Covalent organic frameworks, cross-linked crystalline polymers constructed from rigid organic precursors connected by covalent interactions, have emerged as a promising class of nanoporous materials owing to their highly desirable combination of attributes, including facile chemical tunability, structural diversity, and excellent stability. Despite the distinct advantages offered by three-dimensional covalent organic frameworks, research efforts have predominantly focused on the more synthetically-accessible, two-dimensional variants. Here we present an overview of synthetic approaches to yield three-dimensional covalent organic frameworks, identify synthetic obstacles that have hindered progress in the field and recently-employed methods to address them, and propose alternative techniques to circumvent these synthetic challenges.
Nanoporous materials have garnered tremendous interest in recent years owing to their specific and exceptional attributes, notably permanent porosity and large and accessible internal surface areas1,2,3,4,5. Conventional nanoporous materials used commonly as adsorbents and heterogeneous catalysts and catalyst supports, such as zeolites and activated carbon, are based on inorganic building blocks; nevertheless, research interest in nanoporous materials bearing organic components has expanded rapidly1,5,6. This is in part due to the exquisite structural and functional control such components provide and the flexibility they afford for designing materials specifically tailored towards the intended application5.
A large number of such nanoporous organic polymers have been fabricated in recent years, including polymers of intrinsic microporosity (PIMs)5,6, porous polymer networks (PPNs)7, and conjugated microporous polymers (CMPs)8,9,10. These materials are uniformly amorphous and composed of multifunctional building blocks linked by covalent bonds, and many studies have demonstrated their synthesis and utility7,11,12,13. Unfortunately, the amorphous nature of these materials can yield significant pore size dispersities, inhibiting their utilization in certain applications such as size- and shape-based gas separation and storage2,11.
Crystallinity, in contrast, is characterized by ordered structure and uniform porosity, ideal attributes for gas separation and storage, catalysis, and optoelectronic devices2,14. Metal-organic frameworks (MOFs) are one such class of crystalline nanoporous materials that have been investigated extensively. MOFs are constructed from metal ions or clusters linked by organic ligands through coordination bonds, thus possessing both the chemical and structural tunability of the organic ligands, the coordination possibilities of various metal ions, and the uniform porosity and high surface area of a crystalline nanoporous material3,15,16,17. Examples of this class of materials necessarily contain a large amount of potentially toxic or reactive metal centers, and their relatively weak coordination bonds exhibit varying stability under high humidity and temperature, conditions ubiquitous in industrial applications18,19,20,21.
A particularly exciting development in this field was the landmark synthesis of covalent-organic frameworks (COFs) by Yaghi and coworkers in 200522. In this seminal work, two COFs were synthesized from the self-condensation of 1,4-benzenediboronic acid (COF-1) or co-condensation with hexahydroxytriphenylene (COF-5), establishing the first class of crystalline nanoporous organic frameworks linked exclusively by covalent bonds. Although the strength of covalent bonds contributes to significantly improved stability, the general irreversibility of kinetically controlled reactions prevents the molecular rearrangement necessary to form a crystalline structure. Fortunately, the addition products of several covalent bond-forming reactions are known to either revert to the constituent reactants or rearrange under specific reaction conditions. These dynamic covalent reactions, utilizing reversible covalent bonds, which can be formed and broken rapidly under appropriate conditions, are capable of obtaining thermodynamically as opposed to kinetically controlled product distributions. This thereby provides a mechanism for error-correction and facilitates the assembly of the most thermodynamically stable covalent structure, equivalent to conventional self-assembly with non-covalent, intermolecular interactions19. In contrast with the aforementioned amorphous nanoporous polymers and MOFs, COFs offer a unique combination of chemical modularity and structural diversity, crystallinity, high surface area, tunable pore size, thermal stability, and low density3,11,14,23.
Based on the dimensionality of the covalent connectivity, COFs can be classified as either two-dimensional (2D) COFs or three-dimensional (3D) COFs. Two-dimensional COFs are fabricated from planar building blocks, and the framework is restricted to 2D sheets, which can then be stacked to form a layered eclipsed structure through, e.g., π-orbital overlap, generating ordered, one-dimensional channels that are well-suited for charge transport1,3. In contrast, 3D COFs are synthesized from aplanar (typically tetrahedral) building blocks to form highly porous networks, which are similar in structure to MOFs and have been found to possess exceptionally high surface areas (>5000 m2/g) and low densities (<0.13 g/cm3)24, making them attractive synthetic targets. Indeed, although studies examining 3D COF applications remain sparse, several simulation and experimental studies have assessed the gas storage capacity of 3D COFs and predicted or empirically demonstrated performance equal to or exceeding the best-performing MOFs owing to their exceptional porosity, surface area, and low density25,26,27,28,29,30. In addition, the promising performance of 3D COFs as superb adsorbents has also been shown31.
Despite the attractive attributes of 3D COFs, research efforts have predominantly focused on their more synthetically accessible 2D counterparts. This review seeks to provide a comprehensive overview of the current state of 3D COFs, address the synthetic challenges attributable to the significant disparity between 2D and 3D COFs, and submit alternative approaches that might be employed to circumvent these synthetic challenges.
Linkages and modification of 3D COFs
The first synthesis of 3D COFs, reported in 2007 again by Yaghi and coworkers, brought a new dimension to the field32. There have since been many reports describing new 2D COF structures33,34, novel synthetic strategies such as microwave synthesis35, flow synthesis36,37,38, and vapor-assisted synthesis39,40, and construction and modification of 2D COFs towards applications including catalysis41,42, membrane fabrication43, and gas storage44. In comparison, there have been only a handful of new 3D COF structures reported, and little beyond structural explorations and preliminary applications. Whereas a variety of dynamic covalent bond-forming reactions have been employed for the synthesis of 2D COFs, only a few have been used for constructing 3D structures. Consequently, the linkages that govern 3D COFs can be generally categorized as boron–oxygen linkages, imine linkages, and other linkage types. A list of linkage chemistries that have been reported to date for 3D COFs is shown in Fig. 1.
Most early 3D COF structures were formed utilizing boron–oxygen (B–O) linkages. The first 3D COFs, COF-102, COF-103, COF-105, and COF-108 were synthesized from the self-condensation of boronic acids into boroxine rings and co-condensation with catechol into boronate ester rings (Fig. 2a, b). These syntheses were performed under solvothermal conditions from suspensions of precursors in a mixture of mesitylene/dioxane, resulting in the lowest density crystals known at the time (COF-108, 0.17 g/cm3) and Brunauer-Emmett-Teller (BET) surface areas (COF-103, 4210 m2/g) far exceeding those of porous carbons, silicates, 2D COFs, and PIMs, and comparable to some of the highest reported for MOFs (MOF-177, 4500 m2/g)32. Although rapid microwave synthesis and purification was later successfully demonstrated for both 2D and 3D boroxine and boronate ester-linked COFs, this approach has not received significant further study for 3D COFs, and the solvothermal approach has emerged as the prevalent method for 3D COF synthesis32,45. In addition to boroxine and boronate ester linkages, a borosilicate cage was also utilized as a linkage for the synthesis of COF-202 (Fig. 2c)46.
The exceptionally low densities and high-surface areas of these 3D COFs makes them highly promising gas storage candidates. Indeed, grand canonical Monte Carlo (GCMC) simulations on H2 binding for 2D and 3D COFs containing B–O linkages, which was confirmed experimentally for COF-105, predicted that 3D COFs outperform 2D COFs in hydrogen storage capacity by a factor of 2.5–3, attributable to higher surface area and free volume in the 3D variants26. Three-dimensional COFs were also expected to significantly outperform the best-performing MOFs in H2 gravimetric uptake owing to reduced densities and comparable volumetric storage capacity, while doping with lithium ions was anticipated to further increase storage capacity26,27,28. Subsequent experimental investigation of the H2 storage capacity of these COFs confirmed that these 3D COFs demonstrate best-in-class H2 saturation uptake (72.4 mg/g for COF-102), far exceeding 2D COFs (39.2 mg/g for COF-10) and comparable to MOFs (72.4 mg/g for MOF-5) at 77 K. The same study also showed that 3D COFs perform remarkably in the storage of methane and carbon dioxide, comparing favorably to other nanoporous materials including zeolites and MOFs, and that larger intrinsic surface area (or pore volume) generally correlate to higher uptake capacity for these gases30. Further theoretical studies predicted that COF-102 and COF-103 outperform other 2D and 3D COFs and the benchmark MOF-177 in volumetric uptake and delivery amount of methane at high pressure25; however, 3D COFs were predicted to exhibit only average hydrogen storage capacity compared to other MOFs, and required the introduction of stronger H2 interaction sites in the COF material for improved performance29,47. In addition to small gas molecules, the organometallic host-guest chemistry of COF-102 was also examined by infiltration of metallocenes, and similarities between MOFs and COFs as hosts for organometallics was demonstrated48.
More recently, metalation of a 3D COF containing B–O linkage was also demonstrated utilizing dehydrobenzoannulene (DBA), a planar triangular macrocycle that can complex with low oxidation state transition metals, as a building block. The synthesized DBA-3D-COF-1 (Fig. 2d) possesses the highest BET surface area (5083 m2/g) and lowest density (0.13 g/cm3) reported to date for a COF, and subsequent metalation of the COF with nickel resulted in retention of crystallinity and minimal reduction in surface area and pore volume24. In addition, a 3D, γ-cyclodextrin-based COF (CD-COF) was synthesized utilizing a unique tetrakis(spiroborate) linkage, marking the first instance of a 3D anionic COF constructed from flexible aliphatic building blocks (Fig. 3a)49.
Although many of the early 3D COFs relied on B–O linkages, these linkages suffer from poor stability towards hydrolysis and oxidation, limiting their practical utility. Consequently there has been a notable trend away from such linkages towards more robust nitrogen-containing linkage chemistries for COF design and synthesis50. Imine linkages, synthesized from multi-functional, amine- and aldehyde-bearing precursors, currently dominate the field of 3D COFs owing to their excellent thermal and chemical stability.
The first imine-linked 3D COF, COF-300, was reported by Yaghi and coworkers in 2009, and is synthesized from tetrakis-(4-aminophenyl)methane (TAPM) and terephthalaldehyde (Fig. 4b). COF-300 was assigned as a fivefold interpenetrated diamond structure (dia-c5 topology), is stable up to 490 °C, and is insoluble in water and common organic solvents51. It was later reported that by first aging the reaction mixture prior to synthesis, an interpenetration isomer dia-c7 COF-300 possessing a sevenfold interpenetrated diamond structure, could be obtained52. The two isomers exhibited identical covalent bonding at the atomic level and identical thermal stability but were structurally different as revealed by X-ray diffractometry. Ma et al.53 recently reported the construction of single-crystal COF-300 by employing a large excess of aniline as a nucleation inhibitor to prevent immediate precipitation of amorphous networks and increase the reversibility of imine bond formation and dissociation53. They showed that crystal size could be controlled by adjusting aniline concentration and were able to obtain single COF-300 crystals of up to 100 µm in size after 30–40 days.
Single-crystal X-ray diffraction (SCXRD) characterization allowed the resolution of ambiguity in the interpenetration and revealed that COF-300 exhibits a sevenfold interpenetrated structure, and that previous assessment of fivefold interpenetration was owing to structural contortion. SCXRD measurements also revealed that hydration of COF-300 led to structural distortion and a drastic 34% reduction in unit-cell volume, which may be attributed to hydrogen bonding between water molecules and the imine bonds. The authors also synthesized COF-303, an analog of COF-300 with a reversed imine condensation between a tetratopic aldehyde and diamine, and demonstrated that the switch in imine bond direction was not differentiable by conventional powder X-ray diffraction (PXRD), but could be detected by SCXRD53.
COF-300 has also been utilized in conjunction with the zirconium-carboxylate-based MOF UiO-66 to fabricate a composite laminate where a COF-300 layer was grown on top of a prefabricated UiO-66 membrane. These composite membranes demonstrated excellent H2 permeability as well as a highly enhanced H2/CO2 selectivity, far surpassing that of the parent UiO-66 membrane54. Additionally, layer-by-layer synthesis of COF-300/silica composites was recently demonstrated to afford particles with potential utility as a chromatographic stationary phase55. Yaghi and coworkers also reported COF-320, essentially an extended version of COF-300 constructed from a biphenyl dialdehyde linker, and determined its single-crystal structure using 3D rotation electron diffraction (Fig. 4c)56. COF-320 was later utilized for the encapsulation of a common ionic liquid, 1-ethyl-3-methylimidazolium bis(trifluoromethylsulfonyl)imide, in its pores57.
Since the first report on COF-300, TAPM has been utilized as the tetrahedral amine building block of choice for a range of new imine-linked 3D COF structures. The first instance of a dynamic 3D COF, LZU-301, was synthesized from condensation of TAPM with (3,3′-bipyridine)-6,6′-dicarbaldehyde (Fig. 4d). As the bipyridine analog of COF-320, LZU-301 exhibits symmetry breaking and lattice expansion upon tetrahydrofuran (THF) solvation, which the authors attributed to the conformation change of the –C = N– bond, serving as a ‘‘molecular pedal’’ in the crystal structure58. Lin et al.59 synthesized a pyrene-based 3D COF by condensing TAPM with 1,3,6,8-tetrakis(4-formylphenyl)pyrene (Fig. 4e), resulting in a novel structure that featured selective adsorption of CO2 over N2 and emitted yellow-green luminescence, marking the first report of a fluorescent 3D COF. Two porphyrin-based 3D COFs, 3D-Por-COF and 3D-CuPor-COF, were synthesized from the condensation of TAPM with porphyrin-based tetraaldehydes (Fig. 4f), and exhibited photocatalytic activity towards the generation of highly reactive singlet oxygen under visible light irradiation60. A 3D chiral COF, CCOF-5, was synthesized by condensation of TAPM with a chiral tetraaldehyde, which subsequently underwent imine oxidation to afford an amide-linked framework, CCOF-6, that retained the crystallinity and permanent porosity of the parent COF (Fig. 4g). Although both CCOF-5 and CCOF-6 could be used as chiral stationary phases (CSP) for high performance liquid chromatography (HPLC), CCOF-6 exhibited superior resolution performance in addition to improved acid and base stability compared to CCOF-561.
An alternative tetrahedral amine commonly used for 3D COF synthesis is 1,3,5,7-tetraaminoadamantane (TAA). Li et al.62 co-condensed TAA with the heterobifunctional 4-formylphenylboronic acid and its fluorinated derivative to obtain DL-COF-1 and DL-COF-2, respectively (Fig. 5a), the first 3D COFs to feature dual linkages (imine and boroxine). The bifunctional catalytic capabilities of these two COFs was then demonstrated through acid-base catalyzed one-pot cascade reactions utilizing acidic sites supplied by the boroxine ring and basic sites from the imine bond. While the hydrolytic and oxidative stability of the imine linkage is higher compared to B–O linkages found in earlier 3D COFs, they can be further improved by enol-keto tautomerization without affecting the COF structure. This was demonstrated by the Yan group, who reported the first instance of a 3D β-ketoenamine COF, BF-COF-2, in addition to the imine-linked BF-COF-1 (Fig. 5b–c). These COFs were strongly alkaline owing to the high pKa of the alkyl amine building blocks (TAA) employed, and the excellent catalytic activity and size selectivity of these COFs for the Knoevenagel condensation reaction was shown63. Recently, an alternative adamantane-based tetrahedral amine, 1,3,5,7-tetrakis(4-aminophenyl)-adamantane (TAPA), was employed for 3D COF synthesis, undergoing reaction with terephthalaldehyde to form COF-DL229 (Fig. 5d). In comparison with COF-300, COF-DL229 possesses higher BET surface area (1762 m2/g vs. 1360 m2/g) owing to the more extended radiating arms of TAPA compared with TAPM. Additionally, COF-DL229 achieved an exceptional iodine uptake capacity of 82.4 wt% in iodine vapor adsorption experiments while simultaneously exhibiting retentiveness and quick release capabilities. The authors also noted that the exclusively organic skeleton of COFs in general are ‘‘soft’’, and observed reduced crystallinity and iodine uptake in recycled COF-DL229, attributed to local structural deformation to fit solid iodine within the pores upon adsorption31.
Utilizing imine chemistry, Yaghi’s group fabricated the first woven COF, COF-505, by employing an aldehyde-functionalized derivative of the copper bis-phenanthroline complex (Fig. 6a). They weaved helical organic threads that complexed to Cu(I) ions as points of registry, and demonstrated that the structure and topology of COF-505 was retained through demetalation and remetalation, although the demetalated COF-505 did exhibit reduced crystallinity64. This work was followed by the synthesis of woven COF-112 from a homogeneous solution, utilizing the gradual in situ deprotection of tert-butyloxycarbonyl-protected amines (N-Boc) to facilitate the formation of nuclei directly from solution and direct growth into crystalline frameworks and avoid precipitation of amorphous insoluble intermediates, while conventional heterogeneous one-pot synthesis resulted in only amorphous materials (Fig. 6b). Synthesis of a prototype 2D imine COF, LZU-1, utilizing the same protected amine species under rapid microwave heating resulted in nanocrystals with a surface area (729 m2/g) more than 1.5 times that of the original report (457 m2/g), and the fabrication of LZU-1 thin films on silicon substrates was also demonstrated through homogeneous synthesis65. An imine-linked 3D COF based on β-cyclodextrin (β-CD-COF) was also synthesized (Fig. 3b)66.
Recently, Guan et al.67 demonstrated the fast ionothermal synthesis of 3D COFs under ambient temperature and pressure, synthesizing three 3D ionic liquid-containing COFs (3D-IL-COFs) from tetrakis(4-formylphenyl)methane (TFPM) and diamines instead of the more prevalent tetraamine and dialdehyde combination (Fig. 7). By utilizing the ionic liquid 1-butyl-3-methylimidazolium bis((trifluoromethyl)sulfonyl)imide as both solvent and catalyst for the imine formation reaction, the authors were able to synthesize crystalline solids at ambient temperature and pressure within 12 h, significantly faster than the 3–7 days required for the conventional solvothermal method. The ionic liquid can be reused without activity loss, and the 3D-IL-COFs were determined to contain 8–12% ionic liquid in their pores, which contributed to the high adsorption selectivity for CO2/N2 and CO2/CH4. This works presents an exciting new stage in 3D COF synthesis, and will be discussed in greater detail in the Perspective section below.
In addition to the B–O and imine linkages, a handful of other linkages have also been utilized for constructing 3D COFs (Fig. 8). Beaudoin et al.68 reported COFs constructed using reversible self-addition polymerizations of nitroso groups to form trans-azodioxy linkages, resulting in covalent nitroso polymer networks NPN-1, NPN-2, and NPN-3 (Fig. 8a). Ren et al.69reported the first 3D covalent triazine framework (CTF), a class of porous polymers related to COFs, which exhibited reasonable BET surface area (1152 m2/g) but was not crystalline (Fig. 8b). The Yan group synthesized two polyimide COFs, PI-COF-4 and PI-COF-5, by condensation of TAA and TAPM with pyromellitic dianhydride (Fig. 8c). These PI-COFs possessed high BET surface area (2430 m2/g for PI-COF-4 and 1876 m2/g for PI-COF-5) and pore widths (13 and 10 Å, respectively) and were thus examined for controlled drug delivery. The authors found that in vitro release rate of drugs in COFs was directly related to pore size and geometry, and that the two drug-loaded PI-COFs exhibited good release control, achieving ca. 95% release of initial loading after about 6 days, compared to the typical 2-h biological half-life. This marked the first time COFs were utilized for drug delivery70. Yahiaoui et al.71 recently reported the first synthesis of a three-coordinated anionic 3D COF, based on novel reversible Si–O chemistry and resulting in a topology that had not been previously reported for 3D COFs (Fig. 8d). This work also marked the first instance of a 3D COF that did not require tetrahedral building blocks. Several other linkages, including hydrazones, azines, and imides, have been utilized for the synthesis of 2D COFs, but have yet to be explored for 3D COFs50.
Post-synthetic modification of 3D COFs
The organic nature of COFs affords facile chemical tunability, leading to immense structural and functional diversity compared to their inorganic counterparts. As such, modification and functionalization of the COF structure becomes a crucial step towards tailored applications. Excluding the use of different monomers or alternative linkages, post-synthetic modification (PSM) is the most common approach to COF functionalization. A common PSM method is embedding reactive functionalities into constituent monomers and applying subsequent chemistry to those groups upon completion of the initial COF synthesis. Using this approach, Dichtel and coworkers carried out a series of interior functionalization studies on COF-102. Utilizing a monomer-truncation strategy, they co-condensed the tetrahedral boronic acid building block of COF-102 with a truncated version in which one of the four arylboronic acid groups was replaced with a dodecyl or allyl group, obtaining internally functionalized COF structures with the truncated moieties distributed throughout the material that retains the crystallinity and high surface area of COF-102 (Fig. 9a)72. The introduced allyl group was subject to post-synthetic functionalization using thiol–ene chemistry, achieving full conversion of the allyl group while retaining crystallinity and permanent porosity (Fig. 9b)73.
Dichtel and coworkers74 also explored the functionalization of COF-102 utilizing the monofunctional tolylboronic acid instead of the trigonal truncated monomers of the previous studies (Fig. 9c), and found that COF-102-tolyl crystallized even in the presence of up to 36 equivalents of tolylboronic acid relative to the tetra-boronic acid and demonstrated incorporation of up to 36 mol% of tolylboronic acid into the framework while maintaining crystallinity and porosity, which the authors postulated as a fundamental limit for the COF-102 structure. Similarly, Lu et. al75 demonstrated the synthesis of a carboxylated, imine-linked 3D-COOH-COF by performing PSM on a 3D hydroxy-functionalized COF (Fig. 9d). An alternative PSM technique for imine-linked COFs is the direct modification of the imine bond. For example, Han et al.61 converted their imine-linked 3D COF CCOF-5 into an amide-linked CCOF-6 by oxidation of the imine bonds, achieving enhanced chemical stability compared to its predecessor (Fig. 4g). Reversible enol-keto tautomerization has also been shown by the Yan group in the conversion between BF-COF-1 and BF-COF-2 (Fig. 5c)63.
A number of other chemistries have been employed for PSM of 2D COFs, including copper(I)-catalyzed azide-alkyne cycloaddition76,77, acylation of phenol groups44, and the ring-opening of succinic anhydride with phenol groups to form carboxylic acids78; these chemistries are wholly transferrable to 3D COFs. Some alternative PSM techniques have also been implemented in 2D COFs. For example, Chen et al.79 highlighted the ability to lock 2D COF networks with hydrogen bonds by introducing hydroxy groups into the terephthalaldehyde linker, which subsequently form hydrogen bonds with imine-centered nitrogen atoms. Structural modification of COFs has also been achieved through induction of cis-trans isomerization to facilitate a reversible conformation change. Zhang et al.80 demonstrated this concept utilizing the trans-cis photoisomerization of azobenzene, using an azobenzene diboronic acid to produce a boronate ester-linked 2D Azo-COF that underwent photoisomerization under 365 nm UV irradiation. The dynamic behavior of the 3D LZU-301, highlighted in the previous section, can be similarly attributed to an imine bond conformation change58. An important consideration for applying PSM to 3D COFs is the reaction site accessibility within the pores. Modification of internal structure of 3D frameworks requires ready access of reactant species to internal functionalization sites, which may impose additional barriers for the translation of 2D COF PSM techniques to their 3D counterparts. In contrast, PSM techniques developed for 3D MOFs, such as the introduction of polymerizable methacrylamide functionalities into MOF UiO-6616 or the removal of photolabile o-nitrobenzyl pendant groups81, could be more readily implemented in 3D COFs.
Challenges in 3D COF development
Disparity between 2D and 3D frameworks
Although there have been notable advances in the field of 3D COFs, progress persistently lags behind that of 2D COFs. For example, several dynamic covalent linkages that have been employed for synthesizing 2D COFs, such as hydrazones and azines, have yet to see similar utilization for 3D COFs50. Moreover, compared to the more abundant and systematic studies on the synthesis, modification, and application of 2D COFs, the current research in 3D COFs revolves around the synthesis and characterization of novel structures and preliminary applications that arise from the unique traits of each structure.
Addressing the crystallization problem
A major factor behind this COF development disparity is the so-called ‘‘crystallization problem’’, originating from the inherent conflict between the use of robust covalent bonds to form stable crystalline frameworks, which necessitates the formation of reversible or rearrangeable linkages to facilitate error-correction, and the tendency of covalent bonds to form irreversible interactions82. Even in these dynamic covalent bond-forming reactions, the kinetic trapping of amorphous networks often occurs owing to the bulkiness and rigidity of the monomeric precursors impeding proximity between reactive groups, precluding further network rearrangement into the desired crystalline framework. Indeed, in contrast to 2D COFs where reaction sites are readily accessed and van der Waals interactions from π-orbital overlap provide additional driving force outside of covalent bonds towards the stacked layer structure, the synthesis of 3D COFs relies solely on inaccessible covalent interactions for the rearrangement of its rigid building blocks61. Nevertheless, as the synthesis of contemporary 3D COFs have relied primarily on boronic acid and imine condensation reactions, the formation of stoichiometric quantities of water provides a convenient factor in the mediation of the reaction equilibrium, which can be accomplished by using water immiscible solvents or controlling reactor pressure82.
To date, the synthesis of 3D COFs has primarily been performed under heating, commonly at 120 °C but even at temperatures of up to 160 °C70, either via the predominant solvothermal approach for extended periods or under rapid microwave heating, providing additional energy for covalent bond rearrangement as well as the necessary mobility for the COF building blocks to achieve the desired connectivity. This is essentially a ‘‘brute force’’ method to overcome the crystallization problem, and these reaction conditions impose limitations on the utility of 3D COFs. Reactions that proceed over multiple days may be too slow for industrial relevance, and heating to high temperatures reduces functional group compatibility and precludes certain applications such as the encapsulation of folded biomacromolecules. The development of milder conditions capable of rapidly yielding crystalline materials will be key to unlocking the potential of 3D COFs for a broader range of applications, and researchers have just begun to explore various means of overcoming the crystallization problem outside extended heating.
In the case of imine-linked COFs, a mechanistic study of the 2D TAPB-PDA COF has revealed that the amine and aldehyde monomers very quickly precipitate into amorphous networks, which then slowly rearrange into crystalline networks after extended heating, demonstrating imine exchange as the rate limiting step in COF formation83. An acid catalyst, commonly acetic acid, is often employed to promote imine formation and exchange19; however, acetic acid is a relatively inefficient catalyst for transamination84. Lewis acidic rare earth metal triflates are promising alternative catalysts owing to their effectiveness in mediating imine exchange reactions, tolerance of both aqueous and organic environments, and functional group compatibility84. These metal triflates, particularly scandium triflate (Sc(OTf)3), have recently been shown to catalyze the formation of crystalline 2D imine-linked COFs at room temperature in as little as 10 min while yielding improved material properties such as BET surface area (2175 m2/g vs. <1000 m2/g from the solvothermal method)84. Although similar studies have yet to be described for 3D COFs, the utilization of improved catalysts, such as metal triflates, for network rearrangement is a promising approach towards milder reaction conditions. Of course, the reduced driving force for 3D COF network formation suggests that the directly applicability of conditions identified for the 2D TAPB-PDA COF (2% Sc(OTf)3 loading, 10 min at room temperature)84 is unlikely, and some combination of elevated temperature, extended reaction duration, and higher catalyst loading may be required to induce formation of a crystalline, imine-based 3D network. Interestingly, whereas low rare earth metal triflate concentrations catalyze imine rearrangement reactions, at raised concentrations these compounds no longer act catalytically and instead affect the reaction equilibrium to favor the precursor reactants85, an attribute likely to find synthetic utility in mediating framework crystallinity and post-synthetic modification.
Notably, the room temperature synthesis of 3D COFs has recently been demonstrated. Guan et al.67 used an ionic liquid as both solvent and catalyst to obtain highly crystalline, imine-linked 3D COFs in as little as three minutes at ambient temperature and pressure. Although this ionothermal approach holds promise, several aspects of this approach remain subject to optimization. The 3D-IL-COFs synthesized in this study contained 8–12% ionic liquid in their pores, potentially contributing to their relatively low internal surface areas. For example, 3D-IL-COF-1 exhibited a BET surface area of 517 m2/g67, whereas COF-300, whose structure differed from 3D-IL-COF-1 only by the directionality of the imine bonds, offered a BET surface area of 1360 m2/g51, suggesting that this ionothermal synthetic approach may compromise the internal surface area of 3D COFs, one of their most important characteristics. Moreover, applications of 3D COFs invariably revolve around host-guest interactions within the pores, and the apparent retention of ILs presents an additional complication in the compatibility of the guest species. Finally, the applicability of this approach to generic imine-based frameworks still needs to be demonstrated. Whereas the three 3D-IL-COFs synthesized in this paper possessed similar structures, differing only by the number of phenyl rings in the linear diamine linker67, further investigation is necessary to determine the breadth of ionothermal synthesis utility. In a separate study, Ma et al. also demonstrated the ability to synthesize single crystalline COF-300 at room temperature by utilizing aniline as a nucleation inhibitor and extending the reaction duration to 30–40 days, and elucidated greater insight into the COF structure through single-crystal analysis53. Unfortunately, the extended reaction times required by this strategy would likely curtail adoption of the resultant 3D COFs for industrial applications.
The lack of control over the rapid precipitation of amorphous intermediates during COF synthesis can lead to kinetic trapping of said intermediates, preventing the rearrangement necessary to form a crystalline structure. Limiting the concentration of available monomers in the reaction through controlled addition of reactants or through in situ deprotection or generation of reactant species can contribute to reaction rate control, mediating the rate of crystal nucleation and growth, and ultimately overcoming kinetic trapping. The Dichtel group reported the successful growth of the first discrete colloidal 2D boronate ester-linked COF-5 particles via gradual monomer addition, whereas faster addition led predominantly to the formation of new particles with smaller crystalline domains86. Similarly, Yuan et al.87 demonstrated the use of heterogeneous SiO2 seeds coated with a thin layer of amorphous Schiff-base polymer from which the imine-linked 2D COF-LZU-1 network was grown, suppressing the rapid precipitation of amorphous materials and promoting crystallization. The frameworks were obtained in significantly shorter time frame than conventional solvothermal methods and exhibited high crystallinity and surface area after the SiO2 particles were etched away. Additionally, interfacial crystallization, multiple demonstrations of which have been reported for 2D COFs88,89, may be applicable to 3D COFs. For example, Li et al.90 demonstrated a novel approach to yield high-quality 2D COF nanosheets at the interface of two miscible organic solvents, each of which contained one of the two constituent monomers in solution, by adding a low density solvent interlayer as a buffer between the two main solvent layers. Alternatively, in situ deprotection can also control monomer release rate and precipitation, an approach that even enables the use of precursor monomers bearing multiple, covalently coreactive functional group types. In situ deprotection of catechol was previously reported for the incorporation of insoluble and unstable building blocks in boronate ester COF synthesis91, and in situ deprotection of certain reactant functional groups can curtail the condensation reaction rate and hence mediate the rate of precipitation to avoid kinetic trapping92. Yaghi’s group recently applied this concept to woven 3D COFs, employing in situ deprotection of Boc-protected amine monomers to slow down the initial imine condensation and synthesize the woven COF-112 homogeneously without the precipitation of amorphous intermediates, using trifluoroacetic acid (TFA) as a dual-role catalyst. This approach also afforded greater control over COF morphology, allowing the synthesis of uniform nanocrystals and thin films based on 2D imine-linked COF LZU-165. Similarly, Yahiaoui et al.71 utilized the in situ generation of silicon source tetramethoxysilane (TMOS) by gradual disproportionation of methyltrimethoxysilane to synthesize SiCOF-5, while direct condensation of constituent monomers HHTP and TMOS did not yield a crystalline framework. Establishing more precise control over the monomer availability in the reaction system, either through slow addition, heterogeneous nucleation, or in situ deprotection or generation of constituent species, will likely prove indispensable to circumvent kinetic trapping for a broad range of 3D COF syntheses.
Deficient systematic understanding
Another notable issue that has plagued the COF community is the fragmentary understanding of both their inherent structure and the contributions of COF synthetic conditions, particularly for 3D COFs. To date, most 3D COF synthetic efforts have yielded amorphous or polycrystalline products, and their crystalline morphologies have been determined by PXRD; however, elucidation of the precise structure, including atomic positions, interpenetration, and pore guest arrangement, has proven challenging. This dilemma may be resolved by the construction of single crystals of 3D COFs, enabling a more definitive understanding of their structure via SCXRD53. Beaudoin et al.68 synthesized monocrystalline COFs by utilizing reversible, self-addition polymerization of tetrahedral nitroso compounds to afford diamondoid azodioxy networks which were then subject to SCXRD characterization, enabling elucidation of the location and bonding of essentially every atom. Ma et al.53 further demonstrated the characterization utility of single crystalline COFs by employing single crystals of COF-300 to resolve prior ambiguity regarding their degree of interpenetration as well as structural distortion upon hydration. These reports represent an important direction in the field of 3D COFs, and continued emphasis on single crystalline 3D COF synthesis will enable definitive resolution of their structures.
The influence of 3D COF synthetic conditions remains poorly understood. Duncan et al.19 conducted a study on the kinetic and thermodynamic factors in imine-linked 3D COF synthesis, and found that acetic acid is a crucial component of the reaction, acting as both a catalyst and a co-solvent. In addition, they evaluated the suitability of a range of organic solvents for synthesis and reported that dimethylformamide and THF were the most suitable solvents for obtaining highly cross-linked materials, although the polymer networks they obtained remained amorphous19. Dichtel’s mechanistic study of the crystallization process of 2D imine-linked COFs provided the first real insight into the synthetic process, and successfully elucidated the mechanism of rapid amorphous precipitation followed by gradual rearrangement into crystalline structures. In addition, the crucial role of acetic acid and water in inducing crystallinity and maintaining high yields was shown83. Li et al.93 used a kinetic Monte Carlo model to describe the nucleation and growth of 2D COF-5 from solution which agrees with experimentally measured growth kinetics and showed that nucleation and growth processes could be described by the same model, which could lead to informed 2D COF syntheses and improved control over nucleation and growth. Similar insight into 3D COF synthesis would offer improved understanding and control of the crystallization process.
Other than the aforementioned reaction conditions, additional factors affecting the synthesis of 3D COFs need further elucidation. For example, whereas COF-300 is typically synthesized from a suspension of starting materials, homogeneous starting conditions were reported to yield the best results in a boronate ester 3D COF synthesis24,51. A controlled variable study comparing 3D COF synthesis from a suspension or homogeneous solution would inform the influence of these initial conditions. Additionally, COF-300 synthesis has required freeze-pump-thaw degassing and subsequent reaction vessel flame sealing prior to heating51, where raised pressure through sealing the reaction vessel has been touted as key to obtaining a crystalline solid82. This methodology has been universally adopted for 3D COFs synthesized by the solvothermal method; however, overpressure has proven unnecessary for the synthesis of COFs containing B–O linkages, as an open reaction vessel with a reflux condenser attached for collecting water achieved similar results as a sealed reaction vessel in microwave synthesis45. Since water plays a similar role in mediating the reaction equilibrium in both boronic acid condensation and imine condensation, one might conclude that a sealed reaction vessel serves as a convenient method for retaining water in the system, but it is not the only way of doing so. Even if the use of a sealed reaction vessel is desired, degassing is potentially unnecessary. Again, controlled variable experiments comparing 3D COF synthesis from a degassed and pressurized versus simply a sealed reaction system, are required to assess this hypothesis, and if confirmed these findings can contribute to simplification of the established 3D COF synthetic process.
Limited topologies and building blocks
A second reason behind the disparity of studies on 2D and 3D COFs is the limited variety of available molecular building blocks and consequent network topologies59,71. Compared to 2D COFs, which can be constructed from a variety of ditopic and tritopic linkers, 3D COFs have, with the recent exception of the three-coordinated SiCOF-5 with srs topology, utilized tetrahedral building blocks and adopted a topology belonging to one of five nets (dia, bor, ctn, rra, or pts)49,59,71. The chemical diversity of these building blocks is similarly limited, as many 3D COFs based on B–O linkages have been synthesized from tetra(4-dihydroxyborylphenyl)methane, and the majority of imine-linked 3D COFs employed TAPM and TAA as precursors82.
From a geometry perspective, tetrahedral nodes are the most direct method of sustaining an infinite 3D cross-linked network. Though employing a non-planar tritopic linker would also result in a non-planar structure, growth in the z-direction may be finite and would not necessarily assemble into a true 3D framework. Employing higher functionality linkers would conceivably yield 3D frameworks with higher degrees of cross-linking; however, limited functional group accessibility, steric hindrance, and kinetic trapping, which, as discussed earlier, are already present when utilizing tetratopic linkers, would become increasingly prevalent and further impede the synthetic accessibility of crystalline structures. As such, tetratopic linkers are ubiquitously employed as the most straightforward way to sustain an infinite 3D cross-linked network around a tetrahedral node, while avoiding increased steric hindrance and kinetic trapping from monomers with higher order functionalities. This limit in topology and building block diversity has limited the number of attainable 3D COF structures, and novel building block structures must be discovered in addition to employing different linkages and COF structure modifications to access increased compositional and structural complexity.
Controlling network interpenetration
Interpenetration, where the empty space described by the crystalline framework accommodates one or more additional networks94 and which can adversely affect pore volume and impact internal surface area95, is another aspect of 3D COFs that requires improved understanding and synthetic control. Whereas interpenetration in 3D COFs has typically been determined by structural modeling and unit-cell indexing and is reported as an inherent characteristic, efforts to better understand, characterize, and even modify degrees of interpenetration have been recently reported. For example, the synthesis of an interpenetration isomer was reported for COF-300, representing a preliminary attempt towards modifying the extent of interpenetration in a 3D COF52. More sophisticated approaches to control COF interpenetration might be derived from techniques successfully implemented in MOF syntheses, such as temperature and monomer concentration control96, organic bond structure alteration95, rational design of organic building blocks97, and incorporation of space-filling, photolabile protecting groups that could be post-synthetically cleaved81. These techniques inform the potential for reducing or preventing interpenetration in 3D COFs and could conceivably be translated to 3D COF synthetic approaches to fully realize their potential as crystalline, controllably porous materials.
Covalent organic frameworks are an extremely promising class of nanoporous material, and 3D COFs, possessing notably higher internal surface area than their 2D counterparts, hold significant appeal for applications including gas storage, gas separation, and catalysis. Unfortunately, 3D COFs suffer from poor synthetic accessibility owing to kinetic trapping, a deficiency in systematic understanding of their syntheses, and limited topologies and building blocks. Kinetic trapping of amorphous networks, or the crystallization problem, presents a significant obstacle in obtaining crystalline 3D frameworks. Nevertheless, the development of more effective catalysts for connectivity rearrangement and enhanced control over the rate of precipitation via nucleation inhibition or gradual introduction of monomer species via controlled addition, in situ deprotection, or interfacial polymerization, hold promise for overcoming the crystallization problem. Improved systematic understanding of the COF synthesis reaction would allow for more precise control over the structures and pursuing further synthesis and characterization of single crystals of a wider variety of COFs and systematic investigation of various reaction parameters should be a primary focus. Moreover, diversifying the limited topologies and building blocks and establishing control over network interpenetration would enable the realization of the full potential of 3D COFs as controllable and easily tunable porous materials. We anticipate that these insights can provide guidance and inform future research efforts in advancing the 3D COF field.
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We acknowledge support from the National Science Foundation (NSF) under Award # 1462267. X.J.M. acknowledges Rackham Graduate Student Research Grant support from the University of Michigan.
The authors declare no competing interests.
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Ma, X., Scott, T.F. Approaches and challenges in the synthesis of three-dimensional covalent-organic frameworks. Commun Chem 1, 98 (2018). https://doi.org/10.1038/s42004-018-0098-8
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