BORON-STABILIZED TYPE-I AND TYPE-II CARBON CLATHRATES

Abstract

The present invention provides type-I and II carbon-based clathrate compounds stabilized by boron, including a boron-substituted, carbon-based framework with guest atoms encapsulated within the clathrate lattice. In one embodiment, the invention provides a carbon-based type-I clathrate compound of the formula Ca.sub.8B.sub.xC.sub.46-x.

Claims

1. A carbon-based clathrate compound of the formula Ca.sub.8B.sub.xC.sub.46-x having a clathrate lattice structure.

2. The carbon-based clathrate compound of claim 1, wherein the clathrate lattice structure comprises two small [5.sup.12]-type (pentagonal dodecahedra) cages and six large [5.sup.126.sup.2]-type (tetradecahedra) cages.

3. The carbon-based clathrate compound of claim 1 further comprising a covalent carbon clathrate lattice in which B substitution serves to stabilize the clathrate lattice structure.

4. The carbon-based clathrate compound of claim 2, wherein the clathrate lattice structure is formed of sp.sup.3 hybridized carbon and boron.

5. The carbon-based clathrate compound of claim 3, wherein Ca is a guest atom encapsulated within the clathrate lattice structure.

6. The carbon-based clathrate compound of claim 2 wherein the carbon-based clathrate compound is formulated to yield a bulk modulus of 2448 GPa.

7. The carbon-based clathrate compound of claim 2 wherein the carbon-based clathrate compound is formulated to yield a hardness of 31-39 GPa.

8. The carbon-based clathrate compound of claim 1 wherein at least one of the Ca atoms is replaced with a guest atom chosen from a group of guest atoms comprising strontium, lanthanum, and sodium.

9. The carbon-based clathrate compound of claim 8 wherein the group of guest atoms includes atoms having an atomic radius comparable to that of calcium.

10. A carbon-based clathrate compound of the formula M.sub.24B.sub.xC.sub.136-x having a clathrate lattice structure wherein M is a metallic element and wherein the clathrate lattice structure comprises sixteen small [5.sup.12]-type (pentagonal dodecahedra) cages and eight large [5.sup.126.sup.4]-type (hexadecahedra) cages.

11. The carbon-based clathrate compound of claim 10 wherein at least one of the Ca atoms is replaced with a guest atom chosen from a group of guest atoms comprising strontium, lanthanum, and sodium.

12. The carbon-based clathrate compound of claim 11 wherein the group of guest atoms includes atoms having an atomic radius comparable to that of calcium.

13. The carbon-based clathrate compound of claim 12 having the formula Ca.sub.6B.sub.12C.sub.22.

14. A carbon-based clathrate compound having a clathrate lattice structure wherein the clathrate lattice structure includes carbon, boron, and at least one guest atom, wherein the clathrate lattice structure includes boron site occupation and the guest atom is chosen from a group of elements comprising sodium, strontium, and calcium.

15. The carbon-based clathrate compound of claim 14 having the formula Na.sub.8B.sub.8Ca.sub.8.

16. The carbon-based clathrate compound of claim 14 having the formula Sr.sub.8B.sub.16C.sub.30.

17. The carbon-based clathrate compound of claim 14 having the formula Ca.sub.8B.sub.16C.sub.30.

18. The carbon-based clathrate compound of claim 14 having the formula Ca.sub.6B.sub.12C.sub.22.

19. The carbon-based clathrate compound of claim 14 having the unit cell formula Ca.sub.24B.sub.48C.sub.88.

20. The carbon-based clathrate compound of claim 12 having the unit cell formula Ca.sub.24B.sub.48C.sub.88.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0022] The patent or application file contains at least one drawing executed in color. Copies of this patent or patent application publication with color drawing(s) will be provided by the Office upon request and payment of the necessary fee.

[0023] The invention is more fully described by reference to the following detailed description and the accompanying drawings wherein:

[0024] FIG. 1(a) shows the basic type-I clathrate structure.

[0025] FIG. 1(b) shows the basic type-II clathrate structure.

[0026] FIGS. 2(a), 2(b), 2(c), 2(d), 2(e), and 2(f) show stability trends for type-I and type-II clathrates.

[0027] FIGS. 3(a), 3(b), 3(c), 3(d), 3(e), 3(f), 3(g) and 3(h) show analyses of stability for various compositions and structures of type-I and type-II clathrates.

[0028] FIGS. 4(a), 4(b), and 4(c) show ternary phase diagrams for the Na, Ca and Sr systems, showing low-energy and stable clathrate phases.

[0029] FIG. 5 shows a molecular dynamics trajectory for Ca.sub.8B.sub.16C.sub.30 at 0 GPa and 300 K showing dynamic stability.

[0030] FIGS. 6(a), 6(b), 6(c) show the crystal structure of stable R3 Ca.sub.8B.sub.16C.sub.30 at 50 GPa and electronic density of states.

[0031] FIGS. 7(a), 7(b), and 7(c) show the experimental structure for type-1 Ca.sub.8B.sub.xC.sub.46-x.

[0032] FIGS. 8(a), 8(b), and 8(c) show the XRD refinement for recovered Ca.sub.8B.sub.xC.sub.46-x and ideal strength.

[0033] FIG. 9(a) and 9(b) show unit-cell volume vs. pressure and bulk modulus vs. the pressure derivative for type-I Ca.sub.8B.sub.xC.sub.46-x and type-VII CaB.sub.3C.sub.3.

[0034] FIG. 10 shows phonon dispersion relations for type-I Ca.sub.8C.sub.46 at 50 GPa.

[0035] FIG. 11 shows experimental and calculated unit cell volumes as a function of pressure for type-I Ca.sub.8B.sub.xC.sub.46-x and for (La/Ca).sub.8B.sub.xC.sub.46-x.

DETAILED DESCRIPTION OF THE INVENTION

[0036] Carbon clathrate is an impressive 3D sp.sup.3 material. Carbon-based clathrates are open-framework structures composed of host cages that trap guest atoms in which all host atoms are linked by four-coordinate bonds. As sp.sup.3-bonded frameworks, carbon-based clathrates represent strong and lightweight materials that also offer tunable properties through manipulation of the occupancy and type of guest atoms within the cages. Despite their prominence in other systems with tetrahedral coordination, carbon-based clathrates have not yet been reported due to tremendous challenges associated with their synthesis.

[0037] Attempts to synthesize carbon clathrates go back at least 50 years since they were postulated following the formation of inorganic silicon clathrates, and their possible structures and properties are of longstanding interest. However, carbon clathrates have not been successively synthesized yet. Some proposed but unrealized carbon clathrates are expected to exhibit exceptional mechanical properties with tensile and shear strengths exceeding diamond, while large electron-phonon coupling is predicted to give rise to conventional superconductivity with high transition temperatures. If produced, these materials may represent a class of diamond-like compounds wherein the electronic structure is tunable by adjusting the occupancy of electron-donating (or withdrawing) atoms within the cages.

[0038] The inventors have performed a substantial amount of research to answer the persisting question of whether carbon clathrate structures are accessible by experiment. First-principles DFT calculations indicate that both filled and guest-free carbon clathrates are energetically unfavorable but by energies as low as 0.07 eV/atom relative to diamond (for reference, commercially produced C.sub.60 is metastable by nearly six times that energy). Synthesis of carbon clathrates might therefore proceed through a non-equilibrium pathway (e.g., formation from a high-energy precursor or deposition method) or through a chemical substitution/doping strategy to modify the intrinsic thermodynamic stability. No successful metastable pathways to carbon clathrates have been established yet, although three-dimensional polymers of C.sub.60 have been suggested to resemble carbon clathrate-like structures.

[0039] While non-equilibrium synthesis pathways remain feasible in concept, another strategy is to substitute boron for carbon atoms within the cage frameworks of carbon clathrates. The electron deficient nature of boron creates the ability to form complex chemical bonding with itself or carbon to stabilize polyhedra, such as the icosahedral units in molecular carborane clusters.

[0040] Zeng et al. calculated that boron substitution can improve the intrinsic thermodynamic stability of carbon clathrate frameworks. Nevertheless, no thermodynamically stable carbon-clathrate was predicted after examination of a small subset of possible B substitution schemes in Li-filled carbon clathrates. A comprehensive understanding of potential B substitution schemes was therefore needed to validate this chemical stabilization principle.

[0041] The inventors performed extensive stabilization calculations considering alkali and alkaline earth metals trapped within either the large cages, or both the large and small cages, of type-I and type-II carbon clathrates (See FIG. 1(a) and FIG. 1(b)), and assumed boron substitution schemes that result in overall charge balance (i.e., only insulators). For example, a monovalent guest occupying only the large cages of type-I clathrate would require six boron atoms in the unit cell for charge balance, i.e., a composition of M.sub.6B.sub.6C.sub.40. The number of possible decorations of n carbon sites with nB boron atoms, P(n/nB) is given by the equation:

[00001]$P\left(n-\mathrm{nB}\right)=(\mathrm{nB}!/\left(n-\mathrm{nB}\right)!$

[0042] For the case of type-I clathrate with six boron atoms and 46 framework atoms per formula unit, there are 9,366,819 possible decorations, which is computationally intractable for calculations based on DFT. Similar difficulties arose for most of the boron counts considered for both the type-I and type-II clathrates. To reduce the number of structural combinations, all structures that contain B-B contacts were removed from consideration. This is analogous to the Al-avoidance rule in silicates and aluminates. Such structures are assumed to be electrostatically unfavorable due to formal charges of boron. To further reduce computational complexity in systems with large numbers of unique combinations, we discarded all structures with P-1 space group symmetry (those with only translational symmetry). The resulting boron decoration schemes were enumerated using a brute-force symmetry-based (BFSB) method and a branch-and-bound algorithm. The resulting list of decorations was cross validated by systematically comparing the output from the two methods.

[0043] Table 1 contains a summary of the enumeration results for the cases considered, each of which was calculated using guest atoms of group-I (Li-Cs) and group-II (Mg-Ba) elements at two pressures (10 and 50 GPa). Structures containing Be were not considered due to the small size of the ion and its tendency to form covalent bonds. Approximately 46,000 different DFT calculations were performed to determine detailed stability trends for boron-substituted type-I and type-II clathrates.

TABLE-US-00001 TABLE 1 The number of possible boron-substitution combinations for different clathrate scenarios, unique combinations without duplicates or B-B contacts, and unique combinations without P-1 structures for each composition. Guest, Type B:C Cages n.sub.total n.sub.unique, noB-B n.sub.Non-P 1, noB-B I 6:40 Group I, 9,366,819 42,406 903 [5.sup.126.sup.2] I 8:38 Group I, 260,932,815 262,612 2,071 [5.sup.126.sup.2] + [5.sup.12] I 12:34 Group II, 38,910,617,655 218,179 1,513 [5.sup.126.sup.2] I 16:30 Group II, 991,493,848,554 128 26 [5.sup.126.sup.2] + [5.sup.12] II 2:32 Group I, 561 21 17 [5.sup.126.sup.4] II 4:30 Group I, 46,376 492 123 [5.sup.126.sup.4] + [5.sup.12] II 6:28 Group II, 1,344,904 3,201 310 [5.sup.126.sup.4] II 12:22 Group II, 548,354,040 7 6 [5.sup.126.sup.4] + [5.sup.12]

[0044] FIGS. 2(a) and 2(b) show the enthalpies of formation (H.sub.F=H(M.sub.xB.sub.yC.sub.z)-xH(M)-yH(B)-zH(C), where H represents the enthalpy of each element or compound) as a function of pressure for the type-I and clathrate cases, respectively. Structures containing Rb and Cs as guest elements are excluded from these plots due to their large formation enthalpies, as discussed in detail below. Individual data points for a given composition and pressure form band-like features with a range of formation enthalpies that span roughly 50-150 meV/atom. Comparing the bands of constant composition at two pressures reveals that the structures are generally stabilized as pressure increases from 10 to 50 GPa for both type-I and clathrates. Several of the compositions show negative formation enthalpies for both type-I and type-II clathrates, with particularly large exothermic driving forces relative to mixtures of the ground-state elemental structures at 50 GPa. Increased stability with pressure is consistent with other sp.sup.3 structures including diamond and type-VII C-B clathrates. Both cases with Li in the large cages, and Mg in the large cages for type-II clathrate, are an exception to this trend and are destabilized with increased pressure. The small sizes of Li and Mg cations may not be sufficient to stabilize clathrates at high pressure when only the large cages occupied, and these phases become destabilized with increased compression. Given the overall general trend of enhanced stability with increasing pressure, Applicants focus the disclosure herein on the results obtained at 50 GPa.

[0045] The large number of optimized structures allows for the investigation of possible stability trends with structural symmetry, as shown in FIGS. 2(c) and 2(d). As the symmetry index increases, the symmetry of the decorated phase decreases. For all cases, there is no apparent correlation with symmetry index and formation enthalpy, although in cases where all decorations were examined explicitly, no structures with P-1 symmetry were found as the ground state. While we cannot explicitly rule out the possibility of cases with a P-1 ground state for other clathrate compositions, the assumption of non-P-1 ground states appears justified for the most stable compositions and P-1 structures were not considered for those cases during subsequent analysis.

[0046] As shown in FIGS. 2(e) and 2(f), the formation enthalpies of the various clathrate structures show a strong dependence on the Shannon crystal radii of the metal guest elements. All structures containing K, Rb, Cs, and Ba exhibit positive formation enthalpies which we attribute to their atomic radii being too large for the cages. Clathrates with small ions like Li and Mg may exhibit negative formation enthalpies depending on the specific occupancy configuration, but may be generally too small for ideal clathrate stability. The most stable guest ions are those with intermediate sizes including Na, Ca, and Sr, which appear to best suited to stabilize the boron-substituted clathrate cages, as confirmed by their negative enthalpies of formation. Structures with Li, Na, Mg, and Ca as guest atoms show a general preference for both large and small cages to be filled compared with structures where only the large cages are filled. This trend is not observed for structures with K, Rb, Cs, and Ba, likely due to the energy penalty associated with occupying these larger ions within the small [5.sup.12] cages.

[0047] The large number of optimized clathrate structures with different boron decorations allows for the examination of stability trends for different coloring schemes and to determine the impact of substitutions on specific framework sites. In general, no clear stability trends were observed regarding nearest-neighbor CC, BC or guest-B/C distances, however structures with expanded large [5.sup.1262]/[5.sup.126.sup.4] cages and contacted small [5.sup.12] cages were found to generally exhibit lower enthalpies for both clathrate structure types of a given composition.

[0048] These overall trends are a consequence of the tendency of boron to substitute framework positions within the six-membered rings of the large cages in order to minimize bond angle strain, as shown below.

[0049] Continuing with the most stable guest elements for type-I and type-II clathrates, the enthalpies of structures containing Na and Ca are plotted as a function of the average [5.sup.12] cage radius (average distance between cage centers and vertices) in FIG. 3. Overall, structures with smaller [5.sup.12] cages tend to exhibit lower enthalpies, as do structures with larger [5.sup.1262]/[5.sup.126.sup.4] cages. The specific framework locations of B atoms impact the size of the cages for different colorings because the averaged B-C bond distances (which range from 1.54-1.80 A) are longer than the averaged CC bond distances (1.51-1.69 ), leading to larger cage sizes when more B atoms are positioned on cage vertices.

[0050] For both type-I and type-II clathrates, the energetic favorability of structures with smaller [512] cages is a consequence of preferential boron occupation of framework sites within large cages. This energetic preference is observed through inspection of B occupation on the three specific Wyckoff sites for type-I (6c, 16i, 24k) and type-II (8b, 32e, 96g) clathrates. Note that B-decorated structures possess lower symmetry and different specific Wyckoff sites compared with the undecorated frameworks. For clarity, we refer to the original sites from which substituted positions originate in the parent structures.

[0051] The overall trend of calculated enthalpy as a function of average [5.sup.12] cage radius is divided into layers that correspond to the number of B atoms on specific Wyckoff sites, as illustrated in FIG. 3, where different colors represent the number of B atoms on the 6c and 96g sites for type-I and type-II clathrates, respectively. For type-I clathrates, the symbol sizes are proportional to the number of B atoms located in the hexagonal rings of the [5.sup.126.sup.2] cages.

[0052] The hexagonal rings in type-I clathrate are comprised of both 6c and 24k sites. In contrast, for type-II clathrates, all symbols with the same colors are the same size since the number of B atoms located in the hexagonal rings of the [5.sup.126.sup.4] cages is equivalent to the number of B atoms occupying the 96g sites (hexagonal rings in type-II are exclusively comprised of 96g sites). The single-colored layers observed for type-II clathrate structures are further separated into additional clusters with the same colors for type-I clathrate structures (the same number of B atoms per 6c site). Points within a given cluster have an identical number of B atoms occupied on the other Wyckoff positions, and lower-enthalpy clusters possess more boron atoms per hexagonal ring (larger symbols). These clusters are not present for type-II clathrate structures as the six-membered rings of the [5.sup.126.sup.4] cages are comprised of a single Wyckoff site.

[0053] For monovalent guest atoms in type-I clathrate with exclusive large cage occupation, six boron atoms must be distributed on the framework to preserve charge balance, e.g., Na.sub.6B.sub.6C.sub.4o in FIG. 3(a). The most stable configuration in this case is complete occupation of the 6c site with no change from the starting Pm3.sup. n crystal symmetry. The 6c atoms are located exclusively in the six-membered rings of the large cages, resulting in a structure with the smallest average [5.sup.12] cage radius. When the small cages are also occupied, two additional B atoms must be substituted into the framework, e.g., Na.sub.8B.sub.8C.sub.38 in FIG. 3(b). In this case, the most stable configurations contain partial B occupation of the 6c site (e.g., three of six positions), increased B occupation of the 24k site, and a reduction in unit cell symmetry. Increased B occupation of the 24k site results in the expansion of both cages as this site is shared between [5.sup.12] and [5.sup.126.sup.2] cages. The increased B occupation of 24k is the origin of the trend of decreasing energy with increasing [5.sup.12] cage radius for layers of constant boron occupancy on the 6c sites, which is paradoxical to the overall trend of increasing energy with average [5.sup.12] cage radius.

[0054] Cases with monovalent guest occupancy in type-II clathrates, e.g., FIGS. 3(c) and 3(d), show the same general trend of increasing energy with average [5.sup.12] cage radius. Type-II structures exhibit an energetic preference for boron occupancy on the 96g sites, which exclusively comprise the six-membered rings of the [5.sup.126.sup.4] cages. The 96g sites are shared vertices between [5.sup.12] and [5.sup.126.sup.4] cage types, and the most stable type-II clathrates therefore generally possess larger small cages than type-I clathrates. The different connectivity and ratios of shared vertices between large and small cages of type-I and type-II clathrates result in opposite enthalpy trends within layers of constant 6c/96g boron occupancies with respect to average [5.sup.12] cage radii.

[0055] Cases with divalent guests in both clathrate types, e.g., Ca in FIGS. 3(e) through 3(h), generally show similar trends to cases with monovalent guests, although fewer unique structures are possible for type-II with both cages occupied. Divalent guests require double the amount of boron needed for overall charge balance, and thus specific site occupancy trends differ from the monovalent cases. Both cage occupancy cases for type-I require more than six boron atoms and therefore mixed occupation of the hexagonal-ring 24k and 6c sites provides the most energetically stable structures, while occupation of 16i remains unfavorable. Similarly, occupation of the hexagonal rings on the 96g site remains most favorable for type-II clathrate. The exception to this trend is the occupancy of both cages in type-II, e.g., Ca.sub.6B.sub.12C.sub.22 in FIG. 3(h), where the most stable structure of this limited data set shows partial occupancy on the 32e sites. Occupation of the 32e site appears to reduce the overall cell volume in cases with high boron content and reduces enthalpy from the PV contribution.

[0056] As shown in FIG. 2, several type-I and type-II clathrate structures with various guest atoms show negative formation enthalpies, indicating that a range of structures/compositions may be synthesizable. Given the favorable formation enthalpies calculated for the NaBC, CaBC, and SrBC clathrates, we constructed three-dimensional convex hull plots for these systems at 50 GPa, as depicted in FIGS. 4a-4(c). FIG. 4(a) shows the NaBC system, where the binary compounds Na.sub.2C.sub.2 and NaB.sub.3 are thermodynamically stable. Type-I Na.sub.8B.sub.8C.sub.38 clathrate with both cages occupied is found to be metastable and is located 104.5 meV/atom above the convex hull. Although the lowest-energy, sodium-filled type-II clathrate structure exhibits a negative formation enthalpy, it is 185.1 meV/atom above the convex hull.

[0057] For the CaBC system in FIG. 4(b), Ca.sub.2C, Ca.sub.3C.sub.2, CaC.sub.2, CaB, Ca.sub.2B.sub.5, and CaB.sub.6 were determined to be thermodynamically stable binary phases. In addition, type-I Ca.sub.8B.sub.16C.sub.30 clathrate with both cages occupied was found to be a thermodynamically stable ternary phase located on the convex hull. This structure has the space group R3, and its detailed structural and electronic properties are discussed below. Type-VII CaB.sub.3C.sub.3, the analogue of SrB.sub.3C.sub.3 that was experimentally synthesized, was found to be slightly above the convex hull by 25.8 meV/atom at 50 GPa. In addition, hexagonal CaBC (LiBC structure type) was found to be thermodynamically stable at 50 GPa. For Ca-filled type-II clathrate with both cages filled the formation enthalpy is also negative, however this phase is metastable and located 100.1 meV/atom above the convex hull.

[0058] At 50 GPa, the SrBC system shown in FIG. 4(c) contains Sr.sub.2C.sub.5, SrC.sub.2, SrC, Sr.sub.5C.sub.2, SrB, SrB.sub.2, SrB.sub.4 and SrB.sub.6 as thermodynamically stable binary phases, as well as the known ternary phases SrB.sub.3C.sub.3 and SrBC. Type-I Sr.sub.8B.sub.16C.sub.30 clathrate, the Sr analogue of stable Ca.sub.8B.sub.16C.sub.30, is metastable but is located only 49.5 meV/atom above the hull, making it within the synthesizable energy range of metastable phases. Once again, the most stable type-II clathrate phase with both cages filled with Sr is metastable with a hull distance of 194.3 meV/atom.

[0059] The predicted phase Ca.sub.8B.sub.16C.sub.30 represents the first thermodynamically stable carbon-based, type-I clathrate framework. This phase has a large negative formation enthalpy of approximately 500 meV/atom at 50 GPa suggesting that it may be synthesized from a mixture of constituent elements or binary compounds. Ca.sub.8B.sub.16C.sub.30 is dynamically stable from 0-50 GPa, and molecular dynamics simulations over a limited duration suggest stability at ambient pressure and 300 K as shown in FIG. 5. In addition, several other predicted clathrate structures exhibit negative formation enthalpies and small distances from the convex hull including type-I Sr.sub.8B.sub.16C.sub.30, type-II Ca.sub.6B.sub.12C.sub.22, and type-I Na.sub.8B.sub.8C.sub.38, with hull distances of 50, 100 and 105 meV/atom, respectively. Careful selection of the synthetic precursors and pathway considerations may produce viable strategies to synthesize these dynamically stable structures, and intrinsic thermodynamic stability may improve under different PT conditions. A recent review of the Inorganic Crystal Structure Database (ICSD) revealed that approximately 90% of known crystalline inorganic metastable compounds are within 70 meV/atom of the ground state at 0 K.

[0060] To further confirm the interactions and properties of the clathrates described in this work, Applicants analyzed charge transfer between guest and host, and calculated the electronic density of states for the three most stable compounds. Table 2 shows electronic properties for the most stable boron-substituted type-I carbon clathrate structures filled with Na, Ca and Sr atoms. In all three cases, electrons are transferred from the guest metals to the host frameworks creating positively charged metal ions within the clathrate cavities. Electron-deficient boron can accept an electron to produce tetrahedral bonding in the network with a formal negative charge, as in the B(CH.sub.3).sup.4 model mentioned above. Due to the polar covalent BC bonding between framework atoms, with carbon having a larger electronegativity, B atoms are positively charged and C atoms are negatively charged. For monovalent-filled type-I Na.sub.8B.sub.8C.sub.38, in which the lowest-energy structure has tetragonal symmetry with space group P 42mc, the calculated average Bader charge for Na is +0.72 while the average Bader charges of B and C are +1.74 and 0.52, respectively. For divalent-filled type-I Ca/Sr.sub.8B.sub.16C.sub.30, both ground-state trigonal (space group R3) compounds have similar average Bader charges of approximately +1.33, +1.54 and 1.18 for Ca/Sr, B and C, respectively. All three structures are charge-balanced insulators with DFT band gaps ranging from 2.50 to 2.87 eV, as expected from the initial compositional design of this study. The stability of unbalanced M:B ratios was not explored here, however low-energy metallic structures, similar to SrB.sub.3C.sub.3, are anticipated with different boron compositions or metal guest ratios.

TABLE-US-00002 TABLE 2 Electronic properties of the most stable NaBC, CaBC, and SrBC clathrate structures. The DFT-calculated band gaps likely represent an under-estimate. Space Metal Bader B Bader C Bader Band gap Composition group Charge (e) Charge (e) Charge (e) (eV) Na.sub.8B.sub.8C.sub.38 P 4.sub.2mc +0.72 +1.74 0.52 2.87 Ca.sub.8B.sub.16C.sub.30 R3 +1.31 +1.57 1.20 2.50 Sr.sub.8B.sub.16C.sub.30 R3 +1.34 +1.50 1.16 2.63

[0061] The crystal structure of thermodynamically stable Ca.sub.8B.sub.16C.sub.30 clathrate, which has space group R3 for the ordered, boron-substituted type-I lattice, is shown in FIG. 6(a). Boron within this structure is substituted primarily on the 9b Wyckoff sites, with a portion of B atoms occupying the 3a sites. This optimal substitution scheme corresponds to the majority of boron located at the hexagonal-ring 24k and 6c and Wyckoff sites, with a small fraction of boron located on the 16i sites of the Pm3.sup. n parent structure. The average distance between cage centers and vertices for Ca.sub.8B.sub.16C.sub.30 is 2.473 A and 2.249 A for the large and small cages, respectively. FIG. 6(b) shows the chains of hexagonal rings for stable type-I Ca.sub.8B.sub.16C.sub.30 with occupied boron positions colored in pink. For the case of Ca.sub.8B.sub.16C.sub.30, all hexagonal rings are comprised of alternating boron and carbon atoms, yielding the maximum hexagonal substitution scheme possible without creating any B-B contacts. The hexagonal-plane/BCB angle ranges from 115.4-123.9, while the/CBC angle ranges from 114.7-122.7.

[0062] FIG. 6(c) displays the electronic density of states for the stable type-I Ca.sub.8B.sub.16C.sub.30 phase, indicating it is an insulator with a calculated DFT band gap of 2.50 eV. The total valence electron count for this structure is similar to that of type-I pure carbon clathrate, reflecting overall charge balance and its insulating properties. The dominant contributions to the DOS just below the Fermi level are comprised of C and B hybrid states, whereas the bottom of the conduction band is dominated by Ca states.

[0063] The sp.sup.3, diamond-like lattice of carbon clathrate structures results in exceptional mechanical properties, for example, high hardness and strength. For the case of boron-substituted structures, elastic moduli remain high, although reduced from the case of pure carbon due to the introduction of BC bonds, and increased metallicity in some cases with occupied cages. For Ca.sub.8B.sub.16C.sub.30 the zero-pressure bulk modulus, B.sub.0 is estimated to be 256 GPa, with pressure derivative B.sub.0=3.8, based on DFT calculations. This value is comparable to type-VII MB.sub.3C.sub.3 clathrates and advanced structural ceramic materials such as boron carbide.

[0064] Following predictions of thermodynamically stable Ca.sub.8B.sub.16C.sub.30, the experimental synthesis of this phase was targeted at 50 GPa using laser-heated diamond anvil cells combined with in situ synchrotron X-ray diffraction for structural characterization. After heating compressed precursor samples at temperatures above 2500 K, new diffraction peaks appeared that were readily indexed to the cubic type-I clathrate structure (a=7.046 at 50 GPa), in addition to cubic type-VII CaB.sub.3C.sub.3 clathrate (a=4.529 , isostructural with SrB.sub.3C.sub.3). Prolonged heating above 3000 K produced grains that were suitable for single-crystal diffraction methods.

[0065] Single-crystal structure solution revealed Ca atoms located on the 2a and 6d positions, and unambiguously revealed the type-I Pm3n clathrate with framework atoms located on the 6c, 16i, and 24k positions. The initial all-carbon framework solution provides excellent structural refinement indicators (R1=0.035), however this model (i.e., Ca.sub.8C.sub.46) is energetically implausible with a calculated convex hull distance >700 meV/atom at 50 GPa. Furthermore, Ca.sub.8C.sub.46 is dynamically unstable with imaginary phonon frequencies throughout the first Brillouin zone as shown in FIG. 10. Thus, boron atoms must substitute within the type-I framework for stability, and the high quality of the all-carbon structural model reflects the difficulty in distinguishing carbon from boron using X-ray diffraction given the one-electron differential between the elements. After systematic refinement of possible boron distribution schemes in the cubic unit cell, a model with partial boron occupation of the 24k site provided the best structural refinement indicators (R1=0.032) with the composition Ca.sub.8B.sub.8.8(14)C.sub.37.1(14) (1 standard uncertainty), or Ca.sub.8B.sub.93C.sub.373 with 95% probability (2 level confidence interval). Boron occupation of the 16i site is disfavored, leading to unphysical occupancy factors. A small fraction of boron on the 6c site, in addition to 24 k, is statistically possible (R1=0.033), and with partial occupancy of both sites, the estimated uncertainty in the refined B composition, x, ranges between 7x15 with 95% probability. Detailed refinement models and parameters are shown in TABLES 3 and 4.

[0066] The experimentally observed structure is in good agreement with the thermodynamically stable phase predicted by Applicant. A key difference is the requirement of ordered boron decorations in the static calculations, which require a lowering of symmetry from cubic (Pm3n) to rhombohedral (R3) for the unit cell to accommodate the boron atoms. Partial site occupancies are used to treat the statistical distribution of boron substitutions empirically. Nevertheless, the calculated rhombohedral distortion is miniscule with a=7.03 and =89.99 for the optimized cell at 50 GPa (cf., a=7.05 and =90 from experiment), and the structure can be approximated as cubic, but with ordered Wyckoff positions.

[0067] The experimentally determined type-I CaBC clathrate structure is shown in FIG. 7(a) through 7(c). Like the predicted stable R3 Ca.sub.8B.sub.16C.sub.30 structure, boron atoms in the experimental Pm3n structure are primarily located on the 24k Wyckoff position. (Note that the 3a and 9b sites of R3 are related back to sites found in the parent structure). Boron occupation of the 24k site in the experimental structure is clearly reflected in average bond distances. Average distances containing BC contacts are longer (24 k-24 k=1.772(4) , 24 k-6 c=1.633(2) , 24 k-16 i=1.6148(14) ) than distances that are exclusively CC (16i-16i=1.535(4) ). The 24 k and 6c Wyckoff positions are associated with the hexagonal rings of the large [5.sup.126.sup.4] cages. The 6c site is exclusive to the large cages, while sites of the hexagons associated with the 24k sites are common between small cages. Chains of perpendicular hexagonal rings (rotated 90 about the 6c position) run parallel along all opposing faces of the unit cell. Boron occupation of the hexagonal rings allows for the minimization of bond angle strain for the 120 hexagonal angle compared with the ideal 109.5 angle for tetrahedral carbon, in excellent agreement with Applicant's predictions. It is notable that Al doping within type-I silicon clathrates follows a similar substitution scheme, whereas B doping in Si clathrates occurs predominantly on the 16i positions due to size mismatch.

[0068] Based on Applicant's predicted requirements for charge balance (i.e., 2B per Ca), the theoretical R3 Ca.sub.8B.sub.16C.sub.30 structure is an insulating phase with a calculated DFT band gap of 2.5 eV.40 While single-crystal diffraction results unambiguously confirm the cubic type-I clathrate structure with boron occupation on 24k, refinements of substitutionally disordered boron in the Pm3n lattice apparently violate this charge balance, although large uncertainties are associated with the XRD-derived boron composition. That is, the best structural refinements suggest only 6-12 boron atoms per unit cell, which cannot entirely compensate charge from fully occupied calcium ions. Future electrical transport measurements on phase-pure samples (the coexisting CaB.sub.3C.sub.3 phase is metallic) will elucidate the electronic structure of the type-I clathrate and potential relevance to high-T.sub.c superconductivity as in related materials. Many clathrate compounds of heavier tetrel elements are known to deviate from precise electron counts. The possibility for substitutions of a variety of guest ions within the large and small cages (e.g., mono/trivalent), in combination with different framework coloring schemes, provides wide potential to systematically tune the physical properties of these compounds.

[0069] Powder X-ray diffraction measurements obtained during decompression as shown in TABLE 5 indicate that the clathrate is recoverable to ambient conditions and persists in air for the maximum duration tested (several hours during synchrotron time). Rietveld refinement of powder data obtained at ambient pressure reveals only minor perturbations from the structural model obtained at 50 GPa, showing an expanded lattice parameter of a=7.4040(2) at 1 atm as shown in FIG. 8(a). Pressure-dependent refinements of the type-I unit cell volume and equation of state analysis revealed a zero-pressure bulk modulus B.sub.0=244(8) GPa, in good agreement with the calculated value for R3 Ca.sub.8B.sub.16C.sub.30 (B.sub.0=256 GPa). This agreement suggests that calculated structural properties of the R3 model are largely representative of the experimentally observed cubic cell. The type-I compressibility is similar to type-VII SrB.sub.3C.sub.3 and LaB.sub.3C.sub.3 clathrates, and 14% larger than that of CaB.sub.3C.sub.3(experimental B.sub.0=214(10) GPa; calculated B.sub.0=224 GPa). Based on first principles calculations, the smallest tensile strength of the new clathrate is estimated to be 30 GPa along <100>, with a similar magnitude of the shear strength, which is weakest for {100} sheared along <001> as shown in FIGS. 8(b) and 8(c). These values are suggestive of a Vickers hardness near 30 GPain agreement with semi-empirical model estimates between 31-39 GPaplacing the new clathrate on the cusp of known superhard materials with advanced mechanical properties similar to those of boron carbide. It is important to note that the introduction of Ca and B into the framework significantly alters the mechanical properties of the clathrate as compared with hypothetical all-carbon C.sub.46. The bulk modulus of the pure allotrope is calculated to be 400 GPa and the tensile and shear strengths are both estimated to exceed 100 GPa. Nevertheless, the incorporation of boron enables the thermodynamic synthesis of the type-I framework, and the introduction of a variety of guest atoms holds potential to access a wide range of electronic properties while maintaining a robust covalent lattice.

[0070] In one embodiment of the invention, the carbon-based clathrate structures are composed of entirely sp.sup.3 hybridized carbon and boron, which results in diamond-like bonding. In another embodiment of the invention, different guest atoms may be substituted within the cages to create a new class of diamond-like materials with tunable properties. Many other guest atoms and their combinations are possible within the clathrate cages.

[0071] The following is a more detailed description of the present invention with reference to working examples for prediction, synthesis of compounds and characterization of the same. The present invention is in no way limited to the following examples.

[0072] Applicants used DFT, as implemented in the Vienna Ab Initio Simulation Package (VASP) version 5.4.4, to perform geometry optimizations and electronic structure calculations with the gradient-corrected exchange and correlation functional of the Perdew-Burke-Ernzerhof (PBE) method. The core states were treated with the projector augmented wave (PAW) method with a plane-wave basis set and an energy cutoff of 500 eV. The -centered k-point grids were automatically generated using the Monkhorst-Pack method in a way that the product of the lattice constants and the number of grid divisions along each reciprocal lattice vector was 30 for structural optimizations and 50 for all other calculations. Structural optimizations were performed for the 5,000 unique structural combinations listed in TABLE 1 at both 10 and 50 GPa for a total of 46,000 variations. Applicants used the ISYM=2 tag to constrain symmetry during geometry optimizations in VASP. To determine if constraining symmetry impacted the optimization results, we compared the outcomes with ISYM=2 (Symmetry Constrained) and ISYM=0 (Symmetry Unconstrained) for several cases, and found no significant effect on the outcome. Phonon calculations within the harmonic approximation were performed using VASP coupled with the Phonopy package. For all phonon calculations, the total number of atoms in a generated supercell was always greater than 90. Using Bader's method, we analyzed electronic charge density within VASP's CHGCAR format to delineate atom-specific charges and volumes.

[0073] Stress-strain relations were calculated by estimating the stress response to structural deformation along specific loading paths using a quasistatic relaxation method. The stress response under tensile and shear strains was used to establish the ideal strengths, i.e., the lowest stress to plastically deform a perfect crystal.

Experimental Synthesis

[0074] Precursor powders were prepared by ball milling CaB.sub.6 (Sigma, 99.5%), CaC.sub.2 (>98%, prepared following a literature method) and glassy carbon (Sigma, 99.95%) under argon at 600 rpm for 99 one-minute cycles, targeting a bulk composition of Ca.sub.8B.sub.16C.sub.30. The milled powder was pressed into 50 m 50 m 10 m pellets using 1 mm flat diamond anvils, and the pellets were loaded into diamond anvil cells (DAC) equipped with 300 m culets and 40 m thick Re gaskets with 150 m diameter sample chambers. All sample pellets were loaded within an inert Ar glovebox with O.sub.2/H.sub.2O<1 ppm. The sample chambers were subsequently loaded and clamped with Ne at 1 kbar, which served as thermal insulation, the pressure medium and XRD pressure calibrant.

[0075] The DAC samples were compressed to 50 GPa and heated with a double-sided infrared laser system with in situ synchrotron X-ray diffraction at the Advanced Photon Source, Sector 13 (GSECARS) and Sector 16 (HPCAT). Diffraction data were collected using a Pilatus3 CdTe 1 M hybrid photon counting detector, which was calibrated using LaB.sub.6/CeO.sub.2 powder standards and an enstatite single-crystal standard. After high-pressure, high-temperature synthesis, powder X-ray diffraction patterns were obtained from samples during decompression to establish the PV equation of state (third-order Birch-Murnaghan) using a EoSFit. Type-I samples were measured at ambient conditions in air and did not decompose over a period of hours. Powder data were analyzed using Dioptas and GSAS/EXPGUI.

Single-Crystal XRD

[0076] A multigrain sample was recrystallized from powder at 48(2) GPa using the laser heating system at GSECARS. Prolonged heating at >3000 K led to the formation of grains large enough to obtain diffraction patterns amenable to multigrain analysis with a synchrotron beam size <5 m 5 m. Frames were recorded between =32 to +32 in 0.5 steps with an exposure time of 5 s or 3 s per frame. Reflections were harvested using CrysAlisPRO, assigned to individual grains with DAFi, and subsequently indexed and integrated using the CrysAlisPRO software suite. Crystal structures were solved with SHELXT 2018/2 and refined using SHELXL 2019/3, invoked from within the Olex2 suite. Reflections from three individual grains were merged using SORTAV for structure refinement of type-I clathrate. SORTAV was invoked from WinGX. In the case of type-VII clathrate, diffraction data from one grain was used.

Crystal Structure Models

[0077] Table 3 contains crystal data and structure refinement parameters for type-I Ca.sub.8B.sub.xC.sub.46-x and type-VII CaB.sub.3C.sub.3. The initial crystal structure solution revealed fully occupied Ca atoms located on the 2a and 6d positions as well as clathrate framework atoms on the 6c, 16i, and 24k positions. Initially, only models with ordered framework atoms were refined (see models 1 and 2a-2c in Table 3). It was found that the pure-carbon framework model gives the best refinement indicators among the ordered models. However, Applicant's computations have shown that Ca.sub.8C.sub.46 is energetically and dynamically unstable. Hence, refinement of disordered arrangements of C/B atoms was attempted. It was found that the introduction of C/B disorder on the 16i leads to unphysical negative boron occupancy, while disorder on 6c does not significantly change boron occupancy from zero as shown in models 3a and 3c in TABLE 3. Only the introduction of the disorder on the 24 k position (model 3b in Table 3) leads to significant improvement of refinement indicators and to a boron occupancy significantly different from zero (see TABLE 3). Introduction of B/C disorder on both 24k and 6c positions (model 3d) does not lead to improvement of refinement indicators compared with model 3b and the occupancy of B on the 6c position does not differ significantly from zero. Therefore, model 3b is preferred to model 3d. Finally, anisotropic displacement parameters for clathrate framework atoms have been refined as shown in model 4 in TABLE 3.

[0078] Mixed La/Ca type-1 clathrate was produced using the experimental procedure above starting from mixed La/Ca carbide/boride precursors, targeting a bulk composition of La.sub.2Ca.sub.6B.sub.16C.sub.30. Structural determination as a function of pressure revealed expanded/contracted lattice parameters as compared to the single-guest Ca.sub.8B.sub.xC.sub.46-x case, indicating the incorporation of La within the clathrate cages, as shown in FIG. 11. The experimental validation of binary guest occupancy, combined with a range of favorable guest elements from DFT calculations indicates a broad range of potential guest occupancy combinations/mixtures/solid solutions.

TABLE-US-00003 TABLE 3 Single-crystal refinement parameters for type-I and type-VII CaBC clathrates at 48(2) and 52(2) GPa, respectively. Empirical formula Ca.sub.8B.sub.8.81.4C.sub.37.11.4 CaB.sub.3C.sub.3 CSD number 2338100 2338099 Formula weight 862.55 108.54 T/K 293(2) 293(2) Crystal system cubic cubic Space group Pm3n Pm3n a / 7.0464(12) 4.529(2) V/.sup.3 349.87(18) 92.89(14) Z 1 2 .sub.calc/g .Math. cm.sup.3 4.094 3.881 /mm.sup.1 0.299 0.370 F(000) 427.1 106 Crystal size/ 0.005 0.005 mm3 0.005 0.005 0.005 0.005 Radiation Synchrotron ( = 0.3344 ) ( = 0.2952 ) 2 range for 3.40 to 30.2 5.99 to 30.0 data collection/ Index ranges 11 h 10, 2 h 3, 12 k 11, 6 k 6, 11 l 11 6 l 6 Reflections 2324 107 collected Independent 195 [R.sub.int = 0.059, 28 [R.sub.int = 0.1815, reflections R.sub.sigma = 0.030] R.sub.sigma = 0.0512] Data/restraints/ 195/0/16 28/0/3 parameters Goodness-of- 1.15 1.26 fit on F.sup.2 Final R indexes R.sub.1 = 0.032, R.sub.1 = 0.085, [I >= 2(I)] wR.sub.2 = 0.066 wR.sub.2 = 0.221 Final R indexes R.sub.1 = 0.046, R.sub.1 = 0.096, [all data] wR.sub.2 = 0.072 wR.sub.2 = 0.242 Largest diff. +0.62/0.53 +1.8/1.14 peak/hole/e.sup.3

TABLE-US-00004 TABLE 4 Comparison of different structural models for type-I CaBC clathrate. data/model 1 2a 2b 2c 3a Atom positions Ca (2a) Ca (2a) Ca (2a) Ca (2a) Ca (2a) Ca (6d) Ca (6d) Ca (6d) Ca (6d) Ca (6d) C (16i) B (16i) C (16i) C (16i) B/C (16i) C (24k) C (24k) B (24k) C (24k) C (24k) C (6c) C (6c) C (6c) B (6c) C (6c) Reflections collected 2324 [R.sub.int = 0.059, R.sub.sigma = 0.030] Independent reflections 195 Data/restraints/parameters 195/0/10 195/0/11 Chemical formula Ca.sub.8C.sub.46 Ca.sub.8B.sub.16C.sub.30 Ca.sub.8B.sub.24C.sub.22 Ca.sub.8B.sub.6C.sub.40 Ca.sub.4B.sub.0.2C.sub.23 10.sup.3 .Math. U.sub.11 (Ca (2a))/.sup.2 3.7(3) 3.4(5) 3.9(3) 3.8(3) 3.8(3) 10.sup.3 .Math. U.sub.11 (Ca (6d))/.sup.2 4.0(4) 3.6(6) 4.0(4) 4.0(4) 3.9(4) 10.sup.3 .Math. U.sub.33 (Ca (6d))/.sup.2 6.0(3) 5.9(5) 6.2(3) 6.0(3) 6.1(3) 10.sup.3 .Math. U.sub.iso (C/B (16i))/.sup.2 5.7(4) 1.9(7) 6.2(5) 5.8(5) 6.9(5) 10.sup.3 .Math. U.sub.iso (C/B (24k))/.sup.2 6.8(4) 6.6(6) 3.2(4) 6.8(4) 6.7(4) 10.sup.3 .Math. U.sub.iso (C/B (6c))/.sup.2 7.2(7) 7.4(12) 7.2(8) 3.7(8) 7.2(7) B molar fraction* <0 Goodness-of-fit on F.sup.2 1.12 1.26 1.19 1.19 0.843 Final R indexes [I 2(I)] R.sub.1 = 0.035, R.sub.1 = 0.045, R.sub.1 = 0.037, R.sub.1 = 0.038, R.sub.1 = 0.036, wR.sub.2 = 0.075 wR.sub.2 = 0.136 wR.sub.2 = 0.093 wR.sub.2 = 0.089 wR.sub.2 = 0.086 Final R indexes [all data] R.sub.1 = 0.049, R.sub.1 = 0.060, R.sub.1 = 0.052, R.sub.1 = 0.053, R.sub.1 = 0.049, wR.sub.2 = 0.082 wR.sub.2 = 0.147 wR.sub.2 = 0.103 wR.sub.2 = 0.096 wR.sub.2 = 0.098 .sub.max/.sub.min/e.sup.3 +0.62/0.65 +1.2/0.66 +0.79/0.61 +1.2/0.77 +0.61/0.68 data/model 3b 3c 3d 4 Atom positions Ca (2a) Ca (2a) Ca (2a) Ca (2a) Ca (6d) Ca (6d) Ca (6d) Ca (6d) C (16i) C (16i) C (16i) C (16i) B/C (24k) C (24k) B/C (24k) B/C (24k) C (6c) B/C (6c) B/C (6c) C (6c) Reflections collected 2324 [R.sub.int = 0.059, R.sub.sigma = 0.030] Independent reflections 195 Data/restraints/parameters 195/0/11 195/0/12 195/0/16 Chemical formula Ca.sub.8B.sub.9.12C.sub.36.88 Ca.sub.8B.sub.0.78C.sub.45.22 Ca.sub.8B.sub.10.92C.sub.35.08 Ca.sub.8B.sub.8.88C.sub.37.12 10.sup.3 .Math. U.sub.11 (Ca (2a))/.sup.2 3.9(3) 3.7(3) 3.9(3) 3.8(3) 10.sup.3 .Math. U.sub.11 (Ca (6d))/.sup.2 4.1(4) 4.0(4) 4.1(3) 4.2(3) 10.sup.3 .Math. U.sub.33 (Ca (6d))/.sup.2 6.1(2) 6.0(3) 6.1(2) 6.1(2) 10.sup.3 .Math. U.sub.iso (C/B (16i))/.sup.2 5.7(4) 5.7(4) 5.8(4) 5.7(4).sup. 10.sup.3 .Math. U.sub.iso (C/B (24k))/.sup.2 5.5(4) 6.8(4) 5.4(4) 5.5(4).sup. 10.sup.3 .Math. U.sub.iso (C/B (6c))/.sup.2 7.2(6) 6.7(8) 6.4(7) 7.6(6).sup. B molar fraction* 0.38(6) 0.13(12) 0.40(6) - 24k 0.37(6) 0.22(11) - 6c Goodness-of-fit on F.sup.2 1.14 1.14 1.13 1.15 Final R indexes [I 2(I)] R.sub.1 = 0.033, R.sub.1 = 0.035, R.sub.1 = 0.033, R.sub.1 = 0.032, wR.sub.2 = 0.069 wR.sub.2 = 0.074 wR.sub.2 = 0.069 wR.sub.2 = 0.066 Final R indexes [all data] R.sub.1 = 0.047, R.sub.1 = 0.049, R.sub.1 = 0.047, R.sub.1 = 0.046, wR.sub.2 = 0.075 wR.sub.2 = 0.080 wR.sub.2 = 0.076 wR.sub.2 = 0.072 .sub.max/.sub.min/e.sup.3 +0.62/0.53 +0.61/0.66 +0.61/0.52 +0.62/0.53 *B molar fraction on the disordered site only; .sup.U.sub.eq since C and B atoms refined anisotropically

TABLE-US-00005 TABLE 5 Rietveld refinement parameters for type-I CaBC clathrate at ambient pressure. Atom Site x y z Fractn Uiso 100 Ca1 2a 0 0 0 1 1.71(6) Ca2 6d 0.25 0.5 0 1 1.71(6) C1 6c 0.5 0.25 0 1 1.1(1) C2 16i 0.1871(5) 0.1871(5) 0.1871(5) 1 1.1(1) C3 24k 0.3058(9) 0.1274(6) 0 0.62(3)* 1.1(1) B3 24k 0.3058(9) 0.1274(6) 0 0.38(3)* 1.1(1) Space group Pm3n a/ 7.4040(2) Radiation Synchrotron ( = 0.3344 ) R.sub.wp-Bknd 0.022 *Initialized composition from high-pressure SXRD data

[0079] FIGS. 9(a) and 9(b) show experimental PV data for type-I Ca.sub.8B.sub.xC.sub.46-x which were modelled using a third-order Birch-Murnaghan equation of state (EOS) to obtain the zero-pressure volume, V.sub.0, bulk modulus, B.sub.0, and its pressure derivative, B.sub.0. Refined experimental parameters are V.sub.0=405.9(3), B.sub.0=244(8) and B.sub.0=4.2(4) for type-I Ca.sub.8B.sub.xC.sub.46-x and V.sub.0=110.5(1), B.sub.0=214(10) and B.sub.0=4.1(6) for type-VII CaB.sub.3C.sub.3, which compare favorably with DFT (PBE) calculations that yield B.sub.0=256 and B.sub.0=3.8 for type-I Ca.sub.8B.sub.xC.sub.46-x and B.sub.0=224 and B.sub.0=3.7 for type-VII CaB.sub.3C.sub.3. FIG. 9(a) shows the experimental unit cell volume as a function of pressure for type-I clathrate (points) and refined EOS (solid line) compared with theoretical equation of state for ordered type-I Ca.sub.8B.sub.16C.sub.30 (dashed line). FIG. 9(b) shows the experimental uncertainty in B.sub.0 and B.sub.0 as confidence ellipses drawn at one and two standard deviations for type-I [0080] Ca.sub.8B.sub.xC.sub.46-x (black) and type-VII CaB.sub.3C.sub.3 (blue).

[0081] FIG. 10 shows phonon dispersion relations for type-I Ca.sub.8C.sub.46 at 50 GPa with a calculated convex hull distance of >700 meV/atom at 50 GPa. As is apparent from the lower region of FIG. 10, Ca.sub.8C.sub.46 is dynamically unstable and yields imaginary phonon frequencies throughout the (first) Brillouin zone. As noted above (see description of FIG. 6(c)) this agrees with Applicant's prediction that boron atoms must substitute within the type-I framework for stability.

[0082] As the present invention may be embodied in several forms without departing from the spirit or essential characteristics thereof, it will be understood that the invention is not limited by the details of the foregoing description, unless otherwise specified, but rather should be construed broadly within its spirit and scope as defined in the appended claims, and therefore all changes and modifications that fall within the metes and bounds of the claims. Accordingly, the invention is defined by the appended claims wherein: