K[(CuII,MnII,MnIII)2(TeO3)3]∙2H2O, the first zemannite-type structure based on a Jahn-Teller-distorted framework

Synthetic single crystals of K[(CuII,MnII,MnIII)2(TeO3)3]·2H2O were obtained from an overconcentrated alkaline aqueous solution in the system K2O-MnO-CuO-TeO2 under hydrothermal conditions at T ≤ 220 °C. Subeuhedral single crystals have been investigated by means of single-crystal X-ray diffraction. The crystal structure of this new zemannite-type representative adopts a monoclinic twofold superstructure. The doubling of the unit-cell volume is accompanied by a hexagonal-to-monoclinic symmetry reduction, resulting in threefold twinning with individual crystal domains following the space group symmetry P21. Refinements of site-occupation factors and the evaluation of bond valences suggest a distribution of di- and trivalent cations at the octahedrally coordinated M sites with a ratio (CuII + MnII):MnIII approximating 1:1. Based on arguments about the cation sizes and the individual bond valence sums, a distribution of CuII1–xMnIIIx and MnIIx MnIII1–x at each two of the four M sites can be assumed with x between ~ 0.14 and ~ 0.50. The K+ cations and H2O molecules inside the channels are located off the central channel axis. In contrast to most other known zemannite-type phases, the extra-framework atoms show full occupancies and are not disordered. The distribution of the channel contents supports the anisotropic deformation of the surrounding framework, which follows the local symmetry reduction as required for the Jahn-Teller distortion of the octahedrally coordinated M sites within the framework. The arrangement of the deformed channels can be understood as the origin of the existing superstructure.


Introduction
The zemannite structure type was reported for the first time in connection with structural studies of the rare mineral zemannite, described as a new species from the Moctezuma mine in Mexico, originally assuming the composition Na x H 2-x [(Zn II ,Fe III ) 2 (TeO 3 ) 3 ]·yH 2 O (Matzat 1967;Mandarino et al. 1969). Based on crystal structure and crystallochemical investigations, the composition of zemannite was revised subsequently to the idealized formula Mg 0.5 [Zn II Fe III (TeO 3 ) 3 ]·4.5H 2 O (Miletich 1995a). Crystal structure determinations of the minerals kinichilite (Hori et al. 1981), ilirneyite (Pekov et al. 2018) and keystoneite (Missen et al. 2021) reveal those minerals to be isostructural to zemannite. Its crystal structure represents a channel structure, with Mg 2+ cations and H 2 O molecules occupying the extra-framework sites inside enclosed channels.
Within the scope of systematic experimental work aiming at the synthesis of novel analogous oxidotellurate(IV) phases, hydrothermal syntheses have been performed on various transition-metal bearing systems using alkaline solutions almost 30 years ago (Miletich 1993a). Among them, series of formation studies were conducted in the system K 2 O-MnO-CuO-TeO 2 with targeting at novel microporous oxidotellurates(IV) adopting the denningite or zemannite structure. Both structure types are characterized by isolated channels within a framework composed of transition metals and Te IV in O-based coordination. Individual synthesis experiments resulted in an unexpected loss of water due to inappropriate sealing of the reaction containers, so that K-bearing oxidotellurates(IV) could form from the overconcentrated alkaline hydrothermal solutions. In this context, K 2 [Zn 2 (TeO 3 ) 3 ]·3H 2 O and K[(Mn,Cu) 2 (TeO 3 ) 3 ]·nH 2 O were coincidently obtained as compounds structurally related to zemannite, but their crystal structures have not yet been determined. In the case of K 2 [Zn 2 (TeO 3 ) 3 ]·3H 2 O, it was due to the lack of suitable untwinned crystals, as powder diffraction measurement indicated a monoclinic unit-cell as derived from peak splitting. Following our most recent findings on novel synthetic zemannite-type phases (Eder et al. 2023), it was possible to grow crystals of a less hydrated K-Zn-zemannite phase (i.e. K 2 [Zn 2 (TeO 3 ) 3 ]·2H 2 O), which, however, was found to be metrically hexagonal and not monoclinic.
Nevertheless, the preliminary investigations on the K-(Cu,Mn)-zemannite phase by means of X-ray film techniques (Miletich 1993a) clearly revealed twinning by nonmerohedry of non-hexagonal lattice domains. It was deduced that the crystal structure of this K-(Cu,Mn)-zemannite has a unit-cell with twice the size of the usual hexagonal zemannite basic cell (a ≈ 9.3 Å, c ≈ 7.7 Å), showing a doubling of one of the a-axes and thus leading to a symmetry reduction, which most likely corresponds to the monoclinic system. At that time, the appearance of the superimposing threefold twinned pseudohexagonal domains was a distinct limit for diffractometry, which in this case inhibited any successful attempt to solve the crystal structure. All that remained, was the unverified assumption that the deviation from the original hexagonal symmetry, and thus the distortion of the lattice in this particular zemannite, is probably due to the Jahn-Teller effects of the Cu II and Mn III cations, which are incompatible with the site symmetry in the parental P6 3 /m symmetry of the archetype framework.
On the occasion of the 100 th anniversary of the birthday of Prof. Josef Zemann (1923Zemann ( -2022, after whom the mineral was named and who is therefore the namesake of this structural family, we decided to determine the crystal structure of the K[(Cu,Mn) 2 (TeO 3 ) 3 ]·nH 2 O (n ≈ 2) zemannite phase with a modern CCD-based diffractometer to resolve the problems related to an apparent symmetry reduction. The upcoming anniversary was motivating to us in that Prof. Zemann was not only a pioneer in the structural chemistry of oxidotellurates(IV) (Zemann 1968(Zemann , 1971(Zemann , 1974, but also dealt with the peculiar crystal chemistry of mineral structures with Jahn-Teller-active cations, especially Cu II , in countless examples (e.g. Gattow and Zemann 1958 (Miletich 1993b). A stoichiometric mixture of 0.128 g MnCl 2 ·4H 2 O, 0.211 g CuCl 2 ·2H 2 O and 0.621 g TeO 2 , corresponding to the molar ratio 1 Mn:2 Cu:6 Te, was placed inside a Teflon-lined steel autoclave. The reaction container measuring ~ 4.5 to 5 cm 3 in volume was filled with water and concentrated KOH solution in such a way that a pH value of 9.5 was achieved at a filling level of about 70%. Then the mechanically sealed autoclave was heated to 220 °C and kept at this temperature under autogenous pressure for 92 h. When opening the autoclave after cooling to room temperature, it was observed that the filling level of the hydrothermal fluid had significantly decreased from more than two thirds to ~ 20%. The insufficiently closed autoclave inadvertently led to high fluid losses in this specific experiment, so that an exceptionally high concentration of the K contents, which are otherwise preferred to fractionate into the remaining fluid phase, led to the crystallization of a K-containing oxidotellurate(IV) phase as a unique by-product.
The crystalline reaction products of this run ( Fig. 1) were identified as a mixture of a denningite-type (Walitzi 1965) (Cooper and Hawthorne 1996) and rayite, Cu II Te 2 O 5 (Hanke et al. 1973), and subordinate amounts of the title compound K[ -(Cu II ,Mn II ,Mn III ) 2 (TeO 3 ) 3 ]·2H 2 O, as identified by means of X-ray powder and single crystal diffraction. The subeuhedral K-(Cu,Mn)-zemannite crystals are characterized by an intensive dark brown colour and exhibit large hexagonal pillars up to 0.5 mm in length, morphologically dominated by the faces of the hexagonal prism.

X-ray diffraction measurement and refinement
Single crystal X-ray diffraction measurements were conducted on a Bruker Kappa Apex-II diffractometer using graphitemonochromatized MoK α radiation and a CCD area detector. Data sets were recorded based on ω-and φ-scans (0.5° per frame, 30 s exposure time per frame), in the range 2.55° < 2ϑ < 61.0° for the reciprocal space covering ± h ± k ± l (with h ≤ 13, k ≤ 11, l ≤ 22). Details of the data collection and the crystal specimen used for the measurement are summarized in Table 1. Calculation of measurement strategies and integration were carried out with the instrument software APEX-4 (Bruker 2021a) and SAINT (Bruker 2021b), absorption correction with SADABS (Krause et al. 2015); the structure solution was achieved with SHELXT (Sheldrick 2015a), and the subsequent refinements performed with SHELXL 2018/3 (Sheldrick 2015b). Four reflections (101, 101 , 002, 201) appearing at the lowermost diffraction-angle range were omitted from the refinement as their intensities were significantly influenced by shadowing of the primary beam stop. For structure refinement, threefold twinning with the twin law was considered using a hklf-5-type file comprising intensity data of separated and overlapping reflections of the three Merging of the reflections during scaling in SAD-ABS (Krause et al. 2015) led to smaller k and l ranges in the hkl file, as Friedel pairs were averaged. Since the final crystal structure model is non-centrosymmetric, it was also tried to suppress merging of Friedel pairs, thus resulting in six twin domains. However, the fractions of these additional three twin domains always resulted in negative values and corresponding refinement attempts did not converge appropriately. Therefore, all further refinements were carried out based on the data reduction with the above-mentioned threefold twinning.
The corresponding twin fractions were refined to values of 0.4256(16), 0.3223(16) and 0.2521(16), thus proving the suspected triplication of somewhat equal proportions of crystal domains. Apart from this twin triplication due to the parental pseudohexagonal arrangement, many reflections, which can be ascribed to only one of the three domains, still show a weak further splitting (Fig. 2a). This could be an indication of a further reduction in symmetry, possibly giving evidence of a weak triclinic distortion as manifested by the observed faint splitting. This feature has not been observed for the preliminary investigations carried out by precession photograph techniques 30 years ago (Fig. 2b). As this further splitting of the reflections is rather small and cannot be resolved properly for separate integration, it was ignored for any further consideration within the scope of this study.
The crystal structure was determined by means of direct methods as employed by the algorithm of SHELXT thus providing fractional coordinates corresponding to those transformed by the  (Hanke et al. 1973, green, 3) and the title compound K[(Cu II ,Mn II ,Mn III ) 2 (TeO 3 ) 3 ]·2H 2 O (dark brown, 4). The light brown crystals probably originate from minor amounts of α-MnTeO 3 (Trömel and Schmid 1972, 5) matrix relative to positions given by Miletich (1995b).
Structure refinement attempts in the non-centrosymmetric space group P2 1 exhibited some issues, because the entire crystal structure exhibits P2 1 /m as a pseudosymmetry, which is only violated through the occupational distribution of the M atoms at their sites. Therefore, the y coordinates and the U 12 and U 23 values of the anisotropic displacement parameters (ADPs) of the atoms, which are located at sites sitting on the supposed m mirror plane in P2 1 /m, did not converge properly. The corresponding y/b positional parameters consistently indicated to prefer equally two nearby positions close to the ideal mirror symmetry and did not achieve convergence even after hundreds of refinement cycles. This behaviour was suppressed by application of a stronger dampening term to the refinement using the DAMP command in SHELXL (Sheldrick 2015b). Moreover, the symmetry reduction led to larger correlations between pairs of positions related by the missing m [010] plane. Other than in P2 1 /m, the O atoms could not be refined with ADPs in P2 1 because of negative values for several atoms. The final refinements were carried out in P2 1 space group symmetry using isotropic displacement parameters for all O atoms. Particular attention was also paid to the distribution of Mn and Cu atoms at the M positions, as well as the occupancy of K in the channels with regard to the variable distribution of divalent and trivalent cations. Accordingly, different models with or without partial (Cu, Mn) occupancies at Cu1 or Cu2, with different valences (Mn II , Mn III ), or with a possible partial occupancy of K at the K1 and K2 sites were taken into account and comparative refinements have been carried out.  Miletich (1993a) The results of the final refinement are summarized in Table 1, positional parameters are provided in the cif file (cf. supplement material), and selected interatomic distances are listed in Table 2. Additional details can be found in the joint CCDC/FIZ Karlsruhe online deposition service: https:// www. ccdc. cam. ac. uk/ struc tures/ by quoting the deposition number given in Table 1. Graphical representations of the crystal structure were created with DIAMOND (Brandenburg 2016). As no other equivalent zemannite-type superstructure has been described as a reference phase, atom labels and coordinates were standardized with STRU CTU RE-TIDY (Gelato and Parthé 1987).
The zemannite structure type consists of an anionic framework built up from trigonal-pyramidal [TeO 3 ] units and [M 2 O 9 ] dimers of face-sharing octahedra. These groups are interconnected to the other type of building blocks by corner-sharing. The [M 2 (TeO 3 ) 3 ] yframework encloses large channels that are oriented along [001] of a hexagonal unitcell (a ≈ 9.3 Å, c ≈ 7.7 Å), which has been described in either P6 3 /m or P6 3 space group symmetries. A most recent re-evaluation of the zemannite structure based on a natural sample revealed violations in the systematic absences corresponding to the 6 3 screw axis. The related structure refinements suggest P3 as the true space group symmetry of the archetype crystal structure (Effenberger et al. 2023).
Together with a variable amount of H 2 O molecules, the A cations represent the extra-framework constituents distributed inside these topologically hexagonal channels. Depending on the amount of A cations present in the structure, the A cations are positioned either exactly at the central axis of the channels, such as exemplified in the structure of the mineral zemannite (Miletich 1995a). Alternatively, they are displaced at distances of up to ~ 2 Å off this central axis, due to the confined space inside the channel, in particular if the number or the size of A cations exceeds certain limits (e.g. Symmetry codes: (i) 1-x, 1/2 + y, 1-z; (ii) x, 1 + y, z; (iii) 1 + x, y, z; (iv) 1 + x, y, -1 + z; (v) -1 + x, y, z; (vi) -x, -1/2 + y, 1-z; (vii) x, -1 + y, z; (viii) -x, 1/2 + y, 1-z; (ix) 1-x, 1/2 + y, -z  Miletich 1995b). In the latter case, the occupancies are usually modelled with ~ 1 ∕ 3 for refinements in the parental hexagonal symmetry, which in fact represents only the symmetry of the framework but not that of the channel contents. Equivalent partial occupancies apply to the H 2 O molecules, which in turn belong in most cases to the coordination spheres of hydrated A cations.

Lattice properties of the new K[(Cu,Mn) 2 (TeO 3 ) 3 ]•2H 2 O zemannite
Considering the triplicate twinning along the pseudo-hexagonal axis in analogy to the parental 6/m Laue symmetry as shown in Fig. 2, the individual lattice domains follow monoclinic metrics with the diad aligned parallel to the hexagonal c-axis. Referring to a standard setting of the monoclinic diad being parallel to the b axis, the actual lattice can be described as a doubled zemannite structure (Fig. 3). The doubling occurs along [100], [010] or [ 110] . As [100] or its two symmetry-equivalent directions are three possible directions for doubling of the unit-cell, it is not surprising that threefold twinning was observed, following the lost rotation by each 120°. Accordingly, this threefold twinning leads to the formation of pseudo-sixfold symmetry in the diffraction pattern. The a:c ratio, which in case of an undistorted hexagonal lattice corresponds to 1: √ 3 , clearly deviates with a ratio of 1:1.677 from metrical hexagonality. In addition, a small but significant deviation of β from ideal 90° confirms the observed lattice distortion, which is the reason why the three twin domains do not perfectly coincide, thus suggesting twinning by non-merohedry. This is manifested in reciprocal space in particular at higher h and l values as referring to the monoclinic unit-cell of K[(Cu II ,Mn II ,Mn III ) 2 (TeO 3 ) 3 ] ·2H 2 O. The remarkable shape of the diffraction pattern has already been noted during the original investigation (Fig. 2b,  Miletich 1993a) and a unit-cell of a = 18.54(5) Å, b = 7.76(4) Å, c = 9.39(4) Å, β = 118.1(6)° as transferred to the standard monoclinic setting was derived at that time. Within the scope of the current study, we determined a similar unitcell (a = 9.3857(13) Å, b = 7.6381(10) Å, c = 15.746(2) Å, β = 90.464(4)°), which follows a different base-vector setting in order to achieve a monoclinic angle being close to 90°.

Crystallographic sites in the monoclinic superstructure
Compared to Na 2 [Co 2 (TeO 3 ) 3 ]·3H 2 O (Miletich 1995b) as a representative of the aristotype P6 3 /m symmetry, the crystal structure of K[(Cu II ,Mn II ,Mn III ) 2 (TeO 3 ) 3 ]·2H 2 O is subjected to a loss of the threefold rotation symmetry and the mirror plane perpendicular to the former sixfold axis of rotation. In addition, the doubling of the unit-cell causes the need for further symmetry-independent sites. This is manifested by the fact that the original eight atomic sites, some of which exhibit specific point symmetries, are now distributed over 34 independent sites, all of them corresponding to the general Wyckoff position 2 a in space group P2 1 . The framework sites Te1 (site symmetry m..), Co1 (3..), O1 (m..) and O2 (1) in P6 3 /m are split into six Te, four M (two Cu and two Mn) and 18 O sites in the monoclinic superstructure. The Na1 site, which is only 1 ∕ 3 occupied in Na 2 [Co 2 (TeO 3 ) 3 ]·3H 2 O, results in two fully occupied K sites, corresponding to only half the amount of A atoms p.f.u. compared to Na 2 [Co 2 (TeO 3 ) 3 ]·3H 2 O. With respect to the H 2 O sites O3, O4 and O5 in the parental hexagonal structure, the four Ow sites in K[(Cu II ,Mn II ,Mn III ) 2 (TeO 3 ) 3 ] ·2H 2 O, (viz. Ow5, Ow8, Ow19 and Ow20) are more or less equivalent to O3-type and, with some deviations, to O4-type

Stereochemistry of the [TeO 3 ] groups and [M 2 O 9 ] dimer units
The Te atoms are coordinated by three O atoms in a trigonalpyramidal shape with the resulting [TeO 3 ] units being isolated from each other. The bond valence sums (BVS) of the Te atoms were calculated to 3.90 (Te1), 3.91 (Te2), 3.82 (Te3), 3.88 (Te4), 3.91 (Te5) and 3.90 (Te6) valence units (v.u., Brese and O'Keeffe 1991) based on the Te-O contacts given in Table 2. These values show good agreement with the ideal value of 4 as expected for an oxidotellurate(IV). The marginally smaller values originate from the presence of five additional O contacts for each Te site in the range of 2.8-3.5 Å, which have not been taken into account. Employing the revised parameters reported by Mills and Christy (2013), which require the consideration of all O contacts within 3.5 Å, the BVS values amount to 4.00 (Te1), 3.99 (Te2), 3.95 (Te3), 3.98 (Te4), 3.96 (Te5) and 4.01 (Te6) v.u. in almost perfect agreement with expectations.
The M sites are coordinated by six O atoms with distances ranging from 1.88(2) Å to 2.311(15) Å ( ] octahedra is not surprising, because Cu II (d 9 ) and Mn III (d 4 ) atoms are known for their strong Jahn-Tellereffects (Lufaso and Woodward 2004).
The degree of octahedral distortion was analysed using OCTADIST (Ketkaew et al. 2021) and compared to the zemannite mineral phase Mg 0.5 [ZnFe(TeO 3 ) 3 ]·4.5H 2 O (Miletich 1995a) and the synthetic zemannite-type phase Na 2 [Co 2 (TeO 3 ) 3 ]·3H 2 O (Miletich 1995b) (Table 3). The individual parameters referring to polyhedral distortion are (i) the average M-O distance d mean , (ii) the distance distortion ζ, (iii) the angle distortion Σ, (iv) the tilting distortion Δ, and (v) the torsional distortion θ. Interestingly, the parameters cannot be used to make a clear distinction between the polyhedron types, although the distribution of bond lengths does (cf. Table 2). In comparison with Mg 0.5 [ZnFe(TeO 3 ) 3 ]·4.5H 2 O, which exhibits no Jahn-Teller induced effect for Zn 2+ and Fe 3+ , similar values for most distortion parameters are revealed. Only the tilting distortion Δ shows significant differences. In contrast, synthetic Na 2 [Co 2 (TeO 3 ) 3 ]·3H 2 O exhibits much more regular octahedra with consequently lower distortion parameters.
Apart from the fact that the M sites in these different representatives correspond to different point symmetries, one has to emphasize that octahedral distortion certainly is superimposed by two effects, which is on one hand the topologically induced distortion within the face-sharing dimers, and on the other hand the electronically induced Jahn-Teller effect.
Nevertheless, considering the M-O distances related by the former threefold symmetry, it clearly shows that an influence of the Jahn-Teller effect is present and is apparent for the origin of the symmetry reduction. If one compares the bond lengths to the three O atoms shared within the dimer, clear differences in the M-O distances can be seen: e.g. Cu2-O17 = 2.30(2) Å, Cu2-O18 = 2.03(2) Å, Cu2-O12 = 2.07(3) Å; Mn4-O17 = 2.02(2) Å, Mn4-O18 = 2.18(2) Å, Mn4-O12 = 2.09(3) Å within the [Cu2Mn4O 9 ] dimer. Short and long M-O bonds are arranged in a complementary fashion as it can be expected by the cooperative effect of the Jahn-Teller distortion in connection with balancing the bond valence contributions. While the bond valences of Te IV in the [TeO 3 ] groups are remarkably close to the ideal values, the occupancy of the M positions can only be explained by a significant degree of substitution at any of the four M sites. The BVS as calculated for full occupancy with only Cu II , Mn II or Mn III reveal significant over-or undersaturation for all four M sites, which necessitates a separate discussion of the occupancies.

(Cu II ,Mn II ,Mn III ) distribution at octahedrally coordinated M sites
Since the refinements of the sites corresponding to the extrachannel K + cations revealed full occupancy, each half of the M atoms within the framework must correspond to di-and trivalent transition-metal cations due to charge neutrality. Such a K[M II M III (TeO 3 ) 3 ]·2H 2 O composition reflects an equivalent charge distribution as manifested by the distribution of Zn II + Fe III , Mn II + Fe III , Ni II + Fe III , and Zn II + Mn III in the host frameworks of zemannite and the isostructural minerals (Miletich 1995a;Cametti et al. 2017;Missen et al. 2019b;Effenberger et al. 2023). It therefore can be assumed that each [M 2 O 9 ] dimer formed from two face-sharing [MO 6 ] octahedra hosts one divalent and one trivalent M atom. This assumption is supported by bondvalence considerations for the O atoms of the shared face, which is similar compared to the one discussed by Cametti et al. (2017). When refining in the higher-symmetric P2 1 /m space group, it is not possible to distinguish Cu and Mn sites due to identical environments caused by local mirror-plane symmetry. Lowering the symmetry to P2 1 , the number of M sites doubles from two to four, and each [M 2 O 9 ] dimer now encompasses two different M sites. Of these two, one exhibits a notably higher electronic density and therefore was assigned to be preferentially occupied by Cu atoms. Accordingly, non-centrosymmetric P2 1 was ultimately chosen as the space group, despite the more problematic refinement (such as evidenced by the strong correlation effects, negative ADPs and non-convergence of y/brelated parameters of distinct atoms). The alternative structure model in P2 1 /m is attached in the supplementary materials.
Refining the relative occupancies of Cu and Mn atoms at the same site, a Cu:Mn ratio of 0.35 (2) (Cu II ). If all Mn atoms would be present in the form of trivalent Mn III , a reduction of the K-content in order to balance charges is necessary. However, when freely refining the occupancies of the two K sites, the s.o.f.s account for 0.934(14) on average, which does not correlate with the magnitude of the Mn excess. This, in turn, suggests that the ratio between divalent and trivalent cations indeed is close to 1:1, and therefore Mn II and Mn III atoms must coexist.
Further information on the occupational distribution of atoms at the M sites can be derived by evaluating the bond valences, as calculated for the (Cu,Mn)1, (Cu,Mn)2, Mn3 and Mn4 sites in variations of exclusive occupancy through Cu II , Mn II , and Mn III (  (Table 4) support this assumption. The potential presence of both Mn II and Mn III besides Cu II at the M1 and M2 sites was considered as well. However, this led to a worse agreement of the mixed bond valences with the corresponding charge of the sites than a mixed occupancy with just Mn III besides Cu II .
Additionally, the ideal proportions for a partial Mn III /Cu II occupancy were determined independently from the ratios obtained by the refinement but based on the respective extent of over-or undersaturation of the bond valences Δ BV  (Miletich 1993a).

Distribution of extra-framework K + ions and H 2 O molecules
The distribution of the extra-framework constituents within the topological channels offers a comparatively The unidirectional presence of K + cations and H 2 O molecules in the channels is apparently crosslinked with the distortion of the surrounding framework, as manifested by the lattice parameters and the significant difference of the c/a ratio from ideal √ 3 as discussed previously. The channels have their smallest diameter along the direction corresponding to the section, within which the K atoms are displaced from the central channel axis. Since the H 2 O molecules are further away from the central axis (1.63-1.73 Å) and require a correspondingly larger amount of space for getting accommodated, the channel diameter is larger in those directions.
The distances between the second closest M positions in Fig. 3 (marked with yellow lines) show variations of more than 0.6 Å (8.878(7)-9.532(7) Å), thus demonstrating the deviation from a strict hexagonal symmetry of the channels. When looking at the cross section, the pseudohexagonal channels have an elliptically elongated shape and are stacked next to each other in a herringbone-like pattern with only two out of three possible channel distortions being realized within a single domain. The arrangement of the deformed channels can finally be understood as the origin of the existing superstructure.
Distortions of the channels from the superordinate hexagonal symmetry have been observed for several other zemannite-type phases. In the crystal structures of Ba[M 2 (SeO 3 ) 3 ]·3H 2 O (M = Co, Mn, Mg) (Johnston and Harrison 2011), which exhibit a fourfold zemannite superstructure obtained by doubling a and b of the parent zemannite unit-cell, the M···M distances as drawn in Fig. 3 (Eder et al. 2023) also exhibit such a fourfold superstructure, with the channels widening up in the direction of the A cations due to the lower crystal water content and the higher off-center displacement of the larger Rb + and Cs + cations. Together with the presence of Jahn-Teller-active Mn III within the framework, the larger A cations inside the channels lead to increased distortions of the channels with differences in the corresponding M···M distances (as drawn in yellow in Fig. 3) ranging up to ~ 1.5 Å.