# Hybrid Monolith of Graphene/TEMPO-Oxidized Cellulose Nanofiber as Mechanically Robust, Highly Functional, and Recyclable Adsorbent of Methylene Blue Dye

Authors: Asif Hussain; Jiebing Li; Jun Wang; Fei Xue; Yundan Chen; Tallal Bin Aftab; Dengxin Li
Journal: Journal of Nanomaterials
 (2018)

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## Abstract

Herein we demonstrate first report on fabrication, characterization, and adsorptive appraisal of graphene/cellulose nanofibers (GO/CNFs) monolith for methylene blue (MB) dye. Series of hybrid monolith (GO/CNFs) were assembled via urea assisted self-assembly method. Hybrid materials were characterized by scanning electron microscopy, Fourier transform infrared spectroscopy, X-ray diffraction patterns, Raman spectroscopy, elemental analysis, thermogravimetric curve analysis, specific surface area, surface charge density measurement, and compressional mechanical analysis. It was proposed that strong chemical interaction (mainly hydrogen bonding) was responsible for the formation of hybrid assembly. GO/CNFs monolith showed mechanically robust architecture with tunable pore structure and surface properties. GO/CNFs adsorbent could completely remove trace to moderate concentrations of MB dye and follow pseudo-second-order kinetics model. Adsorption isotherm behaviors were found in the following order: Langmuir isotherm > Freundlich isotherm > Temkin isotherm model. Maximum adsorption capacity of 227.27 mg g−1 was achieved which is much higher than reported graphene based monoliths and magnetic adsorbent. Incorporation of nanocellulose follows exponential relationship with dye uptake capacities. High surface charge density and specific surface area were main dye adsorptive mechanism. Regeneration and recycling efficiency was achieved up to four consecutive cycles with cost-effective recollection and zero recontamination of treated water.


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## Body

## 1. Introduction

The development of competent and eco-friendly adsorbent material for water decontamination has been an ever-growing area for academia and industry, in particular aromatic organic dyes, which possess many hazards such as toxic [1], nonbiodegradable [2], aesthetically objectionable, and light restrictive nature in aqueous environment [1, 3]. Among the various treatment techniques such as biological treatment [4], ozone oxidation [4], catalytic degradation [5], photocatalytic oxidation [6], coagulation and flocculation [3], nanofiltration membrane [7], and unsaturated polyester resins [8], adsorption is the most attractive due to competency for variety of organic dyes, insensitivity to toxic pollutants [9], efficiency for low concentration range [10], easiness of operating, and being economical process [9, 11–21]. Carbon materials in the form of activated carbon are historically dominant for dye decontamination in view of chemical stability, high surface area, and functional active sites [16, 20, 22–26]. Recently, graphene oxide (GO) produced by soft chemistry techniques arouse as highly efficient [10, 15, 21, 27–29] and low cost carbon nanoadsorbent [11, 30] followed by various carbon materials including single/or multiwall carbon nanotubes, since it owns many superior properties such as large theoretical surface area (2630 m2/g) [31], mechanical flexibility, high charge carrier mobility, and chemical stability [32]. Apart from high efficiency, simple and economical recollection cannot be overlooked as well, in view of recontamination through introduction of nanohazard after treatment. So, exploring the eco-friendly formulation couple with high efficiency is of great concern and widely open field.Unique structural features of GO, which is composed of planner sp2 type random aromatic domains and sp3 hybridized sites containing plenty of oxygen functional groups (epoxy, hydroxyl, and carboxyl groups), make this nanomaterial amphiphilic. For example, oxygen functionality imparts high hydrophilicity, while aromatic domain renders GO sheets hydrophobic character [30]. Likewise, oxygen functional groups make this nanomaterial behave like polymer and form variety of covalent or noncovalent bonding reactions [32]. Recently, by taking advantage of fundamental chemistry of graphene oxide a diverse range of functional adsorbents have been formulated, for instance, chemically reduced graphene [27], sponge [12, 31], hydrogels/aerogels [18, 33], and magnetically separable adsorbents [9, 19, 34–37] to improve its competency and recollection issues. However, it suffers from low structural and adsorption capacities, while use of external magnate is practically not feasible as well. It has been reported that the affinity of dye pollutants toward graphene based adsorbent is attributed to active functional sites and pure aromatic domains or combination of them [9, 10, 12–15, 18, 19, 21, 26, 27, 29, 31, 33–36, 38–40]. The former one can bind hydrophilic organic species via noncovalent forces such as vender wall and electrostatic and hydrogen bond interaction, whereas later one forms strong π-π staking/or hydrophobic interaction with benzene ring of organic compounds. It is also widely accepted that porous material can considerably improve the dye capturing ability due to improving surface area. It means that strong interaction of certain pollutant molecules could significantly be improved through modification of structural, surface, and electronic flexibility of graphene. In this regard, self-assembly of graphene (GO) offers simple and scalable approach to integrate the superior properties of 2D nanobuilding blocks into interconnected 3D monolithic materials [41]. The interconnected pores arising from nanosize 2D sheets provide unique physicochemical properties such as microstructure, charge mobility, large surface area, and surface functionality depending on the preparation conditions and reacting precursors [32, 42]. So far, different polymers/or molecules, for example, chitosan [43], resol [44], polymer [45, 46], carbohydrate [43], PVA [47], divalent metal ions [41], carbon nanotube [33], DNA [48], thiourea [31], aqueous ammonia solution [49], luffa sponge [12], and phenolic acid [50], have been reported for the assembly of macroscopic graphene by various physical or chemical interactions. However, very little work was reported for water decontamination applications. Most of the reported work is either selective for oil removal due to highly hydrophobic nature [49] or suffering from mechanically fragile three-dimensional structures and low adsorption capacity [12, 15, 18, 31, 33, 51] due to insufficient functional active sites and large pore size which considerably limit its easy regeneration-recycling properties, thus being not feasible for industrial applications.Nanocellulose biopolymer recently arose as an attractive carbon material due to low cost and being biodegradable and green in nature [52, 53]. Among the various methods, the production of nanocellulose fibers through 2,2,6,6-tetramethyl-1-piperidinyloxy (TEMPO) mediated selective oxidation [54–56] offers the nanolevel dispersibility of individual fibrils in pure aqueous medium, since it possesses high density of sodium carboxylated moieties on the fibril surfaces [55, 56]. Moreover, excellent mechanical strength (140 Mpa) and highly reactive moieties (COONa+) of this nanomaterial allow one to produce variety of mechanically robust functional composites [52, 53] including hydro/aerogels [57]. Inspired by the intrinsic properties of graphene oxide and nanocellulose fibrils, incorporation of these nanobuilding blocks during self-assembly technique could be a promising approach in order to optimize physicochemical properties and functionality of interconnected porous monolith for industrial application, since graphene can form variety of bonding interactions with this nanofiller such as electrostatic repulsion/attraction and hydrogen bonding. To our knowledge, self-assembly phenomena between graphene oxide and TEMPO-oxidized nanocellulose fibers hitherto are not practiced for the fabrication of monolith material.In this study, herein we report on fabrication, characterization, and adsorptive evaluation of graphene/cellulose nanofibers (GO/CNFs) monolith for methylene blue (MB) dye. Series of hybrid monoliths (GO/CNFs) were assembled via urea assisted self-assembly method. Monolith was characterized by scanning electron microscopy (SEM), Fourier transform infrared spectroscopy (FTIR), X-ray diffraction (XRD), Raman spectroscopy, elemental analysis, thermogravimetric curve analysis (TGA), specific surface area (SSA), surface charge density measurement, and compressional mechanical analysis. Adsorption behaviors of dye were examined by equilibrium adsorption isotherms model (Langmuir, Freundlich, and Temkin isotherm) and kinetic model (pseudo-first kinetics and second-order kinetics). Statistical relationship between adsorption capacity and incorporated nanocellulose concentration was established. Regeneration and recycling experiment were performed for four consecutive cycles. Moreover, comparison of MB adsorption capacity with previously reported works was discussed here.


## 2. Experimental Section

### 2.1. Material

Natural flakes of graphite (500 mesh) were provided by Shanghai Yifan Graphite Co. Ltd. (China). Potassium permanganate (KMnO4), sodium nitrate (NaNO3), hydrogen peroxide (H2O2, 30%), sodium hydroxide (NaOH), sulfuric acid (H2SO4, 98%), microcrystalline cellulose (MCC), sodium hypochlorite solution (NaClO, 9%), sodium bromide (NaBr), carbamide, methylene blue dye (C16H18ClN3S, MW: 373.9 g/mol), and 2,2,6,6-tetramethylpiperidine-1-oxyl (TEMPO) were supplied by Sinopharm Chemical Reagent Co. Ltd. (China) and used without any further purification.


### 2.2. Preparation of Graphene Oxide

Graphene oxide (GO) was prepared with slight modification of published work about Hummers and Offeman method [58]. Briefly, 5 g of graphite powder was treated with sodium nitrate (2.5 g) and sulfuric acid (115 ml, 98%); then oxidation was initiated by slow addition of potassium permanganate (15 g) on ice bath (4°C) under constant stirring for 2 h. After that, obtained slurry was set on water bath (35°C, 2 h) under stirring; then 230 ml of distilled water was added and kept at 98°C for further 15 min. After completing the oxidation, the reaction was quenched by adding 700 ml of distilled water followed by hydrogen peroxide (30%, 50 ml). Upon quenching, the color of solution changes from dark brown to bright yellow. The product was centrifuged and purified via washing with HCl (1 : 10, 500 ml) followed by plenty of deionized water until pH = 6. Finally, the product was subjected to freeze-drying and labeled as GO for further use.


### 2.3. Preparation of Carboxylated Cellulose Nanofibers

The primary hydroxyl groups on the surface of fibrous microcrystalline cellulose were selectively oxidized to sodium carboxylate groups (COONa+) using TEMPO/NaOCl/NaBr system according to previous methods [54, 55] and stored at 4°C for further use (see ESI Section 1). To prepare carboxylated nanocellulose fibers (CNFs), suspension of sodium carboxylate cellulose fibers (TOCNFs) was mechanically homogenized (8000 rpm, 10 min) for further defibrillation and centrifuged (12000g, 10 min) for the removal of partly fibrillated fraction. Then, never dry TOCNFs were diluted using ultrapure water (0.1%) and treated with HCL (1 M) for 3 hours for ion exchange and conversion of sodium carboxylated type CNF-COONa+ to CNF-COOH+. The product was washed with water until pH = 4.0 and labeled as CNFs. Finally, desired concentration of suspension (16 mg ml−1) was obtained and stored at 4 Co for further experimental work. The concentration of CNFs was calculated by the weight difference of CNFs suspension (10 ml) after freeze-drying. The carboxyl content of nanofibers (0.547 mmol/g) was estimated according to ESI Section 1. The successful conversion was confirmed by the appearance of new peak at 1732 cm−1 in FTIR spectra (Figure S1).


### 2.4. Fabrication of GO/CNFs Hybrid Monolith

To fabricate the GO/CNFs porous monolith, first, well-dispersed suspension of freeze-dried graphene oxide (2 mg ml−1, 200 ml) was obtained by tip sonication in ultrapure water. Secondly, fixed amount of carbamide salt (800 mg) was mixed with graphene solution (pH = 4.5, 1 h); then known volume (x = 0, 1, 3, 5, and 7 ml) of separately prepared carboxylate cellulose nanofibers (CNFs) suspension was added to graphene/carbamide suspension followed by stirring overnight to obtain the homogenous solution. After that, 25 ml of mixture was sealed in Teflon-lined stainless steel autoclave (50 ml) and placed at 180 Co for hydrothermal treatment (5 hours). After cooling the reactor naturally at room temperature, cylindrical shape monolith was obtained (see graphical Scheme 1). The monolith was dipped into distilled water to remove residual carbamide and subjected to vacuumed freeze-drying (48 h). Product was labeled according to incorporated nanocellulose content as GO/CNF0, GO/CNF1, GO/CNF3, GO/CNF5, and GO/CNF7, respectively, and used for further characterization and dye adsorption studies (see detail in ESI Section 2).Scheme 1
Graphical illustration of GO/CNFs monolith assembly.


### 2.5. Material Characterization

Morphology and microstructure of monolith were analyzed by scanning electron microscopy (SEM-S420, HITACHI) equipped with a field-emission electron gun. The Fourier transform infrared (FTIR) spectra were recorded over the range of 400–4000 cm−1 using KBr pressed disc method (NICOLET-6700, UK). Raman spectra were recorded via Renishaw Raman spectrophotometer (NEXUS-670, USA). The percentage of carbon (% C), hydrogen (% H), and nitrogen (% N) contents were determined by element analyzer (ELMENTAR, VAIRO EL-III, Germany). X-ray diffraction (XRD) patterns were recorded by X-ray diffractometer (RIGAKU, D/Max-2550pc) at operating voltage of 40 kV, current density 200 mA, and 2θ scanning rage of 10°–70° using Cu Kα radiation. Thermal stability of materials was measured by thermogravimetric analyzer (NETZSCH, TG-209F1, Germany) under nitrogen environment and temperature range of 30–900°C using heating rate of 10°C min−1. Compression property of monolith was measured by dynamic mechanical analyzer (HY-940FS, China). Zeta potential measurement (ZP) was carried out by ZETASIZER (Nano-ZS90). Specific surface areas (SSA) of samples were calculated by the following formula [18]:(1)SSA=NAAMBCo-CeVMMBMS,where NA is Avogadro’s number (6.023 × 1023 mol−1), AMB is the covered area per MB molecules (typically assumed to be 1.35 nm2), Co and Ce are the initial and equilibrium concentration of MB, respectively, V is the volume of MB solution, MMB is the relative molecular mass of MB, and MS is the mass of sample.


### 2.6. Dye Adsorption Studies

Aqueous solutions of methylene blue (MB) dye with different concentration (10–100, 150, 200, 250, and 300 mg L−1) were prepared by successive dilution of stock solution (1000 mg L−1) in deionized water. The residual MB concentration was measured by UV-spectrophotometer (Shimadzu UV-spectrophotometer, UV-1800) using an absorbance at λ = 664 nm. Dye adsorption spectra were recorded over the range 200–800 nm using UV-VIS-NIR spectrophotometers (UV-3600, SHIMADZU). Dye adsorption quantity (mg g−1) and percentage removal (%) were calculated by (2) and (3), respectively:(2)Qe=Co-CeVW,(3)Removal%=Co-CtCo×100,where Co (mg L−1) and Ct (mg L−1) represent the initial and final (t) time concentrations of dye in the solution. V (L) is the volume of the solution and W (g) is the mass of adsorbent.


## 2.1. Material

Natural flakes of graphite (500 mesh) were provided by Shanghai Yifan Graphite Co. Ltd. (China). Potassium permanganate (KMnO4), sodium nitrate (NaNO3), hydrogen peroxide (H2O2, 30%), sodium hydroxide (NaOH), sulfuric acid (H2SO4, 98%), microcrystalline cellulose (MCC), sodium hypochlorite solution (NaClO, 9%), sodium bromide (NaBr), carbamide, methylene blue dye (C16H18ClN3S, MW: 373.9 g/mol), and 2,2,6,6-tetramethylpiperidine-1-oxyl (TEMPO) were supplied by Sinopharm Chemical Reagent Co. Ltd. (China) and used without any further purification.


## 2.2. Preparation of Graphene Oxide

Graphene oxide (GO) was prepared with slight modification of published work about Hummers and Offeman method [58]. Briefly, 5 g of graphite powder was treated with sodium nitrate (2.5 g) and sulfuric acid (115 ml, 98%); then oxidation was initiated by slow addition of potassium permanganate (15 g) on ice bath (4°C) under constant stirring for 2 h. After that, obtained slurry was set on water bath (35°C, 2 h) under stirring; then 230 ml of distilled water was added and kept at 98°C for further 15 min. After completing the oxidation, the reaction was quenched by adding 700 ml of distilled water followed by hydrogen peroxide (30%, 50 ml). Upon quenching, the color of solution changes from dark brown to bright yellow. The product was centrifuged and purified via washing with HCl (1 : 10, 500 ml) followed by plenty of deionized water until pH = 6. Finally, the product was subjected to freeze-drying and labeled as GO for further use.


## 2.3. Preparation of Carboxylated Cellulose Nanofibers

The primary hydroxyl groups on the surface of fibrous microcrystalline cellulose were selectively oxidized to sodium carboxylate groups (COONa+) using TEMPO/NaOCl/NaBr system according to previous methods [54, 55] and stored at 4°C for further use (see ESI Section 1). To prepare carboxylated nanocellulose fibers (CNFs), suspension of sodium carboxylate cellulose fibers (TOCNFs) was mechanically homogenized (8000 rpm, 10 min) for further defibrillation and centrifuged (12000g, 10 min) for the removal of partly fibrillated fraction. Then, never dry TOCNFs were diluted using ultrapure water (0.1%) and treated with HCL (1 M) for 3 hours for ion exchange and conversion of sodium carboxylated type CNF-COONa+ to CNF-COOH+. The product was washed with water until pH = 4.0 and labeled as CNFs. Finally, desired concentration of suspension (16 mg ml−1) was obtained and stored at 4 Co for further experimental work. The concentration of CNFs was calculated by the weight difference of CNFs suspension (10 ml) after freeze-drying. The carboxyl content of nanofibers (0.547 mmol/g) was estimated according to ESI Section 1. The successful conversion was confirmed by the appearance of new peak at 1732 cm−1 in FTIR spectra (Figure S1).


## 2.4. Fabrication of GO/CNFs Hybrid Monolith

To fabricate the GO/CNFs porous monolith, first, well-dispersed suspension of freeze-dried graphene oxide (2 mg ml−1, 200 ml) was obtained by tip sonication in ultrapure water. Secondly, fixed amount of carbamide salt (800 mg) was mixed with graphene solution (pH = 4.5, 1 h); then known volume (x = 0, 1, 3, 5, and 7 ml) of separately prepared carboxylate cellulose nanofibers (CNFs) suspension was added to graphene/carbamide suspension followed by stirring overnight to obtain the homogenous solution. After that, 25 ml of mixture was sealed in Teflon-lined stainless steel autoclave (50 ml) and placed at 180 Co for hydrothermal treatment (5 hours). After cooling the reactor naturally at room temperature, cylindrical shape monolith was obtained (see graphical Scheme 1). The monolith was dipped into distilled water to remove residual carbamide and subjected to vacuumed freeze-drying (48 h). Product was labeled according to incorporated nanocellulose content as GO/CNF0, GO/CNF1, GO/CNF3, GO/CNF5, and GO/CNF7, respectively, and used for further characterization and dye adsorption studies (see detail in ESI Section 2).Scheme 1
Graphical illustration of GO/CNFs monolith assembly.


## 2.5. Material Characterization

Morphology and microstructure of monolith were analyzed by scanning electron microscopy (SEM-S420, HITACHI) equipped with a field-emission electron gun. The Fourier transform infrared (FTIR) spectra were recorded over the range of 400–4000 cm−1 using KBr pressed disc method (NICOLET-6700, UK). Raman spectra were recorded via Renishaw Raman spectrophotometer (NEXUS-670, USA). The percentage of carbon (% C), hydrogen (% H), and nitrogen (% N) contents were determined by element analyzer (ELMENTAR, VAIRO EL-III, Germany). X-ray diffraction (XRD) patterns were recorded by X-ray diffractometer (RIGAKU, D/Max-2550pc) at operating voltage of 40 kV, current density 200 mA, and 2θ scanning rage of 10°–70° using Cu Kα radiation. Thermal stability of materials was measured by thermogravimetric analyzer (NETZSCH, TG-209F1, Germany) under nitrogen environment and temperature range of 30–900°C using heating rate of 10°C min−1. Compression property of monolith was measured by dynamic mechanical analyzer (HY-940FS, China). Zeta potential measurement (ZP) was carried out by ZETASIZER (Nano-ZS90). Specific surface areas (SSA) of samples were calculated by the following formula [18]:(1)SSA=NAAMBCo-CeVMMBMS,where NA is Avogadro’s number (6.023 × 1023 mol−1), AMB is the covered area per MB molecules (typically assumed to be 1.35 nm2), Co and Ce are the initial and equilibrium concentration of MB, respectively, V is the volume of MB solution, MMB is the relative molecular mass of MB, and MS is the mass of sample.


## 2.6. Dye Adsorption Studies

Aqueous solutions of methylene blue (MB) dye with different concentration (10–100, 150, 200, 250, and 300 mg L−1) were prepared by successive dilution of stock solution (1000 mg L−1) in deionized water. The residual MB concentration was measured by UV-spectrophotometer (Shimadzu UV-spectrophotometer, UV-1800) using an absorbance at λ = 664 nm. Dye adsorption spectra were recorded over the range 200–800 nm using UV-VIS-NIR spectrophotometers (UV-3600, SHIMADZU). Dye adsorption quantity (mg g−1) and percentage removal (%) were calculated by (2) and (3), respectively:(2)Qe=Co-CeVW,(3)Removal%=Co-CtCo×100,where Co (mg L−1) and Ct (mg L−1) represent the initial and final (t) time concentrations of dye in the solution. V (L) is the volume of the solution and W (g) is the mass of adsorbent.


## 3. Results and Discussion

### 3.1. Macroscopic and Microstructure Analysis

The macroscopic images of hybrid monolith have been presented in FigureS2(a–d). It can be comprehended that all samples can easily be assembled into cylindrical shaped 3D material according to size and shape of the reaction vessel. To further examine the role of nanocellulose, the microstructure morphology of samples was investigated by SEM analysis. From Figure 1, all samples exhibited formation of interconnected 3D morphology and it can be noted that incorporation of CNFs with GO brought significant change in pore wall thickness and shrinkage in average size compared to those of GO/CNF0 (Figures 1(a), 1(c), 1(e), and 1(g)). High magnification SEM image of hybrid samples showed the presence of needle-like nanocellulose fibers in random direction which behave as compact skeleton within the dense and wrinkling type graphene sheets. Thus, it can be inferred that these surface decorated/adsorbed nanocellulose fibers may promote roughness between adjacent graphene sheets that results in compact 3D assembly due to strong chemical interaction (see FTIR section).Figure 1
SEM images of control (a-b), GO/CNF3 (c-d), GO/CNF5 (e-f), and GO/CNF7 (g-h) monolith.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)


### 3.2. FTIR Analysis

To gain insight into the formation chemistry of hybrid monolith, FTIR spectra of samples have been presented in Figure2. The successful oxidation of graphene oxide was confirmed by the presence of various kinds of oxygen functionality such as peak at 3422, 1715, 1628, 1385, and 1076 cm−1, which are mainly bloated from the starching vibration of hydroxyl group (-OH), carboxylic group (-C=O), aromatic skeleton of graphitic domains (C=C) [52], and alkoxy (C-O) and epoxy group (C-O), respectively. Spectra of sodium carboxylated nanocellulose showed shifting of carboxyl band (C=O) from 1619 cm−1 to carboxylic starching 1732 cm−1 which confirmed the successful oxidation and conversion of sodium carboxylated into free carboxylated group after acid treatment. The spectra of carboxylated nanocellulose show characteristic bands at 1430 cm−1, 1284 cm−1, 1163 cm−1, 1061 cm−1, and 898 cm−1 that are attributed to bending vibration of -C6-CH2 group [59], C-C ring starching mode, and C-O-C pyranose ring starching mode of nanocellulose [52], respectively. From Figure 2, hybrid samples showed the combination of distinctive bends compared to pure GO and CNF spectra, for instance, vibration mode of υ(OH), υ(C-O), and υ(C-O-C) of graphene origin and characteristic bend of cellulose position at 1430 and 876 cm−1. Interestingly, the peak associated with υ(COOH) at 1715 and 1732 cm−1 in the spectra of GO and CNF, respectively, disappeared after hydrothermal treatment in both spectra of control and hybrid samples. Compared to GO, control sample exhibits new prominent peaks of carboxylic (C=O) starching (1663 cm−1) and N-H bending (1618 cm−1) of amide I and considerable shift in OH starching (3422–3445 cm−1), while hybrid samples display lower shift in band related to O-H starching (3432–3438 cm−1) and considerable shift in N-H bending (1572–1633 cm−1) and C-O-C and C-O starching (at 1076–1087 cm−1) after hydrothermal treatment. This phenomenon is suggesting that the presence of carbamide plays important role for the self-assembly of monolithic material and promotes chemical interaction force, presumably, hydrogen bonding [60] as evident from shifting of these functional groups, since we failed to obtain 3D monolith in the absence of carbamide (digital image not presented here). However, nature of hydrogen bonding between bare graphene sheets and/or between GO sheets and nanocellulose fibers follows different routes. Compared to control sample, hybrid spectrum exhibits downshifting at starching vibration of hydroxyl (OH), carboxyl (C-O, C-O-C), and N-H bending vibration mode. This shift can be seen as synergy effect of strong hydrogen bonding between graphene sheets and nanocellulose fibers similar to previous reports [60], thus greatly influencing the microstructure morphology and mechanical and thermal properties of hybrid material (see Figures 1, 5, and 6). It can be inferred that strong chemical interaction between GO and CNFs is predominantly influenced by C=O⋯HO and N-H⋯OH type hydrogen bonding during the hydrothermal treatment. Moreover, shrinkage in OH starching was due to deoxygenation of graphene.Figure 2
FTIR spectra of GO, CNFs, and hybrid monolith.


### 3.3. Elemental Analysis

To further expose the surface properties difference, C/O and C/N surface atomic ratio of samples was investigated by elemental analysis (TableS1). The C/O ratio of hybrid samples GO/CNF3, GO/CNF5, and GO/CNF7 showed gradual decrease in C/O atomic ratio (3.46, 2.94, and 2.79, resp.) that is much lower then GO/CNF0 (5.20) but higher than starting material of GO (0.94). This can be ascribed to partial reduction of oxygen containing groups due to incorporated quantity of nanocellulose fibers, accordingly regulating the compatibility of hybrid material with aqueous medium compared to more hydrophobic counterparts (GO/CNF0). Interestingly, The C/N ratio of hybrid exhibits gradual increase compared to GO/CNF0 (11.48) and GO (≤0.05) at the same time. It means, in case of GO/CNF0, reduction process accompanied by incorporation of amine groups between GO sheets while breaking down carbamide during the hydrothermal treatment. On the other hand, it behaves like cross-linker between the GO sheets and cellulose nanofibers chains presumably through a reaction of amide or hydrogen bonding, also confirmed by FTIR and Raman analysis. So we can safely conclude that, by suitable incorporation of nanocellulose with graphene, one can tune the surface property and hydrophobic nature of reduced graphene.


### 3.4. Raman Spectra Analysis

The comparison of Raman spectra has been presented in Figure3. It can be observed that samples such as GO/CNF3, CNF5, and CNF7 display gradual increase in the intensity of D band (C-C) compared to graphene oxide and GO/CNF0 samples (Figure 3 and Table S2). These results are again confirming that, during the hydrothermal treatment, chemical bonding took place between the GO sheets and adjacent CNFs similar to previous reported results [61]. To further confirm the role of CNFs as multifunctional agent we also compare the intensity ratio (ID/IG) of GO with hybrid monolith (GO/CNF3, GO/CNF5, and GO/CNF7). As expected, there is gradual increase in intensity ratio (0.97–1.24) of hybrid with increasing amount of CNFs. This change indicated that the average sp3 hybridized (D) domains of graphene were increased upon compounding of CNFs thereby introducing more C-C atom due to substitution of hydroxyl group with amine that would reduce GO to RGO. Moreover, hybrid surface also shows little increase in sp2 hybridized (G band, C=C) domains in amplitude but smaller number (0.80) compared to GO/CNF0 (0.87) (Figure 3). This finding was in good agreement with strong hydrogen bonding interaction between nanocellulose and graphene sheets (see FTIR).Figure 3
Raman spectra of pure GO, control, and hybrid monolith.


### 3.5. XRD Analysis

The XRD structural patterns of graphene oxide, carboxylated cellulose nanofibers (CNFs), and hybrid samples with different mass ratio of nanocellulose to graphene have been shown in FigureS3. The feature diffraction peak of graphene oxide at 10.7° corresponding to (001) showed remarkable increase in interlay space (8.2 Å), due to existence of oxygenated functional groups and trapped water molecules on both sides of sheet surface [33]. CNFs pattern exhibits feature diffraction peak of cellulose I structure at 16.5° (110), 22.7° (200), and 34.6° (004), respectively. The broad peak at 22.7° confirmed two feature aspects of carboxylated cellulose nanofibers [55]: (1) CFNs retain the original fiber form after TEMPO induced selective oxidation and (2) the introduced reactive carboxyl moieties were not formed inside the crystallites. The structural composition of control (GO/CNF0) and cellulose compounding hybrids showed the disappearance of representative diffraction peak of graphene oxide at 10.7° (002) and appearance of new broad peak at 24.5° (d-spacing = 3.6–3.9 Å) at the same time (Figure S3). This phenomenon can be explained as follows: the interlay space of GO was reduced due to destruction of regular stacks of graphene oxide. Moreover, except GO/CNF0, new diffraction peak at 22.5° (002) originating from cellulose nanofibers crystallites was observed in all CNFs compounding samples which again confirms the successful incorporation of nanocellulose with graphene through strong amide/hydrogen bonding between CNFs with GO sheets, with gradual increase in cellulose originating peak confirming the crystalline nature of hybrid.


### 3.6. Thermal Stability and Chemical Composition Analysis

Thermal stability and chemical composition of samples were examined by TGA curve analysis. TGA curves of GO and CNFs showed minor weight loss at≅100°C (Figures S4 and S5), which was attributed to dehydration of adsorbed water molecules [43]. After that, both samples exhibited one-step degradation behavior with onset temperature of 198°C and 227°C and major mass loss of 20% and 59% due to decomposition of reactive oxygen containing groups from the backbones of GO and CNFs, respectively. This result indicates that prepared graphene oxide and nanocellulose fibers were well oxidized and contain lot of oxygen containing groups. From Figure S5, hybrid samples showed gradual improvement in onset degradation temperature (288°C, 295°C, and 319°C) in order to increase nanocellulose content. The significantly higher thermal stability compared to GO (198°C), CNFs (227°C), and GO/CNF0 (162°C) indicating the formation of more stable oxygen containing functional groups as a result of strong bonding interaction between GO and cellulose molecules [57]. It is interesting to note that, by increasing the content of CNFs (12%, 20%, and 28% w/w), hybrid material showed an incremental mass loss of 6.6% (GO/CNF3), 10.73% (GO/CNF5), and 15.63% (GO/CNF7) as well (Figure S5). This finding is indicating that about 50% oxygen functional groups of cellulose nanofibers were utilized for boding interaction, while remaining 50% had participated in enhancing surface functionality of hybrid monolith, also confirmed by elemental analysis (Table S1). Furthermore, the weight loss trends also suggest that maximum 15.63% mass of CNFs could successfully be incorporated with GO via self-assembly of hybrid monolith.


### 3.7. Compression Stress and Strain Analysis

For industrial point of view mechanical stability of monolith material is very important in order to overcome recontamination issue and reduced operating cost. Compression behaviors of control and nanocellulose incorporated hybrid monolith (GO/CNF7) are shown in Figure4(a). Hybrid monolith displays excellent mechanical property and can maintain its original structure up to 380 Kpa at 80% strain, which was five times higher than that of GO/CNF0 (75 KPa) and about threefold higher than reported graphene sponge (140 Kpa) [31]. This dramatic increase is attributed to synergy improvement in microstructure due to strong interaction between GO and nanocellulose fibers. To further expose the structural ability of hybrid monolith compression stress-strain cycling has been presented in Figure 4(b). It is worth noting that hybrid sample could preserve the structure (25 KPa at 20% strain) and recover to its original shape in all five consecutive cycles. Based on mentioned surface functionality and mechanical and elastic property of hybrid monolith, we can safely conclude that candidate monolithic material would be promising to avoid risk of recontamination during adsorption-desorption cycles, also confirmed by adsorption-desorption cycles of model dye (Video S1).Figure 4
Mechanical property of control and hybrid monolith (a) and cyclic stress and strain performance of GO/CNF7 (b).
(a)
(b)Figure 5
Plots of equilibrium adsorption quantity (a), % removal (b), Langmuir isotherm model (c), and pseudo-second-order kinetics (d) for MB dye.
(a)
(b)
(c)
(d)Figure 6
Effect of % nanocellulose loading (a) and recycling performance (b) for hybrid monolith.
(a)
(b)


### 3.8. Dye Adsorption Studies

Adsorption isotherm studies can provide the information about the surface property and adsorption mechanism for any adsorbent. For this, methylene blue (MB) dye was selected to examine the surface property difference between GO/CNF0, GO/CNF3, GO/CNF5, and GO/CNF7. It is worth noting that nanocellulose compounded samples showed excellent adsorption capacity compared to control one (Figure5(a)) and display linear relationship with initial MB dye concentration in the beginning and then attain saturation at higher concentration range. To further demonstrate the adsorption performance of dye, the logarithmic expression of same dye concentration was plotted against MB removal percentage. From Figure 5(b), it can be comprehended that, except GO/CNF0 (Figure 5(b)), all hybrid samples exhibited complete removal ability (100%) for MB dye in very low to moderate concentration range. This finding indicates that hybrid samples have more available active sites to interact with dye molecules near low to moderate concentration region and vice versa. To confirm the reason behind the different adsorption mechanisms of samples, we investigated their zeta potential measurement. From Table S3, it can be seen that all samples have negative surface charges and their average values were found to be in the following order: GO/CNF7 > GO/CNF5 > GO/CNF3 > GO/CNF0, respectively. It means the higher the surface negative charge, the higher the rate of adsorption and the superior the performance for positively charged MB dye. For that reason, we can conclude that nanocellulose compounded samples have strong interaction for MB molecules compared to GO/CNF0 and follow different mechanism.In order to quantitatively examine the adsorption capacity of GO/CNF3, GO/CNF5, and GO/CNF7, adsorption isotherm data were fitted to linearized form of Freundlich isotherm (EquationS3), Langmuir isotherm (Equation S4), and Temkin isotherm model (Equation S5) (see ESI Section 2). Statistical parameters of model were extracted by fitting the equation of linear regression on experimental data and summarized in Table S5. Form Figure S6, Freundlich and Temkin model showed deviation in linearity compared to Langmuir isotherm model for all hybrid samples (Figure 5(c)). Good linearity and higher value of regression coefficient (r2 = 0.99) for Langmuir model confirm that the MB adsorption follows monolayer type adsorption process and is found to be in the following order: Langmuir model > Freundlich model > Temkin model (Table 1). The 1/n values of Freundlich model lie between 0 and 1, which also confirm the normal Langmuir isotherm. Moreover, samples also exhibit increasing KL value with respect to incorporated quantity of CNF, which reflect the strong affinity for MB molecules via strong electrostatic interaction. Based on Langmuir model, the maximum adsorption capacities of GO/CNF3, GO/CNF5, and GO/CNF7 adsorbent were in the following order: 151.51 mg g−1 < 204.08 mg g−1 < 227.27 mg g−1, respectively. This synergy improvement was inevitable due to alteration in microstructure (see Figure 1) and surface chemistry. For further comprehension, we also measured the specific surface area (SSA) of hybrid adsorbent (Table S3). The specific surface areas of samples were found to be in the following order: GO/CNF3 < GO/CNF5 < GO/CNF7, with corresponding value of 324.28 m2 g−1, 436.79 m2 g−1, and 486.43 m2 g−1, respectively, which can be a result of increasing space between adjacent graphene sheets due to well-dispersed nanocellulose fibers. Consequently, sample with large surface area showed higher MB adsorption due to more available surfaces. However, higher content of CNFs showed little improvement in dye adsorption capacity and specific surface area, which could be explained as follows: higher incorporation of CNFs leads to aggregation into pore orifice thus reducing the full surface area coverage of hybrid monolith for dye molecules. Based on Table S4, candidate hybrid adsorbent showed notable adsorption performance compared with other reported work such as high cost carbon nanotube (CNT) [13], graphene/CNT monolith [33], MWCNT aerogel [51], graphene by toxic hydrazine [27], graphene/luffa sponge [12], thiourea assisted graphene sponge [31], polydopamine microspheres [23], polyaniline hydrogel [26], magnetic particle based graphene composite [9, 19, 34–38], graphene coated biochar [40], and graphene oxide/calcium alginate [14]; for more comparison see Table S4.Table 1
Equilibrium adsorption isotherm parameters of hybrid monolith for MB dye.
Sample (ID)
Freundlich model
Langmuir model
Temkin model
1
/
n
K
F  (L mg−1)
R
2
Q
m
a
x
.  (mg g−1)
K
L  (L mg−1)
R
2
B
T
K
T  (L mg−1)
b
T  (J mol−1)
R
2
GO/CNF3
0.256
34.329
0.954
151.51
0.0365
0.995
26.145
0.798
96.352
0.956
GO/CNF5
0.246
53.357
0.935
204.08
0.0608
0.994
32.413
1.776
77.720
0.962
GO/CNF7
0.238
70.316
0.771
227.27
0.1302
0.998
35.614
3.568
70.734
0.869
Conditions: pH = 6.5;T = 303 K; dosage = 1.11 g L−1; contact time = 24 h; Co = 100–350 @ 50 mg L−1.Generally, adsorption kinetics study predicts the rate of adsorption and nature of interaction for any adsorption process. In this study, pseudo-first order and pseudo-second order were selected to understand the adsorption kinetics of hybrid adsorbent (GO/CNF3, GO/CNF5, and GO/CNF7). Pseudo-first order model considers that rate of adsorption process is proportional to number of unoccupied sites, while pseudo-second-order model suggests that rate of adsorption process is proportional to square of number of unoccupied sites. The linearized forms of pseudo-first order (EquationS1) and pseudo-second order (Equation S2) along with model parameter were incorporated in ESI Section 2. Kinetic parameters were obtained by plotting the linear graph of log⁡(Qe-Qt) versus t (Figure S6) and t/Qt versus t (Figure 5(c)), respectively. From Table 2, pseudo-first-order parameters exhibit poor relationship with lower coefficient of correlation (r2) and significant deviation in calculated and experimental Qe values for all hybrid samples (Figure S6a and Table 2). This finding confirms that the adsorption of MB dye did not follow the pseudo-first-order kinetic model. The linear plot of pseudo-second-order model showed excellent fit with higher correlation coefficient r2 ≥ 0.99 for all hybrid material (Figure 5(c) and Table 2). Good linear relationship and very close calculated and measured values of Qe approve that adsorption process of MB dye onto hybrid samples was mainly governed by pseudo-second-order model and chemisorption type process in nature. Interestingly, upon compounding of nanocellulose fibers, adsorption rate constant (k2) and performance of hybrid samples (GO/CNF3, GO/CNF5, and GO/CNF7) also showed gradual improvement (Table 2). This can be attributed to alteration in surface property and charge density of material and agree with the results of zeta potential measurement (Table S3).Table 2
Adsorption kinetics parameters of hybrid monolith for MB dye.
Sample (ID)
Pseudo-first-order model
Pseudo-second-order model
Q
e
E
x
p
.  (mg g−1)
k
1  (min−1)
Q
e
,
c
a
l
.  (mg g−1)
R
2
k
2  (g mg−1 min−1)
Q
e
,
c
a
l
.  (mg g−1)
R
2
GO/CNF3
0.003961
5.68
0.964
0.00013
88.41
0.995
83.4
GO/CNF5
0.004353
5.42
0.984
0.00018
92.76
0.999
88.94
GO/CNF7
0.005389
4.95
0.968
0.00029
93.28
0.999
95.88
Conditions: Co = 100 mg L−1; pH = 6.56; T = 303 K; dosage = 1.11 g L−1.


### 3.9. Effect of Nanocellulose Quantity

As mentioned above, the incorporation of different content of nanocellulose brought notable change in adsorption efficiency and rate of hybrid adsorbent compared to control sample (Tables1 and 2). To further clarify this, statistical relationship between equilibrium MB adsorption quantity and effect of % CNFs loading was established in Figure 6(a). It can be observed that dye adsorption quantity followed exponential relationship of Qe=30∗exp[-(CNFs/22.72)] with incorporated nanocellulose quantity. Good applicability of this relationship (r2 = 0.994) confirms that nanocellulose loading imparts remarkable change in developed surface such as higher oxygen containing sites, surface roughness, and specific surface area which greatly benefits capturing more MB molecules in solution (see Tables S1 and S3 and SEM images). Based on this, we can safely conclude that interaction of MB dye with control (hydrophobic) and hybrid (hydrophilic) surface followed different mechanism. This means electrostatic interaction was more dominant than hydrophobic type π-π interaction in hybrid adsorbent.


### 3.10. Adsorption-Desorption Studies

From the industrial point of view, the structural stability and recycling study is very important to reduction of operating cost and practical qualification of adsorbent materials. In order to examine the adsorption and regeneration performance, first hybrid GO/CNF5 adsorbent was put into MB aqueous solution and dye concentration was measured every 30 min by UV-VIS spectra analysis. It is worth noting that 100% removal was achieved within 150 min (FiguresS7 and S8). After removal, spent adsorbent was placed in the mixture of HCL (2%) and ethanol (1 : 1 v/v) under mild stirring. Based on Figure S8 and Video S1, MB dye can easily be released from adsorbent without losing any detachable particle in the solution which successfully qualifies the adsorption and regeneration ability of adsorbent with zero release of nanohazard into treated water. To further investigate the recycling ability of hybrid adsorbents, adsorption-desorption process was performed for four consecutive cycles. It is worth noting that, with the exception of little decline in efficiency (≅6%), hybrid adsorbent showed still higher adsorption capacity for four consecutive cycles (Figure 6(b)). Based on excellent adsorption-desorption performances and structural stability, GO/CNFs adsorbent can be promising candidate for water purification industry.


## 3.1. Macroscopic and Microstructure Analysis

The macroscopic images of hybrid monolith have been presented in FigureS2(a–d). It can be comprehended that all samples can easily be assembled into cylindrical shaped 3D material according to size and shape of the reaction vessel. To further examine the role of nanocellulose, the microstructure morphology of samples was investigated by SEM analysis. From Figure 1, all samples exhibited formation of interconnected 3D morphology and it can be noted that incorporation of CNFs with GO brought significant change in pore wall thickness and shrinkage in average size compared to those of GO/CNF0 (Figures 1(a), 1(c), 1(e), and 1(g)). High magnification SEM image of hybrid samples showed the presence of needle-like nanocellulose fibers in random direction which behave as compact skeleton within the dense and wrinkling type graphene sheets. Thus, it can be inferred that these surface decorated/adsorbed nanocellulose fibers may promote roughness between adjacent graphene sheets that results in compact 3D assembly due to strong chemical interaction (see FTIR section).Figure 1
SEM images of control (a-b), GO/CNF3 (c-d), GO/CNF5 (e-f), and GO/CNF7 (g-h) monolith.
(a)
(b)
(c)
(d)
(e)
(f)
(g)
(h)


## 3.2. FTIR Analysis

To gain insight into the formation chemistry of hybrid monolith, FTIR spectra of samples have been presented in Figure2. The successful oxidation of graphene oxide was confirmed by the presence of various kinds of oxygen functionality such as peak at 3422, 1715, 1628, 1385, and 1076 cm−1, which are mainly bloated from the starching vibration of hydroxyl group (-OH), carboxylic group (-C=O), aromatic skeleton of graphitic domains (C=C) [52], and alkoxy (C-O) and epoxy group (C-O), respectively. Spectra of sodium carboxylated nanocellulose showed shifting of carboxyl band (C=O) from 1619 cm−1 to carboxylic starching 1732 cm−1 which confirmed the successful oxidation and conversion of sodium carboxylated into free carboxylated group after acid treatment. The spectra of carboxylated nanocellulose show characteristic bands at 1430 cm−1, 1284 cm−1, 1163 cm−1, 1061 cm−1, and 898 cm−1 that are attributed to bending vibration of -C6-CH2 group [59], C-C ring starching mode, and C-O-C pyranose ring starching mode of nanocellulose [52], respectively. From Figure 2, hybrid samples showed the combination of distinctive bends compared to pure GO and CNF spectra, for instance, vibration mode of υ(OH), υ(C-O), and υ(C-O-C) of graphene origin and characteristic bend of cellulose position at 1430 and 876 cm−1. Interestingly, the peak associated with υ(COOH) at 1715 and 1732 cm−1 in the spectra of GO and CNF, respectively, disappeared after hydrothermal treatment in both spectra of control and hybrid samples. Compared to GO, control sample exhibits new prominent peaks of carboxylic (C=O) starching (1663 cm−1) and N-H bending (1618 cm−1) of amide I and considerable shift in OH starching (3422–3445 cm−1), while hybrid samples display lower shift in band related to O-H starching (3432–3438 cm−1) and considerable shift in N-H bending (1572–1633 cm−1) and C-O-C and C-O starching (at 1076–1087 cm−1) after hydrothermal treatment. This phenomenon is suggesting that the presence of carbamide plays important role for the self-assembly of monolithic material and promotes chemical interaction force, presumably, hydrogen bonding [60] as evident from shifting of these functional groups, since we failed to obtain 3D monolith in the absence of carbamide (digital image not presented here). However, nature of hydrogen bonding between bare graphene sheets and/or between GO sheets and nanocellulose fibers follows different routes. Compared to control sample, hybrid spectrum exhibits downshifting at starching vibration of hydroxyl (OH), carboxyl (C-O, C-O-C), and N-H bending vibration mode. This shift can be seen as synergy effect of strong hydrogen bonding between graphene sheets and nanocellulose fibers similar to previous reports [60], thus greatly influencing the microstructure morphology and mechanical and thermal properties of hybrid material (see Figures 1, 5, and 6). It can be inferred that strong chemical interaction between GO and CNFs is predominantly influenced by C=O⋯HO and N-H⋯OH type hydrogen bonding during the hydrothermal treatment. Moreover, shrinkage in OH starching was due to deoxygenation of graphene.Figure 2
FTIR spectra of GO, CNFs, and hybrid monolith.


## 3.3. Elemental Analysis

To further expose the surface properties difference, C/O and C/N surface atomic ratio of samples was investigated by elemental analysis (TableS1). The C/O ratio of hybrid samples GO/CNF3, GO/CNF5, and GO/CNF7 showed gradual decrease in C/O atomic ratio (3.46, 2.94, and 2.79, resp.) that is much lower then GO/CNF0 (5.20) but higher than starting material of GO (0.94). This can be ascribed to partial reduction of oxygen containing groups due to incorporated quantity of nanocellulose fibers, accordingly regulating the compatibility of hybrid material with aqueous medium compared to more hydrophobic counterparts (GO/CNF0). Interestingly, The C/N ratio of hybrid exhibits gradual increase compared to GO/CNF0 (11.48) and GO (≤0.05) at the same time. It means, in case of GO/CNF0, reduction process accompanied by incorporation of amine groups between GO sheets while breaking down carbamide during the hydrothermal treatment. On the other hand, it behaves like cross-linker between the GO sheets and cellulose nanofibers chains presumably through a reaction of amide or hydrogen bonding, also confirmed by FTIR and Raman analysis. So we can safely conclude that, by suitable incorporation of nanocellulose with graphene, one can tune the surface property and hydrophobic nature of reduced graphene.


## 3.4. Raman Spectra Analysis

The comparison of Raman spectra has been presented in Figure3. It can be observed that samples such as GO/CNF3, CNF5, and CNF7 display gradual increase in the intensity of D band (C-C) compared to graphene oxide and GO/CNF0 samples (Figure 3 and Table S2). These results are again confirming that, during the hydrothermal treatment, chemical bonding took place between the GO sheets and adjacent CNFs similar to previous reported results [61]. To further confirm the role of CNFs as multifunctional agent we also compare the intensity ratio (ID/IG) of GO with hybrid monolith (GO/CNF3, GO/CNF5, and GO/CNF7). As expected, there is gradual increase in intensity ratio (0.97–1.24) of hybrid with increasing amount of CNFs. This change indicated that the average sp3 hybridized (D) domains of graphene were increased upon compounding of CNFs thereby introducing more C-C atom due to substitution of hydroxyl group with amine that would reduce GO to RGO. Moreover, hybrid surface also shows little increase in sp2 hybridized (G band, C=C) domains in amplitude but smaller number (0.80) compared to GO/CNF0 (0.87) (Figure 3). This finding was in good agreement with strong hydrogen bonding interaction between nanocellulose and graphene sheets (see FTIR).Figure 3
Raman spectra of pure GO, control, and hybrid monolith.


## 3.5. XRD Analysis

The XRD structural patterns of graphene oxide, carboxylated cellulose nanofibers (CNFs), and hybrid samples with different mass ratio of nanocellulose to graphene have been shown in FigureS3. The feature diffraction peak of graphene oxide at 10.7° corresponding to (001) showed remarkable increase in interlay space (8.2 Å), due to existence of oxygenated functional groups and trapped water molecules on both sides of sheet surface [33]. CNFs pattern exhibits feature diffraction peak of cellulose I structure at 16.5° (110), 22.7° (200), and 34.6° (004), respectively. The broad peak at 22.7° confirmed two feature aspects of carboxylated cellulose nanofibers [55]: (1) CFNs retain the original fiber form after TEMPO induced selective oxidation and (2) the introduced reactive carboxyl moieties were not formed inside the crystallites. The structural composition of control (GO/CNF0) and cellulose compounding hybrids showed the disappearance of representative diffraction peak of graphene oxide at 10.7° (002) and appearance of new broad peak at 24.5° (d-spacing = 3.6–3.9 Å) at the same time (Figure S3). This phenomenon can be explained as follows: the interlay space of GO was reduced due to destruction of regular stacks of graphene oxide. Moreover, except GO/CNF0, new diffraction peak at 22.5° (002) originating from cellulose nanofibers crystallites was observed in all CNFs compounding samples which again confirms the successful incorporation of nanocellulose with graphene through strong amide/hydrogen bonding between CNFs with GO sheets, with gradual increase in cellulose originating peak confirming the crystalline nature of hybrid.


## 3.6. Thermal Stability and Chemical Composition Analysis

Thermal stability and chemical composition of samples were examined by TGA curve analysis. TGA curves of GO and CNFs showed minor weight loss at≅100°C (Figures S4 and S5), which was attributed to dehydration of adsorbed water molecules [43]. After that, both samples exhibited one-step degradation behavior with onset temperature of 198°C and 227°C and major mass loss of 20% and 59% due to decomposition of reactive oxygen containing groups from the backbones of GO and CNFs, respectively. This result indicates that prepared graphene oxide and nanocellulose fibers were well oxidized and contain lot of oxygen containing groups. From Figure S5, hybrid samples showed gradual improvement in onset degradation temperature (288°C, 295°C, and 319°C) in order to increase nanocellulose content. The significantly higher thermal stability compared to GO (198°C), CNFs (227°C), and GO/CNF0 (162°C) indicating the formation of more stable oxygen containing functional groups as a result of strong bonding interaction between GO and cellulose molecules [57]. It is interesting to note that, by increasing the content of CNFs (12%, 20%, and 28% w/w), hybrid material showed an incremental mass loss of 6.6% (GO/CNF3), 10.73% (GO/CNF5), and 15.63% (GO/CNF7) as well (Figure S5). This finding is indicating that about 50% oxygen functional groups of cellulose nanofibers were utilized for boding interaction, while remaining 50% had participated in enhancing surface functionality of hybrid monolith, also confirmed by elemental analysis (Table S1). Furthermore, the weight loss trends also suggest that maximum 15.63% mass of CNFs could successfully be incorporated with GO via self-assembly of hybrid monolith.


## 3.7. Compression Stress and Strain Analysis

For industrial point of view mechanical stability of monolith material is very important in order to overcome recontamination issue and reduced operating cost. Compression behaviors of control and nanocellulose incorporated hybrid monolith (GO/CNF7) are shown in Figure4(a). Hybrid monolith displays excellent mechanical property and can maintain its original structure up to 380 Kpa at 80% strain, which was five times higher than that of GO/CNF0 (75 KPa) and about threefold higher than reported graphene sponge (140 Kpa) [31]. This dramatic increase is attributed to synergy improvement in microstructure due to strong interaction between GO and nanocellulose fibers. To further expose the structural ability of hybrid monolith compression stress-strain cycling has been presented in Figure 4(b). It is worth noting that hybrid sample could preserve the structure (25 KPa at 20% strain) and recover to its original shape in all five consecutive cycles. Based on mentioned surface functionality and mechanical and elastic property of hybrid monolith, we can safely conclude that candidate monolithic material would be promising to avoid risk of recontamination during adsorption-desorption cycles, also confirmed by adsorption-desorption cycles of model dye (Video S1).Figure 4
Mechanical property of control and hybrid monolith (a) and cyclic stress and strain performance of GO/CNF7 (b).
(a)
(b)Figure 5
Plots of equilibrium adsorption quantity (a), % removal (b), Langmuir isotherm model (c), and pseudo-second-order kinetics (d) for MB dye.
(a)
(b)
(c)
(d)Figure 6
Effect of % nanocellulose loading (a) and recycling performance (b) for hybrid monolith.
(a)
(b)


## 3.8. Dye Adsorption Studies

Adsorption isotherm studies can provide the information about the surface property and adsorption mechanism for any adsorbent. For this, methylene blue (MB) dye was selected to examine the surface property difference between GO/CNF0, GO/CNF3, GO/CNF5, and GO/CNF7. It is worth noting that nanocellulose compounded samples showed excellent adsorption capacity compared to control one (Figure5(a)) and display linear relationship with initial MB dye concentration in the beginning and then attain saturation at higher concentration range. To further demonstrate the adsorption performance of dye, the logarithmic expression of same dye concentration was plotted against MB removal percentage. From Figure 5(b), it can be comprehended that, except GO/CNF0 (Figure 5(b)), all hybrid samples exhibited complete removal ability (100%) for MB dye in very low to moderate concentration range. This finding indicates that hybrid samples have more available active sites to interact with dye molecules near low to moderate concentration region and vice versa. To confirm the reason behind the different adsorption mechanisms of samples, we investigated their zeta potential measurement. From Table S3, it can be seen that all samples have negative surface charges and their average values were found to be in the following order: GO/CNF7 > GO/CNF5 > GO/CNF3 > GO/CNF0, respectively. It means the higher the surface negative charge, the higher the rate of adsorption and the superior the performance for positively charged MB dye. For that reason, we can conclude that nanocellulose compounded samples have strong interaction for MB molecules compared to GO/CNF0 and follow different mechanism.In order to quantitatively examine the adsorption capacity of GO/CNF3, GO/CNF5, and GO/CNF7, adsorption isotherm data were fitted to linearized form of Freundlich isotherm (EquationS3), Langmuir isotherm (Equation S4), and Temkin isotherm model (Equation S5) (see ESI Section 2). Statistical parameters of model were extracted by fitting the equation of linear regression on experimental data and summarized in Table S5. Form Figure S6, Freundlich and Temkin model showed deviation in linearity compared to Langmuir isotherm model for all hybrid samples (Figure 5(c)). Good linearity and higher value of regression coefficient (r2 = 0.99) for Langmuir model confirm that the MB adsorption follows monolayer type adsorption process and is found to be in the following order: Langmuir model > Freundlich model > Temkin model (Table 1). The 1/n values of Freundlich model lie between 0 and 1, which also confirm the normal Langmuir isotherm. Moreover, samples also exhibit increasing KL value with respect to incorporated quantity of CNF, which reflect the strong affinity for MB molecules via strong electrostatic interaction. Based on Langmuir model, the maximum adsorption capacities of GO/CNF3, GO/CNF5, and GO/CNF7 adsorbent were in the following order: 151.51 mg g−1 < 204.08 mg g−1 < 227.27 mg g−1, respectively. This synergy improvement was inevitable due to alteration in microstructure (see Figure 1) and surface chemistry. For further comprehension, we also measured the specific surface area (SSA) of hybrid adsorbent (Table S3). The specific surface areas of samples were found to be in the following order: GO/CNF3 < GO/CNF5 < GO/CNF7, with corresponding value of 324.28 m2 g−1, 436.79 m2 g−1, and 486.43 m2 g−1, respectively, which can be a result of increasing space between adjacent graphene sheets due to well-dispersed nanocellulose fibers. Consequently, sample with large surface area showed higher MB adsorption due to more available surfaces. However, higher content of CNFs showed little improvement in dye adsorption capacity and specific surface area, which could be explained as follows: higher incorporation of CNFs leads to aggregation into pore orifice thus reducing the full surface area coverage of hybrid monolith for dye molecules. Based on Table S4, candidate hybrid adsorbent showed notable adsorption performance compared with other reported work such as high cost carbon nanotube (CNT) [13], graphene/CNT monolith [33], MWCNT aerogel [51], graphene by toxic hydrazine [27], graphene/luffa sponge [12], thiourea assisted graphene sponge [31], polydopamine microspheres [23], polyaniline hydrogel [26], magnetic particle based graphene composite [9, 19, 34–38], graphene coated biochar [40], and graphene oxide/calcium alginate [14]; for more comparison see Table S4.Table 1
Equilibrium adsorption isotherm parameters of hybrid monolith for MB dye.
Sample (ID)
Freundlich model
Langmuir model
Temkin model
1
/
n
K
F  (L mg−1)
R
2
Q
m
a
x
.  (mg g−1)
K
L  (L mg−1)
R
2
B
T
K
T  (L mg−1)
b
T  (J mol−1)
R
2
GO/CNF3
0.256
34.329
0.954
151.51
0.0365
0.995
26.145
0.798
96.352
0.956
GO/CNF5
0.246
53.357
0.935
204.08
0.0608
0.994
32.413
1.776
77.720
0.962
GO/CNF7
0.238
70.316
0.771
227.27
0.1302
0.998
35.614
3.568
70.734
0.869
Conditions: pH = 6.5;T = 303 K; dosage = 1.11 g L−1; contact time = 24 h; Co = 100–350 @ 50 mg L−1.Generally, adsorption kinetics study predicts the rate of adsorption and nature of interaction for any adsorption process. In this study, pseudo-first order and pseudo-second order were selected to understand the adsorption kinetics of hybrid adsorbent (GO/CNF3, GO/CNF5, and GO/CNF7). Pseudo-first order model considers that rate of adsorption process is proportional to number of unoccupied sites, while pseudo-second-order model suggests that rate of adsorption process is proportional to square of number of unoccupied sites. The linearized forms of pseudo-first order (EquationS1) and pseudo-second order (Equation S2) along with model parameter were incorporated in ESI Section 2. Kinetic parameters were obtained by plotting the linear graph of log⁡(Qe-Qt) versus t (Figure S6) and t/Qt versus t (Figure 5(c)), respectively. From Table 2, pseudo-first-order parameters exhibit poor relationship with lower coefficient of correlation (r2) and significant deviation in calculated and experimental Qe values for all hybrid samples (Figure S6a and Table 2). This finding confirms that the adsorption of MB dye did not follow the pseudo-first-order kinetic model. The linear plot of pseudo-second-order model showed excellent fit with higher correlation coefficient r2 ≥ 0.99 for all hybrid material (Figure 5(c) and Table 2). Good linear relationship and very close calculated and measured values of Qe approve that adsorption process of MB dye onto hybrid samples was mainly governed by pseudo-second-order model and chemisorption type process in nature. Interestingly, upon compounding of nanocellulose fibers, adsorption rate constant (k2) and performance of hybrid samples (GO/CNF3, GO/CNF5, and GO/CNF7) also showed gradual improvement (Table 2). This can be attributed to alteration in surface property and charge density of material and agree with the results of zeta potential measurement (Table S3).Table 2
Adsorption kinetics parameters of hybrid monolith for MB dye.
Sample (ID)
Pseudo-first-order model
Pseudo-second-order model
Q
e
E
x
p
.  (mg g−1)
k
1  (min−1)
Q
e
,
c
a
l
.  (mg g−1)
R
2
k
2  (g mg−1 min−1)
Q
e
,
c
a
l
.  (mg g−1)
R
2
GO/CNF3
0.003961
5.68
0.964
0.00013
88.41
0.995
83.4
GO/CNF5
0.004353
5.42
0.984
0.00018
92.76
0.999
88.94
GO/CNF7
0.005389
4.95
0.968
0.00029
93.28
0.999
95.88
Conditions: Co = 100 mg L−1; pH = 6.56; T = 303 K; dosage = 1.11 g L−1.


## 3.9. Effect of Nanocellulose Quantity

As mentioned above, the incorporation of different content of nanocellulose brought notable change in adsorption efficiency and rate of hybrid adsorbent compared to control sample (Tables1 and 2). To further clarify this, statistical relationship between equilibrium MB adsorption quantity and effect of % CNFs loading was established in Figure 6(a). It can be observed that dye adsorption quantity followed exponential relationship of Qe=30∗exp[-(CNFs/22.72)] with incorporated nanocellulose quantity. Good applicability of this relationship (r2 = 0.994) confirms that nanocellulose loading imparts remarkable change in developed surface such as higher oxygen containing sites, surface roughness, and specific surface area which greatly benefits capturing more MB molecules in solution (see Tables S1 and S3 and SEM images). Based on this, we can safely conclude that interaction of MB dye with control (hydrophobic) and hybrid (hydrophilic) surface followed different mechanism. This means electrostatic interaction was more dominant than hydrophobic type π-π interaction in hybrid adsorbent.


## 3.10. Adsorption-Desorption Studies

From the industrial point of view, the structural stability and recycling study is very important to reduction of operating cost and practical qualification of adsorbent materials. In order to examine the adsorption and regeneration performance, first hybrid GO/CNF5 adsorbent was put into MB aqueous solution and dye concentration was measured every 30 min by UV-VIS spectra analysis. It is worth noting that 100% removal was achieved within 150 min (FiguresS7 and S8). After removal, spent adsorbent was placed in the mixture of HCL (2%) and ethanol (1 : 1 v/v) under mild stirring. Based on Figure S8 and Video S1, MB dye can easily be released from adsorbent without losing any detachable particle in the solution which successfully qualifies the adsorption and regeneration ability of adsorbent with zero release of nanohazard into treated water. To further investigate the recycling ability of hybrid adsorbents, adsorption-desorption process was performed for four consecutive cycles. It is worth noting that, with the exception of little decline in efficiency (≅6%), hybrid adsorbent showed still higher adsorption capacity for four consecutive cycles (Figure 6(b)). Based on excellent adsorption-desorption performances and structural stability, GO/CNFs adsorbent can be promising candidate for water purification industry.


## 4. Conclusion

Hybrid monolith of graphene oxide and nanocellulose fibers with robust interconnected network was fabricated via eco-friendly self-assembly method. Pore morphology and surface chemistry (such as hydrophilicity and surface charge density) of monolith were improved. Specific surface area and mechanical property were enhanced about four- and fivefold, respectively, compared to unmodified monolith. It is proposed that strong chemical interaction, mainly hydrogen bonding, was primary driving force for the formation of hybrid monolith. Maximum 15.63% w/w grafting of nanocellulose was achieved. Incorporation of nanocellulose exhibits synergy improvement in dye adsorption performance. Complete removal was achieved for trace to moderate quantity of dye. Adsorption process followed monolayer type Langmuir isotherm model. High surface area coupled with electrostatic interaction was suggested for dye adsorption mechanisms. Adsorption capacity followed exponential relationship with incorporated nanocellulose content. Hybrid monolith showed simple and cost-effective recollection and recycling performance. Further application of hybrid material is underway in our lab.


## Additional Points

Associated Content. Supporting information includes detailed description for preparation of TEMPO-oxidized cellulose and batch adsorption studies: FTIR spectra of carboxylated nanocellulose, macroscopic images of hybrid monolith, X-ray pattern analysis, TGA curve analysis, digital images of dye adsorption, dye desorption video, adsorption isotherm models descriptions and plots, tables of elemental analysis, Raman spectra analysis, zeta potential analysis, specific surface area measurement, adsorption isotherm, kinetics parameters, and comparison of performance for MB adsorption capacity with reported work.



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