Sunflower oil cake-derived cellulose nanocrystals: Extraction, physico-chemical characteristics and potential application
Zineb Kassab, Mounir El Achaby, Youssef Tamraoui, Houssine Sehaqui, Rachid Bouhfid, Abou El Kacem Qaiss
PII: S0141-8130(19)33005-3
DOI: https://doi.org/10.1016/j.ijbiomac.2019.06.049
Reference: BIOMAC 12555
To appear in: International Journal of Biological Macromolecules Received date: 23 April 2019
Revised date: 2 June 2019 Accepted date: 9 June 2019
Please cite this article as: Z. Kassab, M. El Achaby, Y. Tamraoui, et al., Sunflower oil cake- derived cellulose nanocrystals: Extraction, physico-chemical characteristics and potential application, International Journal of Biological Macromolecules, https://doi.org/10.1016/
j.ijbiomac.2019.06.049
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1
Sunflower oil cake-derived cellulose nanocrystals: Extraction, physico-chemical characteristics and potential application
Zineb Kassab 1 , Mounir El Achaby 1, * , Youssef Tamraoui 1 , Houssine Sehaqui 1 , Rachid Bouhfid 2 , Abou El Kacem Qaiss 2
1
Materials Science and Nanoengineering Department (MSN), Mohammed VI Polytechnic University (UM6P), Lot 660 – Hay Moulay Rachid, 43150, Benguerir, Morocco
2
Moroccan Foundation for Advanced Science, Innovation and Research (MAScIR), Institute of Nanomaterials and Nanotechnology (NANOTECH), Laboratory of Polymer Processing, Rabat, Morocco
*Corresponding author: Email: mounir.elachaby@um6p.ma, +212 6 620 10 620 (M. El Achaby)
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2 Abstract
In this work, sunflower oil cake (SOC) was identified as bio-sourced material for cellulose nanocrystals (CNC) production using chemical treatments followed by sulfuric acid hydrolysis.
The hydrolysis was performed at 64 % acid concentration, a temperature of 50 °C and at two different hydrolysis times, 15 min (CNC
15) and 30 min (CNC
30). It was found that CNC exhibited a diameter of 9 ± 3 nm and 5 ± 2 nm, a length of 354 ± 101 nm and 329 ± 98 nm, a crystallinity of 75 % and 87 %, a surface charge density of ~ 1.57 and ~ 1.88 sulfate groups per 100 anhydroglucose units and a zeta potential value of – 25.6 and – 30.7 mV, for CNC
15and CNC
30, respectively. The thermal degradation under nitrogen atmosphere started at 225 °C (CNC
15), which is relatively higher than the temperature for sulfuric acid hydrolyzed CNC from other sources. Due to a high importance of CNC application in aqueous systems, the rheological behaviour of CNC suspensions at various concentrations was evaluated by the steady shear viscosity measurements and the oscillatory dynamic tests. The results showed that the CNC suspensions exhibited a gel-like behaviour at very low CNC concentrations (0.1-1 %) wherein a strong CNC entangled network is formed. Polymer nanoreinforcing capability of the newly produced CNC was also investigated in this study. CNC filled PVA nanocomposite films were produced at various CNC contents (1, 3, 5 and 8 wt%) and their mechanical and transparency properties were investigated, resulting in transparent nanocomposite materials with strong mechanical properties. The study suggested other possibilities to utilize agricultural wastes from SOC for CNC production with potential application as reinforcement in polymer nanocomposites .
Keywords: Sunflower oil cake; Cellulose nanocrystals; Polymer nanocomposites
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3 1. Introduction
Among various natural materials, cellulose is considered the most abundantly available on earth, and has unique properties such as renewability, biodegradability, lightweight and good mechanical properties [1,2]. The main sources for cellulose extraction are cotton and wood, but it can also be derived from a variety of sources, such as marine biomass, marine animal tunicate, invertebrates, bacteria, fungi, annual plants, and other agro-industrial wastes [1,3,4] In its native form, cellulose exhibits a semi-crystalline structure with morphology and dimensions depending on the original source and the local environment [1,2]. The industrial exploitation of cellulose material has been known since the beginning of civilization, and various applications were developed, such as fibrous material in pulp, paper, composites, textiles and food industry [1,2]. Over recent decades, cellulose has certainly attracted more and more attention world- wide due to the possibility of converting it into cellulose nanomaterials with novel properties not present in bulk materials. After production and purification of cellulose fibers from lignocellulosic biomass and agricultural wastes, cellulose nanomaterials, such as cellulose nanofibrils (CNF) and cellulose nanocrystals (CNC), can be extracted by mechanically- or chemically-induced top-down deconstructing strategies [5].
CNC can be produced in two morphological shapes, rod-like or needle-like shape, having
a compact and ordered cellulose structure, which gives it unique properties [6]. In general, the
dimensions of CNC depend on the origin of cellulose and hydrolysis conditions [2]. The
diameter of CNC is generally of the order of few nanometers and the average length is of the
order of few hundred nanometers [5]. In general, CNC are produced by an acid hydrolysis
process, where the cellulose microfibers (CMF) are subjected to concentrated acid to
hydrolyze the amorphous parts of the cellulosic chains and leave the crystalline parts intact
[7]. CNC have been produced using various types of acid treatments, such as hydrochloric,
sulfuric, and phosphoric acids, with each treatment bestowing specific functional groups on
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4 the surface of the extracted CNC that impacts their colloidal stability and their surface functionality [8]. Regarding to this, the sulfuric acid hydrolysis represents the most effective process for obtaining CNC and the largely used for this purpose, because it produces sulphated CNC with high crystallinity and good colloidal water stability [7]. Recently, CNC have garnered tremendous level of attention from both academic and industrial researchers, due to their excellent inherent physical and chemical properties such as high tensile strength (7.5 GPa) and elastic modulus (approximately 100–140 GPa), high specific surface area (∼250–500 m
2/g), low density (1.6 g/cm
3), biodegradability, renewability and reactive surfaces [9].
At present, the most promising application of CNC is as nanoreinforcing agent for
advanced polymer nanocomposites development. It has been reported that the incorporation
of CNC in polymeric matrices resulted in polymer-based nanocomposites with advanced
properties and functional applications [10]. In this context, polyvinyl alcohol (PVA) has been
widely used as a polymeric matrix for developing CNC-filled PVA nanocomposite materials
with improved properties [6,11–16]. The reinforcement effect of the incorporation of CNC
into PVA polymer is strongly related to the CNC-PVA interfacial interaction and the
dispersion state of CNC within PVA polymer [6,12,16]. Generally, weak interfacial
interactions (physically non-covalent interaction) could occur when CNC nanofiller is added
into PVA without surface functionalization or chemical crosslinking, resulting in a weak
reinforcement effect of the final properties of PVA nanocomposites [16]. It is well-known that
acid hydrolyzed-CNC exhibit a functionalized surface, ensuring a good ability to interact with
hydroxyl groups of PVA polymer, and an acceptable reinforcement effect could be achieved
[6,12]. However, it has been reported that a high reinforcement effect could be developed by
chemical cross-linking of PVA and/or functionalization of CNC’s surface, resulting in
improved chemically covalent interaction between CNC and PVA, thus CNC-reinforced PVA
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5 nanocomposites with significant improvement of the final properties could be produced [11,16].
Starting from nature, various biosourced material, lignocellulosic biomass or agricultural waste, were identified and studied as viable and sustainable sources for purified cellulose fibers production and acid hydrolysed CNC extraction [17]. In this investigation, sunflower oil cakes (SOC) waste was identified as an abundant cellulose-rich material for CMF and CNC production. SOC is a waste of vegetable oil extraction, and is composed mainly of cellulose, lignin, hemicellulose and protein [18]. The worldwide production of SOC waste was estimated at about 17.9 million tons [19]. Currently, the SOC waste is classically used as a protein source, complement in animal feed, combustible source and bio-fuels production [18–
20]. Based on these data, it is very interesting to extend the use of SOC waste for production of high-added value materials, i.e. cellulose derivatives (CMF and CNC).
The aim of this work is the extraction of purified cellulose microfibers (CMF) and
cellulose nanocrystals (CNC) from sunflower oil cakes (SOC) waste that, to the best of
authors’ knowledge, has not been reported yet. The conventional processes for CMF and CNC
extraction from lignocellulosic biomass were applied (alkali, bleaching and sulfuric acid
treatments) and the properties of the as-extracted CMFs and CNC were evaluated and
compared to properties of CMF and CNC extracted from other sources. Various
characterisation techniques were used to characterize the materials at different stages of
treatments, including confocal laser scanning microscopy (CLSM), X-Ray diffraction (XRD),
thermogravimetric analysis (TGA), elemental analysis (CHNOS), Fourier transform infrared
spectroscopy (FTIR), zeta potential measurement, atomic force microscopy (AFM),
transmission electron microscopy (TEM) and X-ray photoelectron spectroscopy (XPS). The
rheological behaviour of CNC suspensions, at different concentrations, was also evaluated
using steady shear viscosity measurements and oscillatory dynamic tests. New polymer
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6 nanocomposite materials filled with SOC waste-derived CNC were produced, and the polymer nanoreinforcing ability of the as-produced CNC was evaluated. For that, various CNC contents (1, 3, 5 and 8 wt%) were incorporated into PVA matrix, and the resulting CNC/PVA nanocomposite materials were characterized in terms of their mechanical and transparency properties.
2. Materials and experimental detail
2.1 Materials
The sunflower oil cake (SOC) waste used in this study was obtained from a farm located in Languedoc-Roussillon region, France. The as-obtained SOC waste was firstly ground using a precision grinder (Retch SM100) equipped with a 1 mm sieve. PVA polymer (Mw 31,000–50,000) and all analytical grade chemicals used for the treatment of raw fibers and the extraction of cellulosic materials were purchased from Sigma–Aldrich.
2.2 Preparation of pure cellulose microfibers (CMF)
Pure cellulose microfibers (CMF) were prepared from raw SOC waste using the same processes described in our previous works [6,7,21]. Briefly, ground raw SOC fibers (2 mm) (Fig. 1a) were treated in distilled water for 1 h at 60 °C. Then, the resulted SOC fibers were treated three times with 4 wt% NaOH solution at 80 °C for 2 h under stirring, resulting in alkali treated SOC fibers, after which a bleaching treatment was carried out using a solution made up of equal parts (v:v) of acetate buff er (27 g NaOH and 75 mL glacial acetic acid, diluted to 1 L of distilled water) and aqueous sodium chlorite (1.7 wt% NaClO
2in water).
This treatment was done three times, resulting in pure white colored CMF. In these treatments
the ratio of the fibers to liquor was 1/20 (g/mL). A photograph of the obtained CMF material
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7 is shown in Fig. 1b and the morphology and dimensions were determined by confocal laser scanning microscopy.
2.2 Preparation of cellulose nanocrystals (CNC)
The pre-prepared CMF material was subjected to sulfuric acid hydrolysis to produce CNC in suspension form. The acid hydrolysis process was performed with preheated 64 % sulfuric acid solution at 50 °C under mechanical stirring, according to our previous works reported elsewhere [6,7,21]. Two different hydrolysis times (15 and 30 min) were used to evaluate the effect of hydrolysis time on CNC’s properties. The hydrolysis mixture was diluted with ice cubes to stop the reaction and was washed by successive centrifugations at 12000 rpm at 15 °C for 20 min at each step, resulting in white CNC suspension, which was subjected to a dialysis against distillated water until it reached neutral pH. Afterward, the obtained CNC aqueous suspension was homogenized by using a probe type ultrasonic homogenizer (BRANSON, Sonifier 250) for 5 min in an ice bath, resulting in a white stable CNC gel suspension. Photographs of the obtained CNC
15(CNC extracted at 15 min) and CNC
30(CNC extracted at 30 min) in gel-like suspensions and freeze-dried foams are shown in Fig. 1c-f.
2.3 Preparation of PVA-CNC nanocomposite materials
PVA-based nanocomposite films containing 1, 3, 5 and 8 wt% CNC
30were prepared using solvent casting method (only CNC
30were used for nanocomposites development).
Briefly, 60 ml of CNC aqueous suspension containing the desired amount of CNC
30was
prepared by dilution of a concentrated suspension (3.77 mg/ml). Then, the CNC
30suspension
was sonicated for 1 min and then mechanically stirred for 5 min at 90 °C (using preheated oil
bath), after which the desired amount of PVA powder (99, 97, 95 and 92 wt% regarding to the
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8 total weight of the dried nanocomposite films) was slowly added to the CNC
30suspension and the mixture was mechanically stirred for 1 h at 90 °C. Then, the solutions were kept under agitation until reaching room temperature. The resulting mixture was cast on rectangular Petri dishes (120*120 mm²) and air-dried for 48 h at room temperature to evaporate water. For comparison, neat PVA film control was also prepared by the same procedure without the use of CNC. The obtained films were coded as PVA, PVA-1%, PVA-3%, PVA-5% and PVA-8%
for neat PVA and PVA-CNC
30nanocomposites containing 1, 3, 5 and 8 wt% CNC
30, respectively.
Fig.1: Digital photographs of (a) raw-SOC, (b) extracted CMF and gel-like aqueous suspensions and lightweight foam-like structures of (c,d) CNC
15and (e,f) CNC
302.4 Characterization techniques
(a) (b)
(c) (d)
(e) (f)
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9 Zeta potential measurement of CNC suspensions (CNC
15and CNC
30) was acquired using a Malvern Zeta sizer Nano ZS instrument. For this measurement, a capillary cell was used, and the CNC suspensions were diluted and sonicated for 5 min before being analyzed.
The morphology and dimensions of the as-produced CNC (CNC
15and CNC
30) were determined using transmission electron microscopy (TEM) (Philips CM200 microscope) and atomic force microscopy (AFM) (BioScope Catalyst AFM, Bruker AXS, Santa Barbara, CA).
For TEM analysis, drops of CNC
15and CNC
30diluted suspensions were deposited on the
surface of glow-discharged carbon-coated grids. To enhance the contrast, the samples were
negatively stained in a 2 wt% solution of uranyl acetate. The samples were dried at ambient
temperature before TEM analysis and the measurement was carried out with an accelerating
voltage of 80 kV. For AFM measurement, samples were prepared by depositing droplets of
diluted CNC
30and CNC
15suspensions onto freshly cleaved mica sheets, after being sonicated
for 5 min, and allowing the solvent to dry in air. The measurements were conducted in
tapping mode under ambient temperature at a scan rate of 1.5 Hz. The XPS analysis of freeze-
dried CNC
30and CNC
15was conducted on an Escalab 250 apparatus (Thermo Electron)
equipped with a monochromatic Al Kα radiation at 1486.6 eV. The area of analysis was 400
μm in diameter. The spectra were modified by setting the C-C contribution in the C1 s
emission to 285.0 eV. Fourier Transform Infrared Spectroscopy (FTIR) of all studied samples
was measured on a Tensor27 apparatus. The experiments were recorded in transmittance
mode in the range of 4000–400 cm
−1with a resolution of 4 cm
-1and an accumulation of 16
scans. Thermogravimetric Analysis (TGA) (Mettler Toledo) for all samples was conducted
under a nitrogen atmosphere between 25 and 700 °C, at a heating rate of 10 °C/min. X-ray
diffraction (XRD) characterizations of all cellulosic samples were performed on a Bruker
diffractometer D8 Advance using Cu-Kα radiation. The diffraction patterns were obtained at
diffraction angles between 5 and 35 °, at room temperature.
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10 Ultraviolet–visible (UV–Vis) spectroscopy of the PVA-CNC nanocomposite films was carried out using a Lambda 950 spectrophotometer. The film samples were placed directly in the spectrophotometer test cell, and the air was used as a reference. The optical transmittance of films was measured in the wavelength range of 200–800 nm. Tensile tests were performed using a texture analyzer (TA.XT plus). The tensile specimens were cut in a rectangular shape with dimensions of 80 mm in length and10 mm in width. The gauge length was fixed at 30 mm and the speed of the moving clamp was 5 mm/min. All tests were performed on a minimum of five samples and the reported results were averaged.
3. Results and Discussions
3.1 Processing and physical aspects of cellulosic materials
The raw SOC waste (Fig. 1a) was subjected to alkali and bleaching treatments, resulting in the production of CMF material with high quality and white color, as shown in Fig. 1b.
Generally, the alkali and bleaching treatments are well-known and conventional processes
applied to remove non-cellulosic compounds (lignin, hemicellulose, protein and other
impurities) from raw finely-ground lignocellulosic materials, leading to the extraction of pure
cellulosic fibers [1,11,17]. Once CMF are produced, sulfuric acid hydrolysis was applied to
solubilize the amorphous parts of CMF, leaving the crystalline parts unaltered, which are
identified as CNC. The as-isolated CNC (CNC
30and CNC
15) showed a gel-like suspension
after ultrasonic homogenization process, as illustrated in Fig. 1c,e, which is a typical behavior
of sulfuric acid hydrolyzed CNC [7]. Usually, CNC produced with sulfuric acid can be
completely suspended at the individual nanocrystal level in aqueous solution by electrostatic
repulsion, which are due to sulfate groups negative charges, introduced on the surface of CNC
during sulfuric acid hydrolysis [22–25]. The colloidal stability of CNC aqueous suspension,
which can be deduced from zeta potential measurements, is crucial for nanocomposite
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11 development using water-soluble polymers as matrices [26]. Herein, the produced CNC suspensions showed zeta potential values of – 25.6 and – 30.7 mV for CNC
15and CNC
30, respectively. It was reported that CNC suspension could be considered stable when the absolute value of zeta potential is superior to 25 mV [27]. From this finding, it should be noted that the increase of hydrolysis time resulted in CNC suspensions with high negative zeta potential. Furthermore, higher negative zeta potential values can indicate the presence of a higher number of sulfate groups inserted on the surface of CNC, as will be further shown by XPS analysis (see below).
Fig.2: CLSM images of (a,b) Raw SOC and (c,d) extracted CMF
3.2 Morphologic analysis and dimensionality
Fig. 2 illustrates the CLSM images obtained for raw finely-ground SOC and the extracted CMF. As can be seen, raw SOC exhibits rough surface and wrapped fiber bundles with relatively large dimensions (Fig. 2a,b), because the raw SOC is composed of various compounds (lignin, hemicellulose, cellulose, protein and other impurities) organized in a complex structure [18]. On the other hand, CLSM observation revealed individual CMF with 1
2
(a) (b)
(c) (d)
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12 a homogeneous distribution of length and diameter (Fig. 2c,d), suggesting that the alkali and bleaching treatments were suitable for removal of all non-cellulosic compounds, leaving individual microsized cellulose fibers (CMF) [23,28]. The average diameter and length of CMF were determined by analyzing the obtained micrographs using ImageJ software. It was found that the diameter and length are about 20 ± 6 µm and 226 ± 34 µm, respectively.
Comparatively, the measured diameter of CMF from SOC is comparable to that obtained for CMF extracted from vine shoots waste (≈ 25 µm) [21], and higher than that obtained for CMF from sugarcane bagasse (5-10 µm) [29], using the same bleaching treatment. Importantly, these SOC-derived CMF can be used as mechanical reinforcing fillers for polymer composites development using melt processing techniques, such as melt extrusion process. In this investigation, it was found that the extracted CMF are suitable for acid hydrolysis process to produce CNC.
Fig.3: AFM and TEM images of (a,b) CNC
15and (c,d) CNC
30Due to their nanosized dimensions, the extracted CNC (CNC
15and CNC
30) were visualized by AFM and TEM observations and their shapes and dimensions were determined.
Fig. 3 illustrates the obtained AFM and TEM micrographs for both extracted CNC,
(a)
(b)
(c)
(d)
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13 confirming their successful extraction from SOC-derived CMF via sulfuric acid hydrolysis process. Both CNC (CNC
15and CNC
30) exhibited needle-like shapes with good dispersion on the substrate, due to the electrostatic repulsion between individual CNC generated from the negatively charged CNC surfaces [30]. The average diameter and length were measured at 9
± 3 nm and 354 ± 101 nm for CNC extracted at 15 minutes (CNC15), and 5 ± 2 nm and 329 ± 98 nm for CNC extracted at 30 minutes (CNC
30), respectively. This finding about CNC dimensions confirmed that the hydrolysis time has a direct effect on the final geometric dimensions of CNC. Additionally, these observations confirmed that a hydrolysis time of 15 min was efficient to extract CNC from SOC-derived cellulose, which is very low than that used for CNC extraction from other sources, using sulfuric acid hydrolysis [23,30,31].
Fig. 4: (a,b) XPS survey spectrum and (c,d) high-resolution of S2p photoelectron spectrum of CNC
15and CNC
30samples.
3.3. Structure and surface functionality
1200 1000 800 600 400 200 0
0 1x105 2x105 3x105 4x105
Acount / s
Binding energy (eV) CNC15
(a)
1200 1000 800 600 400 200 0
0 1x105 2x105 3x105 4x105
Acount / s
Binding energy (eV)
CNC30 (b)
180 178 176 174 172 170 168 166 164 162 160 158 4x103
5x103 6x103 7x103 8x103 9x103
Acount / s
Binding energy (eV) CNC15
(c)
178 176 174 172 170 168 166 164 162 4x103
5x103 6x103 7x103 8x103 9x103
Acount / s
Binding energy (eV) CNC30 (d)
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14 The chemical composition and the number of sulfate groups grafted on the surface of CNC were evaluated by XPS measurement. Fig. 4 shows the XPS survey spectrum of the extracted CNC (CNC
15and CNC
30). Both CNC exhibit two main peaks observed at around 531 and 285 eV in the survey spectra, which correspond to the O 1s and C 1s, respectively [32]. Furthermore, from a high-resolution of S2p photoelectron spectrums of CNC
15and CNC
30shown in Fig 4, a small S2p peak is observed at around 167 eV, which is attributed to surface sulfation caused by the sulfuric acid hydrolysis [7]. The surface O/C ratio was determined at 0.78 and 0.70 for CNC
15and CNC
30, respectively. The obtained values of O/C ratio are comparable with those reported for sulfuric acid hydrolysed CNC [7,33], and smaller than the theoretical value of untreated pure cellulose [32].
The atomic percentage of S element was determined at 0.31 % and 0.37 % for CNC
15and CNC
30, respectively. These values correspond to ~ 1.57 and ~ 1.88 sulfate groups per 100 anhydroglucose units for CNC15 and CNC30, respectively, based on the calculation procedure reported elsewhere [34]. It is generally known that the amount of sulfate groups on the surface of the CNC depend on the sulfuric acid concentration and the hydrolysis time [34].
Herein, the obtained amount of sulphate groups is comparable to sulfuric acid hydrolyzed CNC extracted from microfibrillated cellulose found by Li et al. [34].
3.4 Crystalline structure and crystallinity
XRD patterns obtained for different studied cellulosic materials are shown in Fig. 5. All
samples exhibited three major diffraction peaks at around 15.1°, 16.6° and 22.5°,
corresponding to crystallographic planes 11̅0, 110 and 200, respectively. From this result, it
is confirmed that all samples exhibited cellulose I structure, which is typically encountered for
biosourced cellulosic materials and their extracted pure cellulosic parts (cellulose fibers and
CNC), using conventional process, such bleaching and acid hydrolysis [23,30,31].
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15 The crystallinity index (CrI) of the raw SOC, CMF, CNC
15and CNC
30was determined at 49 %, 62 %, 75 % and 87 % , respectively, according to calculations using the following equation: 𝐶𝑟𝐼 = [
𝐼002−𝐼𝐼𝐴𝑚𝑜𝑟𝑝ℎ002
]× 100, where I
200is the peak intensity of the (200) reflection and I
amorphis the minimum intensity between the (110) and (200) peaks at about 18.7° [30,35].
From this result, it is confirmed that the CrI is increased after chemical treatment. Similar finding has been reported elsewhere for treatment of other biosourced materials [23,31]. The increasing of CrI after the bleaching treatment (from raw SOC to CMF) is attributed to the removal of non-cellulosic compounds, such as lignin and hemicellulose [30]. Furthermore, the CrI increased from 62 % for CMF sample to 75 and 87 % for CNC
15and CNC
30, respectively, attributed to the removal of amorphous domains in the cellulose chains without destruction of the crystalline domains, when CMF was subjected to the sulfuric acid hydrolysis [2,30].
Fig.5: XRD patterns of raw SOC, CMF, CNC
15, CNC
303.5 Thermal degradation behaviour
10 20 30 40
110
CNC30
CNC15 CMF
In ten si ty (a. u )
2 Theta (°)
Raw SOC 200
110 -
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16 The thermal degradation behaviour of raw SOC, CMF, CNC
15and CNC
30was investigated by thermogravimetric analysis (TGA/DTG). The resulted TGA and DTG curves are illustrated in Fig. 6. All samples showed a small weight loss around 100 °C due to the evaporation of adsorbed moisture, which is related to the hydrophilic nature of the cellulosic materials [31]. The raw SOC sample showed a multistep degradative behaviour between 185 and 400 °C due to the presence of several components that are characterized by different degradation temperatures. In general, the thermal decomposition of raw lignocellulosic materials begins at a relatively lower temperature for hemicelluloses followed by an early stage of degradation of lignin molecules and then decomposition of cellulose [7,28,31]. The DTG maximum degradation peaks of these compounds are grouped into one broad peak (185- 400 °C) (Fig. 6b). The CMF sample showed only one-step degradation process at 230-400 °C range with a DTG maximum peak at 345 °C. This decomposition is due to degradation processes of cellulose, such as dehydration, decarboxylation, depolymerization and decomposition of glycosyl units [6,23]. This result confirmed the total removal of non- cellulosic compounds after the bleaching treatment, resulting in pure CMF with relatively high thermal stability [23,28].
Fig.6:(a) TGA and (b) DTG curves of raw SOC, CMF, CNC
15andCNC
30(under nitrogen atmosphere)
Raw SOC CMF
100 200 300 400 500 600 700
0 20 40 60 80 100
Weight (%)
Temperature (°C)
(a) CNC15
CNC30
100 200 300 400 500 600 700
DTG (%/°C)
Temperature (°C) Raw SOC CMF CNC15 CNC30 (b)
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17 The extracted CNC
15and CNC
30samples also showed one-step degradation process at low temperature (160 -300 °C) with a DTG maximum peak at 264 and 255 °C, respectively.
The lower degradation temperature of CNC is due to the presence of sulfate groups on their surfaces, having a catalytic effect in the thermal decomposition mechanism, which results in reduced thermal stability for sulfuric acid hydrolyzed CNC [23,31,36]. It is noteworthy that the CNC extracted at 30 min (CNC
30) showed a reduced thermal stability regarding CNC extracted at 15 min (CNC
15). This finding can be explained by the content of sulfate groups present on the surface of CNC
15and CNC
30. As stated above, the sulfate groups content for CNC
15and CNC
30was measured from XPS analysis at 1.57 and 1.88 sulfate groups per 100 anhydroglucose units, respectively, indicating that the sulfate content is increased with increasing of the hydrolysis time. From this result, it can be concluded that the catalytic effect is more pronounced in CNC containing a high content of sulfate groups (CNC
30), in comparison to those containing a low content of sulfate groups (CNC
15), resulting in reduced thermal stability for CNC extracted at relatively high hydrolysis time (CNC
30).
3.6 Rheological properties
The rheological properties of CNC in aqueous solutions are very important for their preparation, processing and combination with other materials [3]. Herein, only CNC
30suspensions were selected to evaluate the rheological properties, due to their high crystallinity
and relatively high aspect ratio. Fig. 7 depicts the shear viscosity curves within the entire
shear rate range (0.01–100s
-1) of CNC
30aqueous suspensions at different concentrations (0.1-
1%). Obviously, the viscosity was gradually increased with increasing of CNC
30concentration from 0.1 to 1%, which is a typical behaviour for stable aqueous suspensions of
rigid nanoparticles [37,38]. All CNC
30concentrations showed typical shear-thinning
behaviour (pseudo-plastic phenomenon), as confirmed by the viscosity decrease with the
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18 increase in the shear rate over the entire range. It may be due to the gelation of CNC
30at very low concentrations (0.1 to 1%), which could be generated from strong interconnection degree and collision possibility of the CNC
30in their gelled form. It is noted that our observation is very different from that typically observed for CNC aqueous suspensions extracted from other sources at different extraction conditions [34,37], in which the viscosity profile shows a three- region behaviour (i.e. Newtonian plateau at low shear rates followed by a shear thinning region at intermediate shear rates and another plateau at high shear rates). Following this, it was reported that CNC
30suspensions are isotropic at low concentrations (up to 3 %), and phase separates to liquid crystalline and isotropic domains at higher concentration [37].
Herein, it was found that the extracted CNC
30suspensions behave as rheological gels even at
low concentrations (from 0.1 to 10 %) with single shear thinning behaviour. This finding may
be related to the original bio-sourced material used in this study (raw SOC) and sulfuric acid
hydrolysis conditions as well as the relatively high CNC
30aspect ratio (65.8). This
observation is similar to that reported in our previous work for CNC
30extracted from
miscanthus fibers using the same sulfuric acid hydrolysis conditions [3]. Additionally, the
same trend was reported by Xu et al. [39] who observed a typical single-region shear thinning
behaviour for rod-like shaped CNC suspensions extracted from commercial microcrystalline
cellulose, but at relatively high concentrations (1 – 6 wt%).
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19 Fig.7: Shear viscosity vs. shear rate of CNC
30aqueous suspensions at different
concentrations
The profiles of storage modulus (G’), loss modulus (G”) and tangent delta (Tanδ) of CNC
30suspensions at different concentrations as a function of frequency are represented in Fig. 8. Clearly, the G’ and G” were increased with increasing CNC
30concentration, indicating that a strong CNC
30network is formed with increasing the concentration. Over the whole investigated range of frequency, the G’ is higher than its corresponding G” (Tanδ < 1) for all CNC
30concentrations (0.1-1%), indicating that CNC
30suspensions display typical gel-like properties due to the formation of strong network generated by electrostatic interactions, hydrogen bonds and Van Der Waals forces [40]. This behaviour is more pronounced for CNC
30concentration higher than 0.2%, in which G’ and G” are almost independent of angular frequency (Fig. 8a,b). Remarkably, it should be noted that G’ and G” are almost coincident in a very wide range of frequency for CNC
30concentrations of 0.1 and 0.2 %, indicating that the concentration of 0.2 % can be considered as a critical percolation for strong network gel formation. In fact, the CNC possess many hydroxyl groups on their surface. These highly active groups enable the CNC
30to greatly interact with each other as well as with the adjacent
0.1% 0.5%
0.2% 0.6%
0.3% 0.7%
0.4% 1.0%
10-2 10-1 100 101 102
10-2 10-1 100 101 102 103 104
Viscosity (Pa.s)
Shear rate (1/s)
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20 water molecules, thus displaying gel-like behaviour [3]. Similar trends were reported for CNC suspensions at relatively high concentrations [37,41].
Fig.8: (a) Storage modulus (G’), (b) Loss modulus (G’’) and (c) Tang delta (δ) Vs. Frequency of CNC
30aqueous suspensions at different concentrations.
3.7 Processing and FTIR analysis of nanocomposite films
In order to explore the usefulness of the extracted CNC for polymer nanocomposites development, various CNC contents (1, 3, 5, and 8wt%) were incorporated into PVA polymer. Only CNC
30were selected for developing PVA nanocomposites, because the CNC
30showed high crystallinity (87%) and relatively high aspect ratio (65.8) with regard to CNC
15(crystallinity of 75 % and aspect ratio of 39.3). It is expected that the CNC
30have a high reinforcing ability for polymer nanocomposites development. On the other hand, the PVA polymer was chosen due to its good film-forming ability and its high compatibility with CNC.
0.1% 0.3% 0.5% 0.7%
0.2% 0.4% 0.6% 1 .0%
10-2 10-1 100 101
10-3 10-2 10-1 100 101 102 103 104 105
G' (Pa)
Frequency (Hz)
(a)
0.1% 0.3% 0.5% 0.7%
0.2% 0.4% 0.6% 1 .0%
10-2 10-1 100 101
10-3 10-2 10-1 100 101 102 103 104 105
G'' (Pa)
Frequency (Hz)
(b)
0.1% 0.3% 0.5% 0.7%
0.2% 0.4% 0.6% 1 .0%
10-2 10-1 100 101
0.25 0.50 0.75 1.00 1.25 1.50
Tang Delta
Frequency (Hz)
(c)
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21 It is worth noting that the interfacial interaction between the polymer and CNC is an important parameter to define the microstructure, CNC dispersion state and final properties of the developed nanocomposite material. In this case, both PVA and CNC possess abundant hydroxyl groups, which can be involved in the formation of hydrogen bonds between them, ensuring high interfacial interaction, and hence the good CNC dispersion [6].
Fig.9: FTIR spectra of PVA-based nanocomposite films at different CNC
30loadings
FTIR analysis was carried out to evaluate the structure of CNC-filled PVA nanocomposite films, and the obtained spectra are illustrated in Fig 9. The neat PVA film shows a broad peak at 3286 cm
−1corresponding to stretching vibration of OH group, due to the strong intermolecular and intramolecular bonds. The peak observed at 2966 cm
−1is assigned to CH alkyl group stretching, and the peak at 1731 cm
−1is attributed to the stretching mode of C=O and C=C in the acetate group. The peak observed at 1683 cm
−1is due to the deformation mode of H-O-H group, and the peaks 1444 and 1357 cm
−1are assigned to the
4000 3500 3000 1500 1000
% T ran smi ttan ce (a. u )
Wavenumber (cm-1) PVA-8%
PVA-5%
PVA-3%
PVA-1%
Neat PVA
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22 bending mode of CH group. The peak at 1114 cm
−1is representative of the bending mode of C-O in the acetate group, respectively [13,42,43].
For CNC-filled PVA nanocomposites, the incorporation of CNC leads to small variations on the FTIR spectra. A slight change in the intensity of the OH stretching vibration (3286 cm
−1) can be observed. This very slight change can be attributed to the interfacial interaction between the hydroxyl group of CNC and PVA matrix [43]. Additionally, the peak at 1114 cm
-1
was split into two peaks at 1139 and 1058 cm
-1, corresponding to the asymmetric ring breathing mode of cellulose and to the C-OH bending vibrations of alcohol groups present in cellulose, respectively [13,44]. This effect is more evident at high CNC content (PVA-8%
sample). These very slight variations along with regular neat PVA peaks, confirmed the presence of CNC in PVA matrix and indicated that the incorporation of CNC did not influence the molecular and chemical structure of PVA. These findings are in accordance with the literature for PVA-based nanocomposite materials [6,42,45].
3.8 Tensile properties of nanocomposite films
The tensile properties of CNC-filled PVA nanocomposites at different CNC weight fractions were probed by uniaxial tests. The measured tensile modulus, tensile strength and strain at break are illustrated in Fig. 10. It can be seen that the modulus and strength of PVA polymer were gradually increased with the addition of CNC at different weight fractions. The tensile modulus and strength of neat PVA films were found to be 934 MPa and 37 MPa, respectively. After the addition of CNC, the modulus and strength improved to 1783 MPa and 67 MPa at CNC content of 5 wt%, and to 1940 MPa and 66 MPa at CNC content of 8 wt%.
These increases corresponded to a gain in the modulus and strength of 91 % and 81 % for 5 wt% CNC, and 107 and 78 % for 8 wt% CNC compared to the neat PVA matrix, respectively.
These findings confirm that the SOC-derived CNC have a high ability to improve the tensile
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23
properties of water-soluble polymers. From the results already published in the literature, the
source of CNC and their extraction conditions may have direct impact on the mechanical
properties of the nanocomposite. CNC isolated from different biosourced materials showed
different reinforcements for PVA polymer [6,11–15,46]. To demonstrate the polymer
reinforcing ability of SOC-derived CNC developed in this work, we performed a comparison
with CNC extracted from various sources, as shown in Table 1. From this comparison, the
CNC developed in this work have a greater ability to improve the tensile modulus and
strength of PVA than CNC from commercial microcrystalline cellulose, phormium tenax, flax
fibers, banana pseudo stems and sugarcane bagasse (Table 1). Fortunati et al. [13] reported
that 5 wt% CNC, extracted from microcrystalline cellulose, phormium tenax and flax fibers at
the same extraction conditions used in this work, resulted in only 14.2 % (microcrystalline
cellulose) and 44.2 % (flax fibers) increase of modulus and strength, respectively. El Miri et
al. [14] reported an increase of 77 % and 12 % of the modulus and strength with the addition
of 5 wt% CNC extracted from sugarcane bagasse at the almost the same extraction conditions
(64 % sulfuric acid, 55 °C, 30 min). Moreover, CNC extracted from cotton fibers at different
extraction condition showed a comparable increase of modulus (100 % at 6 wt% and 114.9 %
at 9 wt%), but only 13.4 % and 19.2 % increase for strength were obtained at these CNC
weight fractions [11]. However, the CNC prepared in this work provided less reinforcing
ability for PVA than that of CNC from corncob, oil palm pulp and red algae (Table 1), even
for the same extraction conditions. CNC from oil palm pulp showed an increase of 291 % and
122 % for the modulus and strength at only 4 wt % CNC [15], which are very large than those
obtained from CNC developed in this work. All these results confirm that the polymer
reinforcing ability of CNC is strongly related to the original source as well as the extraction
methods and experimental conditions. Furthermore, it is also strongly dependent on the CNC
characteristics, such as the aspect ratio, crystallinity and morphology [12,46]. Remarkably,
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24 based on the rheological properties of CNC aqueous suspensions (Fig. 7-8), it was observed that CNC form a strong network gel at concentrations higher than 0.2 %, which is considered as a critical percolation concentration. However, this behaviour is not observed in the CNC- filled PVA nanocomposite films, in which a remarkable improvement of mechanical properties was observed. One reason for not observing a critical percolation for improving mechanical properties may be the formation of interfacial interactions between the macromolecular chains of PVA polymer and CNC that reduce the interactions CNC-CNC, and since the PVA polymer is less rigid than the nanocrystals, the percolation effect was not observed.
Meanwhile, the maximum strain of neat PVA (90 %) was reduced to 64 % and 59 %,
when 5 and 8 wt% CNC were added, which corresponds to a decrease of 29 and 34 % in
comparison with neat PVA, respectively. This trend is due to the stiffening effect of rigid
nanoparticles, which leads to significant local stress concentrations and reduced strain to
failure [46,47]. This finding is in accordance with the literature for acid hydrolysed CNC-
filled PVA nanocomposite materials, in which the maximum strain was gradually reduced
with the addition of CNC at various weight contents [6,11,15].
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25 Fig.10: (a) Tensile modulus, (b) Tensile strength and (c) elongation at break of PVA-based
nanocomposite films at different CNC
30loadings
Herein, we demonstrated that the newly extracted CNC from SOC waste have a superior reinforcing ability to improve the tensile properties of polymer-based nanocomposite materials. This improvement can be attributed to the high quality of CNC in terms of morphology and shape and their excellent characteristics, especially the aspect ratio (65.8) and the crystallinity (87 %). The functionalized surface of CNC (hydroxyl and sulfate groups) and its compatibility with PVA polymer, can result in uniform dispersion of CNC throughout the formation of hydrogen bonds between the macromolecular chains of PVA and the functionalized surface of CNC, thus resulting in efficient load transfer, and hence improving the tensile properties of PVA polymer. Such improvements confirmed that the as-prepared CNC have a great potential for developing nanostructured PVA-based composite materials
Neat PVA PVA-1%
PVA-3%
PVA-5%
PVA-8%
0 200 400 600 800 1000 1200 1400 1600 1800 2000 2200
Tensile Modulus (MPa)
(a)
Neat PVA PVA-1%
PVA-3%
PVA-5%
PVA-8%
0 10 20 30 40 50 60 70 80
Tensile Strenght (MPa)
(b)
Neat
PVA PVA-1%
PVA-3%
PVA-5%
PVA-8%
0 10 20 30 40 50 60 70 80 90 100
Elongation at break (%)
(c)