Preparation of different carbon materials by thermochemical conversion of lignin
- Departamento de Ingeniería Química, Andalucía Tech, Universidad de Málaga, Málaga, Spain
Lignin valorization plays a crucial role within the modern biorefinery scheme from both the economic and environmental points of view; and the structure and composition of lignin makes it an ideal precursor for the preparation of advanced carbon materials with high added-value. This review provides an overview of the different carbonaceous materials obtained by thermochemical conversion of lignin, such as activated carbons, carbon fibers, templated carbons, and high ordered carbons, giving information about the new strategies in terms of the preparation method and their possible applications.
Lignin is one of the three basic components of wood and other lignocellulosics. Lignin is primarily a structural material to add strength and rigidity to cell walls and constitutes between 15 and 40 wt% of the dry matter of woody plants. Lignin may be considered to be a random three-dimensional polymer of phenylpropane units linked together in different ways (Figure 1).
Figure 1. Structure of lignin, composed by phenylpropane units, Adler (1997).
Nowadays, lignin represents 30% of all non-fossil organic carbon on Earth. Its availability exceeds 300 billion tons (Smolarski, 2012), increasing annually by around 20 billion tons. The worldwide production of lignin is between 40 and 50 million tons per annum (The International Lignin Institute, ILI). Besides, most of the produced lignin is consumed as a fuel in the pulp–paper industry to recover energy and chemical reactant, and only the 2% is actually being commercialized.
There are different lignin sources depending on the biomass process, such as pulp and paper industries (i.e., Kraft or lignosulfonate) or new feedstocks specific to the biorefinery scheme (i.e., Organosolv). The most yielded lignin type is the so-called Kraft lignin, which comes from the Kraft pulping process. This is the main traditional method for pulping and hence, it produces the largest volume of lignin (Smook, 2002).
Other important types of lignin are derived from the organosolv process, which is a pulping technique that uses an organic solvent to solubilize lignin and hemicelluloses. In this case, the Alcell® process is the most well-known process in the organosolv-lignin category. In contrast to Kraft lignin, Alcell® lignin contains very small amount of inorganic compounds because of the different pulping process used (Kubo and Kadla, 2004). Interestingly, the Alcell® pulping process exhibits higher pulp yields than the Kraft process and it is also more environmentally friendly (Yawalata and Paszner, 2004). The recovery of solvents by evaporation is easy and it allows obtaining a very pure lignin that can be used as a raw material.
In recent years, isolation of different forms of modified lignin from pulping black liquors and the development of further applications for them has gained a great interest because of the biorefinery process. In this context, lignin will be used as raw material for the preparation of chemicals and carbons materials. The integration of lignin in multi-component materials have been encouraged over the last 10 years by their wide accessibility, low price, and performances, such as low density, high hardness, good thermal properties, chemical, friction, and humidity resistance (Laurichesse and Avèrous, 2014).
The current commercial uses of lignin, except combustion and production of synthetic vanillin and dimethylsulfoxide (DMSO), make use of lignin’s polymer and polyelectrolyte properties. Its use as dispersant, emulsifier, binder, and sequestrant supposes nearly three-quarters of the commercial lignin products. Other, minor applications include adhesives and fillers. Generally, lignin is used in these applications with little or no modification other than sulfonation or thio hydroxymethylation. These uses mainly represent relatively low value and limited volume growth applications.
Furthermore, large amounts of lignin could be generated in future wood-to-ethanol bio-refineries. Therefore, the development of value-added lignin-based products will be crucial to the economic success of the bio-ethanol production by this process.
In this sense, another potential way of lignin valorization is by thermochemical conversion in order to obtain carbon materials with high value added. During thermochemical conversions, a significant devolatilation may occur, with the loss of most of the oxygen functional groups. The reorganization of the structure, mainly by condensation of the aromatic rings, produces carbon materials.
This review is mainly focused on the preparation of advanced carbon materials by thermochemical processes of lignin. Figure 2 shows a scheme of the potential thermochemical conversion routes for lignin, which will be analyzed in this review. As can be seen by thermochemical processes from lignin, it can be prepared by activated carbons (ACs), carbon molecular sieves, high-ordered carbons, catalysts and catalyst supports, carbon fibers (CFs), and tubes and nanostructured carbon materials, also called templated carbons.
As lignin has a high carbon content and a molecular structure similar to bituminous coal, it ought to be an ideal precursor for ACs (Suhas et al., 2007). ACs usually have a well-developed porous structure with a large internal surface area ranging from 500 to 2000 m2/g, high thermal and chemical stability in both highly acidic and alkaline media and, in addition, the chemistry of the carbon surface can be easily modulated. Furthermore, they can be obtained from many diverse materials including different types of lignocellulosic waste (Rodríguez-Mirasol et al., 2005; Ioannidou and Zabaniotou, 2007; Rosas et al., 2009, 2010). All these properties make them very suitable materials as adsorbent and catalyst supports (Radovic and Rodríguez-Reinoso, 1997).
This section of the review tries to compile the main works related to ACs from lignin, analyzing the preparation methods, the properties of the resultant ACs, and the different applications of these materials, such as adsorbents, catalyst supports, or catalysts by themselves (when the authors provided this information). Table 1 provides information related to the type of activation, activation agent, kind of lignin, and the application evaluated in each case. For the sake of clarity, this section is structured as a function of the type of activation method.
Table 1. Experimental conditions, type of lignin, and application of activated carbons prepared from lignin (physical activation) and (chemical activation).
Physical activation is a two-step process that consists of the early formation of a char by pyrolysis (carbonization) of the precursor; and an activation step, where the char is partially gasified by different gases, such as CO2 or steam, producing a well-developed (micro)porous structure.
The effect of carbonization temperature on the porosity development of chars was first analyzed by Rodríguez-Mirasol et al. (1993a,b) using Eucalyptus Kraft lignin. They reported a maximum specific surface area (ABET) value of 496 m2/g at 550°C, decreasing to 278 m2/g at 900°C. They associated this trend to the micropores constriction upon increasingly severe thermal treatment, reducing the accessibility of the N2 molecules in their experimental conditions. However, Xie et al. (2009) reported with organosolv-lignin powder, an increasing tendency in ABET with temperature, reaching values of 449 m2/g at 1000°C. In this case, the heating rate was 2.5°C/min, in contrast with that used by Rodriguez-Mirasol et al., 10°C/min. In this sense, Kijima et al. (2011) analyzed the effect of the heating rate on an alkaline lignin carbonized at 900°C, and they observed that the lower the heating rate, the higher the ABET. They obtained a char at 1°C/min, with 530 m2/g, which was increased to 740 m2/g after washing with water.
Although in the scheme shown in Figure 2, it appears as a separate block, to our best knowledge, only Rodríguez-Mirasol et al. (1996) made high temperature treatments to powder lignin with the goal of obtaining high-ordered carbons, so the preparation of this kind of materials is not going to be considered as a separate part within the review.
In that case, these ordered carbons were obtained from Kraft lignin, under Ar flow, at temperatures in the range between 2400 and 2800°C. The structural order of the carbons was progressively increasing with the temperature, as revealed by XRD and Raman spectroscopy analyses, at the same way than their oxidation resistance. The inorganic impurities of the precursor (mainly Na) seemed to enhance the onset of structural ordering, and the oxidation resistance of the 2800°C carbon prepared from high-ash lignin proved to be similar to that of graphite SP-1.
The most used activating gas during the activation step is CO2. Rodríguez-Mirasol et al. (1993a,b) obtained an AC with 1853 m2/g and a micropore volume (Vmic) of 0.57 cm3/g, at 850°C, for 20 h, in CO2. This high activation time provided information about the low reactivity of lignin chars, owing to its highly cross-linked nature, later confirmed by Sharma et al. (2004).
More recently, Baklanova et al. (2003) analyzed the influence of the carbonization temperature with hydrolytic lignin. They optimized the experimental conditions to prepare microporous ACs, and they observed that carbonization temperatures of 600–700°C could be used for producing microporous char materials with a minimum average size of micropores. In addition, they obtained ACs with 865 m2/g and Vmic of 0.37 cm3/g, with an average width of 0.60–0.66 nm, by steam activation of the carbonized samples produced.
Carrott et al. (2008) analyzed the physical activation in CO2 or steam of kraft and hydrolytic lignins. They observed that lignins obtained from different sources behave differently during pyrolysis and also during activation in CO2 or steam, leading to the formation of ACs with different textural properties, better in the case of hydrolytic lignin. The most porous materials had ABET between 1400 and 1600 m2/g with Vmic between 0.5 and 0.6 cm3/g and between 1.2 and 1.4 nm.
More recently, Fu et al. (2013) prepared ACs directly from black liquor lignin by physical activation with steam, with a maximum ABET of 310 m2/g. at 725°C for 40 min. Higher activation times and temperatures significantly reduced the specific surface area. These ACs were tested as adsorbents for methylene blue (MB).
On the other hand, it is important to mention the works of our research group in this field. Based on the earlier studies of Rodríguez-Mirasol et al. (1993a,b), our research group has continued searching applications for the ACs obtained from Eucalyptus kraft lignin by physical activation with CO2. Specifically, the viability of these ACs to be used as adsorbents in liquid phase has been analyzed by developing adsorbent materials with different properties, in order to achieve selective applications, depending on the molecules to be separated. In this sense, ACs with very different porous structure, with ABET ranging from approximately 700 to 1900 m2/g have been tested. The suitability of these ACs has been analyzed for the removal of aromatic compounds (benzene, methyl ethyl ketone, methanol, nitrobenzene, aniline, p-nitroaniline, toluene, and p-nitrotoluene), surfactants (sodium dodecylbenzene sulfonate), dyes (Congo Red, crystal violet, fuchsine and malachite green), and intermediates or final products in petrochemical, pharmaceutical and food industries (paracetamol, salicylic acid and benzoic acid) (Rodríguez-Mirasol et al., 2005; Cotoruelo et al., 2007b, 2009, 2010, 2011a,b, 2012a,b). These ACs were successfully employed as adsorbents for the removal of these components, analyzing the influence of pH, temperature, and contact time and making a deep study of the thermodynamic and kinetic of the adsorption process. In this context, Bedia et al. (2007), based on the high amount of Na observed in kraft lignin, used these ACs for desiccant applications. To our best knowledge, there is no information about the use of ACs, obtained by physical activation from lignin, as catalyst supports or catalysts by themselves.
ZnCl2 as activation agent
Gonzalez-Serrano et al. (1997) were pioneers to prepare ACs from lignin precipitated from kraft black liquors by using chemical activation, in this case, with ZnCl2. The authors reported ACs with ABET higher than 1800 m2/g. They observed that activation temperatures up to 500°C and high impregnation ratios (R = mass activation agent/mass lignin), up to 2.3, leads to well-developed porosity with a widening of microporosity and an increasing contribution of mesoporosity, recommended for liquid-phase applications.
Later, Hayashi et al. (2000), also with Kraft lignin, found that the maximum ABET were obtained at the activation temperature of 600°C, with R = 1. On the other hand, Maldhure and Ekhe (2011) compared the use of a microwave technique to conventional impregnation method, using Kraft lignin, at R = 1.5 and 600°C. They obtained an overall beneficial effect in terms of porous structure, relatively greater surface area, reduction of time, and energy toward effectiveness of impregnation, with microwave method. Furthermore, the ACs prepared by microwave treatment showed higher capacity for Cu(II) adsorption compared to ACs prepared by the simple method.
Alkali metal compounds as activation agent
Hayashi et al. (2000) also tested for the activation of lignin, different alkali metal compounds, such as NaOH, KOH, Na2CO3, and K2CO3, with R = 1. In that case, the optimum carbonization temperature was 800°C, obtaining ABET higher than 1000 m2/g, except for Na2CO3. In particular, the carbon prepared by K2CO3 activation has a ABET of 2000 m2/g.
Khezami et al. (2005) compared the activation with KOH of different wood components (cellulose, lignin, and xylan) and they obtained an AC from lignin of 514 m2/g, at 700°C and R = 0.25. They also tested the adsorption capacity of the ACs prepared for MB and phenol. On the other hand, Babel and Jurewicz (2008) prepared nanostructured carbons by KOH activation of lignin (from black liquid of pine wood pulping process) at 950°C and R = 4. The AC showed an ABET of 1946 m2/g, with a considerable number of supermicropores and small mesopores (ca., 50%). This AC obtained an efficient hydrogen electrosorption of 510 mA h/g (1.89 wt% in meaning of energy storage) and favorable discharge characteristics at current densities up to 1 A/g.
Torné-Fernández et al. (2009) synthesized highly microporous carbon materials with high ABET (up to 2400 m2/g) from Kraft lignin by activation with NaOH. The optimal conditions were 755°C and approximately R = 5. This AC was tested for MB adsorption with successful results.
Due to K2CO3 salts had shown high transesterification activities when are supported on different materials, Li et al. (2013) prepared and AC from Kraft lignin by chemical activation with K2CO3, at 800°C and R = 0.6. This AC was used as solid base catalyst for biodiesel production. The catalyst, with a potassium element content estimated by XPS of 18 wt% and ABET of 41 m2/g, was evaluated by transesterification of rapeseed oil with methanol, obtaining a biodiesel yield of 99.6%. Furthermore, the catalyst was effectively reused four times, with almost the same activity.
Low-cost AC with high surface area was also prepared from lignin of papermaking black liquor by KOH activation. Fierro et al. (2007a) obtained by the traditional method, an AC with very high ABET, 3000 m2/g, and Vmic of 1.5 cm3/g, at 700°C (for 1 h) and R = 3. The same authors also made a comparison between KOH and NaOH and they found that, whatever the preparation conditions, KOH led to the most microporous materials, having surface areas and micropore volumes typically 1.5 and 1.2 times higher than those obtained with NaOH (Fierro et al., 2007b). Li et al. (2014) obtained very similar results, with an AC with 2763 m2/g, at R = 4, an activation temperature of 750°C and an activation time of 2 h. However, the procedure was slightly different in case of Gao et al. (2013), because the activation step was preceded by a pre-carbonization treatment. These authors obtained, in this case, an AC with a high ABET up to 2943 m2/g. But the results, here, were quite different because the maximum surface area was obtained at R = 0.33, activation temperature of 750°C and activation time of 1 h. This AC was used as adsorbent for Ni (II) removal from aqueous phase.
H3PO4 as activation agent
Hayashi et al. (2000, 2002) also studied the activation of Kraft lignin with H3PO4. They observed a maximum development of the porous structure, with ABET round 1000 m2/g, at an activation temperature of 600°C, although they only optimized the temperature at R = 1. Gonzalez-Serrano et al. (2004) also used H3PO4 as activating agent, at impregnation ratios between 1 and 3, and activation temperatures between 350 and 600°C. They provided an optimum of R = 2, and an activation temperature around 427°C, as the best combination of operating conditions to prepare ACs for aqueous phase applications. Specifically, they tested these carbons with relevant results for the removal of phenol, 2,4,5-trichlorophenol and Cr (VI) as representative of toxic contaminants found in industrial wastewaters.
On the other hand, Montane et al. (2005) made an interesting research on the activation of Kraft lignin with H3PO4. They have developed a phenomenological kinetic model (Montane et al., 2005). They also optimized the preparation condition of AC from Kraft lignin with H3PO4 by modifying the activation temperature (400–650°C), the impregnation ratios (0.7–1.75) and impregnation times (1–48 h) (Fierro et al., 2006). They obtained a maximum ABET (1305 m2/g) and pore volume (0.67 cm3/g) at 600°C. They also pointed out that the effect of impregnation time is more important at high carbonization temperatures due to decomposition of phosphate and polyphosphate bridges cross-linking parts of the carbon structure. In this sense, Fierro et al. (2007c) also analyzed the effect of Kraft lignin demineralization and they found that demineralization process produced lignin polymerization and reduced its ability to react with H3PO4. Furthermore, demineralized Kraft lignin provided ACs with lower adsorption capacities for MB, probably due to the lower ash and sulfur contents.
On the other hand, and being more related to the potential applications of these materials, Sun et al. (2012) used an AC prepared from lignin by H3PO4 activation, at 500°C and R = 2, as molecular sieve. However, despite the AC provided a satisfactory representation of high pressure CO2, CH4, and N2 adsorption, the separation kinetic between CO2 and CH4 was quite limited.
Less effort has been related to study the surface chemistry of ACs from lignin prepared by this method. In this sense, Guo and Rockstraw (2006) prepared carbons from xylan, cellulose, and Kraft lignin by H3PO4 activation. They observed the formation of two different acidic surface groups, such as carboxylic-containing groups of varying acidic strength, and phosphorus-containing groups. They also observed slightly larger amounts of these last groups by using Kraft lignin as precursor.
Specifically in our research group, it has been carried out a deep research of the surface chemistry and the possible catalytic applications of the carbons obtained by chemical activation with phosphoric acid. These carbons present a developed porous structure and also high surface acidity as a consequence of the oxygen–phosphorus groups formed on the carbon surface during the activation process (Rosas et al., 2008, 2009; Bedia et al., 2009). The XPS P2p (Figure 3) results seem to indicate the presence of C-O-P and C-P-O groups on the surface of the ACs. C-O-P and C-P-O is representative of the possible groups formed during the chemical activation and thermal treatment (Table 2). The H present in these groups provides the AC an acid character, stable at high temperature. Furthermore, these acidic groups present high-thermal stability decomposing at temperatures higher than 700°C. Taking advantage of these properties, Bedia et al. (2009) used an AC obtained from Alcell lignin as an acid catalyst for the dehydration of 2-propanol. The carbon acid catalysts were prepared by chemical activation with H3PO4, without the need of incorporating acid surface groups in a complementary step by chemical oxidation of the carbon surface. The conversions of 2-propanol yielded only dehydration products, mainly propylene, with very low amounts of di-isopropyl ether, confirming the acidic nature of the catalyst sites. Furthermore, the presence of water vapor did not affect significantly the conversion and the product distribution, what constitutes an important advantage with respect to some inorganic catalysts.
Figure 3. XPS P 2p region for an activated carbons obtained by H3PO4 chemical activation of Alcell(R) lignin with an impregnation ratio of 3 (wt H3PO4/wt lignin).
Table 2. Possible phosphorus surface groups formed during H3PO4 activation, as C-O-P and C-P-O groups.
The aforementioned phosphorus surface complexes, in the form of COPO3, CPO3 groups, which remain very stable at relatively high temperatures confer to carbons a high oxidation resistance (Wu and Radovic, 2006; Rosas et al., 2009, 2012). We have recently reported a detailed study on the oxidation resistance of these phosphorus-containing ACs obtained among others materials, from Alcell lignin (Rosas et al., 2012). This oxidation resistance is related to the inhibition effect of the phosphorus complexes. This high oxidation resistance opens new possibilities for the use of carbon-based materials as catalyst supports, for metals or metal oxides, for reactions that take place under oxidizing conditions at relatively high temperatures.
In this sense, mesoporous ACs were obtained by chemical activation of kraft lignin with H3PO4 and used as supports for the preparation of carbon-based Pd catalysts with low palladium content (0.5%). Because of the high oxidation resistance of this carbon support, the catalyst was evaluated in the catalytic oxidation of toluene in the temperature range of 150–400°C, obtaining a complete oxidation of toluene to CO2 and H2O, without significant support gasification (Bedia et al., 2010). On the other hand, this catalyst was also tested for hydrogenation and Suzuki reactions. The presence of phosphorus groups on the carbon surface, especially C3P groups, avoids the need of using triphenylphosphine as ligand in the Suzuki–Miyaura reactions (Guillen et al., 2009). For both reactions, the catalyst shows high activity and selectivity, as well as high stability and reproducibility.
Lignin-Based Carbon Fibers
Considering the great technological and industrial importance of CFs, and the high price, scarcity, and growing consume/demand of their conventional fossil precursors (PAN and pitches), the manufacture of low-cost CFs with high added-value from a renewable, abundant, and cheap precursor like lignin is one of its most interesting and promising valorization routes, from both the economic and environmental points of view (Leitten et al., 2002; Lallave et al., 2007; Ruiz-Rosas et al., 2010; Frank et al., 2014; Ragauskas et al., 2014). The usage interest includes both the so-called high-performance CFs, showing excellent mechanical properties for structural applications (advanced composite materials, aerospace, military, sporting and luxury goods, etc.), and the general-purpose CFs for functional applications (adsorption, catalysis, energy storage and conversion, etc.) in which other properties, such as a high surface area and/or a suitable porosity, surface chemistry, electrical conductivity, and oxidation resistance are considered more important than the mechanical ones.
Apart from availability and low cost, the usage of lignin as a source of CFs brings about many other advantages. Its high carbon content (≥ 60%) and efficiency for thermal conversion into carbon materials results in potentially high carbon yields. Compared to conventional PAN and pitch precursors, its higher solubility in volatile solvents avoids the evolution of toxic products (HCN or nitrous gases) during carbonization, and makes cheaper the overall manufacture because the lower cost of both the volatile solvents and their recovery processes, and, on the other hand, its higher inherent oxygen content enables a potentially much faster oxidative thermostabilization and, consequently, conversion into CFs.
In general (simplified) terms, the conventional manufacture of CFs from a given isolated industrial lignin mainly involves five successive processing steps: (i) purification and/or modification to obtain derived lignins with more suitable properties for their subsequent processing and/or optimization of the CF final properties; (ii) spinning into lignin fibers; (iii) oxidative thermostabilization of as-spun lignin fibers (most usually, in air, up to 200–250°C) to avoid their fusion during (iv) the carbonization treatment at high temperatures under inert atmosphere (500-1000°C) to produce lignin-based CFs; and finally, (v) a post-treatment to adjust/optimize their properties for structural (usually graphitization at temperatures above 1200°C) or functional (mainly by physical activation and/or functionalization) applications (Figure 4).
In spite of the advantages of using lignin as precursor, the obtained fibrous carbon materials have not exhibited the needed properties to involve enough or comparable high value. As a consequence, most research in lignin-based CFs is being currently focused on these three aspects: (i) the optimization of lignin derivation and spinning for lignin fibers manufacture; (ii) the development of faster thermostabilization routes; and/or (iii) the achievement of CFs with new or enhanced properties for structural and functional applications.
Manufacture of Lignin Fibers: Different Lignins and Spinning Methods
Similar to other polymers, the manufacture cost and the final morphology and properties of lignin-based CFs depend not only on carbon precursor chemistry and extraction technique but also on the fiber processing methodology. Thus, much research has been focused on the spinnability of several lignins in different fiber processing methods (mainly wet-, dry-, melt-, and electrospinning).
The manufacture of CFs from lignin has been known since the mid-60s, when various methods of forming fibers (wet-, dry-, and melt-spinning) from various lignins and by using additives and/or post-treatments, and their conversion to CF, graphitized CF, and activated CF were described (Otani et al., 1969).
Dry- and wet-spinning
After this pioneer work, the preparation of lignin-based CFs by wet- and dry-spinning processes dominated in the following decade. Both methods require soluble lignins, which were simpler to achieve and process at that time. Headed by Nippon Kayaku Company, lignin-based CFs prepared by dry-spinning of alkaline lignosulfonate/polyvinyl alcohol (PVA) solutions were studied and even commercialized (as Kayacarbon) at small scale (Fukuoka, 1969; Mikawa, 1970). Since infusible lignin was used and thermostabilization was not required, higher carbon yields were obtained through a more cost-efficient process. Nevertheless, and although various related patents and papers have been published until now, the research activity of lignin-based CFs through these methods, almost ceased in the 1980s. Some interesting examples are the co-spinning of lignin sulfonates with low amounts (up to 5 wt%) of polyethylene oxide (PEO) or poly(acrylamide), predominantly by dry-spinning (Mansmann, 1974); and the various publications on the manufacture of CFs from lignin-PAN blends by wet-spinning (Bissett and Herriott, 2012; Seydibeyoglu, 2012).
Among the different technologies for the production of lignin-based CFs, melt-spinning has been the most studied. The method is based on the extrusion of molten (fusible) lignin under inert atmosphere, so no solvents are needed and more homogeneous lignin fibers are obtained from the liquid state. However, the heterogeneous and partially oxidized nature of lignin demands a critical control of the melt-spinning step, so that, isolated lignin usually has to be purified, plasticized with additives and/or chemically modified to show suitable spinnability.
The objective is to prepare lignin with a low enough softening temperature (Ts), to avoid polymerization and/or cross-linking during extrusion, but with a high enough glass transition temperature (Tg) for economically acceptable stabilization rates. Thus, a narrow range of temperatures exists for manufacturing lignin-based CFs via melt extrusion. Hence, most research works have been focused on new strategies to obtain lignin that are suitable for melt-spinning and, at the same time, can be quickly and effectively thermostabilized to give rise to optimum mechanical properties.
The use of raw isolated lignin. The preparation of lignin-based CFs via melt-spinning started to be developed at the end of 1980s. Sudo and Shimizu (1987) described the preparation of CFs from lignin obtained by the high pressure steam treatment of wood. Nevertheless, because of conceptual ease and availability, the adaptation of most conventional pulping processes to obtain spinnable lignin was then the preferred strategy. The first studies arrived from Uraki et al. (1995, 2001), who reported the preparation of CFs from lignin recovered by the acetic-acid-catalyzed fractionation (Organosolv pulping) of wood. After solvent isolation, a direct melt-spinning process was enabled because of the partial acetylation of some of the lignin hydroxyl groups during pulping. The same authors further studied and compared the fusibility of softwood and hardwood acetic-acid lignin. Hardwood lignin (HAL) showed sufficient fusibility for melt-spinning, because of the partial acetylation during the pulping process, whereas softwood organosolv-lignin (SAL) could be converted into a fusible material by removing the infusible fraction. However, the authors did not succeed in converting softwood kraft lignin (SKL) into a fusible material (Kubo et al., 1998). Since then, other lignins recovered from other extraction methods have been investigated as precursor for CF production (Luo et al., 2011; Lin et al., 2012).
Great improvements were achieved by thermal or purification pre-treatments of isolated lignin to control the overall synthesis and properties of lignin-based CFs. Particularly, a thermal pre-treatment under vacuum (145°C for 1 h) was first used by Kadla et al. (2002a) to successfully melt-spin two commercially available (Alcell and Kraft) HALs for CF production. On the other hand, Baker et al. (2008a) proposed the purification of lignins by extraction with organic solvents, as a way to improve their spinnability and reduce their melting temperature. However, lower spinning temperatures necessarily led to the use of lower thermostabilization rates to prevent fusion upon carbonization. Furthermore, the same authors combined thermal and purification pre-treatments to obtain lignins with a narrow molecular weight distribution, suitable for multifilament melt-spinning (Baker and Gallego, 2010), or to enable the melt-spinning of a non-melt-spinnable lignin like SKL (Baker et al., 2012). Since then, other purification treatments of lignin, like that of lignoboost process (Tomani, 2010), or its advanced version by membrane ultrafiltration (Nordström et al., 2012), have been more recently explored for the manufacture of CFs.
Blending with plasticizing additives. The utilization of plasticizing additives to improve the spinnability of lignins has been extensively reported on the literature. In the case of melt-spinning, the pioneers were Kadla and co-workers, who investigated the interactions and spinnability of lignin with PEO, poly(ethylene) (PE), poly(propylene) (PP), poly(ethylene terephthalate) (PET), and PVA. Due to their high miscibility with lignin, PEO and PET were found among the best additives in terms of spinnability and thermal properties. Practically, the role of these additives is to reduce the high softening temperature of some lignins, in order to make them spinnable. For instance, up to a 45°C, a decrease in spinning temperature of commercially available HALs (HKL and HOL) was observed by blending with 5–25 wt% PEO (Kadla et al., 2002a), and a non-spinnable lignin (SKL) was successfully processed into fibers after blending with 50 wt% PEO (Kubo and Kadla, 2004, 2005a). On the other hand, the non-polar character of PE and PP makes them immiscible with lignin, so that, the spinning of homogeneous blends to prepare structural CFs was not possible (Kadla et al., 2002b). In the case of lignin/PVA, the research has been focused on using lignin as a plasticizer to improve the processability of PVA fibers (Kubo and Kadla, 2003). Another promising approach has been the use of fusible (low Tg) HALs as plasticizer of infusible (high Tg) softwood lignins (Baker et al., 2008b; Warren, 2008; Nordström et al., 2012).
The obtainment of novel lignins by chemical modifications. The chemical modification of isolated lignins is also considered an interesting approach for CF manufacture. Some of the studied routes are hydrogenolysis, phenolysis, acetylation, derivatization, and copolymerization, among others. In the pioneer works by Sudo and Shimizu (1992), steam-exploded lignin was hydrogenated by using a Raney Ni catalyst, causing a significant elimination of aliphatic functional groups by cleavage of alkyl–aryl ether bonds and the formation of ethylene bridges between aromatic rings, to lower its softening point to improve melt-spinning. On the other hand, the authors also tested melt-spinnable phenolated lignins produced by different processes (Sudo et al., 1993; Sudo and Shimizu, 1994). Furthermore, demethoxylation (Gould, 1974) and acetylation (Eckert and Abdullah, 2008) were proved.
Another approach has been the chemical derivatization of lignins through their free hydroxyl groups to give plasticizing derivatives attached via ester, ether, and/or urethane functions (Wohlmann et al., 2010). Particular cases of derivatization have been the co-polimerization of lignins with other monomers and polymers, for example, by reaction of the guaiacyl groups of lignin with the formaldehyde groups to form lignin–phenol–formaldehyde (LPF) resins (Shen et al., 2011), and by butyration with poly(lactic acid) (PLA) to form ester functional groups with lignin hydroxyl groups (Thunga et al., 2014), respectively, or the extension of lignin chains by different reactions, like propargylation derivatization of relatively lower molecular weight lignin followed by oxidative coupling reaction or thermal polymerization via the Claisen rearrangement (Sen et al., 2013).
Electrospinning has emerged in recent years as a promising route for the preparation of novel lignin-based fibrous materials. Nevertheless, despite the benefits provided by the use of electrospinning and a cheap precursor like lignin, to date, there are relatively few published reports on the preparation of electrospun lignin fibers.
The research group of professor Cordero succeeded in applying this technique to the manufacture of pure lignin fibers (at room temperature and without chemical modifications or any added polymer), and also with different shapes, like solid pure and metal-supported or hollow lignin fibers (Lallave et al., 2007; Ruiz-Rosas et al., 2010). Highly concentrated ethanol solutions of as-received Alcell lignin were used in the co-axial and tri-axial configurations, respectively (Figure 5) (Loscertales et al., 2002, 2004). The incorporation of a Pt salt in the lignin:ethanol solution enabled the preparation of Pt-doped lignin fibers, while pumping glycerin, like sacrificial template, through the inner spinneret of a tri-axial configuration led to the preparation of glycerin-lignin core-shell co-axial fibers. After suitable thermostabilization and carbonization steps, the new straightforward method allowed the preparation of 200 nm to 2 μm diameter electrospun solid CFs and Pt-containing CFs, see Figures 6A,B with a 0.3–0.6 wt% of well-dispersed Pt particles of around 10 nm, or electrospun hollow CFs.
Figure 5. General set-up used in co-axial and tri-axial electrospinning to produce lignin-based CFs and hollow CFs, respectively, adapted from Ruiz-Rosas et al. (2010).
Figure 6. (A) SEM and (B) TEM images of electrospun carbonized lignin fibers; (C,D) SEM images of (C) fragile non-bonded and (D) bonded lignin-based CFs showing the flexibility (E) of the later ones.
Apart from these results, lignin solutions (including organosolv, kraft, pyrolytic) have been found to display poor electrospinnability, obtaining a substantial bead formation unless neither a small amount of plasticizing additive is added nor a lignin pre-manipulation is performed (Dallmeyer et al., 2010). A solution of purified SKL in DMF/methanol was electrospun to give fibers with varied morphology and 300–500 nm average diameters (Hosseinaei and Baker, 2012).
Regarding the use of plasticizing agents, the first attempt was the electrospinning of SKL/PEO blends to obtain electrospun CFs of ~ 4 μm diameter (Montero et al., 2008). Later, Dallmeyer et al. (2010) studied the electrospinning of seven different technical lignins and found a clear transition from electrospray or beaded fibers to uniform fibers upon addition of PEO. More recently, these authors have presented a correlation of the elongational fluid properties to fiber diameter in electrospinning of SKL solutions (Dallmeyer et al., 2014b). Kang and co-workers reported the electrospinning of PAN/alkali-lignin composites (from 100:0 to 20:80 w/w) to prepare submicron fibrous mats of varying morphology. While uniform and thicker fibers (submicron) were produced for lignin contents up to 50 wt%, a remarkably shift to a beaded morphology was observed for higher lignin concentrations. These changes were assigned to a decrease in solution conductivity with the lignin content (Seo et al., 2011; Choi et al., 2013). In another approach, CFs were prepared by electrospinning of alkali-lignin/PVA 9–12 wt% aqueous mixtures (30/70, 50/50, and 70/30). The average diameters decreased from 300 to 140 nm with increasing the lignin amount, the finest ever reported lignin-based CFs, what was attributed to a decreasing viscosity and increasing conductivity of the blends (Lai et al., 2014a).
On the other hand, PEO has been also used to enable the incorporation of nanomaterials fillers or chemical activating agents and the control of interconnection, or to avoid the stabilization step on micron-sized electrospun lignin fibers. Some authors studied the electrospinning of n-fractionated SKL solutions together with various concentrations of suspended MWCNTs (Lin et al., 2013; Teng et al., 2013). Furthermore, it has been reported that the presence of 10 wt% PEO enables the efficient electrospinning of aqueous NaOH or KOH/Alcali-lignin (ALls) solutions into fibers (Hu and Hsieh, 2013; Hu et al., 2014). Another outstanding method to assist the spinning of advanced fine lignin fibers is the emulsion electrospinning (Lin et al., 2013).
Because the glass transition temperature (Tg) of lignins is much lower than those required for their carbonization, lignin fibers have to be subjected to a stabilization pre-treatment to prevent softening. During this treatment, the lignin fiber keeps infusible whenever its Tg is maintained above the process temperature by cross-linking reactions (Braun et al., 2005). Although other stabilization treatments to induce structural cross-linking have been proposed in the literature, like electron beam irradiation, UV radiation, plasma treatment, etc., the simple oxidative thermostabilization in air is by far the most studied and applied method. Despite lignin needs slow heating rates to avoid fusion, the inherent high oxygen content in this polymer enables faster stabilizations than other polymers (PAN, pitches, etc.).
The oxidative stabilization of lignin fibers has been investigated by different authors. Braun et al. (2005) used several characterization techniques to monitor the changes of HKL upon thermostabilization. At lower temperatures, they observed that oxidation reactions form carbonyl and carboxyl structures, while, at higher temperatures, these groups are incorporated into ester and anhydride linkages producing cross-linking within the lignin molecule. Furthermore, from a continuous heating transformation diagram, the optimum heating rate of HKL to keep its Tg > T was predicted to be 0.06°C/min. In addition, a recent study reveals that, apart from carbonyl and carboxyl-related structures, stabilization remarkably reduces the proportion of methoxy groups present in hardwood Alcell lignin (Foston et al., 2013). Brodin and co-workers found that the carbon yield of kraft lignin increases as the conditions of its oxidative thermostabilization treatment become harsher (slower heating rates, higher temperatures and longer holding times at this temperature) (Gellerstedt et al., 2010; Brodin et al., 2012). By contrast, Baker and Gallego (2010) found an optimum thermostabilization rate to improve CF yields, below which carbon yield was reduced because the balance of oxidation versus degradation became in favor of the latter, and above which lignin volatilization predominated over oxidation and cross-linking.
In general, thermal pre-treatments under different conditions and/or purification processes with suitable solvents or membranes have been carried out to increase the Tg and Ts of different lignins and their thermostabilization rates (Baker et al., 2009; Hosseinaei and Baker, 2012). In other cases, the co-extrusion with suitable additives (PEO, PET, etc.) enables remarkably faster stabilization processes (Kubo and Kadla, 2005b) or even alleviates the need for the thermal stabilization step (Hu and Hsieh, 2013; Hu et al., 2014).
Lignin-Based Carbon Fibers for Structural Applications
As mentioned before, lignin-based CFs were projected to cost much less than any other known method of CF production (Baker and Gallego, 2010). As a result, the optimization of structural properties has been the main objective driving most investigations related to lignin-based CFs. Nevertheless, although the mechanical properties of the lignin-based CFs would fit low grade requirements, with optimized fibers showing tensile strengths up to ~1.10 GPa and Young’s moduli up to 83–109 GPa (Compere, 2005; Baker and Gallego, 2010), they currently have poor mechanical properties compared with petroleum-derived counterparts and do not meet those required from the automotive industry, i.e., a tensile strength of 1.72 GPa, and a modulus of 172 GPa (Warren, 2008; Baker and Gallego, 2010). Hence, much research on the preparation of high-performance lignin-based CFs is currently being done.
In spite of different studies on the carbonization of lignin powder (Rodríguez-Mirasol et al., 1996) or lignin-derived CFs (Baker and Gallego, 2010) revealed the presence of more ordered graphitic structures at elevated temperatures, the early structural investigations carried out by Johnson and Tomizuka (1974) indicated that lignin-based CFs present a low degree of orientation, as well as considerable degree of cross-linking and amount of pores and heterogeneities in their fine structure. Furthermore, the inorganic impurities in lignin precursors act as graphitization catalysts. This provokes density fluctuations and an inhomogeneous melting behavior, thus, preventing any improved tensile strength of the final material.
In this sense, one of the most significant difficulties to produce lignin-derived CFs with enhanced mechanical performance is associated to the heterogeneous nature of lignins (McCarthy and Islam, 2000; Capanema et al., 2004), which also can be strongly modified during the different pulping processes (Lora, 2008). Furthermore, the presence of impurities (ash, etc.) and/or infusible/insoluble components in lignins strongly determine the homogeneity of the CFs (Compere et al., 2004; Suhas et al., 2007). As a consequence, the use of suitable solvents, membranes, and/or thermal treatments, as well as new chemical treatments to purify or modify lignins, respectively, are considered among the most important strategies to enhance the mechanical properties of their derived CFs.
Parallel to the diversity in lignins, there is a lack of knowledge on the influence of the spinning method in the final mechanical properties of lignin-based CFs. Nevertheless, the available literature suggest that the use of plasticizing additives and/or molten lignins via the melt-spinning method may result in more homogeneous lignin fibers and/or facilitate a more homogeneous incorporation of reinforcing fillers. However, the thermal decomposition of the additives and/or cross-linking and degradation of fusible lignins during melt-spinning, thermostabilization, and/or carbonization may result in the development of porosity and heterogeneity and/or hinder the mobility and rearrangement of lignin molecules, weakening the obtained CFs. To deal with these problems, a narrow molecular weight distribution (small difference between Tg and Ts) to ensure uniform increases in molecular weight throughout the material during oxidative thermostabilization, and to provide for a more uniform structure during carbonization, is desirable. Other well-known strategies to strengthen the lignin-based CFs may be their diameter reduction and alignment. This can be readily accomplished through electrospinning, and promising results could arise from aligned or interconnected electrospun lignin fibers obtained from suitable lignins.
Finally, the control of temperature, heating rate, and atmosphere during stabilization and carbonization steps determines not only the time and energy consumption of the overall manufacture process but also the properties of the final carbonized fibers. Thus, during stabilization, the gradual increase in Tg by cross-linking reactions leads to the formation of rigid oxidized segments (Braun et al., 2005) that, although are necessary to avoid fiber swelling and fusion and may increase the carbon yields, could be detrimental to structural carbon order (Hurt and Chen, 2000). However, it has been recently reported that the interconnection in fused CFs enhances the mechanical properties of both the thermostabilized and carbonized materials (Dallmeyer et al., 2014a). An example, see Figures 6C–E. On the other hand, while a high Tg is desired to accelerate the thermostabilization treatment, the achievement of too high temperatures under air atmosphere may cause degradation of lignins and, therefore, more defective or heterogeneous CFs. This compromise relationship among thermostabilization rate, thermal degradation, and cross-linking and mechanical properties demands for a precise control of the process that remarkably hinders the manufacture of lignin-based CFs.
Up to now, the best mechanical properties were obtained by Compere (2005), which evaluated the mechanical properties of soda HAL–PET fibers carbonized at 1200°C, reaching tensile strengths up to 1.03 GPa and Young’s modulus up to 109 GPa, and by Baker and Gallego (2010), which reported CFs, from purified Alcell lignin, with an average tensile strength of 1.07 GPa and moduli of 82.7 GPa, as well as 55% of carbon yield.
Lignin-Based Carbon Fibers for Functional Applications
As aforementioned, CFs can be used for functional applications (adsorption, catalysis, energy storage and conversion, etc.) in which other properties, such as a high surface area and/or a suitable porosity, surface chemistry, electrical conductivity, and oxidation resistance are considered more important than the mechanical ones.
Different methods have been proposed in the literature to obtain AC fibers (ACFs), which can be used in these functional applications. However, to date, the advantageous use of lignin as precursor of lower cost ACFs has been much lesser studied. The different routes to fabricate porous CFs from lignin could be divided into chemical, physical, or inherently driven activation. In his patent, Otani et al. (1969) claimed the production of highly activated CFs, through wet- dry-, and melt-spinning, by the introduction of various chemical agents in the molten lignin (sulfur, ZnCl2) or in the solvents in which lignin is dissolved (NaOH, KOH, H2SO4) and/or by treatment with an activating gas (air, oxygen, stream, etc.) just after carbonization. The claimed ACFs of 15–30 μm diameter showed MB adsorptive powers of 8–25 cm3 as well as chemical and heat resistances, electrical conductivity, and/or textile flexibility (Otani et al., 1969). Recently, submicron ACFs prepared by electrospinning of (ALls)/PEO (9/1 w/w) together with NaOH or KOH showed very high ABET (up to 1400 m2/g) with over 85% attributed to micropores (Hu and Hsieh, 2013). As for physical activation, Uraki and co-workers investigated the preparation of ACFs from acetic acid hardwood (HAL) and softwood (SAL) lignins by steam activation. The HAL-based ACF, activated for 40 min at 900°C, had excellent properties, such as more rapid adsorption rate and comparable or superior iodine and MB adsorption capacities to those commercially available AC powders (Uraki et al., 1997). The authors also reported the use of SAL, free from the high-molecular-mass fraction, to yield ACF with a faster thermostabilization step and larger ABET (1930 m2/g) and pore volume (0.523 cm3/g) than that from HAL. It was found that SAL-ACF had adsorption properties comparable to those of high-performance commercial ACF and a tensile strength equal to that of a pitch-derived ACF (Kubo et al., 1998). On the other hand, several lignin-based ACFs with controllable pore size properties were prepared from LPF resins with varied lignin contents, 8–20% (Qing et al., 2011). Lin et al. (2012) reported the steam activation of CFs, from thermally fusible softwood (cedar) PEG-lignin, at 900°C for 30, 60, and 90 min to give rise to ABET of 2038, 2442, and 3060 m2/g, respectively (the highest ever reported from any lignin precursor) indicating the promising use of this precursor for the manufacture of ACFs.
Based on their specific composition, the carbonization of different pure or composite lignin fibers can result in highly porous fibrous materials (inherently driven activation). Kubo et al. (2007) studied the porosity of HKL/PP-derived CFs and found that, during the thermostabilization process, pores are created by oxidative degradation of PP, whereas upon carbonization, the residual PP is subsequently pyrolyzed to effectively create porosity (up to ~500 m2/g) in the resulting CFs. Similarly, the carbonization of electrospun lignin/PVA (70/30) fibers resulted in ABET of ~580 m2/g (Lai et al., 2014a).
More interestingly, the carbonization of electrospun Alcell lignin gave rise to microporous CFs with high ABET and pore volumes of up to 1200 m2/g and 0.520 cm3/g, respectively. This remarkable porosity development was assigned to the high oxygen contents in the stabilized precursors (~33 wt%), which could act as inherent activating agent during the subsequent carbonization process. In spite of their high porosity and small diameter, and even containing Pt (a well-known catalyst for carbon oxidation), these CFs showed a remarkably high oxidation resistance (those carbonized at 900°C start to oxidize above 500°C) (Figure 7). The presence of Pt only slightly reduces the oxidation resistance. The high oxidation resistance was assigned to a certain degree of structural order and to the lack of surface defects achieved upon carbonization. Furthermore, the same authors carried out a study of the thermal oxidation mechanism of the fibers. At lower carbon burn-offs, the reaction proceeds mainly over the external fiber surface, but it also affects the inner surface at near complete oxidation (90% BO). Because of a wider microporosity induced by Pt, the presence of the metal results in a more homogeneous oxidation of the fibers (Ruiz-Rosas et al., 2010).
Figure 7. Oxidation resistance profiles in air atmosphere of non-stabilized and carbonized lignin-derived CFs (A) without platinum and (B) with platinum adapted from Ruiz-Rosas et al. (2010).
Carbon fibers as electrodes for electrochemical devices
The utilization of more continuous and/or self-standing carbon materials in the shape of various fibrous structures (fibers, tubes, fabrics, meshes, webs, etc.) as electrodes in different electrochemical devices for energy storage and conversion is receiving a growing interest in recent years. Major advantages arise from their much lower inter-particle resistance and the lack of need for expensive additives (binders and conductivity promoters) that make complex the manufacture process. Dallmeyer et al. (2014a) found that the conductivity of interconnected Kraft lignin-based sub-μm diameter CFs were much higher than that of the corresponding non-bonded materials, and that the obtained conductivities (0.6–19.6 S/cm), were comparable to those of other electrospun CFs based on phenolic resin or PAN. In this sense, the use of lignin-derived fibrous carbon materials for applications in energy storage systems like lithium-ion batteries (LIBs), supercapacitors (electrochemical capacitor), or fuel cells has been recently reported.
In the case of LIBs, Wang et al. reported that fusion and N-doping (up to 12.6 wt%) enhance the electrical conductivity (10.53 and 12.24 S/cm, respectively) and LIB specific capacity (445 and 576 mAh/g, respectively, at 30 mA/g) of freestanding CFs prepared by electrospinning of organosolv-lignin/PEO (≥10 wt%) blends. In addition, N-doped fused CFs still maintained a good capacity of ~200 mAh/g even at a high current rate of 2 A/g (Wang et al., 2013). On the other hand, Tenhaeff et al. have recently used fused fibrous carbon materials, from melt-spinning of Alcell lignin, exhibiting specific charge capacities comparable to conventional graphitic anodes in LIBs (350 mAh/g when carbonized at 1000°C). Carbonization at higher temperatures (1500–2000°C) resulted in greater graphitization and lower specific charge capacities, but significant improvements in the first cycle efficiencies (Tenhaeff et al., 2014).
Good performance has been also demonstrated for supercapacitors and fuel cells. ACFs from KOH activation of electrospun (ALls)/PEO (9/1 w/w) blends showed very high specific capacitance of 344 F/g at low electrode mass and scan rate (1.8 mg/cm2 and 10 mV/s, respectively) in 6M KOH aqueous electrolyte, which was maintained at 196 F/g for 10 mg/cm2 and 50 mV/s, giving rise to a high average energy density of 8.1 Wh/kg. Furthermore, over 96% capacitance retention was achieved after 5000 charge/discharge cycles (Hu et al., 2014). On the other hand, mechanically flexible ACFs from electrospun alkali-lignin/PVA 70/30 aqueous mixtures were found to exhibit capacitances (two-electrode cell) of 64 and 50 F/g at current densities of 400 and 2000 mA/g, respectively, in 6M KOH aqueous electrolyte. Moreover, the electrode capacitance merely reduced by ~10% after 6000 cycles (Lai et al., 2014b). In another work, Ag nanoparticles supported on electrospun lignin-based CFs (AgNPs/CFs electrocatalysts) have exhibited high activity toward oxygen reduction reaction (ORR) and a close-to-theoretical four-electron pathway in 0.1M KOH aqueous solution. In particular, the mass activity of 15 wt% AgNPs/CFs system was the highest (119 mA/mg), exceeding even that of a commercial Pt/C catalyst (98 mA/mg), thus, suggesting lignin-derived CFs as promising low-cost supports for highly efficient ORR electrocatalysts in alkaline fuel cells.
In recent years, an intense research on the preparation of materials with controlled pore systems at different length scales has been taking place, since an adequate control of the pore size plays a key role in carbon material properties and performance (Ruiz-Rosas et al., 2014; Saha et al., 2014a). In this context, nanostructured carbons with hierarchical pore arrangement, known as hierarchical porous carbons (HPCs), have shown outstanding behavior in different applications because of the different ranges of interconnected pores.
The preparation of both hierarchical mesopore–micropore carbons and micropore materials with a highly ordered pore structure usually involves the use of the nanocasting technique, which implies a reverse replication of the pore system from a porous material as sacrifice template. Nanostructured carbons with hierarchical pore arrangement (ordered micro- and mesopore network) can be prepared by liquid phase impregnation (LPI) of the pores of a hard template. On the other hand, microporous carbons with a three-dimensional connected and ordered pore structure can be prepared by chemical vapor deposition (CVD) of a light hydrocarbon over a zeolitic material, which is later removed by acid-etching. The preparation of carbon materials by CVD goes out of the goal of this review, since it is only focused on the use of lignin as carbonaceous precursor.
In this sense, Fierro et al. (2013) synthesized microporous–mesoporous carbons via colloidal silica templating by using microwave pretreated Kraft lignin in sodium bicarbonate solution, as a carbon precursor. The authors obtained tunable mesopores after dissolving colloidal silica used as a hard template, whereas the microporosity was created by a post-synthesis CO2 activation method. The resulting activated lignin-based carbons possessed high ABET (up to 2000 m2/g) and microporosity and mesoporosity easily tunable by adjusting activation conditions and optimizing the amount and particle size of the colloidal silica used. The total pore volumes of ACs obtained by using 20 and 13 nm silica colloids as a hard template exceeded 1 and 2 cm3/g, respectively. More recently, Saha et al. (2014a,b) have also reported the preparation of mesoporous carbons with an ordered porous structure using Alcell lignin as a natural carbon precursor, but in their case, a surfactant is used as the sacrifice template. In this new templating technique, named surfactant templating synthesis, the mesoporous carbon is synthesized by cross-linking a suitable organic resin in the presence of some sacrificial surfactants, followed by pyrolysis leading to removal of the surfactant and subsequent carbonization of the matrix. The obtained carbon had a BET surface area of 200 m2/g and pore volume of 0.2 cm3/g. The novelty of these works arises from the use of this mesoporous carbon to control the release of different model drugs, such as captopril, furosemide, ranitidine hydrochloride, and antipyrine, as a relatively newer type of drug-delivery medium.
On the other hand, Valero-Romero et al. (2014) reported the preparation of carbon materials with hierarchical pore structures by liquid-phase impregnation technique with Alcell lignin solutions as the carbon precursor and different zeolites as inorganic templates. The impregnation ratio of 1:1 (1 g of lignin and 1 g of zeolite Y and β, respectively) was selected as the optimum combination for the development of structures with different levels of micro-and mesoporosity development. The infiltrated samples were further dried and carbonized under continuous inert flow. The carbon/zeolite composites prepared through this impregnation method were soaked in NaOH solution to remove the zeolite template. As an example, the TEM images of the parent zeolites and their respective TCs, shown in Figure 8, provide evidence to support the different origins of mesoporosity. Images from Y- and β-based TCs, Figures 8B,D, proved that these materials present similar morphologies to those of the hard templates, indicating the adequate replication of the zeolites. Inset in Figures 8B,D provides evidence of a population of mesopores with sizes around 3 and 10 nm, for Y- and β-based TCs, respectively. In addition to the structural properties, a very interesting feature observed was the presence of oxygen and nitrogen functional groups. The contribution of nitrogen on the TCs was reported to be due to the ammonium cation in zeolite templates, which participated in the reactions during the carbonization step at high temperatures to form carbon surface-N species, such as, pyridine-like species and highly coordinated quaternary nitrogen atoms (pyrrolic or amine moieties). On the other hand, the oxygen presented in the TCs, consisted mainly of carbonyl, phenolic, and anhydride groups, which might have been derived from the dehydroxilation of zeolites during the carbonization.
Figure 8. TEM micrographs of the Y zeolite, bar length: 300 nm (A) and L-Y-700 carbon, bar length: 20 nm (inset: 5 nm) (B); β zeolite, bar length: 40 nm (C) and L-β-900 carbon, bar length: 30 nm (inset 10 nm) (D).
Figure 9 shows the voltammograms obtained for L-Y-700, whereas Figure 9B shows the CO-TPD profiled of L-Y-700 before and after the electrochemical oxidation treatment. The results showed that these materials can be easily electro-oxidized in sulfuric acid electrolyte under positive polarization, producing a large amount of CO-evolving surface oxygen groups that enhance the pseudocapacitance by 30% without compromising the rate performance. This seems to be a consequence of the high concentration of active sites of the carbon fraction generated from the infiltration in the zeolite. These lignin-based templated carbons showed a specific capacitance as high as 250 F/g, at 50 mA/g, with a capacitance retention of 50% and volumetric capacitance of 75 F/cm3 at currents higher than 20 A/g thanks to their interconnected porous texture (Ruiz-Rosas et al., 2014).
Figure 9. (A) Cyclic voltammograms of L-Y-700 before oxidation and after oxidation between 0 and 1.2 V and between 0 and 0.8 V (B) CO TPD evolution profiles obtained from L-Y-700 before and after the electrochemical oxidation treatment, adapted from Ruiz-Rosas et al. (2014).
Conflict of Interest Statement
The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.
This work was supported by the Spanish Ministry of Economy and Competitiveness under CTQ2012-36408 project and by Junta de Andalucia (P09-FQM-5156 and P10-FQM-6778).
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Keywords: lignin, biomass, revalorization, activated carbons, fiber, template
Citation: Rosas JM, Berenguer R, Valero-Romero MJ, Rodríguez-Mirasol J and Cordero T (2014) Preparation of different carbon materials by thermochemical conversion of lignin. Front. Mater. 1:29. doi: 10.3389/fmats.2014.00029
Received: 06 October 2014; Accepted: 14 November 2014;
Published online: 04 December 2014.
Edited by:Emilia Morallón, Universidad de Alicante, Spain
Reviewed by:Diego Cazorla-Amorós, Universidad de Alicante, Spain
Soshi Shiraishi, Gunma University, Japan
Copyright: © 2014 Rosas, Berenguer, Valero-Romero, Rodríguez-Mirasol and Cordero. This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) or licensor are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.
*Correspondence: Tomás Cordero, Departamento de Ingeniería Química, Facultad de Ciencias, Campus de Teatinos s/n, Andalucía Tech, Universidad de Málaga, Málaga 29071, Spain e-mail: email@example.com