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Article

Novel Superhard Tetragonal Hybrid sp3/sp2 Carbon Allotropes Cx (x = 5, 6, 7): Crystal Chemistry and Ab Initio Studies

by
Samir F. Matar
1 and
Vladimir L. Solozhenko
2,*
1
Lebanese German University (LGU), Jounieh P.O. Box 206, Lebanon
2
LSPM–CNRS, Université Sorbonne Paris Nord, 93430 Villetaneuse, France
*
Author to whom correspondence should be addressed.
C 2024, 10(3), 64; https://doi.org/10.3390/c10030064
Submission received: 26 April 2024 / Revised: 23 June 2024 / Accepted: 9 July 2024 / Published: 16 July 2024
(This article belongs to the Collection Nanocarbon-Based Composites and Their Thermal, Electrical, and Mechanical Properties)
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Abstract

:
Novel superhard tetragonal carbon allotropes C5, C6, and C7, characterized by the presence of sp3- and sp2-like carbon sites, have been predicted from crystal chemistry and extensively studied by quantum density functional theory (DFT) calculations. All new allotropes were found to be cohesive, with crystal densities and cohesive energies decreasing along the C5-C6-C7 series due to the greater openness of the structures resulting from the presence of C=C ethene and C=C=C propadiene subunits, and they were mechanically stable, with positive sets of elastic constants. The Vickers hardness evaluated by different models qualifies all allotropes as superhard, with Hv values ranging from 90 GPa for C5 to 79 GPa for C7. Phonon band structures confirm that the new allotropes are also dynamically stable. The electronic band structures reveal their metallic-like behavior due to the presence of sp2-hybridized carbon.

1. Introduction

In recent years, significant efforts in the search for novel phases with advanced properties have benefited from structure prediction programs such as USPEX [1] and CALYPSO [2] and, more recently, from the crystallographic machine learning platform CrystalMELA [3]. The topic of carbon research, especially regarding periodic structures, shows a sustained interest in the search for new allotropes, especially those characterized by ultrahigh hardness close to that of diamond. In view of the large number of carbon structures claimed as novel, a database, SACADA [4], has been created to group all known carbon allotropes, thus helping researchers in their endeavors on the one hand, and avoiding claims of known phases as novel allotropes on the other.
Another avenue of investigation that could be complementary to modern materials science software lies in the crystal chemistry rationale called “structural engineering”. Recently, the body-centered tetragonal tet-C4 (Figure 1a) in space group I-4m2 was proposed by us as one of the simplest three-dimensional (3D) carbon networks to serve as a template for the design of other novel allotropes and chemical compounds [5]. Using the TopCryst crystallography package [6], tet-C4 was identified with dia (i.e., diamond-like) topology. Several chemical compounds also have a dia topology, as categorized in the Reticular Chemistry Structure Resource (RCSR) database [7].
Recently, Wei et al. proposed a superhard tet-C5 allotrope with mixed carbon hybridization (sp2 and sp3) and metallic character based on structure prediction programs and first-principles calculations within DFT [8]. However, such ‘pentacarbon’ should be unstable, because it has some negative elastic constants. Later, in 2020, cubic ‘pentadiamond’ was reported as a novel allotrope with mechanical properties close to diamond, but the paper was retracted due to serious errors in the optimized structure of ‘pentadiamond’ under mechanical deformation admitted by the authors themselves [9]. Such interest in C5 allotropes with mixed carbon hybridization arises from the possible change in the electronic structure of the insulating diamond, leading to metallic-like behavior with potential applications in electronics [10].
In the present work, starting from tet-C4 [5], we construct novel tetragonal carbon allotrope C5 by crystal chemistry modifications, followed by full geometry relaxations using calculations based on the quantum mechanics density functional theory (DFT) [11,12]. The proposed tet-C5 was found to be cohesive and stable both mechanically and dynamically and to exhibit an original undocumented topology. In a subsequent step, new tetragonal C6 and C7 allotropes were proposed and analyzed simultaneously with tet-C5. From a chemical point of view, C5 and C6 emphasize the double bond >C=C< ene, as in the ethene molecule, C2H4. Remarkably linear C3 >C=C=C<, resembling the allene or propadiene molecule, C3H4, characterizes C7. Note that the central carbon in C3 is sp1 hybridized while the end carbons are sp2.
After this contextual introduction and Section 2, which presents the computational framework, the crystal chemistry rationale leading to the novel tetragonal C5, C6, and C7 allotropes is discussed. Section 3 is devoted to the crystal engineering protocol used to develop the various allotropes. Section 4 qualitatively illustrates the charge density projections on and between the atoms. The mechanical, dynamic, and thermal properties are detailed in Section 5, Section 7 and Section 8, respectively, and the electronic band structures are discussed in Section 9.

2. Computational Framework

The structural investigations using structure prediction programs [1,2,3] or requiring crystal engineering, as here, need quantitative support from quantum mechanical calculations. Such investigations are mostly carried out within the framework of DFT [11,12], which is widely accepted by the scientific community. Briefly, the DFT was developed in two works: for the theoretical framework, by Hohenberg and Kohn in 1964 [11]; this was followed by Kohn and Sham in 1965 [12], who established the Kohn–Sham equations for solving the wave equation practically within computational codes built around the DFT. The Vienna Ab initio Simulation Package (VASP) code [13,14] and the Projector Augmented Wave (PAW) method [14,15] for the atomic potentials were used for the identification of the ground-state structures corresponding to the energy minima and the subsequent prediction of their mechanical and dynamical properties. DFT exchange-correlation (XC) effects were considered using the generalized gradient approximation (GGA) [16]. Relaxation of the atoms to the ground-state structures was performed with the conjugate gradient algorithm according to Press et al. [17]. The Blöchl tetrahedron method [18] with corrections according to the Methfessel and Paxton scheme [19] was used for geometry optimization and energy calculations, respectively. Brillouin zone (BZ) integrals were approximated by a special k-point sampling according to Monkhorst and Pack [20]. Structural parameters were optimized until atomic forces were below 0.02 eV/Å and all stress components were <0.003 eV/Å3. The calculations were converged at an energy cutoff of 400 eV for the plane-wave basis set in terms of the k-point integration in the reciprocal space from kx(6) × ky(6) × kz(6) up to kx(12) × ky(12) × kz(12) to obtain a final convergence and relaxation to zero strains for the original stoichiometries presented in this work. In the post-processing of the ground-state electronic structures, the charge density projections were operated on the lattice sites.
The mechanical stability criteria were obtained from the calculations of the elastic constants. The treatment of the results was performed using the ELATE online tool [21], dedicated to the analysis of the elastic tensors. The program provides the bulk (B), shear (G), and Young’s (E) moduli along different averaging methods; here, the Voigt method [22] was used. Two empirical models, the Mazhnik–Oganov [23] model and the Chen–Niu model [24], have been used to estimate Vickers hardness (HV) from elastic constants.
Vickers hardness was also evaluated in the framework of the thermodynamic model [25,26], which is based on thermodynamic properties and crystal structure, and using the Lyakhov–Oganov approach [27], which takes into account the topology of the crystal structure, the strength of covalent bonds, the degree of ionicity, and directionality. The fracture toughness (KIc) was estimated using the Mazhnik–Oganov model [23].
The dynamic stabilities of the new allotropes were confirmed by the positive values of the phonon frequencies. The corresponding phonon band structures were obtained from a high resolution of the tetragonal Brillouin zones according to Togo et al. [28]. The electronic band structures were obtained using the all-electron DFT-based ASW method [29] and the GGA XC functional [16]. The VESTA (Visualization for Electronic and STructural Analysis) program [30] was used to visualize the crystal structures and charge densities.

3. Crystal Structure Engineering

The template tet-C4 (space group I-4m2, No. 119) is characterized by two 2-fold Wyckoff atomic positions for carbon, as shown in Table 1 [5]. The tetragonal body-centered structure in Figure 1a shows the corresponding carbon atoms labeled C1 (brown spheres) at the origin and body center and C2 (white spheres) forming tetrahedra around C1. Considering the structure in the simple tetragonal configuration, the second column of Table 1 explains the four carbon sites. The transformation to C5 retains the tetragonal symmetry, albeit lowered from body-centered (“I” centering) to primitive (“P” centering) and resolved in space group P-4m2, No. 115. This consists of keeping the body-centered carbon (C1 at ½, ½, ½) so that it goes in the C(1c) Wyckoff position—follow the transformation arrows—as well as the two C2s (C2a and C2b), which become C3(2g), where the z coordinate becomes ±z′ instead of ±¼. The additional carbon C2 is provided by parameterizing the z position of C1b, resulting in a two-fold C2 (2e) at 0, 0, ±z. After full geometry relaxation, the resulting structure is shown in Figure 1b, with colored spheres corresponding to the three carbon sites given with the coordinates in Table 1, i.e., with well-determined z = ±0.854 and z′ = ±0.314. The topology of tet-C5 is found to be 3,4^2T1-CA, documented in the SACADA database, while the template tet-C4 has a dia topology. Now, the cohesive energy per atom, Ecoh/atom = −2.06 eV, is lower than that of tet-C4, which is characterized by a large cohesive energy, Ecoh/atom = −2.49 eV (the same as in diamond).
The polyhedral projection of the tet-C5 structure (Figure 2a, center) shows four tetrahedra. More details are observed in the right panel of Figure 2a with a double cell along the c-direction, highlighting the C2-C2 bonds between the tetrahedra in these two cells. The C2-C2 segments form double bonds like C=C ene units, which will be further discussed in Section 4 relevant to the charge density projections.
Using tet-C5 as a template, a new tetragonal C6 allotrope was constructed with the modification of the central carbon position from ½, ½, ½ to ½, ½, z with z ~ 0.4, thus transforming it into a two-fold position (2f) in the primitive tetragonal space group P-4m2, No. 115. However, after full geometry optimization and space group analysis, the (2e) and (2f) positions were merged by symmetry into a single four-fold position with body-center space group I-4m2, No. 119, as shown in Table 2. The topological analysis of the new allotrope revealed a tfa topology similar to that of the recently reported ultrahard C6 allotrope called ‘neoglitter’ [31]. The cohesive energy of the new tet-C6 is Ecoh/atom = −1.73, which allows us to describe it as cohesive but less stable than tet-C5. The structure of tet-C6 is shown in Figure 2b in three representations. Clearly, the tetrahedra are now connected by C2-C2 segments along two adjacent cells, as in C5, but also within the cell, thus exhibiting higher symmetry compared to tet-C5.
The addition of a central carbon atom to tet-C6 results in C7 stoichiometry. The fully geometry-optimized lattice parameters are given in Table 2. There are now four different Wyckoff positions in the primitive tetragonal space group P-4m2, No. 115. The topological analysis led to the assignment of tfa topology, as in the case of tet-C5. The structure of tet-C7 is shown in Figure 2c, with the aligned C=C=C connecting the tetrahedra within the cell. As in C5 and C6, two adjacent cells are connected via C2-C2. However, tet-C7 has the exception of having both C=C ene and C=C=C propadiene subunits. The cohesive energy Ecoh/atom = −1.69 eV is lower than that of tet-C6.
The density changes drastically along the series: ρ(C5) = 3.25 > ρ(C6) = 3.12 > ρ(C7) = 2.84 g/cm3. This is due to the increase in volume caused by the introduction of a larger number of sp2-hybridized carbon atoms into the unit cell. The shortest interatomic distance (1.30 Å) is observed in the case of C7 for the propadiene-like C=C=C subunit, whereas in C6, d(C=C) = 1.44 Å. The other distances shown in Table 2 are in the range of values observed for tetrahedral carbon allotropes. The relevant effects on the phonon frequencies are shown in Section 7.
Simulated X-ray diffraction patterns of three new tetragonal carbon allotropes are shown in Figure 3. It is evident that they all exhibit distinct topologies that differ significantly from diamond.

4. Projections of the Charge Densities

To illustrate the peculiarities introduced by the C=C and C=C=C subunits into the lattice, the analysis was extended to a qualitative illustration of the charge densities. Despite the similar chemical nature of the constituents, i.e., carbon, the different hybridizations (sp3 and sp2) lead to different behaviors of the carbon sites in terms of charge transfer. Figure 4 illustrates the charge density distribution.
The most relevant feature in C5 (Figure 4a) is the red charge cross sections, which indicate the continuous charge density of the red traces through the eight corners toward the adjacent cells along the tetragonal c direction (vertical direction). This feature is also observed within the C6 cell, which shows features similar to C5 regarding the eight corners, as well as the central >C=C< with characteristic sp2 hybridization. Going to C7, the central part of the unit cell contains the >C=C=C< propadiene subunit, while the >C=C< ene subunits are located between the two adjacent cells (Figure 4c). However, the charge density becomes weaker as one moves to the next cell, as shown by the green areas, which indicate less charge between adjacent cells; the charge is now concentrated around the propadiene subunit. This may explain why C7 is the least cohesive of the series studied.

5. Mechanical Properties

An analysis of the mechanical behavior of new tetragonal carbon allotropes has been carried out by calculating the elastic properties by inducing finite distortions of the lattice. The allotropes are fully described by the calculated sets of elastic constants Cij given in Table 3. All Cij values are positive, indicating mechanically stable phases. The major (i.e., C11 and C33) Cij values of C5 are systematically larger than those of C6 and C7. The analysis of the elastic tensors was performed using ELATE software [21], which provides the bulk (B), shear (G), and Young’s (E) moduli, as well as the Poisson’s ratio (ν) along different averaging methods; in the present work, the Voigt approach [22] was chosen. Table 4 shows the calculated elastic moduli, with values that follow the trends observed for Cij.
The Vickers hardness values evaluated using the four contemporary hardness models are summarized in Table 4. A clear tendency of a decrease in hardness in the C5–C6–C7 series due to the increasing openness of the crystal structures is observed for all four models. Since it has been shown earlier that the thermodynamic model is the most reliable in the case of the superhard compounds of light elements [32], and it shows perfect agreement with the available experimental data [33], it is obvious that the hardness values calculated within the empirical models are strongly underestimated. The Oganov–Lyakhov model also gives underestimated (by 10–20%) values.
Table 4. Mechanical properties of new tetragonal carbon allotropes compared with diamond: Vickers hardness (HV), bulk modulus (B), shear modulus (G), Young’s modulus (E), Poisson’s ratio (ν), fracture toughness (KIc).
Table 4. Mechanical properties of new tetragonal carbon allotropes compared with diamond: Vickers hardness (HV), bulk modulus (B), shear modulus (G), Young’s modulus (E), Poisson’s ratio (ν), fracture toughness (KIc).
HVBGVEVνVKIc ‡
T *LO †MO ‡CN §B0 *BV
GPa MPa·m½
Diamond989010093445 **530 **1138 ††0.074 ††6.7 ‡‡
C5 #115908149454104053337840.1777.1
C6 #119867135353913842846840.2036.1
C7 #115796230313603762606340.2195.8
* Thermodynamic model [26]. † Lyakhov–Oganov model [27]. ‡ Mazhnik–Oganov model [23]. § Chen–Niu model [24]. ** Ref [34]. †† Calculated from BV and GV using isotropic approximation. ‡‡ Ref. [35].
The fracture toughness of the new carbon allotropes decreases from 7.1 MPa·m½ for tet-C5, which is higher than that of diamond (KIc = 6.7 MPa·m½ [35]), down to 5.8 MPa·m½ for tet-C7.

6. Equations of State

The comparative energy trends of new tetragonal carbon allotropes have been determined from their equations of state, based on a series of calculations of total energy as a function of volume. The resulting E(V) curves fitted to the third-order Birch equations of state [36] are shown in Figure 5. As can be seen, all three tetragonal carbon allotropes are metastable over the entire range of experimentally accessible pressures. However, the formation of these allotropes is possible at high pressures and high temperatures as a result of alternative metastable behavior, most likely under highly non-equilibrium conditions.

7. Phonon Band Structures

To verify the dynamic stability of the novel carbon allotropes, their phonon properties were studied. The phonon band structures obtained from a high resolution of the tetragonal Brillouin zone according to Togo et al. [28] are shown in Figure 6. The bands (red lines) develop along the main directions of the tetragonal Brillouin zone (horizontal x-axis), separated by vertical lines for better visualization, and the vertical direction (y-axis) shows the frequencies ω, given in terahertz (THz).
The band structures include 3N bands: three acoustic modes starting from zero energy (ω = 0) at the Γ point (the center of the Brillouin zone) up to a few terahertz and 3N-3 optical modes at higher energies. The acoustic modes correspond to the rigid translation modes of the crystal (two transverse and one longitudinal). All panels in Figure 6 show positive phonon frequencies, indicating the dynamic stability of all three new carbon allotropes.
In Figure 6a, relevant to C5, the general aspect is that of dispersed bands with the highest magnitude just below 40 THz. This changes for C6 (Figure 6b), where the highest frequency is closer to 40 THz, corresponding to 1650 cm−1. This value is exactly in the range of C=C vibrations with a strong signal, i.e., 1625–1680 cm−1 in the molecular state, as listed in the web-available “RAMAN Band Correlation Table”. Due to the twice-larger amounts of C=C bonds with sp2 hybridization, there are also more flat lines towards the top of the panel and less dispersion of the bands. These features are confirmed upon inspection of the Figure 6c relevant to C7, where the highest bands are flat, with the highest line found around 55 THz corresponding to the short C–C distance of 1.30 Å in the C=C=C subunit, also identified in C3H4 propadiene (~1900 cm−1).

8. Thermodynamic Properties

The thermodynamic properties of novel carbon allotropes were calculated from the phonon frequencies using the statistical thermodynamic approach [37] on a high-precision sampling mesh in the Brillouin zone. The temperature dependencies of the heat capacity at constant volume (Cv) and entropy (S) are shown in Figure 7 in comparison with available experimental Cp data for diamond [38,39]. For all three allotropes, the heat capacity and entropy are higher than those of diamond and increase in the C5–C6–C7 series, which is to be expected due to the increasing openness of the crystal structures compared to diamond, on the one hand, and the respective conducting versus insulator electronic properties, on the other hand.

9. Electronic Band Structures

The electronic band structures of three novel carbon allotropes were calculated using the all-electron DFT-based augmented spherical method (ASW) [29]. The results are shown in Figure 8. The bands (blue lines) develop along the main directions of the tetragonal Brillouin zone shown in Figure 8d. The zero energy along the vertical axis is considered with respect to the Fermi-level EF, since all three allotropes, C5, C6, and C7, are metallic-like with no energy gap separating the valence band VB from the conduction band CB. Such behavior can be explained by the delocalized nature of the π electrons resulting from the presence of C(sp2) atoms of the C=C and C=C=C subunits.

10. Conclusions

In the present work, the novel superhard tetragonal carbon allotropes C5, C6, and C7, characterized with mixed sp2 and sp3 carbon hybridizations, were found to be cohesive and stable both mechanically (elastic constants and their combinations) and dynamically (phonon band structures). Whereas C5 and C6 contain ethene-like >C=C< subunits, C7 shows both ethene-like and propadiene-like >C=C=C< subunits, with signatures observed from the highest phonon frequencies correlating with Raman vibrations of ethene and propadiene molecules. The density decreases along the C5–C6–C7 series due to the increasing openness of the structures and consequently leads to a decrease in the mechanical properties, in particular the Vickers hardness, which decreases from 90 GPa for C5 to 79 GPa for C7. The energy-volume equations of state show metastability of all three allotropes over the whole range of experimentally accessible pressures, but this does not exclude their possible formation under high pressure—high temperature conditions. Thermodynamically, the temperature dependencies of the heat capacity and entropy of all three allotropes were found to be higher than those of diamond due to the insulating electronic properties of the latter compared to the conducting C5, C6, and C7 as identified from their electronic band structures. Delocalized π electrons of C(sp2) atoms present in the three new allotropes are considered responsible for their metallic-like conductivity.

Author Contributions

Conceptualization, S.F.M.; methodology, S.F.M. and V.L.S.; investigation, S.F.M. and V.L.S.; formal analysis, S.F.M. and V.L.S.; data curation, S.F.M. and V.L.S.; visualization, S.F.M. and V.L.S.; validation, S.F.M. and V.L.S.; resources, S.F.M.; writing—original draft preparation, S.F.M.; writing—review and editing, V.L.S. All authors have read and agreed to the published version of the manuscript.

Funding

This research received no external funding.

Data Availability Statement

The data presented in this study are available on reasonable request.

Conflicts of Interest

The authors declare no conflicts of interest.

References

  1. Glass, C.W.; Oganov, A.R.; Hansen, N. USPEX—Evolutionary crystal structure prediction. Comput. Phys. Commun. 2006, 175, 713–720. [Google Scholar] [CrossRef]
  2. Wang, Y.; Lv, J.; Zhu, L.; Ma, Y. CALYPSO: A method for crystal structure prediction. Comput. Phys. Commun. 2012, 183, 2063–2070. [Google Scholar] [CrossRef]
  3. Correiro, N.; Rizzi, R.; Settembre, R.G.; Del Buono, N.; Diacono, D. CrystalMELA: A new crystallographic machine learning platform for crystal system determination. J. Appl. Cryst. 2023, 56, 409–419. [Google Scholar] [CrossRef] [PubMed]
  4. Hoffmann, R.; Kabanov, A.A.; Golov, A.A.; Proserpio, D.M. Homo Citans and carbon allotropes: For an ethics of citation. Angew. Chem. Int. Ed. 2016, 55, 10962–10976. [Google Scholar] [CrossRef]
  5. Matar, S.F.; Solozhenko, V.L. The simplest dense carbon allotrope: Ultra-hard body centered tetragonal C4. J. Solid State Chem. 2022, 314, 123424. [Google Scholar] [CrossRef]
  6. Shevchenko, A.P.; Shabalin, A.A.; Karpukhin, I.Y.; Blatov, V.A. Topological representations of crystal structures: Generation, analysis and implementation in the TopCryst system. Sci. Technol. Adv. Mater. 2022, 2, 250–265. [Google Scholar] [CrossRef]
  7. O’Keeffe, M.; Peskov, M.A.; Ramsden, S.J.; Yaghi, O.M. The reticular chemistry structure resource (RCSR) database of, and symbols for, crystal nets. Acc. Chem. Res. 2008, 41, 1782–1789. [Google Scholar] [CrossRef]
  8. Wei, Q.; Zhang, Q.; Yan, H.; Zhang, M.; Wei, B. A new tetragonal superhard metallic carbon allotrope. J. Alloys Compd. 2018, 769, 347–352. [Google Scholar] [CrossRef]
  9. Fujii, Y.; Maruyama, M.; Cuong, N.T.; Okada, S. Retraction: Pentadiamond: A hard carbon allotrope of a pentagonal network of sp2 and sp3 C atoms [Phys. Rev. Lett. 125, 016001 (2020)]. Phys. Rev. Lett. 2020, 125, 079901. [Google Scholar] [CrossRef] [PubMed]
  10. Yang, H.; Ma, Y.; Dai, Y. Progress of structural and electronic properties of diamond: A mini review. Funct. Diam. 2021, 1, 150–159. [Google Scholar] [CrossRef]
  11. Hohenberg, P.; Kohn, W. Inhomogeneous electron gas. Phys. Rev. B 1964, 136, 864–871. [Google Scholar] [CrossRef]
  12. Kohn, W.; Sham, L.J. Self-consistent equations including exchange and correlation effects. Phys. Rev. A 1965, 140, 1133–1138. [Google Scholar] [CrossRef]
  13. Kresse, G.; Furthmüller, J. Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set. Phys. Rev. B 1996, 54, 11169. [Google Scholar] [CrossRef] [PubMed]
  14. Kresse, G.; Joubert, J. From ultrasoft pseudopotentials to the projector augmented wave. Phys. Rev. B 1999, 59, 1758–1775. [Google Scholar] [CrossRef]
  15. Blöchl, P.E. Projector augmented wave method. Phys. Rev. B 1994, 50, 17953–17979. [Google Scholar] [CrossRef]
  16. Perdew, J.; Burke, K.; Ernzerhof, M. The Generalized Gradient Approximation made simple. Phys. Rev. Lett. 1996, 77, 3865–3868. [Google Scholar] [CrossRef] [PubMed]
  17. Press, W.H.; Flannery, B.P.; Teukolsky, S.A.; Vetterling, W.T. Numerical Recipes, 2nd ed.; Cambridge University Press: New York, NY, USA, 1986. [Google Scholar]
  18. Blöchl, P.; Jepsen, O.; Anderson, O. Improved tetrahedron method for Brillouin-zone integrations. Phys. Rev. B 1994, 49, 16223–16233. [Google Scholar] [CrossRef] [PubMed]
  19. Methfessel, M.; Paxton, A.T. High-precision sampling for Brillouin-zone integration in metals. Phys. Rev. B 1989, 40, 3616–3621. [Google Scholar] [CrossRef] [PubMed]
  20. Monkhorst, H.J.; Pack, J.D. Special k-points for Brillouin Zone integration. Phys. Rev. B 1976, 13, 5188–5192. [Google Scholar] [CrossRef]
  21. Gaillac, R.; Pullumbi, P.; Coudert, F.X. ELATE: An open-source online application for analysis and visualization of elastic tensors. J. Phys. Condens. Matter 2016, 28, 275201. [Google Scholar] [CrossRef]
  22. Voigt, W. Über die Beziehung zwischen den beiden Elasticitätsconstanten isotroper Körper. Annal. Phys. 1889, 274, 573–587. [Google Scholar] [CrossRef]
  23. Mazhnik, E.; Oganov, A.R. A model of hardness and fracture toughness of solids. J. Appl. Phys. 2019, 126, 125109. [Google Scholar] [CrossRef]
  24. Chen, X.Q.; Niu, H.; Li, D.; Li, Y. Modeling hardness of polycrystalline materials and bulk metallic glasses. Intermetallics 2011, 19, 1275–1281. [Google Scholar] [CrossRef]
  25. Mukhanov, V.A.; Kurakevych, O.O.; Solozhenko, V.L. The interrelation between hardness and compressibility of substances and their structure and thermodynamic properties. J. Superhard Mater. 2008, 30, 368–378. [Google Scholar] [CrossRef]
  26. Mukhanov, V.A.; Kurakevych, O.O.; Solozhenko, V.L. Hardness of materials at high temperature and high pressure. Philos. Mag. 2009, 89, 2117–2127. [Google Scholar] [CrossRef]
  27. Lyakhov, A.O.; Oganov, A.R. Evolutionary search for superhard materials: Methodology and applications to forms of carbon and TiO2. Phys. Rev. B 2011, 84, 092103. [Google Scholar] [CrossRef]
  28. Togo, A.; Tanaka, I. First principles phonon calculations in materials science. Scr. Mater. 2015, 108, 1–5. [Google Scholar] [CrossRef]
  29. Eyert, V. Basic notions and applications of the augmented spherical wave method. Int. J. Quantum Chem. 2000, 77, 1007–1031. [Google Scholar] [CrossRef]
  30. Momma, K.; Izumi, F. VESTA3 for three-dimensional visualization of crystal, volumetric and morphology data. J. Appl. Crystallogr. 2011, 44, 1272–1276. [Google Scholar] [CrossRef]
  31. Matar, S.F.; Solozhenko, V.L. Novel ultrahard sp2/sp3 hybrid carbon allotrope from crystal chemistry and first principles: Body-centered tetragonal C6 (‘neoglitter’). Diam. Relat. Mater. 2023, 133, 109747. [Google Scholar] [CrossRef]
  32. Solozhenko, V.L.; Matar, S.F. Prediction of novel ultrahard phases in the B-C-N system from first principles: Progress and problems. Materials 2023, 16, 886. [Google Scholar] [CrossRef]
  33. Munro, R.; Freiman, S.; Baker, T. Fracture Toughness Data for Brittle Materials; NIST Interagency/Internal Report No. 6153; NIST: Gaithersburg, MD, USA, 1998. [Google Scholar]
  34. Brazhkin, V.V.; Solozhenko, V.L. Myths about new ultrahard phases: Why materials that are significantly superior to diamond in elastic moduli and hardness are impossible. J. Appl. Phys. 2019, 125, 130901. [Google Scholar] [CrossRef]
  35. Matar, S.F.; Solozhenko, V.L. Crystal chemistry and ab initio prediction of ultrahard rhombohedral B2N2 and BC2N. Solid State Sci. 2021, 118, 106667. [Google Scholar] [CrossRef]
  36. Birch, F. Finite strain isotherm and velocities for single-crystal and polycrystalline NaCl at high pressures and 300 K. J. Geophys. Res. 1978, 83, 1257–1268. [Google Scholar] [CrossRef]
  37. Dove, M.T. Introduction to Lattice Dynamics; Cambridge University Press: New York, NY, USA, 1993. [Google Scholar]
  38. DeSorbo, W. Specific heat of diamond at low temperatures. J. Chem. Phys. 1953, 21, 876–880. [Google Scholar] [CrossRef]
  39. Victor, A.C. Heat capacity of diamond at high temperatures. J. Chem. Phys. 1962, 36, 1903–1911. [Google Scholar] [CrossRef]
Carbon 10 00064 g001
Figure 1. From tet-C4 (a) to tet-C5 (b) by changing the atomic positions. The carbon atoms numbers correspond to the numbering in Table 1.
Figure 1. From tet-C4 (a) to tet-C5 (b) by changing the atomic positions. The carbon atoms numbers correspond to the numbering in Table 1.
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Carbon 10 00064 g002
Figure 2. Crystal structures of new tetragonal carbon allotropes in three representations: ball-and-stick (left), polyhedral (middle), and double cells with numbering of atoms as in Table 2: C5 (a); C6 (b); C7 (c).
Figure 2. Crystal structures of new tetragonal carbon allotropes in three representations: ball-and-stick (left), polyhedral (middle), and double cells with numbering of atoms as in Table 2: C5 (a); C6 (b); C7 (c).
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Carbon 10 00064 g003
Figure 3. Simulated X-ray diffraction patterns of new tetragonal carbon allotropes.
Figure 3. Simulated X-ray diffraction patterns of new tetragonal carbon allotropes.
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Figure 4. Charge density projections of tetragonal C5 (a); C6 (b); and C7 (c).
Figure 4. Charge density projections of tetragonal C5 (a); C6 (b); and C7 (c).
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Figure 5. Calculated total energy per atom as a function of volume for new tetragonal carbon allotropes and diamond.
Figure 5. Calculated total energy per atom as a function of volume for new tetragonal carbon allotropes and diamond.
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Figure 6. Phonon band structures of new carbon allotropes along the major directions of the simple tetragonal Brillouin zone: C5 (a); C6 (b); C7 (c).
Figure 6. Phonon band structures of new carbon allotropes along the major directions of the simple tetragonal Brillouin zone: C5 (a); C6 (b); C7 (c).
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Figure 7. Heat capacities at constant volume (CV) (a) and entropies (S) (b) of new tetragonal carbon allotropes compared to diamond. Experimental CV data of diamond [38,39] are shown as gray symbols.
Figure 7. Heat capacities at constant volume (CV) (a) and entropies (S) (b) of new tetragonal carbon allotropes compared to diamond. Experimental CV data of diamond [38,39] are shown as gray symbols.
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Figure 8. Electronic band structures of new tetragonal carbon allotropes: C5 (a); C6 (b); C7 (c); the tetragonal Brillouin zone (d).
Figure 8. Electronic band structures of new tetragonal carbon allotropes: C5 (a); C6 (b); C7 (c); the tetragonal Brillouin zone (d).
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Table 1. C4-to-C5 crystal structure transformation of tetragonal carbon allotropes.
Table 1. C4-to-C5 crystal structure transformation of tetragonal carbon allotropes.
Space Group
Topology		tet-C4 [5]
I-4m2 (No. 119)
dia		Simple Tetragonal C4tet-C5
P-4m2 (No. 115)
3,4^2T1-CA
a, Å2.5272.5272.48
c, Å3.5743.5744.99
Atomic
positions		C1 (2a) 0, 0, 0
C2 (2d) ½, 0, ¼		C1a (½, ½, ½)→C1 (1c) ½, ½, ½
C1b (0, 0, 0)→C2 (2e) 0, 0, ±z
C2a (½, 0, ¼)⌉
C2b (0, ½, ¾)⌋		→C3 (2g) 0, ½, ±z′
Table 2. Crystal structure parameters of new tetragonal carbon allotropes.
Table 2. Crystal structure parameters of new tetragonal carbon allotropes.
Space Group
Topology		C5
P-4m2 (No. 115)
3,4^2T1-CA		C6
I-4m2 (No. 119)
tfa		C7
P-4m2 (No. 115)
tfa
a, Å2.482.4562.563
c, Å4.9986.4157.471
Vcell, Å330.7538.749.07
Density, g/cm33.253.122.84
Shortest bond length, Å1.46/1.50/1.551.44/1.511.30/1.45/1.53
Atomic positionsC1 (1c) ½, ½, ½
C2 (2e) 0, 0, 0.854
C3 (2g) 0, ½, 0.314		C1 (2c) 0, ½, ¼
C2 (4e) 0, ½, 0.888		C1 (1c) ½, ½, ½
C2 (2e) 0, 0, 0.903
C3 (2f) ½, ½, 0.326
C4 (2g) 0, ½, 0.210
Etotal, eV
Ecoh/atom, eV		−43.29
−2.06		−50.06
−1.73		−58.07
−1.69
N.B. E(C) = −6.6 eV. Ecoh/atom (diamond) = −2.49 eV.
Table 3. Elastic constants (Cij) of new tetragonal carbon allotropes (all values are in GPa).
Table 3. Elastic constants (Cij) of new tetragonal carbon allotropes (all values are in GPa).
C11C12C13C33C44C66
C594391361194198337
C6784191351313144270
C7715701311286119268
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Matar, S.F.; Solozhenko, V.L. Novel Superhard Tetragonal Hybrid sp3/sp2 Carbon Allotropes Cx (x = 5, 6, 7): Crystal Chemistry and Ab Initio Studies. C 2024, 10, 64. https://doi.org/10.3390/c10030064

AMA Style

Matar SF, Solozhenko VL. Novel Superhard Tetragonal Hybrid sp3/sp2 Carbon Allotropes Cx (x = 5, 6, 7): Crystal Chemistry and Ab Initio Studies. C. 2024; 10(3):64. https://doi.org/10.3390/c10030064

Chicago/Turabian Style

Matar, Samir F., and Vladimir L. Solozhenko. 2024. "Novel Superhard Tetragonal Hybrid sp3/sp2 Carbon Allotropes Cx (x = 5, 6, 7): Crystal Chemistry and Ab Initio Studies" C 10, no. 3: 64. https://doi.org/10.3390/c10030064

APA Style

Matar, S. F., & Solozhenko, V. L. (2024). Novel Superhard Tetragonal Hybrid sp3/sp2 Carbon Allotropes Cx (x = 5, 6, 7): Crystal Chemistry and Ab Initio Studies. C, 10(3), 64. https://doi.org/10.3390/c10030064

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