# Preparation and Characterization of Polymer-Grafted Montmorillonite-Lignocellulose Nanocomposites by In Situ Intercalative Polymerization

Authors: Tavengwa Bunhu; Nhamo Chaukura; Lilian Tichagwa
Journal: Journal of Applied Chemistry
 (2016)

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## Abstract

Lignocellulose-clay nanocomposites were synthesized using an in situ intercalative polymerization method at 60°C and a pressure of 1 atm. The ratio of the montmorillonite clay to the lignocellulose ranged from 1 : 9 to 1 : 1 (MMT clay to lignocelluloses, wt%). The adsorbent materials were characterized by Fourier transform infrared spectroscopy (FTIR), thermogravimetric analysis (TGA), transmission electron microscopy (TEM), and X-ray powder diffraction (XRD). FTIR results showed that the polymers were covalently attached to the nanoclay and the lignocellulose in the nanocomposites. Both TEM and XRD analysis showed that the morphology of the materials ranged from phase-separated to intercalated nanocomposite adsorbents. Improved thermal stability, attributable to the presence of nanoclay, was observed for all the nanocomposites. The nanocomposite materials prepared can potentially be used as adsorbents for the removal of pollutants in water treatment and purification.


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## Body

## 1. Introduction

Nanotechnology based methods for water purification, if well developed, have the potential to produce highly purified water at low cost. Nanoadsorbents such as carbon nanotubes, zeolites, carbon nanotubes-supported cerium oxide, activated carbon fibres, alginate/carbon nanotubes composites, and layered double hydroxides have been investigated for the removal of pollutants ranging from heavy metals, dyes, and organics from aqueous systems [1]. Viruses and bacteria can also be removed from water using layered double hydroxides (LDH) nanocomposites with removal efficiency greater than 99% [2].Use has been made of different types of nanocomposites for the removal of a wide array of pollutants from contaminated water. Such pollutants include nitrophenols [3], dyes [4], heavy metals [5, 6], perchlorate ions [7], and chlorinated organics [8]. Removal efficiencies of up to 99% were reported for various pollutants by different researchers.Nanocomposites thus have the potential to give highly treated and pure waste water effluents. The major hindrance in the widespread application of nanotechnology, however, is the unavailability of a large quantity of nanomaterials at economically viable prices [1]. Therefore, the search for highly effective, efficient, and low-cost nanoadsorbent materials for water treatment and purification is an on-going challenge.Lignocellulose and montmorillonite clay have been identified as low-cost and potentially effective adsorbent materials. Lignocellulose-montmorillonite clay nanocomposites have been widely studied for application in structural materials especially in the furniture and in the packaging industry. The relatively low-cost lignocellulose-clay nanocomposites can also be used as adsorbent materials for the removal of inorganic and organic pollutants from aqueous solutions. Being derived from biomass, the advantages include low density, low equipment abrasiveness, relatively low cost, and biodegradability. Montmorillonite (MMT) clay is a naturally occurring 2 : 1 phyllosilicate mineral which comes in powder form and when completely delaminated, approximately 1 nm thick platelets or sheets are obtained with surface areas of about 750 m2/g and an aspect ratio >50 in comparison to conventional microsized fillers [9].Most lignocellulose-clay nanocomposites have been prepared using the melt intercalation method. Wang et al., 2003 [10], investigated the mechanical properties, water absorbency, and morphology of poly(propylene)/wood flour/organophilic clay nanocomposites. Poly(ethylene-octene) elastomer-clay-wood flour nanocomposites prepared by melt blending showed an improvement in the mechanical and tensile strength and the thermal stability of the resultant nanocomposites was observed [11]. Poly[methylene-(polyphenyl isocyanate)], aminopropyltriethoxysilane, maleated polypropylene, and copper metallic complex have proved to be effective coupling agents for this composite system [12]. Zhao et al. [13] described the preparation of poly(vinyl chloride)/wood flour/montmorillonite nanocomposites and assessed the effects of coupling agents and amount of layered silicate. The nanocomposites were largely directed at structural materials like furniture boards and flooring materials.In order to achieve a more porous material and unlock more surface area in the product, an in situ intercalative polymerization method was employed in the present study. It was also necessary to achieve covalent bonding of the polymer to both the lignocellulose and the clay to avoid leaching of the polymer (especially the water soluble polymers like poly(methacrylic acid)) into water to avoid secondary pollution problems. As such, the polymers served as swelling agents to trigger clay exfoliation and coupling agents, which served as bridges between the lignocellulose and the montmorillonite clay. The in situ intercalative polymerization method has not been widely applied in the preparation of wood-clay nanocomposites. The prepared nanocomposites were soxhlet-extracted with different organic solvents to remove any unreacted monomers. It is postulated that sodium montmorillonite (NaMMT) clay particles get covalently attached to lignocellulose to create some kind of a brush-like structure with the NaMMT particles sticking out for adsorption of pollutants from aqueous solution.


## 2. Experimental

Platanus x hispanica (London plane) tree leaves were used as a source of lignocellulose. Powdered leaf biomass (lignocellulose) was soxhlet-extracted using a 1 : 1 (v/v) ethanol : water solvent mixture and dried at 50°C for 48 h. Sodium-exchanged montmorillonite (NaMMT) was prepared from montmorillonite nanoclay according to Carrado et al. [14]. All the chemical reagents were used as received.Methyl methacrylate (MAA, 99%) purchased from SAARCHEM (Pty) Ltd was distilled before use and methyl orange was used as received. Methacrylic acid and dibutyl tin dilaurate (DBTDL, 95%) from Sigma-Aldrich were used as received. Methacryloxypropyltrimethoxysilane (MPS, 99%), ammonium persulphate (AMPS, 98%), and aluminium chloride hexahydrate (99%) were from Associated Chemical Enterprises. Dodecylbenzylsulphonic acid (DBS) and sodium metabisulphite (SMBS, 95%) were purchased from BDH Chemicals and sodium chloride salt (99.5%) was from MET-U-ED CC.


### 2.1. Preparation of Poly(methyl methacrylate)-Grafted Lignocellulose-Montmorillonite Nanocomposite (PMMAgLig-NaMMT)

SMBS (4.3 × 10−5 mol) and DBS (4.5 × 10−5 mol) were dissolved in deionized water in a three-neck round bottom flask. Soxhlet-extracted lignocellulose was then added slowly to the mixture under high speed magnetic stirring, which was then followed by the slow addition of NaMMT. The mixture was stirred for 1 h to completely disperse the solids followed by the addition of MMA to form an emulsion. N2 gas was bubbled into the system to purge oxygen and was maintained till the end of the reaction. After mixing for a further 30 min, AMPS (dissolved in 10 mL of deionized water) was added to the mixture and stirred for 30 min before refluxing the mixture at 60°C under N2 for 4 h. The mixture was cooled to room temperature, and the product (PMMAgLig-NaMMT) was isolated by filtration, followed by purification by solvent extraction with THF (20 mL) to remove PMMA homopolymer, and dried at 50°C for 24 h. The materials were prepared at different compositions of montmorillonite ranging from 10 to 50% w/w for all nanocomposite adsorbents. However, the results reported are only for the sample prepared at 40% w/w.


### 2.2. Preparation of Poly(methacryloxypropyltrimethoxysilane)-Coupled Lignocellulose-Montmorillonite Nanocomposite (PMPSgLig-NaMMT)

Soxhlet-extracted lignocellulose (3.0 g) and NaMMT (3.0 g) were dispersed in a 1 : 1 v/v EtOH : H2O solvent (150 mL) mixture under high speed magnetic stirring for 1 h. MPS (1.4 × 10−2 mol) was added to the lignocellulose-NaMMT dispersion and mixed for 10 min. A catalyst, dibutyl tin dilaurate (2.1 × 10−4 mol), was added and the mixture stirred for 10 min. The mixture was then heated to 70°C and left to react at this temperature for 24 h.After 24 h, the mixture was cooled to room temperature and the MPS-coupled lignocellulose-montmorillonite (PMPSgLig-NaMMT) nanocomposite isolated by filtration. THF was used as solvent in soxhlet extraction for 24 h to remove the free MPS monomer, the homopolymerized silane, and the catalyst. The same NaMMT clay loading to lignocellulose of 10 to 50% w/w was used. The PMPSgLig-NaMMT nanocomposite was dried at 50°C for 24 h. The sample was characterized by FTIR, TGA, XRD, and TEM and the results at 40% w/w NaMMT loading were reported.


### 2.3. Preparation of Poly(methacrylic acid)-Grafted Lignocellulose-Montmorillonite Nanocomposites (PMAAgLig-NaMMT)

PMAA-grafted lignocellulose-montmorillonite (PMAAgLig-NaMMT) nanocomposites were prepared at different montmorillonite clay loadings. The required amount of MPS-grafted lignocellulose was slowly dispersed in deionized water (150 mL) to which ethanol (5 mL) had been added. The ethanol was added to improve the dispersion of both the MPS-grafted lignocellulose and MPSgMMT in the water. After all the solids had been homogeneously dispersed in the water (about 1 h), MAA was added and mixed for 30 min, followed by the addition of AMPS. The AMPS was first dissolved in deionized water (10 mL) before being added to the mixture. The system was heated to 70°C under N2 atmosphere to initiate the graft polymerization reaction, and the temperature was maintained for 24 h, after which the mixture was cooled to room temperature and the product (PMAAgLig-NaMMT) isolated by filtration. The NaMMT clay loading to lignocellulose of 10 to 50% w/w was used. The product was washed with 0.01 M NaOH solution and then deionized water until the filtrate was at pH 5. The product was further soxhlet-extracted with THF for 24 h in order to remove all PMAA homopolymer and then dried at 50°C for 24 h. The nanocomposites were characterized by FTIR, TGA, XRD, and TEM and results for the 40% w/w NaMMT loading were reported.


### 2.4. Characterization

FTIR analysis was performed (PerkinElmer, 2000) using the procedure described by Rajendran et al., 2001 [15]. A thermogravimetric analyzer (PerkinElmer, TGA7) fitted with a thermal analysis controller (TAC7/DX) was used for thermogravimetric analysis. The instrument was operated under N2 atmosphere and the samples were heated from 20°C to 900°C at a heating rate of 15°C/minute. XRD measurements were carried out in locked couple mode with a Bruker AXS D8 Advance diffractometer (Cu Kα radiation with λ = 1.5406 Å, 40 kV, 40 mA) equipped with a PSD Lynx-Eye Si-strip detector (with 196 channels), at room temperature.TEM images were recorded on a JEM 200CX transmission electron microscope (JEOL, Tokyo, Japan) at an accelerating voltage of 120 kV. Prior to analysis, the nanocomposites were stained with OsO4, then embedded in epoxy resin, and cured for 24 h at 60°C. The embedded samples were then ultramicrotomed with a diamond knife on a Reichert Ultracut S ultramicrotome at room temperature to give sections about 100 nm thick. The sections were transferred from water at room temperature to 300-mesh copper grids, which were then transferred to the TEM instrument. The results reported are for the nanocomposites prepared at a NaMMT clay loading of 40%.


## 2.1. Preparation of Poly(methyl methacrylate)-Grafted Lignocellulose-Montmorillonite Nanocomposite (PMMAgLig-NaMMT)

SMBS (4.3 × 10−5 mol) and DBS (4.5 × 10−5 mol) were dissolved in deionized water in a three-neck round bottom flask. Soxhlet-extracted lignocellulose was then added slowly to the mixture under high speed magnetic stirring, which was then followed by the slow addition of NaMMT. The mixture was stirred for 1 h to completely disperse the solids followed by the addition of MMA to form an emulsion. N2 gas was bubbled into the system to purge oxygen and was maintained till the end of the reaction. After mixing for a further 30 min, AMPS (dissolved in 10 mL of deionized water) was added to the mixture and stirred for 30 min before refluxing the mixture at 60°C under N2 for 4 h. The mixture was cooled to room temperature, and the product (PMMAgLig-NaMMT) was isolated by filtration, followed by purification by solvent extraction with THF (20 mL) to remove PMMA homopolymer, and dried at 50°C for 24 h. The materials were prepared at different compositions of montmorillonite ranging from 10 to 50% w/w for all nanocomposite adsorbents. However, the results reported are only for the sample prepared at 40% w/w.


## 2.2. Preparation of Poly(methacryloxypropyltrimethoxysilane)-Coupled Lignocellulose-Montmorillonite Nanocomposite (PMPSgLig-NaMMT)

Soxhlet-extracted lignocellulose (3.0 g) and NaMMT (3.0 g) were dispersed in a 1 : 1 v/v EtOH : H2O solvent (150 mL) mixture under high speed magnetic stirring for 1 h. MPS (1.4 × 10−2 mol) was added to the lignocellulose-NaMMT dispersion and mixed for 10 min. A catalyst, dibutyl tin dilaurate (2.1 × 10−4 mol), was added and the mixture stirred for 10 min. The mixture was then heated to 70°C and left to react at this temperature for 24 h.After 24 h, the mixture was cooled to room temperature and the MPS-coupled lignocellulose-montmorillonite (PMPSgLig-NaMMT) nanocomposite isolated by filtration. THF was used as solvent in soxhlet extraction for 24 h to remove the free MPS monomer, the homopolymerized silane, and the catalyst. The same NaMMT clay loading to lignocellulose of 10 to 50% w/w was used. The PMPSgLig-NaMMT nanocomposite was dried at 50°C for 24 h. The sample was characterized by FTIR, TGA, XRD, and TEM and the results at 40% w/w NaMMT loading were reported.


## 2.3. Preparation of Poly(methacrylic acid)-Grafted Lignocellulose-Montmorillonite Nanocomposites (PMAAgLig-NaMMT)

PMAA-grafted lignocellulose-montmorillonite (PMAAgLig-NaMMT) nanocomposites were prepared at different montmorillonite clay loadings. The required amount of MPS-grafted lignocellulose was slowly dispersed in deionized water (150 mL) to which ethanol (5 mL) had been added. The ethanol was added to improve the dispersion of both the MPS-grafted lignocellulose and MPSgMMT in the water. After all the solids had been homogeneously dispersed in the water (about 1 h), MAA was added and mixed for 30 min, followed by the addition of AMPS. The AMPS was first dissolved in deionized water (10 mL) before being added to the mixture. The system was heated to 70°C under N2 atmosphere to initiate the graft polymerization reaction, and the temperature was maintained for 24 h, after which the mixture was cooled to room temperature and the product (PMAAgLig-NaMMT) isolated by filtration. The NaMMT clay loading to lignocellulose of 10 to 50% w/w was used. The product was washed with 0.01 M NaOH solution and then deionized water until the filtrate was at pH 5. The product was further soxhlet-extracted with THF for 24 h in order to remove all PMAA homopolymer and then dried at 50°C for 24 h. The nanocomposites were characterized by FTIR, TGA, XRD, and TEM and results for the 40% w/w NaMMT loading were reported.


## 2.4. Characterization

FTIR analysis was performed (PerkinElmer, 2000) using the procedure described by Rajendran et al., 2001 [15]. A thermogravimetric analyzer (PerkinElmer, TGA7) fitted with a thermal analysis controller (TAC7/DX) was used for thermogravimetric analysis. The instrument was operated under N2 atmosphere and the samples were heated from 20°C to 900°C at a heating rate of 15°C/minute. XRD measurements were carried out in locked couple mode with a Bruker AXS D8 Advance diffractometer (Cu Kα radiation with λ = 1.5406 Å, 40 kV, 40 mA) equipped with a PSD Lynx-Eye Si-strip detector (with 196 channels), at room temperature.TEM images were recorded on a JEM 200CX transmission electron microscope (JEOL, Tokyo, Japan) at an accelerating voltage of 120 kV. Prior to analysis, the nanocomposites were stained with OsO4, then embedded in epoxy resin, and cured for 24 h at 60°C. The embedded samples were then ultramicrotomed with a diamond knife on a Reichert Ultracut S ultramicrotome at room temperature to give sections about 100 nm thick. The sections were transferred from water at room temperature to 300-mesh copper grids, which were then transferred to the TEM instrument. The results reported are for the nanocomposites prepared at a NaMMT clay loading of 40%.


## 3. Results and Discussion

### 3.1. Poly(methyl methacrylate)-Grafted Lignocellulose-Clay Nanocomposite (PMMAgLig-NaMMT)

#### 3.1.1. FTIR Analysis

The presence of the peak at 1734 cm−1 (C=O of the ester linkage of PMMA) (Figure 1(a)) after soxhlet extraction of the sample using THF showed that the grafting reaction had been successful. In a related study on organosilanes, Castellano et al. [16] obtained similar results. The presence of the NaMMT in the nanocomposite was shown by the presence of the peaks at 468 cm−1 and 530 cm−1 which were ascribed to Si-O-Si and Al-O-Si, respectively. The soxhlet extraction was necessary in order to open up the spaces in the nanocomposite which would act as adsorption sites for both heavy metals and organic pollutants.Figure 1
(a) FTIR spectra of raw lignocellulose, NaMMT, and PMMAgLig-NaMMT nanocomposite. (b) TGA thermograms of NaMMT, raw lignocellulose, and PMMAgLig-NaMMT. (c) X-ray diffractograms of NaMMT and PMMAgLig-NaMMT. (d) Transmission electron micrograph of PMMAgLig-NaMMT nanocomposite.
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(d)


#### 3.1.2. Thermogravimetric Analysis

The presence of NaMMT in the lignocellulose matrix resulted in an increased thermal stability of the nanocomposite (Figure1(b)). The raw lignocellulose showed a degradation of temperature of about 344°C whereas the nanocomposite showed a decomposition of temperature of about 375°C. The % mass loss decreased with increase in amount of NaMMT in the nanocomposites. For the nanocomposites prepared with increasing amounts of NaMMT, the thermograms showed that the more the amount of NaMMT, the greater the thermal stability of the nanocomposites (results not shown). A similar trend in thermal stability was observed for the other types of nanocomposites (PMPSgLig-NaMMT and PMAAgLig-NaMMT). The amount of NaMMT in the nanocomposites could also be determined from the ash that remained after heating the samples to 900°C, and this roughly corresponded with the amount of NaMMT in the nanocomposite.


#### 3.1.3. X-Ray Diffraction

A slight shift of the basal reflection peak to lower 2θ angles (an increase in the d-spacing) was observed (Figure 1(c)). The basal reflection peak of montmorillonite shifted from 6.22° (NaMMT) to 5.88° for the PMMA-grafted nanocomposite. This corresponded to a d-spacing of 15.02° for the nanocomposite from 14.20° (NaMMT). This suggests that there was some partial intercalation of the poly(methyl methacrylate) into the interlayer space of the clay sheets.


#### 3.1.4. Transmission Electron Microscopy

The micrograph showed that the NaMMT was dispersed in the lignocellulose matrix at nanoscale (Figure1(d)). However, the clay sheets are still quite ordered, confirming the findings from the XRD data. It can be suggested that the product formed was an intercalated nanocomposite.


### 3.2. Polymethacryloxypropyltrimethoxysilane-Grafted Lignocellulose-Montmorillonite Nanocomposites (PMPSgLig-NaMMT)

#### 3.2.1. FTIR Analysis

The FTIR spectrum for PMPSg-LigNaMMT prepared at a NaMMT loading of 40% is shown in Figure2(a). The C=C stretching vibration peak of the nanocomposite was superimposed over that of the H-O-H bending vibration (1635 cm−1) of adsorbed water molecules (Figure 2(a)). The peaks at 2960 and 2930 cm−1 in the nanocomposite were ascribed to methylene –CH2-asymmetric and –CH2-symmetric stretching vibrations, respectively. The presence of the band at 1724 cm−1 (C=O stretching vibration of the ester group) in the nanocomposite after soxhlet extraction with THF showed that the grafting and/or coupling of lignocellulose and NaMMT was successful.Figure 2
(a) FTIR spectra of PMPS and PMPS-grafted lignocellulose-MMT nanocomposite. (b) Thermograms of raw lignocellulose, NaMMT, and PMPS-grafted lignocellulose-montmorillonite nanocomposite. (c) XRD patterns of NaMMT and PMPS-grafted lignocellulose-NaMMT nanocomposite. (d) Transmission electron micrograph of PMPSgLig-NaMMT nanocomposite.
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#### 3.2.2. Thermogravimetric Analysis

The nanocomposite was more thermally stable compared with the raw lignocellulose, but less stable relative to the NaMMT (Figure2(b)). The nanocomposite showed a degradation temperature of 425°C compared with 343°C for the raw lignocellulose. The increased thermal stability can be attributed to the presence of clay in the lignocellulose matrix [11]. The TGA thermogram and the FTIR spectrum of the MPS-grafted lignocellulose-montmorillonite nanocomposite show NaMMT was incorporated into the lignocellulose matrix.


#### 3.2.3. X-Ray Powder Diffraction Analysis

There was a shift in the montmorillonite basal reflection peak towards lower 2θ angles for the PMPSgLig-NaMMT (Figure 2(c)). This shift might be as a result of partial intercalation and polymerization of the MPS in the interlayer galleries of the NaMMT. The d-spacing increased from 14.20 (NaMMT) to 15.12 Å for the nanocomposite. The XRD patterns show that the NaMMT clay sheets are still ordered in the nanocomposite as judged from the intensity of the basal reflection peak as well as the d-spacing. This might suggest an intercalated nanocomposite or a microcomposite (phase-separated).


#### 3.2.4. Transmission Electron Microscopy

The micrograph of PMPSgLig-NaMMT (Figure2(d)) shows some clay aggregates as well as nanometer-sized clay particles dispersed in the lignocellulose matrix. This suggests that the dispersion of the clay particles was not homogeneous, thus giving a phase-separated composite [17–19].


### 3.3. Poly(methacrylic acid)-Coupled Lignocellulose-MMT Nanocomposites (PMAAgLig-NaMMT)

#### 3.3.1. FTIR Analysis

The PMAA-grafted nanocomposite (PMAAgLig-NaMMT) sample was prepared at a NaMMT loading of 40%. The PMAAgLig-NaMMT spectrum showed an additional peak at 1268 cm−1 (Figure 3(a)) which was assigned to C-O stretching vibration coupled with O-H in-plane bending, associated with the -COOH dimer [20, 21]. This peak is also present in the spectrum for PMAA. Another peak associated with the presence of the PMAA in the nanocomposite can be seen at 2576 cm−1 (O-H stretching vibration carboxylic acid dimers [22] from the grafted PMAA). There was a shift of the C=O stretching vibration peak to higher frequencies in the nanocomposite. This might be a result of the loss of C=C bonds as MAA units reacted with the C=C groups of the grafted MPS, resulting in a saturated ester linkage.Figure 3
(a) FTIR spectra of PMAA, MPS-grafted lignocellulose, and PMAA-coupled lignocellulose-NaMMT nanocomposite. (b) TGA thermograms of MPSgMMT, MPSgLig, and PMAA-grafted lignocellulose-MMT nanocomposite. (c) XRD patterns of NaMMT and PMAAgLig-NaMMT. (d) Transmission electron micrograph of PMAAgLig-NaMMT nanocomposite.
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(d)The structural OH stretching vibration (3646 cm−1) of the MMT was not very visible in the nanocomposite possibly because of the presence of hydrogen bonded OH groups from the lignocellulose.


#### 3.3.2. Thermogravimetric Analysis

The PMAAgLig-NaMMT sample prepared at a NaMMT loading of 40% showed three decomposition steps at temperatures 30–120°C, 220–420°C, and 420–650°C (Figure3(b)). The decomposition steps corresponded to loss of water, decomposition of lignocellulose together with the grafted polymers to form char, and decomposition of the solid residue (char), respectively. A greater thermal stability was recorded for the nanocomposite compared to the MPS-grafted lignocellulose. The % mass loss increased in the order PMPSgMMT < PMAAgLig-NaMMT < PMPSgLig. The higher thermal stability shown by the nanocomposite can be attributed to the presence of NaMMT dispersed in the lignocellulose matrix. A summary of the thermal properties for the synthesized materials (Table 1) shows them to be thermally more robust than lignocellulose, suggesting the synthesized materials can potentially be used at high temperatures.Table 1
Summary of thermal properties of synthesized materials compared to the precursors.
Material
Onset temperature (°C)
Degradation temperature(°C)
Remarks
PMPSgLig-NaMMT
220
220–650
Loss of water at 30–120°C; gradual degradation, showing decomposition of lignocellulose at 400°C
PMPSgLig-NaMMT
320
425–900
Loss of water at 30–120°C; gradual degradation
PMAAgLi-NaMMT
240
240–600
Loss of water at 30–120°C; decomposition of lignocelluloses at 220–420°C, decomposition of grafted polymer at 420–650°C; gradual degradation
NaMMT
220
—
Thermally stable within the analytical temperature range used; only lost moisture around 100–120°C and water of crystallization
Lignocellulose
220
340–600
Loss of water at 30–120°C; fairly rapid degradation


#### 3.3.3. X-Ray Powder Diffraction Analysis

The X-ray diffractograms of NaMMT and PMAAgLig-NaMMT nanocomposite showed a shift of the basal reflection peak to lower 2θ angles. The d-spacing increased from 14.20 to 15.47 Å, showing some opening up of the nanoclay sheets. The nanocomposite obtained had partially intercalated nanoclay sheets.


#### 3.3.4. Transmission Electron Microscopy

TEM showed the NaMMT still fairly ordered within the lignocellulose matrix (Figure3(d)). The PMAAgLig-NaMMT morphology was comparable to that of PMMAgLig-NaMMT. However, relatively poor clay dispersion was observed for the PMAAgLig-NaMMT nanocomposite compared with PMMAgLig-NaMMT in Figure 1(d) which showed distinct NaMMT clay particles. The TEM results confirm the observations made from the XRD results which also showed a highly ordered, partially intercalated clay structure in the nanocomposite. The clay particles displayed some long-range order, indicating the presence of strong van der Waals forces between the clay sheets.


## 3.1. Poly(methyl methacrylate)-Grafted Lignocellulose-Clay Nanocomposite (PMMAgLig-NaMMT)

### 3.1.1. FTIR Analysis

The presence of the peak at 1734 cm−1 (C=O of the ester linkage of PMMA) (Figure 1(a)) after soxhlet extraction of the sample using THF showed that the grafting reaction had been successful. In a related study on organosilanes, Castellano et al. [16] obtained similar results. The presence of the NaMMT in the nanocomposite was shown by the presence of the peaks at 468 cm−1 and 530 cm−1 which were ascribed to Si-O-Si and Al-O-Si, respectively. The soxhlet extraction was necessary in order to open up the spaces in the nanocomposite which would act as adsorption sites for both heavy metals and organic pollutants.Figure 1
(a) FTIR spectra of raw lignocellulose, NaMMT, and PMMAgLig-NaMMT nanocomposite. (b) TGA thermograms of NaMMT, raw lignocellulose, and PMMAgLig-NaMMT. (c) X-ray diffractograms of NaMMT and PMMAgLig-NaMMT. (d) Transmission electron micrograph of PMMAgLig-NaMMT nanocomposite.
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### 3.1.2. Thermogravimetric Analysis

The presence of NaMMT in the lignocellulose matrix resulted in an increased thermal stability of the nanocomposite (Figure1(b)). The raw lignocellulose showed a degradation of temperature of about 344°C whereas the nanocomposite showed a decomposition of temperature of about 375°C. The % mass loss decreased with increase in amount of NaMMT in the nanocomposites. For the nanocomposites prepared with increasing amounts of NaMMT, the thermograms showed that the more the amount of NaMMT, the greater the thermal stability of the nanocomposites (results not shown). A similar trend in thermal stability was observed for the other types of nanocomposites (PMPSgLig-NaMMT and PMAAgLig-NaMMT). The amount of NaMMT in the nanocomposites could also be determined from the ash that remained after heating the samples to 900°C, and this roughly corresponded with the amount of NaMMT in the nanocomposite.


### 3.1.3. X-Ray Diffraction

A slight shift of the basal reflection peak to lower 2θ angles (an increase in the d-spacing) was observed (Figure 1(c)). The basal reflection peak of montmorillonite shifted from 6.22° (NaMMT) to 5.88° for the PMMA-grafted nanocomposite. This corresponded to a d-spacing of 15.02° for the nanocomposite from 14.20° (NaMMT). This suggests that there was some partial intercalation of the poly(methyl methacrylate) into the interlayer space of the clay sheets.


### 3.1.4. Transmission Electron Microscopy

The micrograph showed that the NaMMT was dispersed in the lignocellulose matrix at nanoscale (Figure1(d)). However, the clay sheets are still quite ordered, confirming the findings from the XRD data. It can be suggested that the product formed was an intercalated nanocomposite.


## 3.1.1. FTIR Analysis

The presence of the peak at 1734 cm−1 (C=O of the ester linkage of PMMA) (Figure 1(a)) after soxhlet extraction of the sample using THF showed that the grafting reaction had been successful. In a related study on organosilanes, Castellano et al. [16] obtained similar results. The presence of the NaMMT in the nanocomposite was shown by the presence of the peaks at 468 cm−1 and 530 cm−1 which were ascribed to Si-O-Si and Al-O-Si, respectively. The soxhlet extraction was necessary in order to open up the spaces in the nanocomposite which would act as adsorption sites for both heavy metals and organic pollutants.Figure 1
(a) FTIR spectra of raw lignocellulose, NaMMT, and PMMAgLig-NaMMT nanocomposite. (b) TGA thermograms of NaMMT, raw lignocellulose, and PMMAgLig-NaMMT. (c) X-ray diffractograms of NaMMT and PMMAgLig-NaMMT. (d) Transmission electron micrograph of PMMAgLig-NaMMT nanocomposite.
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(b)
(c)
(d)


## 3.1.2. Thermogravimetric Analysis

The presence of NaMMT in the lignocellulose matrix resulted in an increased thermal stability of the nanocomposite (Figure1(b)). The raw lignocellulose showed a degradation of temperature of about 344°C whereas the nanocomposite showed a decomposition of temperature of about 375°C. The % mass loss decreased with increase in amount of NaMMT in the nanocomposites. For the nanocomposites prepared with increasing amounts of NaMMT, the thermograms showed that the more the amount of NaMMT, the greater the thermal stability of the nanocomposites (results not shown). A similar trend in thermal stability was observed for the other types of nanocomposites (PMPSgLig-NaMMT and PMAAgLig-NaMMT). The amount of NaMMT in the nanocomposites could also be determined from the ash that remained after heating the samples to 900°C, and this roughly corresponded with the amount of NaMMT in the nanocomposite.


## 3.1.3. X-Ray Diffraction

A slight shift of the basal reflection peak to lower 2θ angles (an increase in the d-spacing) was observed (Figure 1(c)). The basal reflection peak of montmorillonite shifted from 6.22° (NaMMT) to 5.88° for the PMMA-grafted nanocomposite. This corresponded to a d-spacing of 15.02° for the nanocomposite from 14.20° (NaMMT). This suggests that there was some partial intercalation of the poly(methyl methacrylate) into the interlayer space of the clay sheets.


## 3.1.4. Transmission Electron Microscopy

The micrograph showed that the NaMMT was dispersed in the lignocellulose matrix at nanoscale (Figure1(d)). However, the clay sheets are still quite ordered, confirming the findings from the XRD data. It can be suggested that the product formed was an intercalated nanocomposite.


## 3.2. Polymethacryloxypropyltrimethoxysilane-Grafted Lignocellulose-Montmorillonite Nanocomposites (PMPSgLig-NaMMT)

### 3.2.1. FTIR Analysis

The FTIR spectrum for PMPSg-LigNaMMT prepared at a NaMMT loading of 40% is shown in Figure2(a). The C=C stretching vibration peak of the nanocomposite was superimposed over that of the H-O-H bending vibration (1635 cm−1) of adsorbed water molecules (Figure 2(a)). The peaks at 2960 and 2930 cm−1 in the nanocomposite were ascribed to methylene –CH2-asymmetric and –CH2-symmetric stretching vibrations, respectively. The presence of the band at 1724 cm−1 (C=O stretching vibration of the ester group) in the nanocomposite after soxhlet extraction with THF showed that the grafting and/or coupling of lignocellulose and NaMMT was successful.Figure 2
(a) FTIR spectra of PMPS and PMPS-grafted lignocellulose-MMT nanocomposite. (b) Thermograms of raw lignocellulose, NaMMT, and PMPS-grafted lignocellulose-montmorillonite nanocomposite. (c) XRD patterns of NaMMT and PMPS-grafted lignocellulose-NaMMT nanocomposite. (d) Transmission electron micrograph of PMPSgLig-NaMMT nanocomposite.
(a)
(b)
(c)
(d)


### 3.2.2. Thermogravimetric Analysis

The nanocomposite was more thermally stable compared with the raw lignocellulose, but less stable relative to the NaMMT (Figure2(b)). The nanocomposite showed a degradation temperature of 425°C compared with 343°C for the raw lignocellulose. The increased thermal stability can be attributed to the presence of clay in the lignocellulose matrix [11]. The TGA thermogram and the FTIR spectrum of the MPS-grafted lignocellulose-montmorillonite nanocomposite show NaMMT was incorporated into the lignocellulose matrix.


### 3.2.3. X-Ray Powder Diffraction Analysis

There was a shift in the montmorillonite basal reflection peak towards lower 2θ angles for the PMPSgLig-NaMMT (Figure 2(c)). This shift might be as a result of partial intercalation and polymerization of the MPS in the interlayer galleries of the NaMMT. The d-spacing increased from 14.20 (NaMMT) to 15.12 Å for the nanocomposite. The XRD patterns show that the NaMMT clay sheets are still ordered in the nanocomposite as judged from the intensity of the basal reflection peak as well as the d-spacing. This might suggest an intercalated nanocomposite or a microcomposite (phase-separated).


### 3.2.4. Transmission Electron Microscopy

The micrograph of PMPSgLig-NaMMT (Figure2(d)) shows some clay aggregates as well as nanometer-sized clay particles dispersed in the lignocellulose matrix. This suggests that the dispersion of the clay particles was not homogeneous, thus giving a phase-separated composite [17–19].


## 3.2.1. FTIR Analysis

The FTIR spectrum for PMPSg-LigNaMMT prepared at a NaMMT loading of 40% is shown in Figure2(a). The C=C stretching vibration peak of the nanocomposite was superimposed over that of the H-O-H bending vibration (1635 cm−1) of adsorbed water molecules (Figure 2(a)). The peaks at 2960 and 2930 cm−1 in the nanocomposite were ascribed to methylene –CH2-asymmetric and –CH2-symmetric stretching vibrations, respectively. The presence of the band at 1724 cm−1 (C=O stretching vibration of the ester group) in the nanocomposite after soxhlet extraction with THF showed that the grafting and/or coupling of lignocellulose and NaMMT was successful.Figure 2
(a) FTIR spectra of PMPS and PMPS-grafted lignocellulose-MMT nanocomposite. (b) Thermograms of raw lignocellulose, NaMMT, and PMPS-grafted lignocellulose-montmorillonite nanocomposite. (c) XRD patterns of NaMMT and PMPS-grafted lignocellulose-NaMMT nanocomposite. (d) Transmission electron micrograph of PMPSgLig-NaMMT nanocomposite.
(a)
(b)
(c)
(d)


## 3.2.2. Thermogravimetric Analysis

The nanocomposite was more thermally stable compared with the raw lignocellulose, but less stable relative to the NaMMT (Figure2(b)). The nanocomposite showed a degradation temperature of 425°C compared with 343°C for the raw lignocellulose. The increased thermal stability can be attributed to the presence of clay in the lignocellulose matrix [11]. The TGA thermogram and the FTIR spectrum of the MPS-grafted lignocellulose-montmorillonite nanocomposite show NaMMT was incorporated into the lignocellulose matrix.


## 3.2.3. X-Ray Powder Diffraction Analysis

There was a shift in the montmorillonite basal reflection peak towards lower 2θ angles for the PMPSgLig-NaMMT (Figure 2(c)). This shift might be as a result of partial intercalation and polymerization of the MPS in the interlayer galleries of the NaMMT. The d-spacing increased from 14.20 (NaMMT) to 15.12 Å for the nanocomposite. The XRD patterns show that the NaMMT clay sheets are still ordered in the nanocomposite as judged from the intensity of the basal reflection peak as well as the d-spacing. This might suggest an intercalated nanocomposite or a microcomposite (phase-separated).


## 3.2.4. Transmission Electron Microscopy

The micrograph of PMPSgLig-NaMMT (Figure2(d)) shows some clay aggregates as well as nanometer-sized clay particles dispersed in the lignocellulose matrix. This suggests that the dispersion of the clay particles was not homogeneous, thus giving a phase-separated composite [17–19].


## 3.3. Poly(methacrylic acid)-Coupled Lignocellulose-MMT Nanocomposites (PMAAgLig-NaMMT)

### 3.3.1. FTIR Analysis

The PMAA-grafted nanocomposite (PMAAgLig-NaMMT) sample was prepared at a NaMMT loading of 40%. The PMAAgLig-NaMMT spectrum showed an additional peak at 1268 cm−1 (Figure 3(a)) which was assigned to C-O stretching vibration coupled with O-H in-plane bending, associated with the -COOH dimer [20, 21]. This peak is also present in the spectrum for PMAA. Another peak associated with the presence of the PMAA in the nanocomposite can be seen at 2576 cm−1 (O-H stretching vibration carboxylic acid dimers [22] from the grafted PMAA). There was a shift of the C=O stretching vibration peak to higher frequencies in the nanocomposite. This might be a result of the loss of C=C bonds as MAA units reacted with the C=C groups of the grafted MPS, resulting in a saturated ester linkage.Figure 3
(a) FTIR spectra of PMAA, MPS-grafted lignocellulose, and PMAA-coupled lignocellulose-NaMMT nanocomposite. (b) TGA thermograms of MPSgMMT, MPSgLig, and PMAA-grafted lignocellulose-MMT nanocomposite. (c) XRD patterns of NaMMT and PMAAgLig-NaMMT. (d) Transmission electron micrograph of PMAAgLig-NaMMT nanocomposite.
(a)
(b)
(c)
(d)The structural OH stretching vibration (3646 cm−1) of the MMT was not very visible in the nanocomposite possibly because of the presence of hydrogen bonded OH groups from the lignocellulose.


### 3.3.2. Thermogravimetric Analysis

The PMAAgLig-NaMMT sample prepared at a NaMMT loading of 40% showed three decomposition steps at temperatures 30–120°C, 220–420°C, and 420–650°C (Figure3(b)). The decomposition steps corresponded to loss of water, decomposition of lignocellulose together with the grafted polymers to form char, and decomposition of the solid residue (char), respectively. A greater thermal stability was recorded for the nanocomposite compared to the MPS-grafted lignocellulose. The % mass loss increased in the order PMPSgMMT < PMAAgLig-NaMMT < PMPSgLig. The higher thermal stability shown by the nanocomposite can be attributed to the presence of NaMMT dispersed in the lignocellulose matrix. A summary of the thermal properties for the synthesized materials (Table 1) shows them to be thermally more robust than lignocellulose, suggesting the synthesized materials can potentially be used at high temperatures.Table 1
Summary of thermal properties of synthesized materials compared to the precursors.
Material
Onset temperature (°C)
Degradation temperature(°C)
Remarks
PMPSgLig-NaMMT
220
220–650
Loss of water at 30–120°C; gradual degradation, showing decomposition of lignocellulose at 400°C
PMPSgLig-NaMMT
320
425–900
Loss of water at 30–120°C; gradual degradation
PMAAgLi-NaMMT
240
240–600
Loss of water at 30–120°C; decomposition of lignocelluloses at 220–420°C, decomposition of grafted polymer at 420–650°C; gradual degradation
NaMMT
220
—
Thermally stable within the analytical temperature range used; only lost moisture around 100–120°C and water of crystallization
Lignocellulose
220
340–600
Loss of water at 30–120°C; fairly rapid degradation


### 3.3.3. X-Ray Powder Diffraction Analysis

The X-ray diffractograms of NaMMT and PMAAgLig-NaMMT nanocomposite showed a shift of the basal reflection peak to lower 2θ angles. The d-spacing increased from 14.20 to 15.47 Å, showing some opening up of the nanoclay sheets. The nanocomposite obtained had partially intercalated nanoclay sheets.


### 3.3.4. Transmission Electron Microscopy

TEM showed the NaMMT still fairly ordered within the lignocellulose matrix (Figure3(d)). The PMAAgLig-NaMMT morphology was comparable to that of PMMAgLig-NaMMT. However, relatively poor clay dispersion was observed for the PMAAgLig-NaMMT nanocomposite compared with PMMAgLig-NaMMT in Figure 1(d) which showed distinct NaMMT clay particles. The TEM results confirm the observations made from the XRD results which also showed a highly ordered, partially intercalated clay structure in the nanocomposite. The clay particles displayed some long-range order, indicating the presence of strong van der Waals forces between the clay sheets.


## 3.3.1. FTIR Analysis

The PMAA-grafted nanocomposite (PMAAgLig-NaMMT) sample was prepared at a NaMMT loading of 40%. The PMAAgLig-NaMMT spectrum showed an additional peak at 1268 cm−1 (Figure 3(a)) which was assigned to C-O stretching vibration coupled with O-H in-plane bending, associated with the -COOH dimer [20, 21]. This peak is also present in the spectrum for PMAA. Another peak associated with the presence of the PMAA in the nanocomposite can be seen at 2576 cm−1 (O-H stretching vibration carboxylic acid dimers [22] from the grafted PMAA). There was a shift of the C=O stretching vibration peak to higher frequencies in the nanocomposite. This might be a result of the loss of C=C bonds as MAA units reacted with the C=C groups of the grafted MPS, resulting in a saturated ester linkage.Figure 3
(a) FTIR spectra of PMAA, MPS-grafted lignocellulose, and PMAA-coupled lignocellulose-NaMMT nanocomposite. (b) TGA thermograms of MPSgMMT, MPSgLig, and PMAA-grafted lignocellulose-MMT nanocomposite. (c) XRD patterns of NaMMT and PMAAgLig-NaMMT. (d) Transmission electron micrograph of PMAAgLig-NaMMT nanocomposite.
(a)
(b)
(c)
(d)The structural OH stretching vibration (3646 cm−1) of the MMT was not very visible in the nanocomposite possibly because of the presence of hydrogen bonded OH groups from the lignocellulose.


## 3.3.2. Thermogravimetric Analysis

The PMAAgLig-NaMMT sample prepared at a NaMMT loading of 40% showed three decomposition steps at temperatures 30–120°C, 220–420°C, and 420–650°C (Figure3(b)). The decomposition steps corresponded to loss of water, decomposition of lignocellulose together with the grafted polymers to form char, and decomposition of the solid residue (char), respectively. A greater thermal stability was recorded for the nanocomposite compared to the MPS-grafted lignocellulose. The % mass loss increased in the order PMPSgMMT < PMAAgLig-NaMMT < PMPSgLig. The higher thermal stability shown by the nanocomposite can be attributed to the presence of NaMMT dispersed in the lignocellulose matrix. A summary of the thermal properties for the synthesized materials (Table 1) shows them to be thermally more robust than lignocellulose, suggesting the synthesized materials can potentially be used at high temperatures.Table 1
Summary of thermal properties of synthesized materials compared to the precursors.
Material
Onset temperature (°C)
Degradation temperature(°C)
Remarks
PMPSgLig-NaMMT
220
220–650
Loss of water at 30–120°C; gradual degradation, showing decomposition of lignocellulose at 400°C
PMPSgLig-NaMMT
320
425–900
Loss of water at 30–120°C; gradual degradation
PMAAgLi-NaMMT
240
240–600
Loss of water at 30–120°C; decomposition of lignocelluloses at 220–420°C, decomposition of grafted polymer at 420–650°C; gradual degradation
NaMMT
220
—
Thermally stable within the analytical temperature range used; only lost moisture around 100–120°C and water of crystallization
Lignocellulose
220
340–600
Loss of water at 30–120°C; fairly rapid degradation


## 3.3.3. X-Ray Powder Diffraction Analysis

The X-ray diffractograms of NaMMT and PMAAgLig-NaMMT nanocomposite showed a shift of the basal reflection peak to lower 2θ angles. The d-spacing increased from 14.20 to 15.47 Å, showing some opening up of the nanoclay sheets. The nanocomposite obtained had partially intercalated nanoclay sheets.


## 3.3.4. Transmission Electron Microscopy

TEM showed the NaMMT still fairly ordered within the lignocellulose matrix (Figure3(d)). The PMAAgLig-NaMMT morphology was comparable to that of PMMAgLig-NaMMT. However, relatively poor clay dispersion was observed for the PMAAgLig-NaMMT nanocomposite compared with PMMAgLig-NaMMT in Figure 1(d) which showed distinct NaMMT clay particles. The TEM results confirm the observations made from the XRD results which also showed a highly ordered, partially intercalated clay structure in the nanocomposite. The clay particles displayed some long-range order, indicating the presence of strong van der Waals forces between the clay sheets.


## 4. Conclusion

Novel adsorbent materials (PMMAgLig-MMT nanocomposite, PMAAgMMT, PMAAgLig, PMPSgLig-MMT, and PMAAgLig-MMT nanocomposite) were prepared through condensation as well as free-radical graft polymerization reactions. The intended modification of the lignocellulose and MMT separately was achieved as confirmed by FTIR, TGA, and XRD. XRD analysis showed some partial intercalation of MMA into the interlayer space of the clay sheets. The nanocomposite adsorbents also showed a slight increase in the basal spacing of the MMT clay sheets. Intercalated nanocomposite adsorbent materials were successfully prepared as shown by FTIR, TGA, and XRD. Modification of lignocellulose with MPS resulted in improved thermal stability. All the nanocomposites prepared also showed an increase in thermal stability, which was attributed to the presence of clay in the lignocellulose matrix. However, modification of lignocellulose with PMMA resulted in a reduction in thermal stability. The nanocomposite materials prepared can potentially be used as adsorbents for the removal of pollutants in water treatment and purification.



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*Source: 4137398-2016-08-17.xml*