OLC, a member of the F family, is a unique carbon structure consisting of quasi-spherical- and polyhedral-shaped graphitic layers close to one another. It stands out from other carbon representatives like graphite, fullerenes (F), and nanotubes [2]. OLCs possess 3 to 8 closed graphitic shell structures with hollow cores of 20–100 nm outer diameters. Various methods have been developed for synthesizing OLCs, including arc discharge, high-electron irradiation, chemical vapor deposition, radio frequency plasma, and thermal annealing of diamond nanoparticles. However, research on OLCs remains limited due to challenges such as uncontrollable reactions, byproduct formation, complex equipment, and high costs. Currently, most OLCs are synthesized using vacuum annealing of NDs particles [13]. The transformation between the NDs and the OLCs was a reversal process that required a significant amount of energy [62]. One example of OLCs preparation from LCMs is the carbonization of Japanese cedar at 700°C under an argon atmosphere for 30 min, followed by natural cooling [63]. Porous carbon nano-onions (CNOs) can be synthesized from rice husks through a facile nickel-assisted graphitization process followed by activation. These CNOs exhibit exceptional electrochemical performance and good cycling stability [64].

NDs are spherical particles with a diamond-like structure, typically 5 nm in diameter. They consist of a diamond core (1–10 nm) composed of sp³-hybridized carbon atoms, surrounded by a carbon cover containing sp²-hybridized carbon atoms. This unique structure allows for flexibility, enabling the NDs to adopt different geometrical forms (sp³ state protected by a carbon cover containing carbon atoms in the sp² state) [63]. The sp²/sp³ bonds in NDs are quite flexible, allowing the ability to assume two geometrical forms, i.e., the stretched face can behave as a G plane, and the puckered G may become a surface [8]. NDs are particularly promising due to their high surface area, ease of functionalization, and doping capabilities. Their optical properties are attributed to the sp³ hybridization of carbon atoms and nitrogen vacancy defects in the core, while their mechanical properties are associated with sp² hybridization [65]. Two primary methods for synthesizing NDs include high-temperature, high-pressure transformation of graphite and detonation of carbon-based explosives [8].

Seed growth involves the chemical synthesis of an organic seed molecule containing one or more diamond lattice units. By incorporating dopant atoms into this seed molecule, specific color centers can be created. A reactive carbon source, derived from a hydrocarbon that decomposes at a lower temperature than the diamond seed, is then introduced. The subsequent growth of diamond around the seed molecule enables precise control over the placement of desired color centers, ensuring at least one fluorescent emitter per ND, regardless of size (Fig. 6a) [66,67].

Conventional methods of ND growth from organic precursors involve a thermal decomposition process, followed by spontaneous nucleation (i.e., high pressure high temperature method). This approach requires high concentrations of reactive carbon species to initiate nucleation and subsequent rapid growth, often resulting in lower-quality ND. In contrast, seeded growth allows for a more controlled process by maintaining lower concentrations of reactive carbon species. This enables slower, more precise growth, leading to higher-quality diamonds with enhanced crystal perfection and chemical purity (Fig. 6b) [67].

Fullerenes (F) are spherical, look like a soccer ball (a buckyball), and are caged molecules with pentagons and hexagons at the corner of a polyhedral structure [4]. The term “fullerene” refers to domes of buildings. The smallest fullerene member is C20 [38]. Most F (e.g., C60) are spheroid in shape, although oblong shapes like a rugby ball also exist (e.g., C70) [8]. F are stable (except small F) but not unreactive [38]. The F molecule requires that the C-C bonds interact through bent sp² hybridized carbon atoms, leading to a strained structure with good reactivity, acting as an electron acceptor. C70 can be seen as a C60 molecule with a belt of five hexagons around the equatorial plane and exhibits a more oval shape. The main properties of C60 are Young’s modulus ≈of 14 GPa, electrical resistivity ≈of 1014 Ω m, thermal conductivity ≈of 0.4 W/mK, and band gap of 1.7 eV. The other fullerene types show similar properties to C60 [68]. C60 and C70 could be synthesized by pyrolysis of naphthalene at 1000°C. C60 can also be synthesized from the reduction of CO₂ via metallic lithium or MgCO₃ at 700°C [10].

The primary growth mechanism for carbon molecules involves reactions with intermediate-sized rings. Planar polycyclic and monocyclic ring compounds they observe react much faster than the fullerene isomers. Responses between the planar ring types create new polycyclic compounds, which can grow further through ring coalescence or anneal to give a F or monocyclic ring. A proposed mechanism for fullerene formation involves a two-step process. Initially, a Bergman cyclization of an enediyne occurs, followed by a “zipping up” of the resulting spiraling polyyne chain, leading to the coalescence of the structure into a fullerene cage (Fig. 7). Monocyclic rings, once formed, can further grow through a process known as coalescence, in which they combine with other planar ring structures. F, on the other hand, typically grows through the addition of smaller carbon-based particles [69].

Carbon black (CB) is one of the spherical carbons (CS) [7,8]. CS can be synthesized with carbon flakes arranged parallel to the central carbon core [69]. The specific arrangement of these flakes significantly impacts the chemical and physical properties of the resulting CSs. The sp² carbon at the edges of these flakes can react with other atoms, such as H and O, to form OH and COOH groups, thereby fulfilling their valence requirements [7]. CB is produced mainly by hydrocarbons’ partial combustion and thermal decomposition of LCMs. Various synthetic methods can be employed, including arc discharge, laser ablation and plasma processes, shock compression techniques, chemical vapor deposition, autoclave processes, and carbonization routes [7]. During CB growth, a carbon source is converted into C, H, and O radicals. The radicals subsequently react to form the CB. Three potential pathways for carbon particle formation have been proposed: polyacetylenes, polyaromatic hydrocarbons, and the formation of carbon vapor [38]. In one study, CB was synthesized by carbonizing the ground-frozen hydrolysis lignin in a horizontal tube furnace ranging from 600°C to 900°C for 6 h under N [70].

CQDs are less than 10 nm in size. They can be synthesized from diverse organic precursors such as natural polymers, amino acids, apple juice, grape peel, and vegetables. Several straightforward methods have been developed for CQD synthesis, including laser ablation, electrochemical oxidation, combustion/thermal microwave heating, chemical oxidation, hydrothermal carbonization, and pyrolysis [71–73].

The proposed methods to prepare CQDs can be classified into “Top-down” by breaking down larger carbon materials into smaller CQDs and “Bottom-up” by building CQDs from smaller molecular precursors. Several challenges exist in CQD synthesis. One major challenge is aggregation, where CQD particles tend to clump together. Electrochemical synthesis is one method to mitigate this issue. Another challenge is controlling the size and uniformity of CQDs. Post-treatment processes can help address this. Additionally, optimizing surface properties for specific applications, such as solubility and functionalization, is crucial and can be achieved through post-treatment techniques. LCMs, like those from the paper (WP), can serve as a sustainable source for CQDs synthesis [74]. Table 3 demonstrates CQDs’ preparation methods, properties, and applications prepared from lignocellulosic materials [39].

CQDs with diverse properties, including crystallinity, and surface properties can be derived from various biomass waste sources such as sugarcane bagasse, garlic peels, and taro peels, using ultrasonic-assisted oxidation of carbonized biomass. CQDs are widely utilized due to their photoluminescence combined with biocompatibility for biomedical applications. The high fraction of α-cellulose is necessary for a high graphitization degree and outstanding CQDs properties [75]. Hydrothermal carbonization of pine wood produced CQDs with excellent fluorescence characteristics, which selectively detected Fe(III) in an aqueous phase [76].

Green hydrothermal techniques have been employed to produce CQDs from corn stalk shells and corncob residues were developed. These CQDs exhibit excellent fluorescence properties, making them promising candidates for applications in detection and bioimaging. Specifically, CQDs derived from corncob residues have shown potential for the detection of Fe(III) ions [77,78].

Aloe peel-derived CQDs were prepared by hydrothermal treatment as accelerants to increase cumulative methane production and total chemical oxygen demand removal efficiency [79]. CQDs were derived from waste acorn cups by a hydrothermal carbonization process and applied as an attractive solution to functionalize PVA material [80].

Lignin-based CQDs have emerged as promising fluorescent nanomaterials due to their excellent luminescent performance, long-term stability, and water solubility. These CQDs can be synthesized from natural lignin via hydrothermal treatment. CQDs efficiently serve as fluorescence-switchable nanoprobes for sensitively detecting common metal ions and for real-time and visual self-detection of formaldehyde gas [81,82]. The prepared CQDs doped with N and Mg elements onto their framework show strong turquoise fluorescence [82].

Nitrogen and phosphorus co-doped CQDs (N, P-CQDs) have been synthesized through a simple one-pot hydrothermal method using cellulose pulp. These N, P-CQDs have demonstrated potential applications in metal ion detection, pH sensing, and cell imaging [83].

Fluorescent CQDs were synthesized through a straightforward one-step microwave heating process involving urea and various biomass sources, including bagasse, cellulose, or carboxymethyl cellulose. These CQDs have found application in the adsorption of Pb(II) ions from aqueous solutions [84].

Graphene Quantum Dots (GQDs) have garnered significant attention due to their exceptional properties, including high surface area, sustainable bright fluorescence, long-term photostability, excellent electrochemical properties, biocompatibility, high chemical stability, high water solubility, and unique drug delivery capacity. These properties make GQDs highly desirable for various applications such as bioimaging, biosensors, photocatalysis, solar cells, light-emitting diodes, optoelectronics, and chemical sensing [85]. GQDs can be synthesized from dispersed lignin in nitric acid solution through an ultrasonication process, followed by hydrothermal treatment in an autoclave at 180°C for 12 h [86]. GQDs were fabricated from Miscanthus (silver grass) biorefinery waste via fractionation, followed by hydrothermal carbonization. The as-fabricated GQDs exhibit a linear fluorescent response towards trace amounts of Fe(III) in real-environment water [87]. GQDs prepared from bagasse were used in composites with activated carbon and embedded with titanium dioxide to enhance activated carbon’s adsorption and photocatalytic efficiency in removing methylene blue dye pollutants [9,84].

The G sheet can be transformed into a cone shape by removing and resealing a wedge. Nanocones can be produced through various techniques, including CO₂ laser ablation of graphite at room temperature and plasma-enhanced chemical vapor deposition using a mixture of Ar + H₂ + CH₄. Due to their high-temperature stability, nanocones are promising candidates for scanning probe applications in harsh environments. They also find use in nanocage applications, such as gas storage and drug delivery [7]. Nanocones form through a unique process involving the growth of a G-sheet on a nickel catalyst anchored to a substrate. This G-sheet then develops into a nearly cylindrical nanostructure with equal base and top radii. As the lateral surface area increases, carbon atoms attach to the edges of the hydrogen-terminated G-sheet, causing the nanocone to grow. The height of the nanocone increases as a new layer forms on the catalyzed surface. The nanocone widens due to the attachment of carbon atoms to the edges of parallel carbon platelets [88,89].

CNFs are 1-D filaments composed of stacked, curved G layers. They exhibit a conical nanostructures with diameter ranged from nanometers to hundreds of nanometers and lengths spanning from sub-micrometer to millimeter scales. The morphology of CNFs varies depending on the angle between the G layers and the fiber axis. This can result in different types, such as plate-like, ribbon-like, or herringbone CNFs [10].

CNFs can be synthesized through two primary methods. The first method, the seeded catalyst method, involves depositing catalyst particles onto a substrate within a reactor. The second method, the floating catalyst method, utilizes evaporation techniques to deposit catalyst particles onto a substrate (Fig. 8) [10].

Microwave pyrolysis of LCMs palm kernel shells at 500°C and 600°C resulted in the formation of hotspots, which acted as nucleation sites for the growth of hollow CNFs. Additionally, bamboo-shaped CNFs were formed due to secondary pyrolysis or a lower temperature at the outer regions compared to the core of the active site [90].

Fractionated sugarcane bagasse lignin, characterized by high molecular weight, narrow polydispersity index, and a linear structure, was obtained through ethanol/water solution fractionation. Electrospinning of this lignin with polyacrylonitrile, followed by thermostabilization and carbonization, yielded high-quality lignin-based CNFs suitable for supercapacitor applications. These CNFs exhibited a large specific surface area, independent filamentous morphology networks, and excellent electrochemical performance [91].

CNT are 1-D rolled G. They can be single-walled (SWCNT) and multi-walled (MWCNT) based on the number of G layers [92]. Chemical bonding involves an entirely sp²-hybrid state with outstanding properties [38]. The diameter varies from 0.4 to 2.5 nm and a few nanometers to 100 nm for SWCNTs and MWCNTs, respectively. Each layer in MWCNT interacts through Vander Waals forces [8,38]. CNTs exhibit remarkable properties, including tensile strength of ≈37 GPa, strain to failure of ≈6%, Young’s modulus of ≈0.62–1.25 TPa, electrical resistivity of ≈1 μΩ cm, thermal conductivity ≈3000 W/mK and density ≈1.33–1.4 g/cm³ (which is half of the density of aluminum, making them very attractive for lightweight applications [22].

There are two primary mechanisms for the growth of SWCNTs. The first mechanism, known as the tip-growth model (Fig. 9a), occurs when the interaction between the catalyst and the substrate is weak. In this process, hydrocarbon decomposition takes place on the top surface of the metal catalyst. The carbon atoms then diffuse through the metal and precipitate at the bottom, pushing the entire metal particle away from the substrate. As the metal particle is lifted, its top surface becomes exposed to new hydrocarbon molecules, allowing for further carbon diffusion and CNT growth. This process continues until the metal particle becomes saturated with carbon, halting the growth of the CNT [93].

The second mechanism for SWCNT growth is the base-growth model (Fig. 9b). In this model, a strong interaction exists between the catalyst and the substrate. Similar to the tip-growth model, hydrocarbon decomposition and carbon diffusion occur initially. However, the CNT precipitation fails to displace the metal particle, leading to the emergence of the CNT from the metal’s apex. Initially, carbon crystallizes as a hemispherical dome, which then extends into a seamless graphitic cylinder. Subsequent hydrocarbon decomposition occurs on the lower peripheral surface of the metal, and the dissolved carbon diffuses upward, resulting in the growth of the CNT with the catalyst particle remaining rooted at its base. For MWCNT growth from acetylene decomposition on Ni particles at 480°C, the Ni cluster had a round shape, which transformed into an elongated shape surrounded by a thin carbon layer. The Ni cluster left the substrate contracted upward, taking a round shape and leaving a hollow CNTs [93,94].

CNTs derived from LCMs possess a diverse array of functional groups, minerals, and a large specific surface area, making them effective adsorbents. Additionally, they can be incorporated as fillers in polymer composites to enhance the polymers’ toughness, stiffness, and electrical conductivity [95].

CNTs were synthesized from wood sawdust through a process involving the mixing of sawdust, Fe (catalyst), zinc (reducing agent), calcite (bed material), and clay. This mixture was arranged in a stainless steel column reactor with perforated plates at both ends. The reactor was then heated to 750°C for 3 h in the absence of air. To prevent the release of CO₂ and CO, KOH was placed at the top of the column, converting these gases into potassium carbonate salt. The CNTs grew in the lower part of the column where the catalysts were located. This process can be summarized as a combination of wood pyrolysis and carbon vapor deposition on the bed material and reactor walls [96].

CNTs were synthesized through a two-step carbonization process involving α-cellulose. Initially, the α-cellulose was carbonized in air at 240°C for 8 h. Subsequently, the temperature was increased to 400°C, and the carbonization process continued for another 8 h at ambient pressure. The resulting carbon samples were then subjected to a purification process. This involved washing the samples with a 15% HCl solution using sonic pulsation, followed by rinsing with deionized water and centrifugation. Finally, the samples were dried at 110°C for 12 h [97]. In another study, CNTs were prepared from sugarcane bagasse, black liquor, and mature beech pinewood sawdust wastes by hydrothermal treatment of raw agricultural waste, followed by hydrolysis of hydrochar product. Multiwalled carbon nanotubes were attained and used efficiency for Ni(II) adsorption [92]. CNTs were prepared from lignin, using iron powders as a catalyst, after thermal treatment at 1000°C for 105 min. The microwave-enhanced pyrolysis method was applied to treat gumwood at 500°C to produce CNTs that are shaped on the surface of biochar [85]. Also, the production of CNTs in lignocellulose materials was achieved through the ablation of cellulose microfibrils within the lignin matrix of the intact secondary plant cell walls during low-temperature carbonization [98].

G is one layer of sp² carbon atoms arranged in a honeycomb lattice and is a separate graphite plane [68]. The C–C bond length is about 0.142 nm. Each carbon atom forms four bonds; s, p_x, and p_y orbitals constitute the σ-bond while p_z electron makes the π-bond [48]. G is the mother of all graphitic forms like graphite, carbon nanotubes, carbon nanofibers, and F [4,5,11]. G can be stacked up to form a 3D graphite crystal, rolled up along a given direction to create a SWCNTs or a MWCNT, depending on the number of G layers, or wrapped up into C60 buckyball, creating F [4,66]. G with a few layers is often referred to as few-layer graphene (FLG), while G with a slightly larger number of layers is classified as ultrathin graphite. Graphene oxide (GO) is a form of G that contains oxygen-containing functional groups, such as hydroxyl, epoxy, and carboxyl groups. Reduced graphene oxide (rGO) is obtained by partially removing these oxygen-containing groups from GO. Graphene nanoplatelets (GNPs) are G flakes with a lateral size in the micrometer range and a thickness of a few atomic layers [99].

G and rGO are easily obtained through the reduction of GO. Besides, G can also be functionalized into its oxidized form (i.e., GO) through the Hummers’ method, which shows a high density of oxygen functional groups [100,101]. This GO can be synthesized from simple and low-cost methods such as chemical oxidation of graphite to GO followed by exfoliation in ultra-sonication [100]. Due to its hydrophilic nature, high specific surface area, and high functional group density, it can be used as an adsorbent and a catalyst for removing organic and inorganic pollutants [102]. The GO’s surface is decorated with oxygen-containing functional groups, including hydroxyl and epoxy groups on sp³ hybridized on the basal carbon plane [3].

Unlike pristine G, GO possesses carbonyl and carboxyl groups attached to the edges of its sp² hybridized carbon-structure. This allows GO to disperse well in polar organic solvents through sonication, forming stable dispersions of single-layer GO sheets. The main advantage of GO over pristine G is its improved dispersibility in various solvents, including organic solvents, water, and inorganic solvents [3,103].

A catalytic graphitization process was employed to fabricate G using lignin as the carbon source in the presence of Fe(III) as the catalyst. The process was conducted at 1000°C using different carrier gases. It was observed that methane and natural gas, as carrier gases, accelerated the formation of multilayer G with a range of 2–30 layers [85]. High-quality G sheets were prepared by initially converting dried monocotyledonous and dicotyledonous materials into biochar through a pyrolysis process at 350°C for 1 h. The biochar was then acidified at room temperature for 14 days. Following acid pretreatment, the biochar was dried at 105°C and subsequently heated at temperatures ranged between 500°C–1500°C under vacuum conditions [104]. G sheet-like porous activated carbons were prepared by mixing a fine powder of Bougainvillea spectabilis flowers with 10% ZnCl₂, stirring at 60°C under an N₂ atmosphere for 24 h. This was followed by carbonization in a tubular furnace at different temperatures for 3 h in the N₂ atmosphere. Finally, the carbonized powder was washed with 1.0 M HCl and hot distilled water until neutral and dried [105].

The synthesis of GO from Indonesian lignocelluloses (coconut shell, rice husk, bagasse) was established through a modified Hummers method employing the KMnO₄ as an oxidant and concentrated H₂SO₄ to exfoliate several layers from the graphite flakes. The hydrothermal pyrolysis of agave fiber was successfully used to synthesize carbon fibers and subsequently potentiate the production of graphite sheets and GO [106]. Also, GO was prepared from different agricultural wastes such as sugarcane bagasse, rice straw, Mature pinewood sawdust, and lignin by separately oxidizing with ferrocene at 300°C in muffled for 10 min under atmospheric conditions [3,5].

G can be synthesized through thermal processes, where carbon radicals from decomposed precursors nucleate and grow into G structures (Fig. 10a); stripping methods, which involve physically exfoliating graphene layers from bulk graphite (Fig. 10b); and chemical vapor deposition (CVD), where carbon atoms from a gas phase adsorb onto a substrate and form G nuclei that coalesce into a continuous film (Fig. 10c) [107]. Table 4 provides a comprehensive overview of various methods and conditions employed for the conversion of different LCMs into G and CNMs.

CNWs, consisting of vertically aligned G sheets forming a 2-D wall structure, possess a large surface area and sharp edges. Their thickness ranges from a few nanometers to a few tens of nanometers. Various synthesis methods have been explored for CNWs, including microwave plasma-enhanced CVD, radio-frequency plasma-enhanced CVD, hot-wire CVD, and electron beam-excited plasma CVD [10]. CNWs can grow both without and with the presence of O₂ gas. Without O₂ gas, carbon nanoislands nucleate on the Si surface at a lower density compared to the oxygen-free case. This is attributed to the cleaning and etching effect of oxygen on the silicon surface, which suppresses the nucleation of amorphous carbon nanoflakes. With O₂ gas, carbon nanoislands were nucleated on the Si surface with lower density than the densities of nanoislands in the case without O₂. This is because of the O₂, which cleans the surface of the Si substrate and etches the amorphous carbon. So, carbon nanoflake nucleation was suppressed to some degree. Isolated carbon nanoislands still exist, and the CNWs grow on them. Each CNW grows without an interface layer. We can say that the nucleation will be controlled by varying the O radical injection [108].

Graphite is the most stable allotrope of carbon. It is composed of stacked parallel G layers with sp² hybridization [34,104]. One carbon atom covalently bonded to three other carbon atoms with a short length of 0.141 nm, forming a hexagonal lattice. The hybridized fourth valence electron is paired with another delocalized electron of the adjacent layer by Vander Waals bonds, giving electric conductive properties to graphite [37]. Methane is first decomposed at high temperatures for the synthesis of G from methane, and the decomposed carbon atoms are then integrated into the Ni substrate. After cooling, the carbon atoms precipitate from the substrate and form G on both sides of the Ni substrate. A new G layer is formed between the G and the Ni substrate. G layers gradually increase, creating the graphite-like film [109].

Porous graphitic carbons were produced from various lignocellulosic biomass sources such as softwood sawdust, bamboo, seed husks, and nut shells. Lignocellulosic biomass is milled, sieved to produce fine powders, and converted to porous graphitic carbons by iron-catalyzed graphitization [110]. Palm kernel shell waste is utilized to produce graphite via the direct impregnation of a catalyst into raw material, followed by a thermal treatment [111].

Diamond is a carbon allotrope in which the carbon atoms are arranged in a face-centered cubic crystal structure. Atoms are bonded covalently with stable 3-D structures [38]. Diamond thin films have optical, electrical, mechanical, and thermal properties, which make these attractive for applications in different fields [112].

The initial stage of diamond growth involves anisotropic etching, which leads to the formation of graphite islands. Disordered and defective carbon regions around the microcrystalline graphite are etched off by H, O, and OH radicals and ions. The created graphite aggregates on the silicon oxide surface, forming various carbon clusters. Some of these clusters then convert into precursors for diamond nucleation, enabling the growth of diamond particles on the carbide intermediate layer [112].

The diamond-like carbon nanofoam (DCNs) was prepared from sucrose by heating sucrose solution with naphthalene at 130°C in a 130 mL stainless steel autoclave for 72 h. After filtering the product with hot water and drying, DCNs was obtained. A control experiment without naphthalene did not yield DCNs, indicating that naphthalene acts as a nucleation seed, initiating the growth of DCNs. These experimental results suggest that these intermediates may lead to DCNs formation [113].