Qi
Zhang
a,
Martin A.
Screen
b,
Leon
Bowen
c,
Yisheng
Xu
a,
Xiangyang
Zhang
*a and
Jonathan W.
Steed
*b
aState Key Laboratory of Chemical Engineering, East China University of Science and Technology, Shanghai, 200237, China. E-mail: zxydcom@ecust.edu.cn; jon.steed@durham.ac.uk
bDepartment of Chemistry, Durham University, Durham, DH1 3LE, UK
cDepartment of Physics, Durham University, Durham, DH1 3LE, UK
First published on 24th March 2025
A graphene-based supramolecular gel was designed and prepared to control the crystallization process and polymorphism of pharmaceuticals. The gelators were modified at the end segments with pyrene moieties, which spontaneously interact with the graphene surface by aromatic stacking interaction resulting in a graphene-incorporated supramolecular gel linked by noncovalent interactions between urea groups. When graphene was included into the gel, the critical gel concentration and system rigidity changed significantly, fluorescence spectroscopy determined the close π–π stacking interaction between the gelator and graphene, and the material was confirmed as a true nanocomposite gel system by electron microscopy. Further the graphene was oxidatively modified to obtain hydroxylated graphene (Gr–OH), which was successfully incorporated into the gel system to serve as a medium for pharmaceutical crystallization. Glycine (GLY), caffeine (CAF) and aripiprazole (APZ) were selected as model drugs for gel surface crystallization and gel phase crystallization by Gr–OH hybrid gels. Incorporation of Gr–OH in the gel allowed close interaction by hydrogen bonding with drug molecules, resulting in different polymorphs of GLY, CAF and APZ compared to solution crystallization and shorter induction time of CAF compared to the native gel.
Graphene (Gr), is a well-known two-dimensional nanomaterial,15 and its surface properties are easily modified by etching and covalent functionalization,16,17 making it a promising substrate for crystallization control.6 Initially used as a template for the preparation of inorganic materials and polymers,18,19 graphene has recently begun to be used for the crystallization of organics and pharmaceuticals.20,21 Specific intermolecular interactions can be identified by the surface chemistry of graphene to induce particular polymorphs of APIs by additive-templated and substrate-templated crystallization methods.22 However, the low dispersion concentration of graphene in solution and the interface between solid and liquid may prevent it from interacting closely enough with drug molecules, limiting its effect on the crystallization process. Incorporation of graphene within a gel medium offers a potential approach to increasing graphene effective concentration and enhancing its influence through nanoconfinement within the gel matrix.
Supramolecular gels are viscoelastic materials that can act as effective crystallization media.23,24 A series of gelators have been developed for the crystallization of various APIs,25 such as carbamazepine,9,26–29 ROY,29,30 sulfathiazole,31,32 thalidomide,33 metronidazole,34 and mexiletine hydrochloride,35 in which the solvent trapped in the gel network can act as a confined crystallization medium to control the specific nucleation and growth process of drug molecules within the gel.8,36 In addition, the supramolecular gel network structure can provide porous pockets to accommodate various nanomaterial hosts by physical hybridization,37–40 and some gelators can interact chemically with nanomaterial to form the incorporated gel system.41–43 Therefore, it should be possible to incorporate graphene into the gel as a soft template for crystallization control, allowing sufficiently close interaction between the graphene surface and drug molecules.
In this work, two gelators containing pyrenyl moieties were synthesized (Scheme 1), of which gelator 2 proved to be an effective gelator and was chosen for subsequent studies. Graphene was successfully incorporated into the gel system through π–π stacking with the pyrenyl groups. To achieve stronger interaction with the API and hence influence the API crystallization outcome, the graphene was further functionalized by hydroxylation (Gr–OH), which also facilitated incorporation into the gel. Finally, the Gr–OH gel was used to explore the effect on polymorphism and nucleation behavior of glycine (GLY), caffeine (CAF), and aripiprazole (APZ) by gel surface crystallization and gel phase crystallization.
Gel screening was carried out for both gelators. Despite many solvent candidates, the gelators showed solubility and gelation in only a few solvents due to the presence of pyrene groups which give rise to relatively low solubility (Table 1). Gelator 1 is less soluble than 2, and gelation occurred only in benzyl alcohol and dimethyl sulfoxide (DMSO). Gelator 2 demonstrated excellent gelation ability, forming gels at low critical gel concentration (CGC). Fig. 1a shows the gel formation of 2 in 1,2-dichlorobenzene, DMSO, 1,2,4-trichlorobenzene and benzyl alcohol at the CGC values of 0.6, 0.85, 1.0, and 1.5% w/v, respectively. Considering the incorporation of graphene into the gel and its application in drug crystallization, we selected the gels formed by 2 in DMSO for further studies, since 1,2-dichlorobenzene requires heating to its boiling point (about 150 °C) before significant dissolution of 2 occurs. Moreover, most APIs are soluble in DMSO.
Morphologies of the DMSO xerogel of 2 were characterized by scanning electron microscopy (SEM) and transmission electron microscopy (TEM). SEM images reveal the entangled nanofibrillar structure of the gel, and these gel fibers are highly cross-linked, shown in Fig. 1b. TEM images show the width of the fibers as 30–360 nm and the length of each fiber as more than 1 μm, shown in Fig. 1c. The width of the gel fiber is much higher than the molecular size of a gelator, suggesting that multiple molecular chains self-assemble to form supramolecular fibers, possibly via a scrolling mechanism.44,45 The formation of entangled fibers demonstrates that the pyrene-containing gelators form the supramolecular gel network as cross-linked aggregates.
Considering the fluorescent nature of pyrene moiety, the interaction of gelator molecules in solution, native and graphene gels in DMSO was compared by fluorescence spectroscopy, shown in Fig. 2b. In solution, the gelator molecule shows the emission peaks at 378, 397 and 418 nm, which is a typical fluorescence pattern of pyrene arising from the non-aggregated pyrene-containing gelator.47 In native gel, the gelator experiences a self-assembly process and exhibits a strong excimer emission peak centered at 490 nm, indicating that pyrene groups of these gelator are dimerized in the gel state. The significant redshift of emission peak of native gel compared to the solution is attributed to the presence of strong π–π stacking interactions between the gelators.48 In graphene gel, the excimer peak is drastically quenched (7-fold reduction in intensity) compared to the native gel, proving that graphene is intercalated between the pyrene groups of gelators in supramolecular self-assembly by aromatic stacking interaction.41,49 The fluorescence quenching is also observed by exposing native and graphene gels to UV light. Such close interaction between graphene and pyrene groups is believed to facilitate the gelator molecule aggregation and further promote the supramolecular assembly and gelation, which explains the initial decrease in CGC of the gel with increasing graphene content.43
Rheology studies were performed to compare the rigidity and flow properties of native and graphene gels. Fig. 2c shows the variation of storage modulus (G′) and loss modulus (G′′) with constant strain at room temperature in frequency sweep experiments for native gel at a concentration 1.5% w/v and graphene gel containing 1.5% w/v gelator and 50 μg mL−1 graphene. For both native and graphene gels, the elastic behavior of the system dominates, with G′ being an order of magnitude larger than G′′, indicating a soft “solid-like” gel material. Interestingly, the incorporation of graphene increases the G′ of the hybrid gel by about 5-fold compared to that of the native gel, suggesting that the graphene-containing gel is more rigid than the native gel. The difference of the two moduli (ΔG = G′ − G′′) at frequency 0.63 rad s−1 shows a higher ΔG value for the graphene gel (2390.5 pa) than the native gel (439.1 pa), demonstrating that the elastic behavior dominates over the viscous behavior in the graphene hybrid gel.
Electron microscopy of the graphene-gel composites gives direct evidence of the intimate incorporation of graphene into the gel. SEM images show the presence of graphene nanosheets and entangled gel nanofibers in the graphene hybrid gels, with the graphene nanosheets included into the gel network. The attached gel fibers are observed on the surface of some graphene sheets, suggesting a close interaction between the gel fibers and graphene (Fig. 2c). TEM images show graphene nanosheets with a honeycomb lattice structure and black graphene flakes with a size of 1.5 μm incorporated in cross-linked gel nanofibers, further confirming that the graphene hybrid gel is a true nanocomposite system (Fig. 2d). The hexagonal lattice size of honeycomb graphene is about 20 nm, much larger than the lattice constant of 0.246 nm for single-layer graphene, which is due to the Moiré superlattice effect caused by the misaligned stacking of multilayer graphene.50,51 Besides, the width of nanofibers in graphene gel is 20–350 nm, which is similar to the size of native gel fibers.
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Fig. 3 (a) FTIR spectra of graphene and Gr–OH; (b) CGC variation of gels at different Gr–OH contents and photo of Gr–OH gel at the minimum CGC; (c) TEM images of the Gr–OH gel in DMSO. |
The properties of Gr–OH gels of 2 were characterized by CGC measurements and TEM, which indicated the incorporation of Gr–OH into the DMSO gel. Fig. 3b shows that the CGC of Gr–OH gel decreases and then increases with the increase of Gr–OH content, which is consistent with the CGC trend observed for the unfunctionalized graphene gel (Fig. 2a). The CGC of Gr–OH gel varies more gradually compared to the graphene gel, which reaches a minimum CGC of 0.56% w/v at a Gr–OH content of 1500 μg mL−1. After the minimum CGC, the CGC of Gr–OH gel begins to increase, indicating that more gelator is needed to interact with Gr–OH for effective gelation. TEM images display direct evidence of Gr–OH incorporation into the gel and interacting with the gelator (Fig. 3c). The hybrid gel reveals the presence of both cross-linked gel nanofibers and black Gr–OH nanosheets. The Gr–OH nanosheets attach to the surface of the entangled fibers rather than lodge in the porous pockets of the gel network, indicating that the Gr–OH nanosheets have close interaction with the gel nanofibers within the nanocomposite system.
The width of fibers in the Gr–OH gel is 25–340 nm, which is almost the same fiber size as the native and graphene gels, meaning that the incorporation of Gr–OH does not significantly change the network structure of the gel. Gr–OH is prepared by mechanical milling (see Section 2.4 of ESI†) with a size of 30–75 nm, therefore its size is much smaller than the graphene sheet, but it is still considered to serve as a heterogeneous nucleation site for drug crystallization.5,52 The above characterization also confirms that the designed pyrene-containing supramolecular gel can universally and easily incorporate various types of graphene into the gel system.
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Fig. 4 Schematic of crystallization methods of (a) gel surface crystallization and (b) gel phase crystallization; (c) three drug systems for gel crystallization. |
GLY is insoluble in DMSO, so an undersaturated aqueous solution of GLY was added dropwise to the surfaces of native and Gr–OH gels, respectively. At room temperature, as the water slowly diffuses into the DMSO, GLY crystallize at the interface of the gel and the solution with a low supersaturation degree, shown in Fig. 5a. The GLY crystals obtained on the native gel surface are Form α, while mixed polymorphs of Forms α and β are obtained on the Gr–OH gel surface, as identified by PXRD in Fig. 5b. Although experimenting with different drop volumes of GLY solution and Gr–OH contents in the gel, pure crystals of Form β were not obtained on the Gr–OH gel surface (see Table S1 of ESI†). This might be because Form β is the most unstable polymorph of GLY and readily transforms to Form α at room temperature.54,55 In addition, Fig. 5b shows the PXRD patterns of GLY crystallized from solution under the same conditions as a control. Form α is obtained from DMSO–H2O solution by cooling crystallization and a mixture of Forms α and β are obtained by adding GLY aqueous solution into DMSO for anti-solvent crystallization, suggesting that Form β generally occurs at high supersaturation in solution crystallization (see Tables S2 and S3 for ESI†). Previous work has reported the failure to obtain Form β at low supersaturation by conventional solution crystallization,55 but Form β crystallized at low supersaturation occurs on the surface of Gr–OH gel, suggesting that Gr–OH sheets in the gel can act as a template to provide specific nucleation sites for Form β to induce its crystallization.
The solubility of CAF in DMSO at room temperature is about 13 mg mL−1, and it was added into the native and Gr–OH gels for gel phase crystallization, respectively. CAF crystals obtained from the native and Gr–OH gels are both identified as Form β (Fig. 5c), but the crystallization timescales are different in both gels. The induction time (tind) for crystallization of CAF in the native gel and the gel with 1000 μg mL−1 Gr–OH was determined, shown in Fig. 5d. At low supersaturation, CAF within Gr–OH gel shows a shorter induction time and faster nucleation rate. Specifically, when the CAF concentration (C) is 30 mg mL−1, crystals are obtained within the Gr–OH gel, while no crystals appear within the native gel. With the increase of concentration, the induction time of CAF in both gels gradually converge, when the degree of supersaturation becomes the controlling factor. In addition, solution crystallization was performed as a control experiment, which obtained the CAF crystals of Form α (see ESI Tables S4 and S5† for experimental details). Form α is a metastable polymorph containing a partially disordered structure, and Form β is the thermodynamically stable polymorph under ambient conditions.56 Different CAF polymorphs obtained by solution and gel phase crystallization indicate that the gel network is able to confine the convection and diffusion of CAF molecules and thus eliminate the structural disorder to obtain Form β.53 The shorter induction time of CAF in Gr–OH gel indicates that the presence of Gr–OH can lower the nucleation energy barrier and thus promote the nucleation of CAF.
APZ has a solubility of about 115 mg mL−1 in DMSO at room temperature. At low supersaturation with 150, 200 and 250 mg mL−1, APZ did not crystallize in either native gel or Gr–OH gel. When the concentration was increased to 300 mg mL−1, APZ crystals were obtained in Gr–OH gel after about 2 days at room temperature, but APZ still did not crystallize in the native gel after 7 days (Fig. 5e). Fig. 5f shows that the APZ crystals obtained from Gr–OH gel are identified as Form IV. In contrast, APZ crystals are obtained by cooling crystallization in DMSO solution without gel and are identified as Form V (see ESI Tables S6 and S7† for experimental details). APZ exists in twelve polymorphs with their transformation significantly affected by the solvent.57 Forms IV and V are both metastable polymorphs, and Form IV has higher a kinetic stability.58 Different APZ polymorphs were obtained in the solution and Gr–OH gel containing 300 mg mL−1 APZ under the same crystallization conditions, indicating that the Gr–OH gel environment can help the APZ molecules to overcome the solvent effect to obtain kinetically stable Form IV at the same supersaturation. No APZ crystals were obtained in the native gel, probably due to the absence of Gr–OH in the gel making it difficult for CAF molecules to nucleate with higher energy barrier, as above CAF has a longer induction time in the native gel.
For above three API systems, compared to the native gel without graphene, GLY appears as different polymorphs on the surface of Gr–OH gel, CAF in the Gr–OH gel phase has a shorter induction time, and APZ is more easily crystallized in Gr–OH gel. All results prove that Gr–OH in the gel significantly affects the polymorphic outcome, nucleation energy barrier and crystallization difficulty of APIs through specific interactions. Additionally, it should be noted that the diffraction peak intensities of experimental and standard PXRD patterns in Fig. 5 are different (probably due to changes in crystal habit and hence preferred orientation effects), but the polymorphism of APIs is primarily determined by recognizing the positions of diffraction peaks.59
FTIR spectroscopy was further used to monitor the interaction between Gr–OH nanosheets and API molecules in gel phase crystallization. Due to the low addition of Gr–OH and gelator in the gels, the FTIR spectra of both native and Gr–OH gels show only solvent absorption peaks but no peaks from the Gr–OH and gelator, and the FTIR spectra of both gels with addition of API show the absorption peaks of API and solvent (see Fig. S1–S3 of ESI†). Therefore, a comparison of the changes of API absorption peaks in the gel was chosen to determine the effect of Gr–OH. Fig. 5g shows the peak shift of CO of CAF from 1704 to 1698 cm−1 and the change of relative peak intensity of C–H of CAF at 745 cm−1 in the presence of Gr–OH in the gel. Fig. 5h shows that the absorption peaks of C–N and C–H of PZA are shifted from 1421 to 1402 cm−1 and from 839 to 831 cm−1 as well as a broader peak at 1402 cm−1 in the presence of Gr–OH in the gel. The C
O, C–N and C–H can form strong hydrogen bonds with hydroxyl group,60 which demonstrates that Gr–OH in the gel can act as a nucleation site and influence the crystallization process through hydrogen bonding interactions with specific groups of API molecule.
Footnote |
† Electronic supplementary information (ESI) available: The synthesis of gelators 1 and 2 and hydroxylated graphene, gel preparation, crystallization methods, induction time measurement, and characterization methods of SEM, TEM, fluorescence, rheology, FTIR, POM and PXRD are described. See DOI: https://doi.org/10.1039/d4sc08087d |
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