 min) for a torque of 6.09 ± 0.09 Nm was achieved for LDPE; meanwhile the torque values for the blends with 10 wt% of AFP (200 mesh) modified (MPF-10-M200) and unmodified (NMF-10-M200) were 7.59 ± 0.02 and 7.08 ± 0.02 Nm, respectively. The slightly higher value of torque in MPF-10-M200 in relation to NMF-10-M200 is attributed to the higher interactions between melt molecules of LDPE and plasma treated AFP. The same behavior is presented at higher contents of AFP; higher values of torque were observed for the blends containing 20 wt% of AFP (200 mesh) in relation to those contained 10 wt% and the values were 8.36 ± 0.04 and 8.19 ± 0.02 for the blends with 20 wt% of AFP modified (MPF-20-M200) and unmodified (NMF-20-M200), respectively.Figure 3
Torque-time curves of the blends containing 10 wt% of unmodified and plasma treated AFP.


### 3.3. Mechanical Properties

The stress-strain diagrams of the composites of LDPE/AFP are presented in Figure4. A typical behavior was observed for LDPE with elongation break up of 450% and the corresponding tensile stress of 13 MPa. The addition of AFP modified or unmodified promotes an increase in the tensile stress and a gradual decrease of the elongation at break as can be observed in Figure 4. However, the formulations containing AFP (200 mesh) modified by plasma at 5 wt% (MPF-5-M200) and at 20 wt% (MPF-20-M200) further improve the tensile stress but present lower values of elongation percent than the composites with untreated AFP at 5 (NMF-5-M200) and 20 wt% (NMF-20-M200). This behavior is due to the fact that the ethylene plasma treated AFP enhances the interfacial adhesion with the polyethylene matrix.Figure 4
Tensile stress-strain curves of the blends containing 5 and 20 wt% of AFP unmodified and modified by plasma.Young’s modulus behavior as a function of the AFP content is presented in Figure5. In a general way, the addition of untreated and treated AFP improves Young’s modulus, but this improvement is higher for composites containing treated AFP (values higher than 10 wt%). The composite with 20 wt% of AFP (200 mesh) labeled as MPF-M200 presented an increase of 21.7% in Young’s modulus with respect to the composite at the same content of fiber (20 wt%) unmodified (NMF-M200). This behavior could be explained by an increase in the interactions between the treated surface of AFP and the polyethylene matrix.Figure 5
Young’s modulus of the composites base of LDPE and AFP modified and unmodified.As a function of the size (200 to 325 mesh) of the AFP modified (MPF-M325) and unmodified (NMF-M325), there is no significant difference in Young’s modulus of the composites especially at contents of AFP lower than 10 wt%. Other authors obtained similar results previously, where plasma treatments with argon and air were used to improve the bonding strength between sisal fibers and polypropylene [30].Other mechanical properties of composites are summarized in Tables1 and 2. All composites have a tendency to decrease in the stress at break value in relation to the stress at break value of LDPE. A similar behavior was also observed for the results of the elongation at break of composites, indicating that the AFP modified transfers its elastic nature to the LDPE and reduces the tenacity of the composites.Table 1
Mechanical properties of composites with pristine AFP at 5, 10, and 20 wt% (200 and 325 mesh).
Composite
AFP (%)
Young’s modulus (MPa)
Stress at break (MPa)
Elongation at break (%)
LDPE
0
129.9 ± 19.1
13.3 ± 0.3
453.4 ± 18.3
NMF-5-M200
5
157.0 ± 21.4
10.6 ± 0.5
64.9 ± 8.7
NMF-10-M200
10
173.9 ± 15.0
11.3 ± 0.1
46.1 ± 1.2
NMF-20-M200
20
171.7 ± 10.9
10.4 ± 0.2
32.8 ± 9.2
NMF-5-M325
5
167.7 ± 8.70
11.2 ± 0.4
72.8 ± 4.0
NMF-10-M325
10
185.0 ± 15.0
11.8 ± 0.1
42.4 ± 7.4
NMF-20-M325
20
231.8 ± 6.30
12.7 ± 0.4
18.6 ± 4.0Table 2
Mechanical properties of composites containing plasma treated AFP at 5, 10, and 20 wt% (200 and 325 mesh).
Composite
AFP (%)
Young’s modulus (MPa)
Stress at break (MPa)
Elongation at break (%)
LDPE
0
129.9 ± 19.1
13.3 ± 0.3
453.4 ± 18.3
MPF-5-M200
5
167.7 ± 12.5
10.5 ± 0.3
48.4 ± 16.0
MPF-10-M200
10
175.3 ± 6.40
10.5 ± 0.2
33.1 ± 8.20
MPF-20-M200
20
209.0 ± 12.3
11.8 ± 0.4
15.7 ± 1.10
MPF-5-M325
5
174.2 ± 6.07
11.1 ± 0.2
109.1 ± 35.9
MPF-10-M325
10
194.5 ± 11.9
11.4 ± 0.4
41.10 ± 8.20
MPF-20-M325
20
221.9 ± 9.40
10.4 ± 0.4
13.90 ± 3.90


### 3.4. Thermal Properties

The thermal properties of the composites such as percent of crystallinity, melting (T
m), and crystallization (T
c) temperatures are shown in Table 3. T
m and T
c were not significantly affected by the addition of both untreated and treated AFP, while an increase in the degree of crystallinity (X
c) was observed and it was a function of the AFP content. It is well known that the fibers have a nucleating effect in the matrix promoting an increase in the crystallinity.Table 3
Thermal properties obtained by DSC of composites at different content of AFP.
Blend
AFP (%)
T
m (°C)
T
c (°C)
X
c (%)
LDPE
112.7
98.6
35.6
NMF-5-M200
5
112.4
98.3
35.2
NMF-10-M200
10
112.3
98.3
37.4
NMF-20-M200
20
112.4
99.0
38.4
NMF-5-M325
5
113.1
99.0
35.0
NMF-10-M325
10
120.2
98.0
35.9
NMF-20-M325
20
119.6
99.8
39.0
MPF-5-M200
5
112.4
98.9
36.2
MPF-10-M200
10
111.8
98.7
38.2
MPF-20-M200
20
112.3
99.4
37.4
MPF-5-M325
5
112.2
99.1
37.1
MPF-10-M325
10
112.1
98.5
36.1
MPF-20-M325
20
112.5
99.3
37.6The crystallinity of composites with 5 and 20 wt% of AFP (200 mesh) modified (MPF-5-M200 and MPF-20-M200, respectively) is slightly greater than those composites with untreated AFP. This could be a result of a better dispersion and compatibility between treated AFP and polyethylene, since plasma treatment of AFP increased their compatibility towards the polymer matrix. However, the composite with 20 wt% of AFP (200 mesh) unmodified (NMF-20-M200) has slightly higher crystallinity than the composite prepared with treated AFP at the same content of agave fiber (MPF-20-M200) and this could be related to the saturation of the system associated with a better dispersion of AFP in the matrix.


### 3.5. Scanning Electron Microscopy

Figure6(a) shows a SEM micrograph of cryogenic fractures of composites that contained unmodified AFP, where the characteristic morphology of AFP can be seen and in the interphase there is a hole indicative of the lack of compatibility between phases due to the difference in polarity of both components [9]. However, the composites containing plasma treated AFP present a good adherence with the polymer matrix, which is associated with the good interfacial adhesion between the two phases, and the adhesion was improved by the plasma treatment of AFP (Figure 6(b)). This evidence of compatibility explains why the composites containing treated AFP had better Young’s modulus.Figure 6
SEM micrographs of the composites with untreated and treated AFP. (a) NMF-20-M200 and (b) MPF-20-M200.
(a)
(b)


## 3.1. Infrared Spectroscopy Analysis of AFP

Figure1 shows the ATR-IR spectrum of the AFP unmodified (Figure 1(A)) as well as the ATR-IR spectrum of AFP modified by plasma (Figure 1(B)). The first broad band located at 3400 cm−1 is due to the stretching vibrations of hydroxyl groups from the cellulose present in the AFP; the band located at 2920 cm−1 is related to C-H stretching of the aliphatic methylene groups [18]. The weak peak at 1730 cm−1 is attributed to hemicellulose, associated with the C=O stretching in nonconjugated ketones, ester groups, and carbonyls [19]. The band located at 1640 cm−1 is attributed to the C=O stretching vibration and the C=C stretching vibration from alkenes groups and aromatic compounds [20]. Aromatic structure vibration from lignin and lignocellulose presents a band between 1510 and 1520 cm−1 [21]. Peaks at 1250 and 1000 cm−1 are related to C-O-C and C-O stretching vibrations on the cellulose chain bone [22]. Finally, the band at 1080 cm−1 associated with the stretch vibration of C-O is attributed to polysaccharides and hemicelluloses as reported previously by Grube and Bodirlau, respectively [23, 24].Figure 1
FTIR spectra of (A) pristine AFP and (B) AFP modified by plasma.In relation to the plasma treated AFP, the same infrared signals were observed in both fibers (pristine and coated). Typically, the amount of these plasma films on the surface of materials is lower than 5 wt% in relation to the substrate, and therefore it is difficult to observe infrared signals of the deposit, since it is beyond the limit of detection of FTIR. Another reason is that the films synthesized by plasma polymerization present a low relation H/C (aprox 1.49) against monomer (2) as has been shown previously by other authors [25], and this fact suggests that the polymeric nanofilm has a highly crosslinked structure and therefore a difference between two spectral signals cannot be seen.In literature, it has been reported that the plasma treatment polymer or plasma coating suffers a partial oxidation due to a reaction with atmospheric oxygen or water vapor after removal of the treated substrate from the vacuum chamber or even with oxygen dissolved in the monomers [25, 26]. These signals associated with the oxidation of polymer films deposited on the surface of the fiber powder by plasma were not detected by infrared due to possible overlap with bands of the AFP.The change on the surface characteristics of AFP after the plasma treatment was measured qualitatively through water dispersion tests in water. The untreated AFP are very well dispersed in water (see Figure2, left) and this behavior is due to the polar groups present in cellulose, which promotes the hydrophilic character of AFP. Meanwhile, plasma treated AFP remains on the water surface up to 2 months indicating that the fibers have a hydrophobic behavior (Figure 2, right). The above can be explained by the presence of a plasma polyethylene thin film coating located at the AFP surface, which inhibits the interaction between the surface of treated AFP and water. This kind of polymeric layer had been reported by several researchers, who have demonstrated that the presence of the plasma polymer at the surface of a substrate reduces the moisture and oxygen permeability, both of which are related to the density and structure of the plasma polymer thin film coatings [27, 28]. The cross-linked structure of polyethylene synthesized by plasma and its low concentration of oxygen in their structure could explain the long time stability of the hydrophobic behavior of treated AFP.Figure 2
Dispersion test of AFP in water. Left: untreated AFP; right: plasma treated AFP (hydrophobic behavior of the plasma treated samples remains upon two months).Another evidence that corroborated the hydrophobic character of the plasma treated AFP was the contact angle measurement and it was 75° approximately. In case of the untreated AFP no contact angle was formed due to the fast absorption of water drop by the agave fibers indicating thus their hydrophilic behavior. It is well known that plasma treatments can change the polarity of several types of fibers and improve their compatibility towards different polymer matrix [29]; this indicates that plasma treatment with ethylene reduces the surface energy, and thus the treated fibers present lower wettability than pristine fibers; also the film coating deposited on the fibers presents low polarity.


## 3.2. Mixing Torque

The torque-time curves during the preparation of the composites in melt state are presented in Figure3; at LDPE feeding, an increase in the torque value of up to 20 Nm can be identified; then it diminished to 10 Nm at 2 min, and it lastly is associated with the melting of LDPE pellets. In the interval from 4 to 6 min there was some increase of the values of torque associated with the addition of the AFP. This means that the presence of AFP increases the melt viscosity of the mixture. After 6 min, the intermolecular forces and physical entanglement between the adjacent molecules decrease, and an equilibrium value (obtained at 12 min) for a torque of 6.09 ± 0.09 Nm was achieved for LDPE; meanwhile the torque values for the blends with 10 wt% of AFP (200 mesh) modified (MPF-10-M200) and unmodified (NMF-10-M200) were 7.59 ± 0.02 and 7.08 ± 0.02 Nm, respectively. The slightly higher value of torque in MPF-10-M200 in relation to NMF-10-M200 is attributed to the higher interactions between melt molecules of LDPE and plasma treated AFP. The same behavior is presented at higher contents of AFP; higher values of torque were observed for the blends containing 20 wt% of AFP (200 mesh) in relation to those contained 10 wt% and the values were 8.36 ± 0.04 and 8.19 ± 0.02 for the blends with 20 wt% of AFP modified (MPF-20-M200) and unmodified (NMF-20-M200), respectively.Figure 3
Torque-time curves of the blends containing 10 wt% of unmodified and plasma treated AFP.


## 3.3. Mechanical Properties

The stress-strain diagrams of the composites of LDPE/AFP are presented in Figure4. A typical behavior was observed for LDPE with elongation break up of 450% and the corresponding tensile stress of 13 MPa. The addition of AFP modified or unmodified promotes an increase in the tensile stress and a gradual decrease of the elongation at break as can be observed in Figure 4. However, the formulations containing AFP (200 mesh) modified by plasma at 5 wt% (MPF-5-M200) and at 20 wt% (MPF-20-M200) further improve the tensile stress but present lower values of elongation percent than the composites with untreated AFP at 5 (NMF-5-M200) and 20 wt% (NMF-20-M200). This behavior is due to the fact that the ethylene plasma treated AFP enhances the interfacial adhesion with the polyethylene matrix.Figure 4
Tensile stress-strain curves of the blends containing 5 and 20 wt% of AFP unmodified and modified by plasma.Young’s modulus behavior as a function of the AFP content is presented in Figure5. In a general way, the addition of untreated and treated AFP improves Young’s modulus, but this improvement is higher for composites containing treated AFP (values higher than 10 wt%). The composite with 20 wt% of AFP (200 mesh) labeled as MPF-M200 presented an increase of 21.7% in Young’s modulus with respect to the composite at the same content of fiber (20 wt%) unmodified (NMF-M200). This behavior could be explained by an increase in the interactions between the treated surface of AFP and the polyethylene matrix.Figure 5
Young’s modulus of the composites base of LDPE and AFP modified and unmodified.As a function of the size (200 to 325 mesh) of the AFP modified (MPF-M325) and unmodified (NMF-M325), there is no significant difference in Young’s modulus of the composites especially at contents of AFP lower than 10 wt%. Other authors obtained similar results previously, where plasma treatments with argon and air were used to improve the bonding strength between sisal fibers and polypropylene [30].Other mechanical properties of composites are summarized in Tables1 and 2. All composites have a tendency to decrease in the stress at break value in relation to the stress at break value of LDPE. A similar behavior was also observed for the results of the elongation at break of composites, indicating that the AFP modified transfers its elastic nature to the LDPE and reduces the tenacity of the composites.Table 1
Mechanical properties of composites with pristine AFP at 5, 10, and 20 wt% (200 and 325 mesh).
Composite
AFP (%)
Young’s modulus (MPa)
Stress at break (MPa)
Elongation at break (%)
LDPE
0
129.9 ± 19.1
13.3 ± 0.3
453.4 ± 18.3
NMF-5-M200
5
157.0 ± 21.4
10.6 ± 0.5
64.9 ± 8.7
NMF-10-M200
10
173.9 ± 15.0
11.3 ± 0.1
46.1 ± 1.2
NMF-20-M200
20
171.7 ± 10.9
10.4 ± 0.2
32.8 ± 9.2
NMF-5-M325
5
167.7 ± 8.70
11.2 ± 0.4
72.8 ± 4.0
NMF-10-M325
10
185.0 ± 15.0
11.8 ± 0.1
42.4 ± 7.4
NMF-20-M325
20
231.8 ± 6.30
12.7 ± 0.4
18.6 ± 4.0Table 2
Mechanical properties of composites containing plasma treated AFP at 5, 10, and 20 wt% (200 and 325 mesh).
Composite
AFP (%)
Young’s modulus (MPa)
Stress at break (MPa)
Elongation at break (%)
LDPE
0
129.9 ± 19.1
13.3 ± 0.3
453.4 ± 18.3
MPF-5-M200
5
167.7 ± 12.5
10.5 ± 0.3
48.4 ± 16.0
MPF-10-M200
10
175.3 ± 6.40
10.5 ± 0.2
33.1 ± 8.20
MPF-20-M200
20
209.0 ± 12.3
11.8 ± 0.4
15.7 ± 1.10
MPF-5-M325
5
174.2 ± 6.07
11.1 ± 0.2
109.1 ± 35.9
MPF-10-M325
10
194.5 ± 11.9
11.4 ± 0.4
41.10 ± 8.20
MPF-20-M325
20
221.9 ± 9.40
10.4 ± 0.4
13.90 ± 3.90


## 3.4. Thermal Properties

The thermal properties of the composites such as percent of crystallinity, melting (T
m), and crystallization (T
c) temperatures are shown in Table 3. T
m and T
c were not significantly affected by the addition of both untreated and treated AFP, while an increase in the degree of crystallinity (X
c) was observed and it was a function of the AFP content. It is well known that the fibers have a nucleating effect in the matrix promoting an increase in the crystallinity.Table 3
Thermal properties obtained by DSC of composites at different content of AFP.
Blend
AFP (%)
T
m (°C)
T
c (°C)
X
c (%)
LDPE
112.7
98.6
35.6
NMF-5-M200
5
112.4
98.3
35.2
NMF-10-M200
10
112.3
98.3
37.4
NMF-20-M200
20
112.4
99.0
38.4
NMF-5-M325
5
113.1
99.0
35.0
NMF-10-M325
10
120.2
98.0
35.9
NMF-20-M325
20
119.6
99.8
39.0
MPF-5-M200
5
112.4
98.9
36.2
MPF-10-M200
10
111.8
98.7
38.2
MPF-20-M200
20
112.3
99.4
37.4
MPF-5-M325
5
112.2
99.1
37.1
MPF-10-M325
10
112.1
98.5
36.1
MPF-20-M325
20
112.5
99.3
37.6The crystallinity of composites with 5 and 20 wt% of AFP (200 mesh) modified (MPF-5-M200 and MPF-20-M200, respectively) is slightly greater than those composites with untreated AFP. This could be a result of a better dispersion and compatibility between treated AFP and polyethylene, since plasma treatment of AFP increased their compatibility towards the polymer matrix. However, the composite with 20 wt% of AFP (200 mesh) unmodified (NMF-20-M200) has slightly higher crystallinity than the composite prepared with treated AFP at the same content of agave fiber (MPF-20-M200) and this could be related to the saturation of the system associated with a better dispersion of AFP in the matrix.


## 3.5. Scanning Electron Microscopy

Figure6(a) shows a SEM micrograph of cryogenic fractures of composites that contained unmodified AFP, where the characteristic morphology of AFP can be seen and in the interphase there is a hole indicative of the lack of compatibility between phases due to the difference in polarity of both components [9]. However, the composites containing plasma treated AFP present a good adherence with the polymer matrix, which is associated with the good interfacial adhesion between the two phases, and the adhesion was improved by the plasma treatment of AFP (Figure 6(b)). This evidence of compatibility explains why the composites containing treated AFP had better Young’s modulus.Figure 6
SEM micrographs of the composites with untreated and treated AFP. (a) NMF-20-M200 and (b) MPF-20-M200.
(a)
(b)


## 4. Conclusions

The addition of ethylene plasma treated AFP improves the interfacial adhesion with the polyethylene matrix, since the coating applied by plasma on AFP has chemical nature similar to the polymer. The composites containing 20 wt% of AFP (200 mesh) modified (MPF-20-M200) presented an increase of 21.7% in Young’s modulus with respect to the composites containing AFP unmodified (NMF-20-M200). Also the presence of the AFP promotes an increase of the degree of crystallinity of LDPE but did not affect significantly its crystallization and melting temperature. These results provided new insights on the use of agave fibers, especially if they are chemically modified to change their surface characteristics, and thus they could be used in a wide number of different applications such as reinforced polymer composites among others.



---

*Source: 2807915-2016-12-27.xml*