Searching for high performance materials for optical communication and laser industry in deep-ultraviolet (DUV) region has been the subject of considerable interest. Such materials by design from scratching on multi-component complex crystal systems are challenging. Here, we predict, through density function calculations and unbiased structure searching techniques, the formation of quaternary NaBeBO3 compounds at ambient pressure. Among the four low-energy phases, the P63/m structure exhibits a DUV cutoff edge of 20 nm shorter than α-BaB2O4 (189 nm) – the best-known DUV birefringent material. While the P-6 structure exhibits one time second-harmonic generation efficiency of KH2PO4 and possesses excellent crystal growth habit without showing any layer habit as observed in the only available DUV nonlinear optical material KBe2BO3F2, whose layer habit limits its wide industrial applications. These NaBeBO3 structures are promising candidates for the next generation of DUV optical materials, and the structure prediction technique will shed light on future optical materials design.
Viable DUV (<200 nm) optical materials play a critical role in optical communication and the laser industry1,2,3,4,5, as they possess wide transparency range and high damage threshold6,7,8,9,10. Among them, birefringent or nonlinear optical (NLO) materials are utilized in polarization beam splitters, optical isolators, semiconductor photolithography and laser micromachining11,12,13,14,15. Only a few materials, such as α-BaB2O4 (α-BBO)1,7,8 and KBe2BO3F2 (KBBF)16,17, can be practically used as birefringent or NLO materials in the DUV region. However, both α-BBO and KBBF do not have DUV commercial availability since α-BBO exhibits high UV cutoff edge (189 nm) and KBBF suffers from a strong layering tendency. As such, it is the subject of considerable interest to investigate DUV birefringent and NLO materials18,19,20,21,22. In the past few years, first principle calculations have been an efficient method to evaluate and verify the physical and chemical properties of optical materials23,24,25.
Theoretical search methods can be classified into three categories. The first method used to search optical crystal structure is atom/group/mixing-substitution26,27,28. It comes from the synthetic train of thought of the experimental scientists, and most structure searches of optical materials belong to this method. This method involves a mixing substitution wherein a hypothetical ABXn compound has A-site and B-site substitution in combination with BXn group rotation. The second method is high-throughput computational materials design29 by analyzing and calculating large quantities of known candidate structures to discover useful material systems. This method requires a good descriptor that can rapidly characterize relative properties, through using this descriptor to search new materials in enormous data repositories. This method has been successfully used for mid-infrared NLO materials30 and scintillators31,32.
Although the above two methods have offered some useful suggestions to experimental synthesis, they do not provide the lowest energy structures on the free energy surface for an undiscovered crystal structure, which are closely related to experimental results. Is there an efficient means to address this issue? The third method provides the suitable solution-crystal structure prediction, which aims at finding the global minimum on a potential energy surface. Structure prediction has been widely applied in high pressure regimes33,34, material surface reconstruction35 and cluster structure search36. However, owing to the complexities of optical material systems, which are always more than binary system, no functional optical material structure prediction has been reported.
Here we first introduce a systematic global structure optimization method to develop the next generation of DUV optical materials in complex beryllium borate quaternary system that is attributable to its very short absorption edges. Through searching free energy surfaces (more than 40,000 structures) via the newly developed Artificial Bee Colony (ABC) algorithm as implemented in the CALYPSO (crystal structure analysis by particle swarm optimization) code37,38, we have extensively explored the stable phases of NaBeBO3 at ambient pressure, and obtained a comprehensive set of structures for NaBeBO3. In particular, we have established for the first time the thermodynamically stable structures. In doing so, the first example of 3-fold coordinated Be atoms in borates is observed among the energetically favorable NaBeBO3 structures. Equally important, the four lowest energy NaBeBO3 structures possess superior linear and nonlinear optical properties, as well as good chemical stability. They are attractive candidates for the next generation of DUV birefringent or DUV NLO materials. Our studies also provide insights and a road map for exploring the design and synthetic strategies for NaBeBO3. Such research also offers a key route to structural determination of materials with specific functional optical properties.
Structure predictions through the ABC technique in the CALYPSO code with simulation sizes up to six NaBeBO3 formula units (f.u.) per simulation cell were performed twice at ambient pressure. The four structures with lowest energy were systematically studied, and the other five structures with higher energy are shown in Supplementary Fig. 1 and Supplementary Table 1. The four energetically favorable structures belong to hexagonal P63/m (2f.u. per cell, Fig. 1a; Supplementary Table 1), hexagonal P-6c2 (2f.u. per cell, Fig. 1b; Supplementary Table 1), trigonal P-3c1 (4f.u. per cell, Fig. 1c; Supplementary Table 1) and hexagonal P-6 (3f.u. per cell, Fig. 1d; Supplementary Table 1) space group. Two of the energetically favored structures are non-centrosymmetric, i.e. hexagonal P-6c2 and P-6. In the four NaBeBO3 structures, P63/m, P-6c2, P-3c1 and P-6, the planar BeO3 and the BO3 units connect with each other through corner-sharing the O atoms to generate a (BeBO3)∞ layer. This layer is perfectly parallel to the ab plane. One (BeBO3)∞ layer links with an adjacent layer through six-coordinate Na atoms. As shown in Fig. 1(a–d), the difference of the NaBeBO3 structures is the direction and position of the planar BeO3 units and BO3 units in the (BeBO3)∞ layer. In addition, the Na-O, Be-O and B-O distances are in the range of 2.432–2.452, 1.543–1.547 and 1.384–1.386 Å, respectively. The O-B-O and O-Be-O angles are all 120° to make the planar BO3 and BeO3 units to be equilateral triangles. Intriguingly, to the best of our knowledge, it is the first time to discover the 3-fold coordinated Be atoms in borates, similar to the Be atoms in Y2BeO4 (ref. 39) and Rb2Be2Si2O740.
Formation enthalpies can be used to assess relative stability of crystalline compounds at low temperatures. The formation enthalpy for NaBeBO3 can be defined as follows:
where hf is the enthalpy of formation per atom and H is the calculated enthalpy per chemical unit for each compound at ambient pressure, here, Na2O, B2O3 and BeO are chosen as the reference structures attributed to their stability at ambient pressure. The formation enthalpies of the NaBeBO3 phases, calculated at higher levels of accuracy, are plotted in Fig. 2. The phase with space group of P63/m is the most stable structure with the formation enthalpy about −0.322 eV/atom, the remaining phases with space groups P-6c2, P-3c1 and P-6 have formation enthalpies of about 2 meV/atom, 5 meV/atom and 5 meV/atom higher than that of the P63/m structure. The formation enthalpies (Supplementary Table 2) of several other reaction paths are also negative, these results indicate that the NaBeBO3 structures might be experimentally synthesizable. The phonon calculations have also shown that these structures are kinetically stable by reason that none of the imaginary phonon mode exists in the whole Brillouin Zone (Supplementary Fig. 2).
Owing to the unexpected discovery of the triangular BeO3 units in NaBeBO3, a detailed bonding analysis was performed. The nature of this bonding was probed by calculating the electron localization functions (ELF) (Fig. 3; Supplementary Fig. 3), which is known to be an effective tool to distinguish different bonding interactions in solids41. In the NaBeBO3 structures, the Na-O bonds are ionic, and the B-O bonds are covalent, that is in accordance with other borates. In particular, the Be atoms in the NaBeBO3 structures are sp2 hybridized and form σ bonds with their neighboring O atoms. These Be-O bonds are reasonable that the Be-O distances (1.54–1.55 Å) are in the range of the reported Be-O σ bonds (1.51–1.87 Å) in Y2BeO4 and Rb2Be2Si2O7. These conclusions are further substantiated by Mulliken population analysis42 listed in Table 1, where the calculated overlap populations for Na-O, B-O and Be-O are 0.03, 0.87 and 0.64 e, respectively, indicating the ionic character of the Na-O bonds and the covalent nature of the B-O and Be-O bonds.
The calculated electronic band structures (Fig. 4; Supplementary Fig. 4) for the NaBeBO3 structures reveal that the phases with space groups P63/m, P-6c2, P-3c1 and P-6 are all indirect band gaps, which are 4.81, 4.80, 4.75 and 4.73 eV by the PBE functional and 7.32, 7.30, 7.25 and 7.24 eV by the PBE0 hybrid functional (Supplementary Fig. 5), respectively. The latter functional has been shown to be more precise for band gap calculations in borates43,44. Our calculated band gaps by the PBE0 hybrid functional are in good agreement with experimental and earlier theoretical predictions of sodium beryllium borates45.
Since the electronic transitions from occupied states to unoccupied states reveal the microcosmic origin of the optical properties, it is essential to analyze the partial density of states (PDOS) of the NaBeBO3 structures in detail. The NaBeBO3 structures have much similar electronic states distribution near the band gap. The top region of the valence band (VB) is mainly occupied by the 2s orbitals of the boron atoms and the 2p orbitals of the boron, beryllium and oxygen atoms. The B 2s, 2p states and the Be 2p states show a wide hybridization with O 2p states from −7 to 0 eV, indicating that the B-O and Be-O bonds, that belong to the (BeBO3)∞ layers, make the main contribution to the top of the VB in the NaBeBO3 structures. The bottom region of the conduction band (CB) is mainly occupied by the 2p states of Na, Be, B and O atoms. It is clear that the B-O and Be-O groups in the (BeBO3)∞ layers are the main contributor to the optical properties. In addition, because of the small contribution of Na to the top of the VB and the bottom of the CB, its impact on the optical properties is negligible.
Birefringent crystal material candidates
The calculated refractive indices and birefringence of the NaBeBO3 structures are shown in Fig. 5a and Supplementary Fig. 6. Because their point groups belong to hexagonal or trigonal crystal system, they are all uniaxial crystals with the birefringence values equal to |ne−no|. The birefringence values of the phases with space groups P63/m, P-6c2, P-3c1 and P-6 are 0.0825, 0.083, 0.085 and 0.084 at 589.3 nm, respectively. Their large birefringence, which is related to their strong optical anisotropy, derives from the parallel arrangement of the (BeBO3)∞ layers. The calculated charge densities (Supplementary Fig. 7) show large electron density anisotropy for the (BeBO3)∞ layers, supporting our argument that the (BeBO3)∞ layers are the major contributors to the optical anisotropy.
Interestingly, the NaBeBO3 structures are the first kind of negative uniaxial borate crystal structure type to produce large birefringence summarized by us46, that is effectively fundamental building units in a parallel arrangement with a high number density. To further verify this conclusion, two simulated NaBeBO3 structures with space group P63/m (Fig. 5b,c; Supplementary Table 3), that belong to the second kind of positive uniaxial borate crystal structure type to induce large birefringence, are chosen to investigate the optical anisotropy. In the two simulated NaBeBO3 structures, the planar BO3 and BeO3 groups form equilateral triangle arrangements and are parallel to the b or c axis. The birefringence values (Δn = ne − no; Supplementary Fig. 8) of the simulated structures are 0.0850 and 0.0813 at 589.3 nm, respectively. The large birefringence values of the phases with space group P63/m and two other simulated P63/m structures well validate the two large birefringence structure type in uniaxial borates.
The UV cutoff edges of the phases with space groups P63/m, P-6c2, P-3c1 and P-6 are 169.4 (7.32 eV), 169.9 (7.30 eV), 171.0 (7.25 eV) and 171.2 nm (7.24 eV) respectively, which are 20, 20, 18 and 18 nm shorter than that of α-BBO (189 nm). That is to say, these compounds have large birefringence and short deep UV cutoff edges, which demonstrate that they are excellent candidates for birefringent materials.
Nonlinear optical material candidates
The second-harmonic generation (SHG) effects are estimated owing to the absence of inversion symmetry in the phases with space groups P-6c2 and the P-6. The calculated SHG coefficients are d21 = −d22 = d16 = −0.07 pm/V for the P-6c2 structure, which is only 1/5 times that of KH2PO4 (KDP, d36 = 0.39 pm/V). For the P-6 structure, the coefficients are d11 = −d12 = −d26 = 0.07 pm/V and d22 = −d21 = d16 = −0.40 pm/V, the d22 coefficient contributes to the effective SHG coefficients (Φ = 90° for type-I phase matching), that is equivalent to that of KDP. The SHG-weighted electron densities (Fig. 6a; Supplementary Fig. 9), where only the virtual-electron attributed to its large contribution (more than 90%), indicate that the BeO3 and BO3 groups are mainly responsible for second-order NLO effects.
A marked difference in the SHG response is found in the P-6c2 and the P-6 structures. Their structures are similar that the BO3 and the BeO3 units in adjacent (BeBO3)∞ layers are almost in opposite directions, that is considered to weaken the SHG effects. Then what is the key to the notable SHG difference? The answer is the number of (BeBO3)∞ layers in the primitive cell, the P-6c2 phase has two (BeBO3)∞ layers, whereas the P-6 phase has three (BeBO3)∞ layers. As no additional layer counteracts the third layer’s SHG effect, the P-6 phase exhibits superior NLO properties to the P-6c2 phase.
In negative uniaxial crystal, the SHG phase-matching condition can be summarized as follows: ne(λ/2) ≤ no(λ), where ne(λ/2) and no(λ) are the corresponding refractive index at the SHG and fundamental wavelengths, respectively. The calculated refractive index (Fig. 6b; Supplementary Fig. 10) reveals that in the P-6c2 and the P-6 phases ne(200 nm) < no(400 nm), indicating that these two NaBeBO3 structures achieve the SHG phase-matching condition in the DUV region. The shortest SHG wavelengths for the P-6c2 and P-6 are all about 195 nm.
Equally important, good crystal growth habit is essential to DUV functional optical material. It is well known that KBBF is the only material to generate coherent light in the DUV region by direct SHG response, whereas its layer habit seriously impedes its commercialization. The interlayer spacing of the P-6c2 and P-6 phases (about 3.27 Å; Fig. 7) is 2.98 Å shorter than that of KBBF (6.25 Å). Their adjacent (BeBO3)∞ layers are connected by the NaO6 polyhedra (about 2.43 Å), whose interlayer binding forces far outweigh that of KBBF. This confirms the reduction of layering tendency in P-6c2 and P-6.
By using the newly developed ABC structure searching algorithm and density functional total energy calculations, we systematically studied the possible existing phases of the NaBeBO3 quaternary compound at ambient pressure. The sp2 hybrid 3-fold coordinated Be atoms, which are never found in borates before, are discovered in four lowest energy NaBeBO3 structures. More importantly, the four lowest energy NaBeBO3 structures have short DUV cutoff edges about 170 nm and reduce the layer habit, and they exhibit extraordinary optical properties. The large birefringence values show that the NaBeBO3 structures are excellent candidates for DUV birefringent materials. The electronic structures and the SHG-weighted electron densities clearly show that the parallel (BeBO3)∞ layers are the main origin of the optical properties in these energetic favorable NaBeBO3 structures. On the whole, the P-6 phase exhibits a short UV cutoff edge of 171 nm (7.24 eV), a good SHG efficiency about one time that of KH2PO4, and is capable of being phase-matcheble in the DUV region. Importantly, it mitigates the laying tendency as observed in KBBF. All these facts demonstrate that NaBeBO3 with P-6 space group is a promising DUV NLO material. In summary, this work represents a significant step forward in predicting global optimization structures of complex crystal system, and also provides a successful manner to search for the next generation of DUV functional optical materials.
Before exploring the title compound, several known functional optical materials were predicted in the same manner. The experimental structures of KBe2BO3F247, BPO448, AgGaS249, ZnGeP2 (ref. 50) were all successfully reproduced at ambient pressure through ABC technique, validating our methodology in application to functional optical materials. The results are listed in Supplementary Fig. 11 and Supplementary Table 4.
Crystal structure prediction
We obtain candidate structures of NaBeBO3 by using swarm-intelligence CALYPSO (Crystal structure AnaLYsis by Particle Swarm Optimization) structure searching simulations unbiased by any prior known structure knowledge and in conjunction with first-principles density functional calculations. The artificial bee colony (ABC) algorithm, which is originally attributed to Karaboga et al.51, with symmetry constraint is implemented into CALYPSO software to keep the structural symmetry during structure evolution. The remarkable feature of this methodology is the capability of predicting stable structure with the only knowledge of the chemical composition.
We searched for structures of NaBeBO3 with simulation cell sizes of 1–6 formula units (f.u.) at ambient pressures using the CALYPSO package52. The local structural relaxations calculations were performed in the framework of density functional theory, using the generalized gradient approximation53 within the Perdew-Burke-Ernzerhof exchange functional theory54, and the frozen-core projector-augmented wave (PAW) method as implemented in the VASP code55. The adopted PAW pseudopotentials of Na, Be, B and O treat 3s1, 2s2, 2s22p1 and 2s22p4 electrons as valence. The cutoff energy 900 eV and appropriate Mnokhorst-Pack k-meshes were chosen to ensure that all enthalpy calculations were well converged to better than 1 meV/atom. The phonon calculations have been carried out by using a supercell approach as implemented in the PHONOPY code56. More computational details can be found in the Supplementary Information.
After ranking the enthalpy order of the NaBeBO3 structures, the electronic band structure, DOS and optical property calculations of the four low enthalpy structures were performed within the framework of DFT within the generalized gradient approximation (GGA) in the scheme of Perdew–Burke–Ernzerhof54, as implemented by CASTEP code57. The norm-conserving pseudopotentials used treat 2s22p63s1, 2s2, 2s22p1 and 2s22p4 as valence electrons for Na, Be, B and O atoms, respectively. The cutoff energy 810 eV and Monkhorst-Pack k point meshes with a grid of 0.025 Å−1 for Brillouin zone sampling were chosen to achieve a well-converged electronic structure and optical properties.
PBE0 hybrid functional58 was used to calculate the band structures. The calculation of optical properties was scissor corrected by the calculated energy gap difference between the PBE and the PBE0, the scissor operators of the four lowest energy structures are 2.51 eV (P63/m), 2.50 eV (P-6c2), 2.50 eV (P-3c1) and 2.50 eV (P-6). The SHG-weighted electron densities analysis59 was used to analyze NLO response of the NaBeBO3 structures. The theoretical methods were applied with success in a previous study to analyze the SHG coefficients of the NLO crystals60.
How to cite this article: Bian, Q. et al. Predicting Global Minimum in Complex Beryllium Borate System for Deep-ultraviolet Functional Optical Applications. Sci. Rep. 6, 34839; doi: 10.1038/srep34839 (2016).
The authors gratefully acknowledge the financial support of this work by National Basic Research Program of China (Grant No. 2014CB648400), National Natural Science Foundation of China (Grant Nos 11474353, 51425206), the Recruitment Program of Global Experts (1000 Talent Plan, Xinjiang Special Program), the Xinjiang International Science & Technology Cooperation Program (20146001), Xinjiang Key Laboratory Foundation (Grant No. 2014KL009), the Science and Technology Project of Urumqi (Grant No. 51425206).
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