The hidden features of fullerene rotation in the crystal lattice

Abstract

Rotational dynamics in the crystal lattice is a characteristic attribute of fullerenes caused by their spherical shape. It lies in the background of various multifaceted phenomena, ranging from severe disorder, often hampering diffraction studies of fullerenes, to rotational order–disorder transitions or controlled switching of molecular orientations in nanoscale devices. Understanding these dynamics and their real-space presentation still remains a complex problem, especially for endohedral metallofullerenes, as their encapsulated species may show additional rotational degrees of freedom. In this work, we used variable-temperature single-crystal X-ray diffraction (VT SC-XRD) to elaborate on the phase transition in Sc₃N@C₇₀ crystals caused by the rotation of fullerene molecules. Snapshots of the molecular rotation taken with 10 K steps in a broad temperature range provided in-depth description of the process and revealed details usually overlooked by SC-XRD studies of metallofullerenes. In particular, analysis of thermal ellipsoids at various temperatures allowed to distinguish hidden static disorder from apparent dynamic disorder caused by thermal motion. The results mark a leap to the fundamental understanding of the unique metallofullerene structural characters, paving the way to control fullerene movement state in single molecule devices built from fullerenes.

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Introduction

Endohedral metallofullerenes (EMFs) are molecules with metal ions encapsulated inside fullerene cages. The coordination of metal ions to the inner wall of carbon cage with its extended π-system results in unique physicochemical properties, promising wide potential in biomedicine, energy, and emerging molecular devices.^1–7 The coordination between encapsulated metal ions and the fullerene cage is fundamentally important to understand the structure–property relations.^6,7 As one of the most interesting properties of EMFs, the intrinsic dynamics of metallofullerene molecules in solid state is still poorly understood, in strong contrast to the deep understanding of structural versatility of metallofullerenes.^8–20 A strategy to tackle this challenge is to observe the metal movement driven by temperature with variable temperature single crystal X-ray diffraction (VT SC-XRD). A few notable examples of this strategy include observing the standing still La/Gd ions in adamantylidene-derivatized C₈₂ cage until 293 K;^21,22 standing still of two La ions in adamantylidene-derivatized C₈₀ cage till 273 K;²³ jumping of Yb ion in C₈₀ cage;²⁴ moving of M₃N (M₃ = Ho₂Lu, Lu₃, Dy₂Sc, and Sc₃) in C₈₀ cage;^25–28 rotation of Dy₂ in benzyl-derivatized C₈₀;²⁹ moving of UN in C₈₂;³⁰ and rotation of the whole Sc₃N@C₇₀ molecule with C_2v(7854) carbon cage³¹ in the crystal lattice (Fig. 1 and Fig. S1 in the ESI†).³² The current state-of-the-art variable temperature single crystal X-ray diffraction studies captured the movement information with coarse precision, but the detailed information on the movement in high precision is still missing, although such information is pivotal to evaluate the intra/inter-molecular interactions. The strong coordination between Sc ions and the adjacent pentagon pairs of C₇₀ in Sc₃N@C₇₀ effectively excludes the degree of freedom for metal ions movement relative to the fullerene cage in the studied temperature range,^33–35 thus disentangles the complicated simultaneous movements of metal ions and fullerene cage in the crystal lattice. Therefore, this crystal exemplifies an ideal system to study the details of metallofullerene movement in the crystal lattice. In this work, we took a lot of snapshots for fullerene rotation with VT SC-XRD, to unravel the hidden details of fullerene movement in the crystal lattice.

Fig. 1 Coordination of Sc₃N@C₇₀ molecule to the NiOEP in two orientations present in different ratio in all crystals of Sc₃N@C₇₀·NiOEP·0.5(C₆H₆)·C₇H₈ studied in this work. The shown structures are for crystal 2 at T = 50 K, the major orientation I has occupancy of 79%, the minor orientation II has occupancy of 21%. Color code: grey for C in NiOEP, blue for N, white for H, magenta for Sc, red and cyan for C in fullerene cages. The probability of thermal ellipsoids was set to 30%.

Results and discussion

The crystals Sc₃N@C₇₀·NiOEP·0.5(C₆H₆)·C₇H₈ were grown by layering the toluene solution of Sc₃N@C₇₀ on the benzene solution of nickel octaethylporphyrin (NiOEP).^32,36 Analysis of the VT-SC-XRD data in this work is based on the studies of three crystals from two growth batches. Crystal 1 was studied in ref. 32 at 100, 160, and 220 K and revealed first indication of the phase transition below 160 K. Two orientations of the fullerene molecule present at occupancy ratio of 0.76/0.24 at 100 K, attained an equal occupancy at 160 K, while the crystal space group changed from P2₁/c to C2/m. In the following discussion, the main/minor orientations in the low-temperature crystals are denoted as orientation I/II (Fig. 1). Since the crystal had small solvent molecules (toluene and benzene) tending to slowly escape from the lattice, more recent attempts to perform detailed VT-SC-XRD study of crystal 1 showed that it degraded over time of ∼6 months. New batch of crystals was therefore grown in this work reproducing the growth conditions from ref. 32. The composition and a structure of new crystals closely reproduced those of crystal 1, aside from the small variation of the solvent content as will be discussed in more details below. One crystal from the new batch (crystal 2 hereafter) was studied at temperatures below 100 K applying cooling with He stream, while another one (crystal 3) was measured with small temperature steps above 100 K using cooling with N₂ stream. X-ray diffraction data collection was carried out at the BESSY II storage ring (BL14.2 and BL14.3, Berlin-Adlershof, Germany).³⁷ XDSAPP2.0 suite was employed for data processing.^38,39 The structure was solved by direct methods and refined by SHELXL-2018.⁴⁰ Hydrogen atoms were added geometrically and refined with a riding model. The crystal data are presented in Tables S1–S3 in the ESI.†

The driving force for the phase transition in Sc₃N@C₇₀·NiOEP crystals around 160 K is the slightly higher thermodynamic stability of the state, in which molecules in a certain orientation are surrounded by molecules in the same orientation.³¹ Above the phase transition temperature, thermally-induced re-orientational motion equalizes two orientations, while below 160 K, one of the orientations gains higher occupancy leading to the lower crystallographic symmetry. Therefore, the phase transition can be followed by monitoring the ratio of the occupancies with temperature as shown in Fig. 2a. In crystal 1, orientations I and II show the 0.5/0.5 ratio at 220 and 160 K, but change to 0.76/0.24 at 100 K. The detailed investigation of site occupancies in crystal 3 between 100 and 190 K showed that the ratio gradually changes from 0.5/0.5 at 170–190 K, to 0.52/0.48 at 160 K, and all the way to 0.79/0.21 at 100 K (see Fig. 1 and S2, Table S4 in the ESI for more details†). Reorientation of Sc₃N@C₇₀ is accompanied by a switching of coordinating NiOEP molecule between two positions, related by a translational movement and shifted from each other by less than 0.6 Å (see Fig. S3 and Table S4 in the ESI for details†). To analyze if further redistribution between orientations I and II is possible below 100 K, crystal 2 was studied with He cooling. The trend towards larger difference between occupancies at lower temperature was observed here as well, but the changes between 80 K (0.74/0.26) and 50 K (0.79/0.21) appeared less pronounced than at 100–170 K. Thus, the low-temperature ratio between two orientations seems to saturate at 0.8/0.2.

Fig. 2 (a) The site occupancy of Sc₃N@C₇₀ orientation I vs. temperature. (b) Temperature dependence of the average equivalent atom displacement parameter (U_equiv) of the carbon cage in two orientations of the Sc₃N@C₇₀ molecule (I and II), error bars denote standard deviations within the sets of 70 carbons; dashed purple line is the fit of the data for orientation I in crystal 3 between 100 and 170 K by a function a + bcth(hν/2kT).

Notably, different crystals show certain variation in I/II occupancy ratio when compared at the same temperatures. For instance, equal occupancies of I and II are found at 160 K in crystal 1 but at 170 K in crystal 2, and a similar occupancy of 0.76/0.24 and 0.75/0.25 was observed for crystals 1 at 100 K, and 2 at 110 K, respectively, showing that there is a systematic shift of ∼10 K between the two crystals. Likewise, the ratio of 0.74/0.26 determined for crystal 2 at 80 K is similar to the 0.75/0.25 ratio in crystal 3 at 110 K. One of the plausible reasons is the variation of the crystal quality between these three crystals. To verify this possibility, we refined the structures with flexible site occupancies for solvent molecules and obtained 0.898(C₇H₈)/0.479(C₆H₆) for crystal 1 at 100 K, 0.915(C₇H₈)/0.47(C₆H₆) for crystal 2 at 50 K, and 0.930(C₇H₈)/0.482(C₆H₆) for crystal 3 at 100 K (see Tables S1–S3 in the ESI for details†). The ideally perfect solvent composition used in the refinement is C₇H₈/0.5(C₆H₆). As uncertainties in occupancy determination is less than 0.009, the deviations from 1.0/0.5 are statistically significant and can be attributed to the escape of solvent molecules from the lattice, leaving behind imperfections in the crystal. Crystal 3 has the highest solvent occupancy, indicating the highest perfection of the structure. Since the solvent-fullerene interaction effectively hinders the fullerene rotation,²⁸ the higher perfection in terms of the solvate content leads to the higher phase transition temperature. This finding highlights the importance of using fresh crystals in SC-XRD studies of fullerene solvates. Another factor to be considered is that molecular re-orientation requires overcoming of an energy barrier and can therefore become more hindered at low temperatures.⁴¹ This makes the ratio between orientation I and II dependent on the cooling rate and can eventually result in the freezing of the I/II ratio when thermal energy becomes insufficient to overcome the barrier.

Observing the crystal structures with temperature intervals of 10 K results in the detailed description of the phase transition process. Fig. 3 presents the structures of crystal 3 measured at temperatures ranging from 100 to 170 K. Two overlapping orientations of Sc₃N@C₇₀ are equally populated at 170–190 K, with the C2/m crystal space group. When temperature decreases below 170 K, part of Sc₃N@C₇₀ molecules rotates from orientation II to orientation I, thus resulting in their unequal populations and the loss of the mirror symmetry and reducing the crystal space group to P2₁/c. Remarkably, thermal ellipsoids of the two molecular orientations exhibit very different temperature evolution. At 100 K, the size of thermal ellipsoids in I is several times smaller than in orientation II. But then, ellipsoids in orientation II barely change between 100 and 170 K, whereas the size of ellipsoids in orientation I increases four-fold in the same temperature range (Fig. 3). Numerically, this phenomenon is visualized in Fig. 4 using equivalent atom displacement parameters (ADPs, U_equiv). While ADPs for orientation I plotted in the upper panel show pronounced temperature dependence, a much weaker temperature variation and a larger scattering of ADPs are seen for orientation II in the lower panel. Temperature dependence of ADPs averaged over carbon cage in two orientations further substantiates this observation (Fig. 2b).

Fig. 3 Structures of crystal 3 measured at 100 K (a), 110 K (b), 120 K (c), 130 K (d), 140 K (e), 150 K (f), 160 K (g), and 170 K (h). The solvent molecules were omitted for clarity. The probability of thermal ellipsoids was set to 30%. The two orientations of C₇₀ were highlighted with red for I, and cyan for II. The marked fragment was zoomed in to highlight the changes of the thermal ellipsoids with temperature. Color code: grey for C in NiOEP, blue for N, white for H, magenta for Sc.

Fig. 4 The equivalent atom displacement parameters (ADPs, U_equiv) of Sc₃N@C₇₀ and NiOEP and their variation with temperature for orientation I (top panel) and orientation II (bottom panel). To guide the eye, the range of atom numbers corresponding to the carbon cage is shaded.

Temperature dependence of ADPs is associated with the variation of vibrational amplitudes, which in harmonic approximation scale with the temperature as u_i² ∼ cth(hν_i/2kT). Indeed, the growth of averaged cage ADPs in orientation I between 100 and 170 K is well described by cth(hν/2kT) with ν of 480 ± 30 cm⁻¹ (Fig. 2b). This frequency should not be understood as that of one particular mode but rather as a cumulative contribution of many vibrations. Thus, ADPs in orientation I show temperature variation typical for vibrational motions. The increased size of ellipsoids and the lack of their temperature dependence in orientation II indicate that the size of ellipsoids is likely to be determined by the static disorder. Presumably, the orientation II in fact contains several sub-orientations with small orientational differences, which cannot be resolved in a routine SC-XRD analysis. Thus, different temperature dependence of thermal ellipsoids allows VT SC-XRD analysis to distinguish two types of disorder co-existing in the crystal.

The concrete information observed with single crystal X-ray diffraction allows one to specifically check the chemical environment of the interested target. Fig. 5 shows the environment of Sc₃N@C₇₀ in the crystal lattice, presenting four nearby solvent molecules, of which one toluene molecule interacts with fullerene cage through π–π interaction, while the other two toluene and one benzene molecules interact with fullerene cage through C–H⋯π interaction. Fig. S4 and S5 in the ESI† highlights the solvent molecules interacting with NiOEP. Disorder usually poses higher uncertainty on the observed structural parameters, Table S5 in the ESI† presents the Sc–N bond lengths at variable temperatures. As the axis of fullerene rotation locates near the N position, the Sc–N bond lengths are weakly affected by the rotation and present rather low uncertainty at variable temperatures.

Fig. 5 The structure of crystal 3 at 100 K viewed perpendicular to the NiOEP plane. Both Ball-stick model (a) and space-filling model (b) are shown to highlight the environment of Sc₃N@C₇₀. Color codes: red/cyan for fullerene orientations I/II, pink/rose for NiOEP orientations I/II, blue for benzene/toluene molecules interacting with the fullerene cage and NiOEP.

Conclusion

In conclusion, detailed information of fullerene Sc₃N@C₇₀ rotation in the crystal lattice unravels two unprecedentedly important phenomena: first, the subtle variation of the solvent content affects the phase transition temperature; second, co-existence of thermal vibrational motion and static disorder in one crystal was visualized and clearly distinguished through the highly contrasting behavior of thermal ellipsoids. The results lay concrete evidence on the detailed information of fullerene movement in the crystal lattice, paving the way to control the fullerene movement state in single molecule device.

Data availability

Crystallographic data for crystals of Sc₃N@C₇₀ measured at different temperatures has been deposited at the CCDC under numbers 2362043–2362055† and can be obtained from https://www.ccdc.cam.ac.uk/structures/

Conflicts of interest

There is no conflict of interest to report.

Acknowledgements

This research was made possible as a result of a generous support from Deutsche Forschungsgemeinschaft (grants LI 3055/3-1, PO 1602/7-1, and PO 1602/11-1), the Jiangsu Specially-Appointed Professorship, and the China Scholarship Council for Fellowship to YH. Diffraction data have been collected on BL14.2 and BL14.3 at the BESSY II electron storage ring operated by the Helmholtz-Zentrum Berlin.³⁷

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Footnote

† Electronic supplementary information (ESI) available: Details of single crystal X-ray diffraction data. CCDC 2362043–2362055. For ESI and crystallographic data in CIF or other electronic format see DOI: https://doi.org/10.1039/d4qi01562b

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