Demilade T. Adedipea,
Ajibola A. Bayode*b and
Odunayo T. Ore
*c
aState Key Laboratory of Marine Pollution, Department of Chemistry, City University of Hong Kong, Hong Kong, China
bDepartment of Chemical Sciences, Faculty of Natural Sciences, Redeemer's University, P.M.B. 230, 232101 Ede, Nigeria. E-mail: bayodea@run.edu.ng
cDepartment of Chemistry, Kogi State University, P.M.B. 222, Kabba, Nigeria. E-mail: oreodunayo@yahoo.com
First published on 29th August 2025
Graphene-based materials (GBMs) have emerged as versatile and efficient candidates for gas adsorption and air pollution mitigation, particularly targeting COx, NOx, SOx, and volatile organic compounds (VOCs). This review highlights recent advances in the design and fabrication of GBMs, including green synthesis, heteroatom doping, and metal oxide hybridization. Emphasis is placed on emerging fabrication strategies that enhance porosity, surface chemistry, and gas selectivity. Notably, nitrogen-doped graphene has been shown to improve NOx adsorption by up to 45%, while rGO–metal oxide composites demonstrate enhanced CO2 selectivity under low humidity conditions. We analyse performance data trends and benchmark results from recent studies, outlining the key factors influencing adsorption efficiency. The sustainable development of GBMs using biomass and industrial waste precursors is also explored within the context of the circular economy. Finally, the review underscores the importance of integrating techno-economic analysis (TEA) into future research to support the scalable deployment of GBMs in industrial gas separation technologies.
Air pollutants are classified based on their physicochemical features and consist of a heterogeneous mixture of suspended gases, liquids, and solids (Fig. 1). Combustion of fossil fuels and biomass, whether created artificially or naturally, is one source of air pollution.10,11 Industrial processes, burning materials, automobile emissions, and ambient tobacco smoke are examples of man-made/anthropogenic sources of air pollution.12 Volcanic ash, wildfires, different gases, and spontaneous secondary pollutants are examples of naturally occurring sources.13,14
Clean/pristine air should not contain pollutants ranging from suspended particulate matter to volatile organic compounds and heavy metals. These pollutants, including PM2.5, PM10, NO2, SO2, CO2, CO, CH4, polyaromatic hydrocarbons (PAHs), and heavy metals like Ni, Cd, As, and Pb, constitute human health risks and pose a significant threat to the ecosystems.15,16 Studies conducted on animals and in vitro have demonstrated that exposure to allergens and air pollution together may have synergistic negative effects on allergic respiratory diseases.17,18 Thus, the scientific world has focused on the development of advanced nanomaterials for the capture of hazardous materials and air cleanup in the last century.
The term “graphene” was proposed by the IUPAC commission to replace “graphite layers”, which was inadequate for studying single carbon layer structures, as “graphite” denotes a three-dimensional stacking structure. Graphene is now defined as a two-dimensional monolayer of carbon atoms, serving as the fundamental unit of graphitic materials like fullerene, nanotube, and graphite.19–21 Despite graphite's ancient use dating back 6000 years for pottery decoration, research on graphene, essentially a single-atom plane of graphite, became more prominent in the 1960s when enhanced basal-plane conductivity was observed in graphite intercalation compounds.22–24 This discovery sparked excitement in the scientific community, envisioning graphene as a lighter, cheaper alternative to metal conductors, yet uncertainty persisted regarding its high conductivity and future applications. Graphene research has progressed significantly in the last two decades, unveiling superior physicochemical properties in graphene layers and several composite forms.25–28
Significant advancements have been achieved in the development of graphene-based materials (GBMs) for a wide range of applications, particularly in gas adsorption technologies (see Fig. 2). As the diversity of GBMs continues to expand rapidly, there is an increasing need for a systematic and thorough comparison of functionalized GBMs in their efficacy for gas adsorption. This comprehensive review critically examines emerging synthesis strategies, including innovative approaches such as chemical vapor deposition and liquid-phase exfoliation, while also addressing the inherent limitations present in current volatile organic compound (VOC) and carbon dioxide (CO2) mitigation systems. Furthermore, the review identifies essential research directions aimed at overcoming these limitations, such as enhancing the selectivity and capacity of GBMs for targeted gas molecules, improving the scalability of production methods, and exploring novel functionalization techniques to optimize material properties for specific gas adsorption applications.
Notably, quite a few groups have reported that graphite (pristine) can be exfoliated to single-layer graphene devoid of defects using diverse solvents like benzylamine, ionic liquid, N,N-dimethylformamide (DMF), N-methyl pyrrolidone (NMP), ortho-dichlorobenzene, or water-surfactant solutions.37,38 For instance, as illustrated in Fig. 4, Hernandez et al. showed that graphite can be dispersed and exfoliated in solvents like N-methyl pyrrolidone, whose exterior energy is comparable to that of graphene, allowing the graphite layers to be exfoliated because the solvent–graphene interaction balances the energy needed for the exfoliation.
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Fig. 4 (A) SEM picture of pristine graphite, (B) SEM picture of sediment following centrifugation, (C)–(E) bright field TEM picture of single-layer graphene flakes deposited from GBL, DMEU and NMP respectively, (F) a folded graphene sheet (bright field, deposited from NMP), (G) multi-layer graphene (bright field, deposited from NMP), (H) an NMP dispersions histogram showing the number of visual assessments of flakes as a function of the total amount of monolayers for each flake.37 |
While the mechanical exfoliation method is simple and effective for producing high-quality GBM (HQGBM), one issue with this approach is that the solvents that work well for this purpose frequently have high boiling temperatures, making it challenging to get rid of the solvents.39 However, O'Neill's research team40 posited that graphene can be exfoliated at greater concentrations with a thickness of fewer than ten layers in low-boiling point solvents like isopropanol and chloroform. In addition, this method suffers a major disadvantage which is low scalability and an inability to regulate the resulting graphene flakes' size and form.35,41
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Fig. 5 Depicts the process of liquid-phase exfoliation (LPE) of graphite with the inclusion of naphthalene, comprising mixing, exfoliation, centrifugation, and vacuum filtration steps. Adapted with permission from ref. 45. |
Yi and Shen reported that aqueous or non-aqueous solvents with surface energies (SE) within 70–80 mJ m−2 or surface tension within 40–50 mJ m−2 are good for graphite exfoliation because they match graphite surface energy of 46.7 mJ m−2, due to the similarities in their SE to graphite ensuing in lesser mixing enthalpy, good wettability and simple exfoliation procedure.46 The solvent should be able to overcome the van der Waals force from the interaction between GLs, which are held within the π–π stacking distance of 3.35–3.4 Å.47 As a result, dimethylformamide (DMF, 35.2 mJ m−2), dimethylacetamide (DMA, 36.4 mJ m−2), and N-methyl-pyrrolidone (NMP, 41.3 mJ m−2)44 are often employed to exfoliate graphene. Solvents liquid phase exfoliation offers scalability and the ability to produce graphene dispersions, but the quality and yield of graphene can vary depending on the solvent and process conditions. Despite its many benefits, some studies have shown that sonication may result in flaws in the margins and basal planes of the GBM.48
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Fig. 6 Mechanistic synopsis of anodic and cathodic electrochemical exfoliation.51 |
More specifically, the ECEX of graphite is typically carried out in aqueous media, and the following are the primary procedures involved in this process:50,51
• Hydrolyzing water and generating O2 and OH radicals.
• The transfer of O2 and OH radicals to graphite and the opening of its edge.
• The creation of gas as a result of the electrolyte species intercalating and expanding the graphite.
For instance, Parvez et al. explored the exfoliation of graphite in an H2SO4 aqueous solution.52 To this purpose, they used a +10 V for two minutes to investigate the impact of H2SO4 concentration on exfoliation efficiency. The results indicated that 0.1 M H2SO4 had a higher exfoliation efficiency and yield than 1 M and 5 M H2SO4, most likely as a result of the more concentrated H2SO4 solutions producing bigger graphite particle pieces. On the other hand, exfoliation efficiency was decreased if the H2SO4 concentration was too low, most likely as a result of fewer anions. The scientists then looked at 1:
1 H2SO4/acetic acid mixtures and pure H2SO4; in these instances, there was virtually little exfoliation and just a small amount of expansion. This demonstrated the worth of water in the electrochemical process as it may generate OH and O2 radicals, which help with exfoliation and intercalation. The HQGBM that was exfoliated in a 0.1 M H2SO4 solution had a single sheet with a low sheet resistance of 4.8 kΩ per square, a large sheet size of around 10 μm, and a low oxygen concentration of 7.5 wt%.52
In another experiment, a straightforward electrochemical process for creating graphene/α-MoO3 composites was described by ref. 53. High-purity graphite rods, PTFE, sodium dithionite, potassium hydroxide, and sodium molybdate were utilized. In this research, an electrolysis cell containing 40 mL of 0.2 M sodium molybdate as the electrolyte was filled with two graphite rods. After applying a static potential of 10 V for 30 minutes, the anode graphite rod began to corrode. Subsequently, 0.15 grams of Na2S2O4 were introduced into the electrolyte to adjust the pH level. After two hours, the α-MoO3 GBM was removed from the reactor and cleaned in ethanol and deionized water until the pH reached neutrality. Afterward, they were dried for twelve hours at 60 °C in an oven. The α-MoO3 GBM was subsequently annealed at 200 °C in the air for two hours before being cooled to ambient temperature to produce a suitable conductive material. Their findings demonstrated that the α-MoO3 GBM has high thermal performance and that the α-MoO3 NPs are evenly dispersed on the surfaces of graphene sheets (GSs). Fig. 7 provides a schematic representation of the single-step ECEX and functionalization of graphene with α-MoO3. The MoO42− anions migrate to the graphite anode when the anodic voltage is applied, and in very acidic circumstances, MoO42− intercalates into the graphite underlayers and transforms into α-MoO3. Then, graphene/α-MoO3 composites are formed as a result of the exfoliation events.53
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Fig. 7 Plausible mechanism for the synthesis of α-MoO3 GBM by the ECEX process.53 |
In another study, different amounts of zinc nitrate in an electrolyte solution were utilized to create a variety of zinc oxide/graphene (ZnO/Gr) nanocomposites via an electrochemical exfoliation process. The authors found that ZnO/Gr nanocomposite produced using 7 mmol of zinc nitrate displayed a sheet-like morphology with an even decoration of ZnO NPs over the GSs, and was more effective in dye degradation application.54 Similarly, Kotkin et al. exfoliated cobalt and placed it surface of graphene utilizing the ECEX approach aided by plasma. Combining the 0.01 M CoSO4 solution with the 1 M Na2SO4 solution produced the utilized electrolyte. For ten hours, an alternating +300 V (anodic) and −150 V (cathodic) was employed Cobalt is deposited on the cathode's surface during the anodic mode of operation. The deposited cobalt particles are then dissolved in the cathodic type operation which produces the graphene/cobalt oxide composites.55 Motta's research team56 employed sonication for anodic ECEX of HOPG in an aqueous solution of sodium dodecyl sulfate and Na2SO4 electrolyte. It was discovered that the system with sonication generated largely four-layer graphene flakes, whereas the system with sonication supplied primarily bilayer graphene flakes. Additionally, sonication-assisted graphene sheet production yields higher-quality results than the non-sonication approach, as demonstrated by Raman spectroscopic observations. This is probably because graphite may be exfoliated more easily by ultrasonication, which shortens the period that graphite is intercalated and oxidized. Consequently, there may be a decrease in C–OH and CO oxygenated functional groups and defects.
In another study, Parvez and colleagues explored the exfoliating effects of a range of inorganic salt aqueous electrolyte solutions in anodic exfoliation, including (NH4)2SO4, K2SO4, NaNO3, NH4Cl, Na2SO4, and NaClO4.57 Notably, sulfate ions (SO42–) were discovered to have superior exfoliation efficiency compared to other anions. Investigations were also conducted on the impact of electrolyte concentration in the (NH4)2SO4 system. At concentrations below 0.01 M, less than 5 weight percent of the initial graphite was exfoliated. A yield of greater than 75 weight percent was obtained at concentrations up to 1 M. Nevertheless, because of the low water content and reduced graphite edge oxidation at concentrations of 3 M and 5 M, less than 50 percent yield was realized. In this study, it was discovered by the authors that ideal settings were 0.1 molar aqueous solution of (NH4)2SO4 with a +10 V. Under these circumstances, over 85% of GSs exhibit three layers or less, while over 80% exhibit a lateral dimension greater than five μm. About 44 μm was the biggest graphene sheet that was found using SEM. The ID/IG ratio was found to be 0.25 via a Raman spectroscopy investigation, which is significantly less than chemically reduced GO. The exfoliated graphene seemed to have a 5.5% oxygen content, according to XPS measurements. Additionally, the generated graphene demonstrated outstanding hole mobility of 310 cm2 V−1 s−1.57
Similarly,58 devised a facile technique that utilized anodic exfoliation of graphite in a mild NaOH/H2O2/H2O system. Exfoliation in this system is mostly dependent on H2O2, with exfoliation efficiency rising sharply between 0 and 130 mM H2O2 concentrations. The ideal exfoliation conditions were 3 M NaOH, 130 mM H2O2, and a working voltage of 1 V for ten minutes at room temperature, followed by 3 V for ten minutes. Under these circumstances, 95% of the high-quality GSs with three to six layers were formed. The product's ID/IG, a measurement of graphene flaws, was 0.67 in the Raman spectra as opposed to 0.54 for graphite. The introduction of oxygenated functional moieties during the ECEX process, which results in disorder at carbon edges, is what drives the rise in ID/IG.59,60 By and large, the electrochemical exfoliation approach offers a simple, fast, and scalable method for producing graphene, but the quality of the obtained graphene can vary depending on the electrolyte composition and process parameters.
In addition, the reductive process of GO is an essential process that is used in the restoration of the electrical conductivities and modification of the surface chemistry for specific usage.67 Although chemical reducers such as hydrazine hydrate and sodium borohydride can do the same task, they are very hazardous to the environment and to human health. On the contrary, ascorbic acid (vitamin C) has recently become a green non-toxic and biocompatible alternative material for the reduction of GO. Recently, it has been shown that the reduction of GO in mild conditions under the catalytic effect of L-ascorbic acid can be effective and that the resultant reduced graphene oxide (rGO) has greatly improved electrochemical properties and an insignificant environmental burden.67,68 It should, however, be noted that concentration that is too high may lead to partial reoxidation of rGO. Hence, there is the need to optimize reaction conditions in order to maintain the reduction efficiency.67
In recent times, solvothermal reduction and bioreduction methods using biogenic resources have been employed in material synthesis.69–72 For example, as shown in Fig. 8,73 present a simple and effective method for producing highly-rGO (P. glutinosa-HRGO) through the bio-reduction of GtO with plant extract from Pulicaria glutinosa. In addition to reducing GtO, the phytomolecules74–76 in the P. glutinosa extract also functionalize the biogenic HRGO nanosheets' surface and stabilize them in a range of solvents, reducing the need for additional, potentially hazardous chemical reductants and surfactants. By making biogenic HRGO with varying concentrations of P. glutinosa, the impact of P. glutinosa on its dispersibility in different solvents was examined. The dispersibility of biogenic HRGO was then contrasted with that of chemically rGO. The biogenic HRGO was of higher quality than chemical RGO73 owing to the various phytochemicals present in the biogenic extract.32,77,78 GtO reduction, like liquid phase exfoliation, may achieve large-scale graphene fabrication;29 however, this method is somewhat constrained by intricate procedures and structural flaws, as well as presenting environmental concerns.
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Fig. 8 Reduction of GtO utilizing an aqueous extract of the P. glutinosa.73 |
In another study, Lv et al. reported dry ball milling for the fabrication of graphene nanosheets. In this study, the authors used the soluble salt-assisted method to manufacture graphene nanosheet powder.81 A stainless-steel jar containing 50 g of Na2SO4 powder, and some graphite was subjected to a 24-hour ball milling process at 150 rpm. As the ratio of Na2SO4 was increased, the number of layers rapidly dropped to bi-layers from multi-layers. Similarly, Lin's research group82 employed a ball milling technique combined with shear force to grind elemental sulfur, which aids in exfoliation and attachment onto GSs in a structure with 73 wt% sulfur. The research group developed high crystalline GSs by using sulfur, a substance that is somewhat sticky for the graphite plane, as a substitute for Scotch tape. Ball milling is a scalable and simple method for producing graphene, but the process parameters must be carefully controlled to prevent contamination and damage to GSs.
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Fig. 9 Diagrammatic depiction of the arc discharge process used for fabricating graphene.85 |
Similarly, Cheng et al. employed a vacuum ADC approach integrated with a high-temperature furnace was used to synthesize graphene on copper foils. By combining the benefits of vacuum ADC with chemical vapour deposition, SLG may be produced at a base temperature of 600 °C using a tiny furnace.86 The substrate surface can then be quickly heated to 1100 °C using photon radiation from the vacuum arc. Through a series of studies on processing time, arc currents, cooling, and ambient pressure, the ideal fabrication condition was found. SEM, Raman spectroscopy, and optical microscopy observations revealed that the principal products were SLG, which has a consistent thickness across the substrate. The findings showed that a simple and inexpensive way to synthesize GSs for graphene-based applications is to combine a vacuum arc with a thermal approach that employs graphite as a carbon source.86
In another study, an ideal He ADC approach uses an 80 A current and 550 torr of He atmospheric pressure to fabricate GSs. The result shows that single-layer, double-layer, and few-layer GSs were produced.87 In a similar study, Kim's team88 demonstrated that high-quality BLG and FLG could be produced with fewer layers of graphene by using the aqueous ADC technique; the mean lateral diameters of these products ranged from 4.4 to 28.3 μm. The interlayer gap was preserved at around 0.34 nm for every level of the ADC power, and the regulation of the quantity of GLs stacked was achieved by adjusting the power of the ADC. Notably, in contrast to earlier research, the arc-discharge approach was used by ref. 89 to study the development processes of FLG under real production settings including He, O–He, and H–He. The production of a few layers GSs with lateral widths ranging from 50 to 300 nm was seen exclusively in the presence of reactive gases. This finding may suggest that the growth process of FLG involved the evaporation of graphite followed by the reactive gas-confining crystallization of the evaporated carbon clusters. The major advantage is that the ADC approach is an eco-benign and inexpensive technique that can effectively fabricate HQGBM in relatively high yields.90,91 However, this method has the disadvantage of carbonaceous impurities.92 Since the kinds of buffer gases and arc parametric settings affect the quality of graphene, additional adjustment of these factors is necessary to increase the effectiveness of the preparation process.29 Therefore, more investigation into the fundamental mechanics behind the synthesis of graphene is needed for a more in-depth understanding of process parameters and techniques required to obtain desired graphene morphology and physicochemical properties.
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Fig. 10 (a–f) Showing the different stages of the fabrication of a graphene fibre and integration with PDMS.101 |
Following the report of Chen's team,101 various researchers102–104 have employed diverse carbon sources and or reaction conditions to synthesize high-quality three-dimensional GBMs using the template-assisted CVD technique. For instance, Liu's group104 produced a graphene film with great crystallinity by using asphalt as a carbon source. In this research, after one hour of immersion in the asphalt-toluene solution, the cleaned Ni foam was dried. The Ni foam encased in asphalt was put in the middle of the tube furnace and given a 10-minute breakdown treatment at 940 °C and 1.5 × 103 Pa. After the NF was removed by etching, graphene foam made up of two to five layers of GSs was produced. In another experiment, Kim's group105 employed the CVD approach to produce graphene on commercial 3D Cu foam (CF). To preserve the 3D structure, a poly(methyl methacrylate) layer was spin-coated on the 3D graphene/CF. After chemically etching the CF out of (NH4)2S2O8 solution (1 wt%), a 3D GBM was produced.
Conversely, Wei's group106 fabricated a 3D graphene network without needing a solvent. In this study, CF was first obtained by annealing Cu powder at 1000 °C with 200 sccm H2. Next, using the CVD process, GLs were produced on this 3D Cu foam. By using a high-temperature evaporation procedure to take out the Cu template, a 3D graphene network was created without the need for a solvent process. In another study, rapid thermal CVD produced around 12.31% more graphene domains than thermal CVD did.107 Another work by Liu's group108 used naturally occurring scallops as the raw material to create a low-cost, readily removable CVD template. The scallop was heated in the air to produce a very porous CaO framework. Next, using the CVD process, GLs are developed on the constructed framework. After the CaO was finally etched in diluted HCl and freeze-dried, a self-supporting 3D GF was produced. Also, HQGBM with several layers was synthesized on Cu–Ag alloy powder by in situ CVD at 900 °C by ref. 100. In another study, by allowing carbon atoms to diffuse through the nickel template, Xu's research team109 synthesized a centimetre-scale, extended SLG on a Ni surface placed on a highly oriented pyrolytic graphite substrate. Their findings show how to optimize the temperature and annealing time, two critical factors for graphene formation, to produce precise control over the degree of thickness and structure of the GLs.
In another investigation, the significance of kinetic variables in the CVD preparation of homogenous large-area graphene utilizing Cu catalyst has been explored by ref. 110. It was discovered that at low methane concentrations (ppm), graphene grew as a monolayer, and at higher concentrations (5–10% by volume), it formed multilayers at atmospheric pressure. Another research group111 shows the use of centimetre-scale Cu substrates as a novel path for the industrial-scale fabrication of high-quality GSs. This efficient, time- and money-saving roll-to-roll approach yielded 30-inch GSs while also offering a large-scale, high-quality, and productive graphene synthesis for real-world use. Although, the CVD method is effective and controllable as stated earlier.29,112 Nevertheless, it is extremely difficult to precisely manage graphene's edge structure and topology.39 Additionally, when CVD GBM is formed on catalytic metal substrates like Pt and Ir, defects can occur.98 Hence, to control the grade of the GBM, it is crucial to adjust preparation parametric conditions including growth temperature, working pressure, deposition duration, substrate type, and flow frequency of H gases and C precursor appropriately.
In a more recent study, a four-inch single-crystal monolayer graphene wafer grew on Cu90Ni10 film owing to the substantial increase in catalytic activity of trace Ni, and this growth process occurred fifty times more quickly than on Cu.115 Furthermore, many research teams have created alternative EG growth methods to produce larger and better-quality graphene.60 For example, in place of the previously employed vacuum breakdown of SiC, Emtsev et al. described the fabrication of single-layer GSs with greater domain sizes (3 × 50 μm2) using an ex situ graphitization of Si-terminated SiC at argon atmosphere under 900 mbar.116 They have improved the control rate of Si sublimation using this novel method, which has improved the material's surface morphology. In like manner, through the development of an alternative growth approach, De Heer and his colleagues117 were able to regulate the Si sublimation by encasing the SiC crystals in graphite enclosures. They prevented Si from escaping, resulting in a high Si vapour pressure and excellent control over the graphitization temperatures. Consequently, they were able to create homogeneous GLs of excellent quality on both the C-facing and the Si-terminated face of the SiC single crystal. The epitaxial growth method and the result obtained by ref. 117 are similar to the one reported by ref. 118 but by adopting a Si flux approach that used disilane gas to manage the Si vapour pressure, which improved graphene's quality.
Notably, the following are the main benefits of epitaxial growth: (i) the material produced may be guided by properly tailoring the substrate; (ii) there are no trapped contaminants beneath the graphene, and (iv) the material does not need to be transported from the metal to another dielectric substrate.39 Nevertheless, the primary constraints of this technique are the high temperature employed throughout the procedure and its non-transferability to alternative substrates. Hence, further investigation is needed into the proper substrate choice and how it affects the growth and crystalline quality of graphene.
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Fig. 11 Synthesis of PDAPP and its benzannulation to form GNR.121 |
Furthermore, a variety of nanographenes with different architectures and thicknesses may be synthesized by adjusting the structure of the precursor monomers.122,123 For example,122 propose a surface chemical pathway that makes it possible to synthesize customized nanographenes from polyphenylene precursors with atomic precision. Scanning tunnelling microscopy and density functional theory are used to study the cyclodehydrogenation of a typical polyphenylene on Cu. The research findings provide unheard-of insight into a dehydrogenative intramolecular aryl–aryl coupling process. The authors discover that thermally driven cyclodehydrogenation occurs via many intermediary stages, two of which may be stabilized on the surface. Unfortunately, the main issue in the field of organic synthesis of nanographene is how to practically process large polycyclic aromatic hydrocarbons (PAHs).
Specifically, it has been discovered that strong intramolecular π–π interactions lead PAHs bigger than hexabenzocoronene to be insoluble in organic solvents or sublimable without crumbling.124 Interestingly, it has been accentuated that bringing the long, flexible aliphatic chains to the edge of the planar nanographene is one method of solubilizing the nanographene.125,126 Nevertheless, this strategy becomes less effective as graphene gets bigger, thus the need to develop novel approaches to address this issue. Sun et al. attempted to address this setback by using a metal catalyst substrate and a temperature of 800 °C to deposit large areas of HQGBM with controllable thickness without the use of aromatic polymers.127 The organic synthesis technique is a useful addition to CVD growth as it allows for relatively low-temperature development and gets around the CVD method's constraint on the use of gaseous ingredients. However, graphene's large-scale production is limited by the comparatively high cost of the organic synthesis route.
For example, Lin and colleagues employed a CO2 infrared laser to directly scribe commercial polymer films, yielding porous graphene films with intricate three-dimensional structures. They also utilized a fast and versatile laser reduction technique on GO, enabling the direct formation of graphene on solid surfaces with submicron dimensions, without the need for chemicals.131 In 2020, Stanford and co-workers132 developed laser-induced graphene (LIG) by utilizing a visible 405 nm laser, connected to a fibre with a low power of roughly 161 mW, a diameter of about 3 μm, and a pulse duration ranging from 2 μs to 100 ms, on a polyimide (PI) surface. By positioning this laser setup atop an SEM chamber, they observed the real-time formation of laser-induced graphene through secondary electron imaging. A minimum fluence of 83.4 J per cm2 per pulse was necessary to generate laser-induced graphene. The process resulted in laser-induced graphene formation within the upper 5 μm of the substrate, with a lateral resolution of approximately 12 μm, forming a pattern of around 60 μm in size as depicted in the images. In another study, using a CO2 infrared laser scriber,133 devised an alternative method for fabricating 3D porous graphene on PI in ambient settings. Using this novel method, modified PI (m-PI) was created by combining poly(amic acid) (PAA) with N-methyl-2-pyrrolidone additions and then drying the mixture. When the m-PI was exposed to laser light, different compositions of LIG were formed. The thicknesses of the LIG produced ranged from 20 μm to 1 cm. The researchers then looked at how LIG formed on lignocellulose materials such as bread, potatoes, and wood. The results were good; when a defocused laser point of about 1 mm was employed to laser-seed in an inert or reducing environment, many wrinkles appeared in the LIG. Furthermore, this team investigated the feasibility of scale-up manufacturing to meet the needs in practical applications, and they presented two solutions for the mass production of LIG.133
Kulyk's research team also created LIG on cellulosic materials by irradiating filter paper with a CO2 laser.134 The study explored how various factors like distance between substrates, scanning speed, and laser intensity impacted the result. Creating paper LIG involved two laser phases: the first, out-of-focus phase charred the cellulose, while the second, in-focus phase transformed the char into LIG. To prevent cellulose from becoming LIG prematurely, 6 × 6 mm2 filter paper pieces, 290 μm thick, were treated with a fire retardant. Using a power of 1.1 W caused significant damage to the paper, while powers ranging from 600 to 800 mW were effectively utilized without harm. Different scanning speeds and defocusing distances were tested, resulting in samples retaining their fibre structure with minimal visible flaws and maintaining high morphological integrity.134 In another study,135 created micron-scale LIG by irradiating a positive photoresist (PR), which is often used in commercial photolithography and is made of 15–25% Novolak resin. The scriber utilized for this process had a spatial resolution of around 10 μm and was made of a 10.6 μm CO2 infrared laser. An acetone bath was used to dissolve the unsealed PR. To begin with, Si wafers were spin-coated with PR at 500–3000 rpm. Wafers were hard-baked at 120 °C for 45 minutes after spinning. As precursors, thin PR (3–8 μm) were used. A defocused laser beam repeatedly illuminates the same area because of the increase in spot size. To produce LIG in one pass, a defocus of 1.78 to 2.54 mm is needed. As the frequency of laser passes rises, the thickness of the defocused laser LIG varies. Initially, its growth is fueled by the development of gas impurities on the initial laser surface, yet it gradually diminishes as additional material is vaporized and graphene is generated through successive laser treatments. The sheet resistance fluctuates based on laser intensity, the number of treatments, and the deviation in focus, all contingent on the specific conditions during laser processing. Due to film degradation in the form of blistering or cracking, it has lower values at high power. Moreover, doing more passes enhances the sheet resistance.135
Researchers have also tried to use pulsed laser irradiation to ablate carbonaceous targets in liquid, vacuum, and gas environments to fabricate GBM.136–138 For the first time, Qian's research group137 detailed their findings on producing 2D graphene by employing pulsed laser exfoliation of HOPG with a pulsed neodymium-doped yttrium aluminum garnet (Nd:YAG) laser. They utilized a 532 nm laser with a pulse width of 7 ns, repeating at 1 Hz, and varying laser fluences from 0.8 to 20.0 J cm−2. The substrate employed was a silicon wafer. The substrate was a silicon wafer. Different phases of carbon nanostructures, such as thin graphite films, few-layer graphene, and amorphous carbon, were created. In particular, GSs with dimensions of tens of micrometres, a thickness of a few nanometers, and a diameter of around 3.9 nm were produced. In like manner, as shown in Fig. 12, Nancy's work139 served as an example of a unique laser-induced synthesis of silver nanoparticles (Ag NPs) that are attached to the GO layers using a single-step green approach known as pulsed laser ablation. Colloidal Ag–GO nanohybrid materials are created by producing Ag NPs from a bulk solid silver target ablated in an aqueous solution of GO using the second and third harmonic wavelengths (532 nm and 355 nm) of a Nd:YAG pulsed laser.
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Fig. 12 The setup for producing colloidal Ag–GO nanohybrid graphene.139 |
Russo, Hu140 also reported a novel, green, scalable, and one-pot method for synthesizing graphene quantum dots and porous graphene by ablation of HOPG in water utilising a pulsed laser with a wavelength of 800 nm, a repetition rate of 1 kHz, a pulse duration of 35 fs, and a fluence of 20–30 J cm2. For 20 minutes, the precursor was ablated continuously at a steady fluence. Porous graphene (quantum dots) of varying layer thicknesses, spanning from one layer to many sheets, were observed abundantly within the product generated post-ablation, looking like stacked layers floating atop the water–air interface of the resultant solutions. Their typical diameters were ≥100 but ≤200 nm, featuring a textured surface marked by folds attributed to the deposition process of the silicon substrate. Exhibiting a three-dimensional porous architecture, the layers contained pores ranging from 10 to 20 nm in size.140 Generally, laser-induced graphene commonly has high thermal stability greater than 900 °C, admirable conductivity between 5–25 S cm−1, and a high SSA of up to 340 m2 g−1.141 This approach is better than CVD since it may be carried out in conditions where accurate regulation of pressure and the presence of ultra-pure gases are not necessary. In addition, by using roll-to-roll automation, it may be readily scaled up to produce graphene on a huge scale, offering tremendous commercialization prospects.
GBMs | Volatile organic compound | Adsorption capacities | Removal efficiency (%) | Reference |
---|---|---|---|---|
ZIF-8/GO | Toluene | 116 mg g−1 | — | 155 |
rGO/KOH | Acetaldehyde | 630 mm3 g−1 | — | 156 |
rGO | Toluene | 454 mg g−1 | — | 157 |
Graphene-PhAPTMS | Toluene | — | >95 | 158 |
Cu-BTC/GO | Toluene | 183 mg g−1 | — | 159 |
rGO/polypyrrole | Benzene | 15.8 mmol g−1 | — | 160 |
GO/ordered mesoporous carbon composite | Benzene | 9.6 mmol g−1 | — | 161 |
rGO MW/KOH | Toluene | 3510 mm3 g−1 | 98 | 156 |
Acetaldehyde | 630 mm3 g−1 | 30 | ||
Thermally expanded graphene powder | Toluene | 691 cm3 g−1 | 92.7–98.3 | 162 |
Xylene | 191 cm3 g−1 | 96.7–98 | ||
Few layered mesoporous graphene | Toluene | — | 260 mg g−1 | 163 |
Graphene/metal–organic composites | Benzene | — | 72 cm3 g−1 | 164 |
rGO | Benzene | — | 276.4 mg g−1 | 149 |
Toluene | — | 304.4 mg g−1 | ||
Thermally exfoliated graphene oxide | Benzene, toluene, xylene | — | 98 ± 2 | 165 |
Graphene | Benzene | 8.8–158 mg g−1 | — | 166 |
Xylene | 8.53–156 mg g−1 | |||
n-Hexane | 7.13–126 mg g−1 | |||
Toluene | 8.76–162 mg g−1 | |||
Carbon tetrachloride | 9.6–166 mg g−1 | |||
L-GO/polypropylene masks | Xylene | 804 mg g−1 | 98.9 | 167 |
Graphene-based adsorbents were employed in a study to remove acetaldehyde and toluene gases. The study treated graphene oxide with KOH activation and microwave irradiation to form micro sized pores. The results of the study indicated that the graphene surface expanded, and its specific surface area increased when pristine graphene was heated to about 800 °C under KOH activation and then exposed to microwave radiation. Impressive maximum volume capacities of 3510 m3 g−1 for toluene and 630 m3 g−1 for acetaldehyde gas were demonstrated by the material. The exceptional removal efficiency of toluene (98%) in contrast to acetaldehyde (30%) gas was ascribed to the strong interactions that transpired between the toluene molecules and the pristine graphene surface.156 In consonance with the literature, the adsorption of toluene on the graphene material is largely due to the non-covalent interaction occurring between the aromatic ring of toluene and the π electron-rich region in the basal plane of the graphene.168,169
In addition, adjusting several factors such as surface functional groups, humidity, boiling point, polarity, pore distribution, pore size, and specific surface area have been shown to enhance the chemisorption or physical adsorption performance of adsorbents.170,171 A study investigated the use of mesoporous graphene powders produced by thermal expansion method as adsorbents in the removal of toluene and xylene.162 The results of the study showed that the thermally expanded graphene powder (TEGP) exhibited relatively high adsorptive capability at each tested concentration of toluene and xylene. Despite the high specific surface area exhibited by TEGP, there were variations in its total adsorbed volume capacity of toluene and xylene, suggesting that the adsorption of the gas molecules is not only predicated on specific surface area. It is noteworthy to point out that the study reported 691 cm3 g−1 and 191 cm3 g−1 total adsorbed volume capacities for toluene and xylene, respectively. This significant variation was attributed to the relatively smaller molecular size of toluene which indicates more of the toluene gas would be adsorbed at any given volume.162
It has been suggested that the specific technique adopted in building graphene architectures is an influential factor for its hierarchical porosity and large specific surface area. Some of the widely adopted techniques have included activating the graphene material with various activating agents.172–174 However, these activating agents cause the resulting activated graphene materials to exhibit extra hydrophilic sites and random porous architectures. To circumvent this, the chemical vapour deposition method stands out as a promising and attractive technique in the construction of graphene materials with mesoporous structures for the adsorption of VOCs.175–177 Wang et al. (2019) employed a graphene material fabricated by the chemical vapour deposition method in the adsorption of toluene. The study showed that a three-dimensional architecture made of graphene layers was demonstrated using the as-prepared few-layered mesoporous graphene (FLMG). The remarkable adsorption capabilities of FLMG were a result of its distinctive architecture, especially when it comes to toluene at low concentrations (120 ppm). Strong π–π interactions and a large specific surface area (SSA) of 1990 m2 g−1 were important factors in this adsorption behaviour. Interestingly, even at a low heating temperature of 95 °C, a high desorption ratio of 92% ± 4% was achieved owing to interconnected mesopores that promote efficient desorption. These features allow FLMG to demonstrate reusability. Furthermore, FLMG is endowed with inherent thermostability and hydrophobicity via the chemical vapour deposition technique. FLMG maintained 80.1% ± 3.4% of its initial adsorption capability even at high humidity levels.163
Similarly, another study employed the use of the chemical vapour deposition method in synthesizing graphene and the activated graphene was used in the adsorption of benzene, toluene, and xylene.178 The results of the study showed that the activation of the graphene material increased its surface area from 298 to 568 m2 g−1. In addition, the study reported that a significant quantity of benzene, toluene, and xylene was adsorbed from a typical gasoline vapour using the synthesized activated graphene, highlighting that hydrophobic interactions, π–π bonds, and electrostatic interactions are the effective forces responsible for the adsorption of these compounds.149,178
Graphene oxide has phenolic hydroxyl and epoxide groups on its basal plane and carboxylic groups on its edges. Reduced graphene oxide is generally produced by thermal annealing or chemical treatment which eliminates the functional groups present on the graphene oxide.148 The reduced graphene oxide is preferred to graphene oxide due to its higher surface area, higher hydrophobicity, and lower oxygen content, all of which give it superior adsorption capability.179 A facile and cost-effective method was adopted by Yu et al. (2018) to prepare reduced graphene oxide, which was adopted for the adsorption of VOCs. According to the results of the adsorption experiment, reduced graphene oxide was able to adsorb more benzene and toluene than graphene oxide. At room temperature and normal pressure, reduced graphene oxide's breakthrough adsorption capacity was 304.4 mg g−1 for toluene and 276.4 mg g−1 for benzene, respectively.149
Recently, extensive research has been carried out to enhance the adsorption efficiency of carbon-based materials by modification using metal elements.180–182 A density functional calculation study was conducted by Liu et al. (2019) to understand the adsorption mechanisms of pristine PG monolayer and Al-modified PG (Al-PG) monolayer in the removal of VOCs. The findings of the study showed that PG monolayers are excellent adsorbents for volatile organic compounds (VOCs). The adsorption energy of carbonyl-containing VOCs (CVOCs) is enhanced further after Al decoration, and it is nearly twice as high as that of CVOCs adsorption on PG monolayer. The electronic structure analysis (Mulliken charge distribution, electronic density distribution, and the density of state) revealed that the carbonyl group can attract the Al atom with the formation of a C–Al bond, which causes the connection of CVOCs and Al-PG substrate in the adsorption process and also greatly strengthens the adsorption of CVOCs.183
Despite the great application potential shown by porous carbon materials including graphene in the adsorption of VOCs, most of these porous materials exist in block or powder form and as such cannot be used in wearable personal protective applications. Polypropylene masks are more flexible and comfortable to wear than carbon materials, but they are unable to intercept small VOCs due to electrostatic interactions and visible fibre pores. Hence, a possible combination of carbon materials and polypropylene masks would result in a personal protective fabric with the ability to effectively absorb VOCs. This led Cheng et al. (2024) to create a novel method for carbonizing polypropylene mask surfaces by making use of graphene's superior laser responsiveness. To create a thick layer of graphene oxide, they applied an aqueous solution of the material to the mask's surface. Next, they used a more controllable 1064 nm near-infrared laser to irradiate the graphene oxide coating.167 This novel double-layer fabric has two functions: it efficiently performs solar-powered desorption and recycling and recovers low-concentration VOCs from gas, achieving about 98.9% removal in just 30 seconds. The fabric's design makes use of easy-to-use and cost-effective coating and laser irradiation techniques. The hydrophilic porous channels created by laser-induced thermal degradation of graphene oxide coatings in ambient air are responsible for this fabric's exceptional adsorption capability. These channels help conjugated double bonds and hydrophilic groups interact with the benzene rings found in VOCs.167
From the foregoing, it suffices to say that the utilization of graphene composites, which involve combining graphene with other materials, significantly broadens their range of applications. In most cases, the removal efficiencies were well over 95%, suggesting that these materials are capable of removing the target VOCs. These composites are very useful in practical applications because they have additional characteristics, including chemical stability, mechanical strength, and flexibility. Novel strategies for solar-driven desorption and recycling improve the energy efficiency and sustainability of graphene-based adsorbents. This is in line with the increasing emphasis on eco-friendly technologies. Additionally, the creation of wearable and flexible adsorbent materials presents intriguing new opportunities for personal protective equipment, particularly in environments where VOCs are present in high concentrations.
A large surface area is essential for any adsorption-based filter. If the surface area were greater, more particulate matter would be caught during the process of adsorption onto the filter surface. Broadly speaking, a two-dimensional (2-D) material is larger than a three-dimensional (3-D) material by nature in terms of surface area per weight. Most of the filters used currently are 3-D nanofibers or nanoparticles.189 This informed the development of a 2-D material, reduced graphene oxide, in the design of a filter for the removal of PM2.5.189 According to the findings of the study, the filter's highly porous and void structure minimizes pressure loss while allowing air to flow through it quickly. Particulate matter (PM) can be effectively removed because there are enough sites for adsorption on the wide surface area. Interestingly, the quality factor of the filter is almost twice as high as the best-reported literature values. Additionally, dual filtering for both incoming room air and recirculated air is made possible by the foam built on both sides of the copper mesh. The filter's robustness is demonstrated by the fact that it still performs more than 99% PM reduction after five cleaning and reuse cycles. Its low power consumption, bidirectionality, scalability, and ease of manufacture make it a viable option for high-efficiency PM2.5 removal filters.189
A relatively recent technique called electrospinning can be used to create ultrathin polymer and polymer composite fibres. A new and flexible technique for creating fibres made of spiderweb-like nanowebs that may be used for a range of applications is electrospinning.190 Due to their huge surface area and great mechanical strength, electrospun fibres are able to collect both ultrafine particles and high-mass droplets. Additionally, because of the advantages of the reticular support structure and winding pore channels, electrospun fibres can be used to synchronously implement air flow and have the desirable capacity to tackle PM.191 Dai et al. (2021) prepared a PAN/GO/PI nanofibrous membranes by incorporating graphene oxide and polyimide into a solution of polyacrylonitrile. When compared to pure PAN and PAN/GO nanofibrous membranes, the air filter made of PAN/GO/PI nanofibrous membranes was more successful at capturing PM2.5 particles. The PAN/GO/PI nanofibrous membranes exhibit exceptional mechanical properties, superior thermal stability, reduced pressure drops, and great filtering efficiency. The interaction between PM2.5 particles and PAN/GO/PI nanofibrous membranes, which have the ability to draw in and firmly adsorb PM2.5 particles, is responsible for the high filtration efficiency (99.5%).192
Similarly, a filter based on rGO-functionalised PAN nanofibrous membrane was fabricated by electrospinning and used in the removal of PM2.5.193 Based on both hydrogen bonding and dipole–dipole interaction forces, the study showed that the rGO nanosheets scattered on/in the PAN NFM significantly increase the PM2.5 capture sites on the uncross-linked nanofibers. Furthermore, because of the superior mechanical qualities of the rGO nanosheets, the tensile strength of the rGO-functionalized PAN NFM (0.48–1.25 MPa) is significantly higher than that of the pure PAN NFM (0.19 MPa). During air filtration, the composite NFM's increased tensile strength efficiently increases gas permeability. Thus, for resisting the airflow with a high gas velocity of 20 L min−1, the ideal NFM containing 2.5 wt% rGO nanosheets demonstrated >99.9% PM2.5 removal efficiency, 0.094 Pa−1 quality factor, and only 70 Pa pressure loss.193
Graphene aerogels areemerging super elasticity macroscopic and low-density porous materials with a wide range of uses. The development of a flexible approach for large-area, high-performance graphene aerogels at ambient conditions, which is essential for their practical applications, is still a difficulty.194 Yan et al. (2019) developed a strategy to fabricate graphene aerogels under ambient conditions and this was used in the adsorption of PM2.5. The results of the study showed that the as-formed aerogels are suited for pressure/strain sensors because of their super-elasticity (rapidly recoverable from 95% compression), low density of 3.6 mg cm−3, and stable honeycomb-like coarse-pore structure. Additionally, aerogel shows strong recycling potential and better particulate matter adsorption efficiency (PM2.5: 93.7%).194
Furthermore, most of the current research on air purification using graphene is widely focused on the mixing of graphene with other additives to obtain composite materials. However, Zou et al. (2019) prepared a graphene oxide membrane and used it in air purification. The efficiency of particulate matter (PM) removal as well as the effects of wind speed and pollutant concentration on a graphene oxide (GO) membrane were examined in the study. Notably, the GO membrane attained its maximum efficiency of 99.46% PM2.5 removal at a wind speed of 0.1 m s−1, with a minimum pressure drop of 7 Pa and a quality factor (QF) of 0.75 Pa−1. The GO membrane exhibited prolonged adsorption efficiency. Furthermore, the removal effectiveness of the GO membrane was improved by larger import concentrations and lower wind velocities. The effective PM2.5 capture by the GO membrane was verified by energy-dispersive X-ray spectroscopy (EDS) and scanning electron microscopy (SEM).195
The high efficiency of graphene-based materials in the adsorption of PM2.5 has been demonstrated in this study. Nevertheless, it is imperative to ensure the high effectiveness of PM2.5 filtration in addition to an ideal airflow with minimum pressure drop. Previous research has focused on methods to minimize pressure loss; nevertheless, more studies are needed to guarantee efficient air circulation in practical situations. There are still issues with the cost-effectiveness and scalability of graphene-based filters. Even though laboratory-scale research shows promising results, it is still unclear how large-scale manufacturing and commercial viability can be achieved.
Graphene was doped with transition metals (Cu, Ni, Co, and Fe) and it was investigated in the adsorption of NO, NO2, and other gas molecules. The adsorption properties were calculated using a first-principle study.199 The results of the DFT study indicated that among all the metal dopants, only Fe exhibited covalent bonding with graphene. The greater oxidation state of the Fe atom was attributed to be the likely cause of this phenomenon. Interestingly, in terms of charge transfer, the adsorption energy linked to transition metal doping is greater than that of pure graphene. Moreover, Fe exhibited the best adsorption energy, charge transfer, and intermolecular distances when transition metal atom doping is taken into account.199 Furthermore, doping has been reported to enhance the electronic behaviour of semi-conductor materials.200 Many kinds of dopants have been adopted to enhance and expand the applications of graphene.201–203 The use of aluminum has been associated with the modification of electron density allocation around the doped atom and this has found applications for different purposes.204–206 In a study, a nanostructure adsorbent, Al-modified graphene, was developed for the adsorption of N2O and NO2, with density functional theories.207 The study showed that introducing aluminum (Al) doping to the graphene structure can significantly change the originally weak physisorption of gas molecules on pristine graphene into chemisorption. The electronic structure of graphene is altered by the presence of doped Al, which leads to strong adsorption of the gas species. Interestingly, Al-doped graphene (AlG) showed high adsorption of these gas molecules, but pristine graphene (PG) showed weak adsorption. The density of state analysis (Fig. 13) successfully confirmed this contrast.207
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Fig. 13 The density of state for isolated PG, PG-NO2, PG-N2O, isolated AlG and the most stable configurations of AlG-NO2 and AlG-N2O.207 |
Moreover, tuning the thermoelectric, optical, electronic, mechanical, and structural properties of two-dimensional layered materials is widely influenced by native defects.208–211 The presence of inactive surfaces on pristine graphene has led to low adsorption energies during the detection of several gas molecules.212,213 However, the chemisorption of gas molecules is facilitated by the presence of defects in graphene.214 It has been suggested that the enhancement and induction of selectivity can be achieved by decorating graphene with nanocomposites.215,216 Ali and Tit (2019) carried out a study to investigate the adsorption of NO and NO2 on ozone-treated graphene using density functional theory. The findings indicated that in addition to improving the selectivity of the sensor, ozone treatment of graphene requires more carbon vacancies in order to accommodate gas molecules. In agreement with experimental data, the findings showed that higher sensor response is a consequence of the chemisorption of NO2 on graphene with mono-vacancy, compared to NO.217
Due to its exceptional structural qualities, such as its ultrahigh specific surface area, and its electronic characteristics, such as its high electron mobility and low electrical noise, graphene, or monolayer graphite, has drawn a lot of interest in gas sensing.218 Because surface adsorbates operate as electron donors or acceptors, they alter the local charge carrier density, which in turn affects the conductance of graphene sheets, which is the basis for several graphene-based sensors.219 Because of its high surface area, strong chemical and thermal durability, high functionalization capability, and versatility in comparison to other nanostructure gas sensor systems, graphene is a good choice for high-sensitivity, label-free chemical sensors.219,220
Although pristine graphene by itself is not very good at sensing gases such as H2O, NH3, CO, NO2, and NO,221 scientists have discovered a useful method to improve its sensitivity and performance. This entails substitutional doping of graphene, which shows potential for creating even more sensitive sensors.222 This informed the study undertaken by a group of researchers to investigate the comparative potential of pristine graphene and Ga-doped graphene in the adsorption of NO2, NO and other gases using density functional theory.223 The results of the study (Table 2) showed that there is little charge transfer because of the weak adsorption of gas molecules on pristine graphene. This is explained by the weak interaction between the gas molecules and graphene's π electrons. As opposed to pristine graphene, Ga-doped graphene showed a noticeably higher affinity for the studied gas molecules. Chemisorption on Ga-doped graphene was observed by analyzing the density of states (DOS) and electron density plots (Fig. 13). This process is characterized by comparatively high adsorption energies. Strong chemical bonds and a significant band gap are formed as a result of the interaction between the orbitals of gas molecules and the electron cloud. Due to prominent changes in the electronic structure and charge transfer between the gas molecule and Ga-doped graphene, NO2 notably exhibited greater adsorption energies on Ga-doped graphene (Fig. 14).223
Adsorbate | Pristine graphene | Ga-doped graphene | ||||
---|---|---|---|---|---|---|
Ead | Q | h | Ead | Q | h | |
a Where Ead = adsorption energies, Q = Hirshfeld charge transfer, and h = adsorption height. | ||||||
NO | −0.191 | 0.030 | 3.164 | −0.779 | −0.034 | 2.079 |
NO2 | −0.425 | −0.199 | 2.841 | −1.928 | −0.239 | 1.957 |
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Fig. 14 Electronic deformation density for NO2 molecule on Ga-doped graphene under an electric field of (a) 1 V per Angstrom, (b) 0 V per Angstrom and (c) −1 V per Angstrom.223 |
While a study showed that the adsorption of gas molecules including NO and NO2 is significantly enhanced by decorating graphene oxide with lighter, cheaper, and more eco-friendly metals such as Al and Li,224 another study investigated the doping of pristine graphene with Fe (FeG) and reported the high stability and increased adsorption of nitrogen oxides on FeG relative to pristine graphene,225 and another study reported that doubly doped defective graphene with boron, nitrogen and oxygen are more promising candidates for gas adsorption than pristine graphene although doubly doped defective graphene with fluorine was reported to be unsuitable for gas adsorption owing to large structural deformation, high formation energy, and high recovery time despite its interaction with the gas molecules in high adsorption energies,226 the recurring theme in all of these studies is that doping significantly improves the adsorptive properties of graphene based materials towards gas molecules and this is consistent with many other studies in the literature.227,228
The adsorption of various gas molecules, including NO and NO2, onto pristine graphene is characterized by weak physisorption. This phenomenon primarily arises from the relatively weak interaction between the gas molecules and the π electrons of graphene. Consequently, minimal charge transfer occurs, leading to low adsorption energies and corresponding adsorption heights. As highlighted, defect engineering and doping are pivotal in improving the adsorptive capabilities of materials. Nevertheless, it is important to learn more about the durability and resilience of these modified materials to make sure they are practically feasible. For practical applications, longevity and resistance to environmental degradation are equally essential. Getting graphene-based materials onto the market for gas adsorption will require overcoming the tremendous obstacle of scaling up manufacturing while maintaining consistent quality and performance. Material integrity must be balanced with mass production.
Pan and his colleagues synthesized HKUST-1, a widely utilized metallic organic framework (MOF), which several researchers have reported to be very reactive for the adsorption of toxic gases.229 Despite its high reactivity, it has a major drawback of instability under humid conditions due to the interaction of water molecules with the unsaturated CU-site present on the surface of the HKUST-1 MOF. To overcome this drawback, HKUST-1 was modified with graphene oxide (GO) using hydrothermal methods. The result proved that 200 mg HKUST-1@1.2% GO synthesized hydrothermally performed excellently for the adsorption of SO2 at 120 min, with an adsorption capacity of 72.49 mmol g−1. HKUST-1@1.2% GO proved to be sustainable and stable, with the ability to absorb SO2 over five cycles with only a 0.8% adsorption efficiency decrease observed.
In another study, SO2 was adsorped on intrinsic graphene (IG), Ni-doped graphene (NiG) and Pd-doped graphene (PdG), respectively. It was theoretically studied based on the first principle of density functional theory. It was reported that there was a strong chemisorption between the contact surface with the Eads of SO2 molecules absorbed on NiG and PdG being −4.213 eV and −5.779 eV. the result also proved that the adsorption of SO2 on IG was significantly improved due to the doping with Ni and Pd.230 Interestingly another study by Karami and his colleagues reported the use of Beryllium-Oxide (BeO), Zinc-Oxide (ZnO), and Ni-decorated graphene applying the DFT first-principles study. The results also showed that the SO2 molecules were chemisorbed on Ni-decorated graphene sheets with an adsorption energy of −2.297 eV as compared to the BeO and ZnO sheets which had physical adsorption.231 Luo and his colleagues232 conducted a study on the adsorption of SO2 on graphene (G), N-doped graphene (N-G), Ti-doped graphene (Ti-G), and N–Ti co-doped graphene (N–Ti-G). They used DFT simulation and found that SO2 molecules were adsorbed through physisorption on N-G and chemisorption on Ti-G and N–Ti-G. The study reported that N–Ti-G was the best material for SO2 adsorption with the lowest adsorption energy −2.836 eV and excellent charge transfer 0.735e moved from N–Ti-G to SO2, making it ideal for selecting and removing SO2 (Luo et al., 2022).
The investigation of adsorption and oxidation of SO2 on graphene oxides (GOs) GP, HO-GP, O-GP, and HO-OGP proved to be efficient and provided valuable insights into the mechanism. The study revealed that hydroxyl groups on the surface of GO enhance the adsorption of SO2 through H-bonding interactions and reduce the reaction barrier for its oxidation to SO3 due to its bifunctionality. The material's performance was reported as GP, HO-GP, O-GP, and HO-OGP, respectively.233 Another researcher explored four graphene structures including pristine graphene (PG) vacancy-defected graphene (VG), Ti-doped graphene (Ti-G), and Ti-doped graphene with vacancies (Ti-VG) explored for the adsorption of SO2 using the DFT first-principle calculations. It was reported that PG and vacancy defects formed very weak physical adsorption of SO2. Upon doping with Ti, the adsorption energy and charge density of the adsorption system improved and also promoted chemisorption.234
DFT first principle calculations were utilized to investigate the efficacy of Co-doped (CoG), Ti-doped (IG-Ti), and Co–Ti co-doped (CoG-Ti) graphene on SO2 adsorption.235 CoG-Ti had the optimum performance for SO2 adsorption with its adsorption energy as −4.635 Ev. It was reported that the performance of the doped graphene was better than that of the intrinsic graphene (IG) for SO2 adsorption based on the results of the analysis of the materials' structures and electronic properties at different adsorption sites.
The sorbent material's chemical and physical properties determine the mechanism of CO2 adsorption. GBM has been shown to be able to absorb CO2 through both chemisorption and physisorption.244 GBMs have a large surface area, which provides a large number of CO2 adsorption sites. Physisorption of CO2 is driven by van der Waals interaction, which involves weak bonds between molecules of similar sizes without a net charge and does not require the formation of chemical bonds, the sharing of electrons, or modifications to the chemical structures of interacting molecules.245,246 The physisorption mechanism is driven by weak van der Waals interactions between the graphene surface and the CO2 molecules (Fig. 15).
The efficacy of GBM in capturing CO2 is influenced by various factors such as temperature, pressure, and the presence of other gases.247 Higher temperatures lead to a decrease in van der Waals interactions between CO2 molecules and the graphene surface, resulting in reduced adsorption capacity. This reduction is indicative of an exothermic nature of physisorption. The binding energy for physisorption typically ranges from 20 to 40 kJ mol−1.248 Lower pressures diminish graphene's adsorption ability due to fewer CO2 molecules available for adsorption. Gases like N2, O2, CO, and CH4, which share similar kinetic properties with CO2, can compete for adsorption sites, affecting graphene's selectivity for CO2.249 Additionally, moisture in the gas stream decreases graphene's adsorption capacity by blocking adsorption sites and hindering CO2 facilitation on the adsorbent surface.
The CO2 adsorption performance and surface area of GBMs are compared in Table 3. It is quite instructive to note there is a positive correlation between the specific surface area of the GBMs and adsorption capacities. Furthermore, surface modification involving amine-functionalization, formation of aerogels, doping with MOFs, and activation of GBMs using CO2 and NaOH/KOH have successfully demonstrated the potential to enhance CO2 adsorption of GBMs. Following the works carried out separately by Yun et al. (2016)250 and Xia et al. (2021),251 an amalgamation of both methods that will involve CO2 activation of monolithic RGO aerogel may be worth pursuing for the future advancement of CO2 capture by GBMs. Furthermore, it is noteworthy to mention that most research so far focuses on creating adsorbents with increased adsorption capacity and reduced regeneration energy consumption. However, for engineering applications and real-world applications, research on practical aspects and adsorption techniques is also required, particularly for high CO2 sources, such as flue gas and syngas.
GBMs | Surface area (m2 g−1) | CO2 adsorption capacities (mmol g−1) | Reference |
---|---|---|---|
Graphite nanofibers | 567 | 59.2 mg g−1 | 252 |
Graphene | 443 | 2.16 | 253 |
GO/TiO2 | 99.536 | 1.88 | 254 |
GO/ZnO | 236 | 44.8 cm3 g−1 | 255 |
meta-Phenylenediamine-GO | 44.33 | 0.61, 0.74, and 0.91 for GO-PEHA, GO-TETA, and GO-MPD | 256 |
Triethylenetetramine-GO | 14.40 | ||
Pentaethylenehexamine-GO | 9.39 | ||
EDA-GO cryogels | 167.66 | 1.18 | 257 |
Chitosan-GO cryogels | 33.32 | 0.257 | 258 |
Urea-KOH-GO | 1032 | 2.40 | 259 |
CO2-activated graphene | 2518 | 4.06 | 251 |
NaOH-activated graphene | 843 | 1.74 | |
3D crumpled graphene | 1316 | 2.45 | 260 |
Monolithic rGO aerogel | 1622 | 6.31 | 250 |
GO/MOF-200 | 3359 | 1.34 | 261 |
GO/Cu-MOF | 1015–1820 | 2.50–9.05 | 262 and 263 |
UV-irradiated GO/Cu3(BTC)2 | 1097–1324 | 2.53–5.14 | 264 |
GO/UiO-66 | 1184 | 3.37 | 265 |
RGO/Polymer | 110 | 3.56–3.85 | 266 |
GO/Polyaniline | <5 | 1.31 | 267 |
GO/MgO | 12 | 2.79–3.34 | 268 |
RGO/PMMT | 50.77 | 0.49 | 269 |
Graphene sheets | 484 | 2.894 | 260 |
The other complex factor is the surface functionalization of the materials. The adsorptive property and selectivity of graphene can be improved through functionalization of the surfaces that are usually attained in processes where functional groups are introduced to the graphene. Although this is to the advantage of performance, technically it is difficult to deposit uniform and rigid functionalization, which does not have dramatic implications on properties of interest, e.g., conductivity or surface area. Besides, the use of chemicals which are toxic and production of hazardous by-products that arise during the process of functionalization present some reservations in the minds of the people regarding safety and effect on the environment. On the other hand, adsorbents composed of graphene are prone to be destroyed in high moisture or at areas where chemical activities are taking place. When chemicals are exposed to wet or reactive gases and are allowed to agglomerate on the surface or structural collapse occurs, surface oxidation, surface agglomeration and structural collapse may occur and the resultant effect would require the materials to no longer be effective. This weakness does not make them suitable in the ambient air or industrial gas treatment units where stability is of utmost essence.
Also, there is the selectivity of the gases that makes the application of the graphene nanomaterials more difficult. On one hand, they have a large surface area and tunable chemistry and have been seen to be promising when utilised as a selective adsorbent. It turns out, however, when trying to apply these materials practically, that they are quite bad at the ability to distinguish between similar gas molecules, particularly in high high-complexity mixture. This is a generality that renders them of little value in life circumstances when more than a single pollutant could exist and require remediation with highly detailed action plans.
Finally, long-term application still faces significant challenges when it comes to regeneration and reusability. To ensure the economic viability as well as the operative feasibility of the graphene-based adsorbents, the adsorbents cannot only be deemed to guarantee high single-cycle performance, but they must also be able to exhibit high performance even after a number of adsorption–desorption cycles.
Newly synthesized GBMs meant for industrial use needs to show their effectiveness in different gas–solid contact systems (like fixed, fluidized, moving, or rotating beds) and in particular technological regeneration configurations (like pressure, temperature, electricity, or combined cycles). This evaluation is crucial because it finally establishes the economic viability of a technology for gas extraction. The full potential of GBMs can only be realized by selecting the ideal gas–solid reactor configuration and regeneration mode, with the goal of minimizing operating and capital costs and expediting the commercial deployment of GBM-aided adsorption technology. Indeed, it is clear that the nature of gas–solid contacting system and regeneration technique has a significant impact on the capture performance in terms of gas recovery, purity, and productivity, as well as the energy requirement. Therefore, it is germane that new computational and characterization techniques must be developed, in tandem with experimental research for further development of the most efficient systems. Furthermore, computational techniques may also prove to be an extremely effective means of conducting rapid, extensive screening of novel materials and forecasting their properties. This advanced tool may also shed light on the dynamic conditions for the most promising GBMs for more real-world multi-component mixtures.
Different adsorption-based gas separation techniques using GBMs, reactor configurations, and regeneration modes have all been demonstrated at various scales. However, adequate techno-economic and life cycle assessment (LCA) studies are still missing, which would give a clear estimate of the cost of adapting GBMs in current plants, as well as the real energy costs brought on by this capture technology. Therefore, before GBM-based gas capture processes are implemented in actual plants, all the aforementioned factors and key points need to be comprehensively addressed.
The following are some performance metrics and potential research directions in gas capture with GBMs:
• Simplifying GBM synthesis will lower production costs, expedite preparation, and make it easier to analyze parameters influencing adsorbent properties. Investigate current synthesis techniques to find ideal circumstances, GBM-specific factors, and novel material architectures for improved gas absorption. Improve innovative synthesis techniques that make use of inexpensive chemicals and raw materials to drastically reduce manufacturing costs (e.g., waste biomass, industrial wastes).
• GBMs with high mesoporosity, microporosity, and specific surface area are prioritized to enhance gas adsorption capacity and kinetics. There is a need to select the most appropriate GBM for a certain industrial application while taking the synthesis method, material costs, manufacturing procedure, life cycle assessment, and modification techniques into account. It is necessary to increase GBMs' robustness in dealing with moisture. Hence, research on how contaminants and water vapor affect gas absorption is crucial for maximizing removal effectiveness.
• Creation of general protocols for gas capture that take into account textural features, performance standards, application types, and appropriate process condition ranges (temperature, pressure, gas concentration, desired gas purity). Techno-economic analysis should be utilized to analyze promising GBMs for industrial use, providing details on costs associated with stability, scalability, and technological variants, as well as GBM-specific parameters.
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