Synthesis and Structural Characterization of the New Clathrates K8Cd4Ge42, Rb8Cd4Ge42, and Cs8Cd4Ge42

Schäfer, Marion C.; Bobev, Svilen

doi:10.3390/ma9040236

Open AccessArticle

Synthesis and Structural Characterization of the New Clathrates K₈Cd₄Ge₄₂, Rb₈Cd₄Ge₄₂, and Cs₈Cd₄Ge₄₂

by

Marion C. Schäfer

and

Svilen Bobev

^*

Department of Chemistry and Biochemistry, University of Delaware, Newark, DE 19716, USA

^*

Author to whom correspondence should be addressed.

Materials 2016, 9(4), 236; https://doi.org/10.3390/ma9040236

Submission received: 3 March 2016 / Revised: 17 March 2016 / Accepted: 21 March 2016 / Published: 25 March 2016

(This article belongs to the Special Issue Inorganic Clathrate Materials)

Download

Browse Figures

Versions Notes

Abstract

:

This paper presents results from our exploratory work in the systems K-Cd-Ge, Rb-Cd-Ge, and Cs-Cd-Ge, which yielded the novel type-I clathrates with refined compositions K₈Cd_3.77(7)Ge_42.23, Rb₈Cd_3.65(7)Ge_42.35, and Cs_7.80(1)Cd_3.65(6)Ge_42.35. The three compounds represent rare examples of clathrates of germanium with the alkali metals, where a d¹⁰ element substitutes a group 14 element. The three structures, established by single-crystal X-ray diffraction, indicate that the framework-building Ge atoms are randomly substituted by Cd atoms on only one of the three possible crystallographic sites. This and several other details of the crystal chemistry are elaborated.

Keywords:

clathrates; type-I structure; germanium; cadmium; Zintl phases

Graphical Abstract

1. Introduction

Clathrates of silicon and germanium with the alkali metals have been known now for almost half a century [1]. The idea of phonon-glass electron-crystal (PGEC), coined by G. Slack [2], succinctly captures the two most important structural features of these clathrates: rigid open frameworks, made up of covalently bonded atoms, and guest atoms residing in the large cages. The stable frameworks contribute to the favorable carrier mobilities, while the filler atoms that vibrate (or “rattle”, as is frequently said) in the oversized cages are believed to be the reason for the low lattice thermal conductivity exhibited by many clathrates. Therefore, this class of compounds has gained interest for their prospects as thermoelectric materials [2,3,4,5].

Most studied clathrate compounds are based on the group 14 elements Si, Ge, and Sn (Tt). These atoms form extended networks adopting several different structure types. Fractions of the framework atoms can be substituted by group 13 and 12 elements, as well as late transition metals (M), which can be stabilized in tetrahedral coordination. There are large cages in the clathrate structures, which are partially or fully occupied by guest atoms (A). The typical guest atoms are alkali metals, alkaline earth metals, or Ce and Eu from the rare earth metals [6,7,8,9,10].

This paper deals with three new clathrate phases with compositions K₈Cd_3.77(7)Ge_42.23, Rb₈Cd_3.65(7)Ge_42.35, and Cs_7.80(1)Cd_3.65(6)Ge_42.35, which adopt the type-I structure (Figure 1). The nominal formula for this structure is A₈(Cd,Ge)₄₆, and it boasts cages of 20- and 24-atoms. Here, we would like to mention that numerous clathrates of germanium with the alkali metals are known as of today, but this study is among very few to identify cadmium as a substituent of germanium-based clathrates—the quaternary phase K₆Eu₂Cd₅Ge₄₁ appears to be the only report of similar chemistry so far [11]. The corresponding systems K-M-Ge and Rb-M-Ge with M being the group 12 elements Zn and Hg have already been explored, and the structures of the type-I clathrates K₈Zn₄Ge₄₂ [12], K₈Hg_3.19Ge_42.81, and Rb₈Hg_3.03Ge_42.97 [13] have been published.

2. Results

2.1. Crystallographic Analysis

The structure solutions and refinements proceeded in a straightforward manner (Table 1), and only a few details deserve special mention. First, the contrast between the X-ray atomic scattering factors of Cd and Ge is significant, allowing precise refinements of the site occupation factors should there be mixed-occupied sites. Indeed, in all cases, when the occupancies of the framework sites were first freely refined (individually, while the remaining ones were kept fixed), it was noted that the occupation factors for 16i and 24k sites did not deviate from 100%, while sites 6c in all three structures appeared to be “heavier”. This indicates that Cd (Z = 48) and Ge (Z = 32) co-occupy framework site 6c only (in a ratio ca. 60% Cd, 40% Ge). Such distribution of group 12 and group 14 elements is consistent with the published refinements for K₈Hg_3.19Ge_42.81 and Rb₈Hg_3.03Ge_42.97 [13], K₈Zn_3.46Si_42.54 and Rb_7.86Zn_3.63Si_42.37 [14], and K₈Zn_3.78Sn_42.22, Rb₈Zn_3.52Sn_42.48, and Cs₈Zn_3.44Sn_42.56 [15]. If one considers the alkaline earth clathrates, such as Ba₈Zn₇Si₃₉ [16], the 6c site is also mostly occupied by Zn (77% Zn, 23% Si), with the remainder of the Zn found at 24k (9% Zn, 91% Si).

Notice that, in all three structures, the Zintl-Klemm concept [17], which appears to be followed by many other clathrates [8], is not completely satisfied by the above-mentioned compounds. For instance, based on the rationalization [A⁺]₈[M²⁻]₄[Tt⁰]₄₂, one should expect the structural formulae to be A₈M₄Tt₄₂ (A = alkali metal, M = Zn, Cd, Hg; Tt = tetrel, or Si, Ge, Sn). The same holds true for Ba₈Zn₈Si₃₈ (=[Ba²⁺]₈[Zn²⁻]₈[Si⁰]₃₈). The reasons for the slightly lower refined content of Zn, Cd, or Hg are not yet understood. This would mean, however, that all these materials are metallic conductors, not semiconductors, as expected from the Zintl-Klemm concept. One might argue that the structures have both Cd/Ge positional disorder and defects on the 6c sites, i.e., in analogy with Ba₈Zn_xGe_46–x–y☐_y and Ba₈Cd_xGe_46–x–y☐_y (☐ = vacancy) [18,19]. This certainly is a valid argument, which warrants further investigations. We will note here that, while for Ba₈Zn_xGe_46–x–y☐_y and Ba₈Cd_xGe_46–x–y☐_y the hypothesis for vacancies in the framework had been supported by the low occupation factors and elongated displacement parameters of the atoms neighboring the defects, none of these indicators of additional structural disorder are observed for the herein discussed structures.

We also need to mention the fact that when checking the occupancies of the guest atoms in the reported structures 1 and 2, they did not deviate from full. However, when the occupancies of the Cs sites in 3 were checked, it became obvious that site 2a is underoccupied (occupation factor 89.8(4)%). This is the center of the smaller pentagonal dodecahedral cage in the type-I clathrate, which might be not large enough to accommodate the very large Cs atom. Therefore, 3 is the only structure without 100% filled cages, refined as Cs_7.80(1)Cd_3.65(6)Ge_42.35. To help the reader of this article appreciate the subtleties of the refinements Cs_7.80(1)Cd_3.65(6)Ge_42.35 vs. Cs₈Cd_3.65(6)Ge_42.35, the .CIF for the latter is provided as supporting evidence (please see the supplementary electronic information associated with this article). Despite the respectable residuals, quick convergence and quite reasonable anisotropic displacement parameters, the relatively deep hole in the difference electron density map (the Fourier synthesis indicates a hole of 4 e⁻/Å³ just 0.2 Å away from Cs2) is a telling sign that the respective position is not fully occupied. Indeed, when the occupation factor of Cs2 is freed, the difference Fourier map flattens out completely (Table 1 and Table 2).

Lastly, while commenting on the size of the guest atoms and the clathrate cages, we should point the attention to the anisotropic displacement parameter of K1 in structure 1, site 6d (Table 3). This atom is at the center of the larger tetrakaidecahedral cage (Figure 2). The size/shape of the thermal ellipsoid is not dependent on the site occupation factor (deviates from unity less than 3σ). The equivalent isotropic displacement parameter for K1 is, by far, the largest of all. Its slightly oblate shape may hint at off-centering (Table 3), but such positional disorder is very small and could not be resolved from the available crystallographic data. For comparison, the disorder in the type-I clathrates of tin, where the tetrakaidecahedral cages are even larger, is easily modeled from data collected on an in-house diffractometer [20,21,22]. Sr₈Ga₁₆Ge₃₀ and Ba₈Ga₁₆Ge₃₀ are other well-known examples of filler atoms being off-centered from their equilibrium positions, and both structures have been worked out from synchrotron and neutron diffraction data [23,24,25].

2.2. Structural Metrics

As seen in Table 1, the unit cell parameters of the three cubic type-I clathrates (space group Pm

\bar{3} n

(No. 223)) increase from a = 10.8710(4) Å for K₈Cd_3.77(7)Ge_42.23, to a = 10.9099(5) Å for Rb₈Cd_3.65(7)Ge_42.35, to a = 10.9643(7) Å for Cs_7.80(1)Cd_3.65(6)Ge_42.35. This increase can be attributed to the increase in size of the alkali metal atoms (r_K ≈ 2.03 Å, r_Rb ≈ 2.16 Å, r_Cs ≈ 2.35 Å, according to Pauling [26]). The small deviations in the refined Cd content must also have an effect on the unit cell volumes, but it is expected to be subtle (the difference in the refined Cd content is less than 2σ). Notice, however, that in the single-bonded Pauling radii for the Cd and Ge are quite different, r_Ge ≈ 1.24 Å, r_Cd ≈ 1.38 Å [26], and, as a result, the Cd substitutions to the Ge-based framework result in enlargement of the unit cell, clearly seen by comparing our data with the data for the known binary type-I clathrates K₈Ge₄₄☐₂ [27] and Cs₈Ge₄₄☐₂ [28], which have periodicity constants of a = 10.686(4) Å and a = 10.8238(2) Å, respectively. Of course, the presence of vacancies in the framework for K₈Ge₄₄☐₂ and Cs₈Ge₄₄☐₂ (☐ = vacancy) should not be overlooked, as it contributes to the contraction of the unit cell. Given that Cd and In are neighboring elements in the periodic chart with similar atomic radii (r_In ≈ 1.42 Å [26]), it is no surprise that the type-I clathrates from the systems K-In-Ge, Rb-In-Ge, and Cs-In-Ge show similar characteristics. The unit cell parameters of the latter increase are in the following order: a = 10.997(2) Å for K₈In_8.14Ge_37.86; a = 11.033(2) Å for Rb₈In_7.81Ge_38.19; a = 11.079(2) Å for Cs₈In_8.22Ge_37.78 [29,30]. Another relevant comparison can be made between K₈Cd_3.77(7)Ge_42.23 on the one hand, and K₈Zn₄Ge₄₂ and K₈Hg_3.19Ge_42.81 on the other [12,13]. The atomic size of Zn is slightly smaller than that of Cd (r_Zn ≈ 1.21 Å [26]), hence the smaller unit cell parameter for K₈Zn₄Ge₄₂ (a = 10.7488(1) Å) [12]. Mercury and cadmium are very similar in size (r_Cd ≈ 1.38 Å; r_Hg ≈ 1.39 Å [26]), but the refined Hg content in K₈Hg_3.19Ge_42.81 is lower that the Cd content in K₈Cd_3.77(7)Ge_42.23, hence the smaller unit cell parameter for the former (a = 10.8489(13) Å) [13]. The same is true for Rb₈Cd_3.65(7)Ge_42.35 (2) vs. Rb₈Hg_3.03Ge_42.97 (a = 10.8750(13) Å [13]).

The net result of the substitution of the larger Cd for the smaller Ge is a small increase in the cage sizes, and therefore an expansion of the unit cells (vide supra). This can be also observed in the atomic distances (see Table 4), which fall in the intervals of d_Ge–Ge = 2.4931(4) to 2.52(1) Å for 1, d_Ge–Ge = 2.5029(4) to 2.539(1) Å for 2, and d_Ge–Ge = 2.5118(4) to 2.570(1) Å for 3, respectively. Notice that, since Cd substitutes only at the 6c site, Cd-Cd contacts are avoided. This site only neighbors Ge1 and the corresponding d_Cd/Ge3-Ge1 distances monotonically increase in the following order: 2.5858(6) Å for 1, 2.5912(5) Å for 2, and 2.6019(5) Å for 3, respectively. The distances from the guest atoms in the cages to the framework follow the same trend (Table 4).

3. Discussion

In 2014, we reported for the very first time the occurrence of the type-I and type-II clathrates Rb_5.20Na_2.80(4)Zn_3.85Si_42.15(2) and Rb₈Na₁₆Zn_8.4Si_127.6(1) [31]. Shortly after, another team reported the structure determination for K₈Zn_3.46Si_42.54 and Rb_7.86Zn_3.63Si_42.37 [14]. Subsequently, we set out to synthesize the Cd-analogs of these compounds, but these studies did not yield any clathrates.

As a result, we turned our attention to the germanium clathrates. We noticed that there were prior reports on K₈Zn₄Ge₄₂ and the mixed-cation K_xBa_8–xZn_yGe_46–y [12]. K₈Hg_3.19Ge_42.81 and Rb₈Hg_3.03Ge_42.97 [13] have also been known for some time. The mixed-cation clathrates K₆Eu₂(Zn or Cd)₅Ge₄₁ also appear in the literature [11], but the corresponding crystallographic information is not available from the ICSD.

Given that mercury and cadmium are very similar in size, we thought it was surprising that the corresponding K-Cd-Ge, Rb-Cd-Ge, and Cs-Cd-Ge systems had not been carefully explored. This work fills this gap in the literature by detailing the structures of the type-I clathrates K₈Cd_3.77(7)Ge_42.23, Rb₈Cd_3.65(7)Ge_42.35, and Cs_7.80(1)Cd_3.65(6)Ge_42.35. However, the latter clathrate phases are always co-crystallizing with small amounts of secondary phases, irrespective of the tried different synthesis routes. As mechanical separation was not achievable either, measurements of the transport properties could not be performed.

In further investigations, we will aim to resolve the synthetic problems leading to impurity phases and study the transport properties. One of our more distant goals will be to explore the systems Cs-Na-Cd-Ge and Rb-Na-Cd-Ge. The mixed cations (large and small) can prove promising for synthesizing the hitherto unknown Cs₈Na₁₆Cd₁₂Ge₁₂₄ and Rb₈Na₁₆Cd₁₂Ge₁₂₄ type-II clathrates. We will recall that the crystal chemistry and the chemical bonding in many type-I clathrate structures are satisfactorily understood because they are more easily accessible in ternary systems. For type-II clathrates, the difficulty of synthesizing selectively new compounds remains an open challenge, which has been attributed to the fact that the cavities of the type-II clathrates have a larger difference in size. Therefore, we have speculated (and have shown experimentally on the examples of (Cs or Rb)₈Na₁₆(Si or Ge)₁₃₆ [32]) that the directed synthesis of type-II can be greatly facilitated by choosing spatially different guest atoms. This idea, combined with the proper choice of a framework-substituent, can lead to new clathrate type-II, as demonstrated by the subsequent studies on Cs₈Na₁₆Ag_6.7Ge_129.3 [33] and Cs₈Na₁₆Cu₅Ge₁₃₁ [34]. Very recently, the applicability of notion that two types of different guest atoms will be preferred for the complete and ordered filling of both cavities in the type-II compounds was confirmed for the tin-based Cs₈Ba₁₆Ga_39.7Sn_96.3 and Rb_9.9Ba_13.3Ga_36.4Sn_99.6 [35], suggesting that the Cs-Ba-Cd-Ge and Rb-Ba-Cd-Ge systems are worthy candidates for further investigations.

4. Materials and Methods

4.1. Synthesis

The syntheses were carried out by loading stoichiometric mixtures of the respective elements in suitably prepared Nb tubes, which were then sealed by arc-welding.

Due to the extremely high reactivity of the alkali metals to moisture and oxygen, all manipulations were done with great care in an argon-filled glove box. The atmosphere in the glovebox was maintained at O₂/H₂O level below 1 ppm. The elements were purchased from Alfa or Sigma-Aldrich with a stated purity higher than 99.9 wt % (metal basis). In order to carry out the reactions in a safe and reliable manner, the elements were weighed in a ratio of A:M:Ge = 8:4:42 (A = K, Rb, Cs). Total mass in each case was ca. 300 mg. After arc-welding, the Nb tubes with the reactants inside were enclosed in fused silica tubes. Under dynamic vacuum, the fused silica tubes were baked and then flame-sealed.

The samples were heated slowly in programmable muffle furnaces to 950 °C with a rate of 10 °C/h, annealed for 15 h, and then cooled down (rate −150 °C/h) to 650 °C, dwelled for 4 d, and cooled down (rate −5 °C/h) to room temperature. The obtained type-I clathrates were stable in air and moisture and were handled on the bench. Based on the powder X-ray diffraction patterns, the yields were high, estimated to be over 70–80 wt %, with some small impurity phases, yet unidentified, present in each specimen.

4.2. Powder X-ray Diffraction

X-ray powder diffraction patterns of selected crystals were carried out at room temperature on a Rigaku MiniFlex powder diffractometer using Cu-Kα radiation. The data collection scans were done in θ-θ mode (2θ_max = 65°) with a step of 0.05° and 2 s/step counting time. The data were analyzed with the JADE 6.5 software package. The intensities and the positions of the experimentally observed peaks and those calculated based on the corresponding single-crystal structures matched very well with one another.

4.3. Single-Crystal X-ray Diffraction

Single-crystal X-ray diffraction data were collected on a Bruker CCD-based diffractometer using graphite-monochromated Mo-Kα radiation (λ = 0.71073 Å). Temperature was maintained at 200(2) K. Suitable single-crystals from each compound were selected and cut to smaller dimensions (less than 0.1 mm) under mineral oil. The SMART [36] and SAINTplus [37] programs were used for the data collection, integration, and the global unit cell refinement from all data. Semi-empirical absorption correction based on equivalent reflections was applied with SADABS [38]. The structures were refined to convergence by full-matrix least-square methods on F², as implemented in SHELXTL [39]. All sites were refined with anisotropic displacement parameters.

Selected details of the data collections and structure refinement parameters are listed in Table 1. The atomic coordinates and equivalent isotropic displacement parameters are given in Table 2. The anisotropic displacement parameters are tabulated in Table 3, and selected interatomic distances are summarized in Table 4. Additional details of the crystal structure analyses may be requested from the Fachinformationszentrum Karlsruhe, D-76344 Eggenstein-Leopoldshafen (Karlsruhe, Germany) on quoting the depository numbers CSD-430998 for K₈Cd_3.77(7)Ge_42.23, CSD-430999 for Rb₈Cd_3.65(7)Ge_42.35, and CSD-431000 for Cs_7.80(1)Cd_3.65(6)Ge_42.35, respectively.

4.4. Energy-Dispersive Analysis

Multiple crystals for each composition were analyzed by means of energy dispersive X-ray spectroscopy (EDX). Data were gathered using a JEOL 7400F electron microscope equipped with an INCA-OXFORD energy-dispersive spectrometer. Only the specified elements (i.e., no unrecognized impurities) could be detected in ratios consistent with the refined compositions.

5. Conclusions

With this paper, our team presented the synthesis and the structural characterization of the type-I clathrates K₈Cd_3.77(7)Ge_42.23, Rb₈Cd_3.65(7)Ge_42.35, and Cs_7.80(1)Cd_3.65(6)Ge_42.35. In the future, we will be exploring the systems Cs-Na-Cd-Ge and Rb-Na-Cd-Ge. Based on the presented results and the overview of the current literature, we believe that using mixed cations (large and small) can yield the hitherto unknown Cs₈Na₁₆Cd₁₂Ge₁₂₄ and Rb₈Na₁₆Cd₁₂Ge₁₂₄ type-II clathrates.

Supplementary Materials

The following are available online at www.mdpi.com/1996-1944/9/4/236/s1. Structure refinement for Cs₈Cd_3.65(6)Ge_42.35, in .CIF.

Acknowledgments

Svilen Bobev acknowledges financial support from the U.S. Department of Energy, Office of Science, Basic Energy Sciences, under Award DE-SC0008885.

Author Contributions

Marion C. Schäfer and Svilen Bobev conceived and designed the experiments; Marion C. Schäfer performed the experiments; Marion C. Schäfer and Svilen Bobev analyzed the data; Svilen Bobev wrote the paper.

Conflicts of Interest

The authors declare no conflict of interest. The funding sponsors had no role in the design of the study, in the collection, analyses, or interpretation of data, in the writing of the manuscript, or in the decision to publish the results.

Abbreviations

The following abbreviations are used in this manuscript:

PGEC	Phonon-Glass Electron-Crystal
Tt	Tetrel, group 14 elements Si, Ge and Sn
A	group 1, 2 and 3 elements, which partially or fully occupy the cages within the clathrate framework
M	group 13 and 12 elements, as well as late transition metals, substituting framework atoms
☐	vacancy

References

Kasper, J.S.; Hagenmuller, P.; Pouchard, M.; Cros, C. Clathrate structure of silicon Na₈Si₄₆ and Na_xSi₁₃₆ (x < 11). Science 1965, 150, 1713–1714. [Google Scholar] [PubMed]
Slack, G.A. New materials and performance limits for thermoelectric cooling. In CRC Handbook of Thermoelectrics; Rowe, D.M., Ed.; CRC Press: Boca Raton, FL, USA, 1995; pp. 407–440. [Google Scholar]
Christensen, M.; Johnson, S.; Iversen, B.B. Thermoelectric clathrates of type-I. Dalton Trans. 2010, 39, 978–992. [Google Scholar] [CrossRef] [PubMed]
Nolas, G.S.; Cohn, J.L.; Slack, G.A.; Schjuman, S.B. Semiconducting Ge clathrates: Promising candidates for thermoelectric applications. Appl. Phys. Lett. 1998, 73, 178–180. [Google Scholar] [CrossRef]
Sales, B.C.; Chakoumakos, B.C.; Mandrus, D.; Sharp, J.W. Atomic displacement parameters and the lattice thermal conductivity of clathrate-like thermoelectric compounds. J. Solid State Chem. 1999, 146, 528–532. [Google Scholar] [CrossRef]
Bobev, S.; Sevov, S.C. Clathrates of group 14 with alkali metals: An exploration. J. Solid State Chem. 2000, 153, 92–105. [Google Scholar] [CrossRef]
Beekman, M.; Nolas, G.S. Inorganic clathrate-II materials of group 14: Synthetic routes and physical properties. J. Mater. Chem. 2008, 18, 842–851. [Google Scholar] [CrossRef]
Shevelkov, A.V.; Kovnir, K. Zintl clathrates. In Structure and Bonding; Springer: Berlin, Germany, 2011; Volume 990, pp. 97–142. [Google Scholar]
Paschen, S.; Carrillo Cabrera, W.; Bentien, A.; Tran, V.H.; Baenitz, M.; Grin, Y.; Steglich, F. Structural, transport, magnetic and thermal properties of Eu₈Ga₁₆Ge₃₀. Phys. Rev. B 2001, 64. [Google Scholar] [CrossRef]
Prokofiev, A.; Sidorenko, A.; Hradil, K.; Ikeda, M.; Svagera, R.; Waas, M.; Winkler, H.; Neumaier, K.; Paschen, S. Thermopower enhancement by encapsulating cerium in clathrate cages. Nat. Mater. 2013, 12, 1096–1101. [Google Scholar] [CrossRef] [PubMed]
Paschen, S.; Budnyk, S.; Köhler, U.; Prots, Y.; Hiebl, K.; Steglich, F.; Grin, Y. New type-I clathrates with ordered Eu distribution. Physica. B 2006, 383, 89–92. [Google Scholar] [CrossRef]
Kishimoto, K.; Sasaki, Y.; Koyanagi, T.; Ohoyama, K.; Akai, K. Crystal structure and thermoelectric properties of K_xBa_8–xZn_yGe_46–y clathrates. J. Appl. Phys. 2012, 111. [Google Scholar] [CrossRef]
Kaltzoglou, A.; Ponou, S.; Faessler, T.F. A₄Ge₉ (A = K, Rb) as precursors for Hg-substituted clathrate-I synthesis: Crystal structure of A₈Hg₃Ge₄₃. Eur. J. Inorg. Chem. 2008, 29, 4507–4510. [Google Scholar] [CrossRef]
Baran, V.; Faessler, T.F. Si-based clathrates with partial substitution by Zn and Ga: K₈Zn_3.5Si_42.5, Rb_7.9Zn_3.6Si_42.4, and Cs_8–xGa_8–ySi_38+y. Z. Anorg. Allg. Chem. 2015, 641, 1435–1443. [Google Scholar] [CrossRef]
Schäfer, M.C.; Bobev, S. Copper and zinc substitutions in clathrates of tin: Synthesis, structural characterization, and physical properties of A₈Cu_2.67Sn_43.33 and A₈Zn₄Sn₄₂ (A = K, Rb, Cs) with the type-I structure. Chem. Mater. 2013, 25, 3737–3744. [Google Scholar] [CrossRef]
Nasir, N.; Grytsiv, A.; Melnychenko-Koblyuk, N.; Rogl, P.; Bauer, E.; Lackner, R.; Royanian, E.; Giester, G.; Saccone, A. Clathrates Ba₈{Zn,Cd}_xSi_46–x, x~7: Synthesis, crystal structure and thermoelectric properties. J. Phys. 2009, 21, 385404. [Google Scholar] [CrossRef] [PubMed]
Kauzlarich, S.M. Chemistry, Structure, and Bonding of Zintl. Phases and Ions; VCH: New York, NY, USA, 1996. [Google Scholar]
Melnychenko-Koblyuk, N.; Grytsiv, A.; Fornasari, L.; Kaldarar, H.; Michor, H.; Roehrbacher, F.; Koza, M.; Royanian, E.; Bauer, E.; Rogl, P.; et al. Ternary clathrates Ba–Zn–Ge: Phase equilibria, crystal chemistry and physical properties. J. Phys. Condens. Matter. 2007, 19, 216223. [Google Scholar] [CrossRef]
Melnychenko-Koblyuk, N.; Grytsiv, A.; Berger, S.T.; Kaldarar, H.; Michor, H.; Roehrbacher, F.; Royanian, E.; Bauer, E.; Rogl, P.; Schmid, H.; et al. Ternary clathrates Ba-Cd-Ge: Phase equilibria, crystal chemistry and physical properties. J. Phys. Condens. Matter. 2007, 19, 046203. [Google Scholar] [CrossRef]
Schäfer, M.C.; Bobev, S. K and Ba distribution in the structures of the clathrate compounds K_xBa_16−x(Ga,Sn)₁₃₆ (x = 0.8, 4.4, and 12.9) and K_xBa_8−x(Ga,Sn)₄₆ (x = 0.3). Acta. Cryst. 2013, C69, 319–323. [Google Scholar] [CrossRef] [PubMed]
Schäfer, M.C.; Yamasaki, Y.; Fritsch, V.; Bobev, S. Ternary compounds in the Sn-rich section of the Ba-Ga-Sn system: Ba₈Ga_16–xSn_30+x (1.1 ≤ x ≤ 2.8) clathrates of type-I and type-VIII, and BaGa_2–xSn_4+x (x ≈ 0.2) with a clathrate-like structure. Crystals 2011, 1, 145–162. [Google Scholar] [CrossRef]
Von Schnering, H.-G.; Carillo-Cabrera, W.; Kröner, R.; Peters, E.-M.; Peters, K. Crystal structure of the clathrate β-Ba₈Ga₁₆Sn₃₀. Z. Kristallogr. New Cryst. Struct. 1998, 213, 679. [Google Scholar]
Chakoumakos, B.C.; Sales, B.C.; Mandrus, D.; Nolas, G.S. Structural disorder and thermal conductivity of the semiconducting clathrate Sr₈Ga₁₆Ge₃₀. J. Alloys Compd. 2000, 296, 80–86. [Google Scholar] [CrossRef]
Chakoumakos, B.C.; Sales, B.C.; Mandrus, D. Structural disorder and magnetism of the semiconducting clathrate Eu₈Ga₁₆Ge₃₀. J. Alloys Compd. 2001, 322, 127–134. [Google Scholar] [CrossRef]
Nolas, G.S.; Weakley, T.J.R.; Cohn, J.L.; Sharma, R. Structural properties and thermal conductivity of crystalline Ge clathrates. Phys. Rev. B 2000, 61, 3845–3850. [Google Scholar] [CrossRef]
Pauling, L. The Nature of the Chemical Bonding, 3rd ed.; Cornell University Press: Ithaca, NY, USA, 1960; p. 403. [Google Scholar]
Von Schnering, H.-G.; Llanos, J.; Peters, K.; Baitinger, M.; Grin, Y.; Nesper, R. Refinement of the crystal structure of K₈Ge₄₄☐₂, an intermetallic clathrate I. Z. Kristallogr. New Cryst. Struct. 2011, 226, 9–10. [Google Scholar]
Veremchuk, I.; Wosylus, A.; Boehme, B.; Baitinger, M.; Borrmann, H.; Prots, Yu.; Burkhardt, U.; Schwarz, U.; Grin, Y. Preparation and crystal structure of the clathrate-I Cs_8–xGe_44+y☐_2–y. Z. Anorg. Allg. Chem. 2011, 637, 1281–1286. [Google Scholar] [CrossRef]
Von Schnering, H.-G.; Menke, H.; Kroener, R.; Peters, E.M.; Peters, K.; Nesper, R. Crystal structure of the clathrates Rb₈In₈Ge₃₈ and K₈In₈Ge₃₈. Z. Kristallogr. New Cryst. Struct. 1998, 213, 673–674. [Google Scholar]
Menke, H.; Carrillo Cabrera, W.; Peters, K.; Peters, E.M.; von Schnering, H.-G. Crystal structure of the clathrate Cs₈In₈Ge₃₈. Z. Kristallogr. New Cryst. Struct. 1999, 214, 14. [Google Scholar] [CrossRef]
Schäfer, M.C.; Bobev, S. New type-I and type-II clathrates in the systems Cs–Na–Ga–Si, Rb–Na–Ga–Si, and Rb–Na–Zn–Si. Inorganics 2014, 2, 79–95. [Google Scholar] [CrossRef]
Bobev, S.; Sevov, S.C. Synthesis and characterization of stable stoichiometric clathrates of silicon and germanium: Cs₈Na₁₆Si₁₃₆ and Cs₈Na₁₆Ge₁₃₆. J. Am. Chem. Soc. 1999, 121, 3795–3796. [Google Scholar] [CrossRef]
Beekman, M.; Wong-Ng, W.; Kaduk, J.A.; Shapiro, A.; Nolas, G.S. Synthesis and single-crystal X-ray diffraction studies of new framework substituted type II clathrates, Cs₈Na₁₆Ag_xGe_136−x (x < 7). J. Solid State Chem. 2007, 180, 1076–1082. [Google Scholar]
Beekman, M.; Kaduk, J.A.; Gryko, J.; Wong-Ng, W.; Shapiro, A.; Nolas, G.S. Synthesis and characterization of framework-substituted Cs₈Na₁₆Cu₅Ge₁₃₁. J. Alloys Compd. 2009, 470, 365–368. [Google Scholar] [CrossRef]
Schäfer, M.C.; Bobev, S. Novel tin clathrates with the type-II structure. J. Am. Chem. Soc. 1999, 121, 3795–3796. [Google Scholar]
SMART NT, version 5.63. Bruker Analytical X-ray Systems Inc.: Madison, WI, USA, 2003.
SAINT NT, version 6.45. Bruker Analytical X-ray Systems Inc.: Madison, WI, USA, 2003.
SADABS NT, version 2.10. Bruker Analytical X-ray Systems Inc.: Madison, WI, USA, 2001.
SHELXTL, version 6.12. Bruker Analytical X-ray Systems Inc.: Madison, WI, USA, 2001.

Figure 1. Schematic view of the clathrate with type-I structure. For the drawing, the structural information for Cs_7.80(1)Cd_3.65(6)Ge_42.35 was used and the atoms are labeled accordingly.

Figure 2. Representative fragment of the K₈Cd_3.77(7)Ge_42.23 structure, drawn with thermal ellipsoids at the 98% probability level. U_eq (as one third of the trace of the orthogonalized U_ij tensor) for K1 is more than twice that of K2, hinting at small vibrations about the equilibrium position.

Table 1. Selected crystal data and structure refinement parameters for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).

**Table 1.** Selected crystal data and structure refinement parameters for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).
Compound	1	2	3
Fw/g·mol⁻¹	3803.2	4170.2	4519.1
Crystal system	Cubic
Space group	Pm $\bar{3} n$ (No. 223), Z = 1
a/Å	10.8710(4)	10.9099(5)	10.9643(7)
V/Å³	1284.72(8)	1298.56(10)	1318.08(15)
T/K	200(2)
Radiation	Mo Kα, λ = 0.71073 Å
ρ/g·cm⁻³	4.92	5.33	5.69
μ/cm⁻¹	264.3	329.7	304.7
data/restraints/parameters	291/0/17	318/0/17	327/0/18
R₁ (I >2σ(I)) ^a	0.0182	0.0178	0.0138
wR₂ (I >2σ(I)) ^a	0.0359	0.0365	0.0298
R₁ (all data) ^a	0.0241	0.0232	0.0180
wR₂ (all data) ^a	0.0378	0.0386	0.0314
GOF	1.156	1.064	1.116
largest peak & hole/e⁻·Å⁻³	0.54 & −0.57	0.62 & −0.85	0.63 & −0.56

^a R₁ = ∑||F_o| – |F_c||/∑|F_o|; wR₂ = [∑[w(F_o² – F_c²)²]/∑[w(F_o²)²]]^1/2, where w = 1/[σ²F_o² + (A·P)² + (B·P)], and P = (F_o² + 2F_c²)/3, A and B weight coefficients.

Table 2. Atomic coordinates and equivalent isotropic displacement parameters (U_eq/Å²) for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).

**Table 2.** Atomic coordinates and equivalent isotropic displacement parameters (U_eq/Å²) for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).
Atom	Site	x/a	y/b	z/c	Occupancy	U_eq ^a
K₈Cd_3.77(7)Ge_42.23
K1	6d	0	¹/₄	¹/₂	100%	0.0358(7)
K2	2a	0	0	0	100%	0.0175(9)
Ge1	24k	0	0.30355(5)	0.11589(5)	100%	0.0129(2)
Ge2	16i	0.18327(4)	x	x	100%	0.0119(2)
Ge/Cd3	6c	¹/₄	0	¹/₂	37(1)/63(1)%	0.0137(3)
Rb₈Cd_3.65(7)Ge_42.35
Rb1	6d	0	¹/₄	¹/₂	100%	0.0254(3)
Rb2	2a	0	0	0	100%	0.0124(3)
Ge1	24k	0	0.30365(5)	0.11637(5)	100%	0.0123(2)
Ge2	16i	0.18356(3)	x	x	100%	0.0114(2)
Ge/Cd3	6c	¹/₄	0	¹/₂	39(1)/61(1)%	0.0127(3)
Cs_7.80(1)Cd_3.65(6)Ge_42.35
Cs1	6d	0	¹/₄	¹/₂	100%	0.0204(2)
Cs2	2a	0	0	0	89.8(4)%	0.0117(3)
Ge1	24k	0	0.30334(4)	0.11719(4)	100%	0.0123(1)
Ge2	16i	0.18370 (3)	x	x	100%	0.0116(2)
Ge/Cd3	6c	¹/₄	0	¹/₂	39(1)/61(1)%	0.0136(3)

^a U_eq is defined as one third of the trace of the orthogonalized U_ij tensor.

Table 3. Anisotropic displacement parameters (U_ij/Å²) for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).

**Table 3.** Anisotropic displacement parameters (U_ij/Å²) for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).
Atom	U₁₁	U₂₂	U₃₃	U₂₃	U₁₃	U₁₂
K₈Cd_3.77(7)Ge_42.23
K1	0.038(1)	0.032(2)	=U₁₁	0	0	0
K2	0.0175(9)	=U₁₁	=U₁₁	0	0	0
Ge1	0.0121(3)	0.0137(3)	0.0130(3)	0.0000(2)	0	0
Ge2	0.0119(2)	=U₁₁	=U₁₁	−0.0006(1)	=U₂₃	=U₂₃
Ge/Cd3	0.0157(5)	0.0127(4)	=U₂₂	0	0	0
Rb₈Cd_3.65(7)Ge_42.35
Rb1	0.0278(4)	0.0205(6)	=U₁₁	0	0	0
Rb2	0.0124(3)	=U₁₁	=U₁₁	0	0	0
Ge1	0.0119(3)	0.0127(3)	0.0124(3)	0.0003(2)	0	0
Ge2	0.0114(2)	=U₁₁	=U₁₁	−0.0005(1)	=U₂₃	=U₂₃
Ge/Cd3	0.0144(5)	0.0119 (3)	=U₂₂	0	0	0
Cs_7.80(1)Cd_3.65(6)Ge_42.35
Cs1	0.0226(2)	0.0159(3)	=U₁₁	0	0	0
Cs2	0.0117(3)	=U₁₁	=U₁₁	0	0	0
Ge1	0.0115(2)	0.0122(3)	0.0132(3)	0.0003(2)	0	0
Ge2	0.0116(2)	=U₁₁	=U₁₁	−0.0002(1)	=U₂₃	=U₂₃
Ge/Cd3	0.0158(4)	0.0125(3)	=U₂₂	0	0	0

Table 4. Selected interatomic distances for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).

**Table 4.** Selected interatomic distances for K₈Cd_3.77(7)Ge_42.23 (1), Rb₈Cd_3.65(7)Ge_42.35 (2), and Cs_7.80(1)Cd_3.65(6)Ge_42.35 (3).
Compound 1	d/Å	Compound 2	d/Å	Compound 3	d/Å
Ge1-Ge2 (2×)	2.4931(4)	Ge1-Ge2 (2×)	2.5029(4)	Ge1-Ge2 (2×)	2.5118(4)
Ge1-Ge1	2.520(1)	Ge1-Ge1	2.539(1)	Ge1-Ge1	2.570(1)
Ge1-Ge/Cd3	2.5858(6)	Ge1-Ge/Cd3	2.5912(5)	Ge1-Ge/Cd3	2.6019(5)
Ge2-Ge2	2.513(1)	Ge2-Ge2	2.511(1)	Ge2-Ge2	2.518(1)
Ge2-Ge1 (3×)	2.4931(4)	Ge2-Ge1 (3×)	2.5029(4)	Ge2-Ge1 (3×)	2.5118(4)
Ge/Cd3-Ge1 (4×)	2.5858(6)	Ge/Cd3-Ge1 (4×)	2.5912(5)	Ge/Cd3-Ge1 (4×)	2.6019(5)
K1-Ge1 (8×)	3.6789(4)	Rb1-Ge1 (8×)	3.6932(4)	Cs1-Ge1 (8×)	3.7167(4)
K1-Ge2 (8×)	4.0438(3)	Rb1-Ge2 (8×)	4.0564(3)	Cs1-Ge2 (8×)	4.0758(3)
K1-Ge/Cd3 (4×)	3.8435(2)	Rb1-Ge/Cd3 (4×)	3.8572(2)	Cs1-Ge/Cd3 (4×)	3.8765(2)
K1-Ge1 (4×)	4.2157(6)	Rb1-Ge1 (4×)	4.2262(5)	Cs1-Ge1 (4×)	4.2378(5)
K2-Ge2 (8×)	3.4507(7)	Rb2-Ge2 (8×)	3.4686(6)	Cs2-Ge2 (8×)	3.4885(6)
K2-Ge1 (12×)	3.5322(6)	Rb2-Ge1 (12×)	3.5477(5)	Cs2-Ge1 (12×)	3.5654(5)

© 2016 by the authors; licensee MDPI, Basel, Switzerland. This article is an open access article distributed under the terms and conditions of the Creative Commons by Attribution (CC-BY) license (http://creativecommons.org/licenses/by/4.0/).

Share and Cite

MDPI and ACS Style

Schäfer, M.C.; Bobev, S. Synthesis and Structural Characterization of the New Clathrates K₈Cd₄Ge₄₂, Rb₈Cd₄Ge₄₂, and Cs₈Cd₄Ge₄₂. Materials 2016, 9, 236. https://doi.org/10.3390/ma9040236

AMA Style

Schäfer MC, Bobev S. Synthesis and Structural Characterization of the New Clathrates K₈Cd₄Ge₄₂, Rb₈Cd₄Ge₄₂, and Cs₈Cd₄Ge₄₂. Materials. 2016; 9(4):236. https://doi.org/10.3390/ma9040236

Chicago/Turabian Style

Schäfer, Marion C., and Svilen Bobev. 2016. "Synthesis and Structural Characterization of the New Clathrates K₈Cd₄Ge₄₂, Rb₈Cd₄Ge₄₂, and Cs₈Cd₄Ge₄₂" Materials 9, no. 4: 236. https://doi.org/10.3390/ma9040236

APA Style

Schäfer, M. C., & Bobev, S. (2016). Synthesis and Structural Characterization of the New Clathrates K₈Cd₄Ge₄₂, Rb₈Cd₄Ge₄₂, and Cs₈Cd₄Ge₄₂. Materials, 9(4), 236. https://doi.org/10.3390/ma9040236

Note that from the first issue of 2016, this journal uses article numbers instead of page numbers. See further details here.

Article Menu