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Structure and Electronic Properties of Transition Metal Doped Kaolinite Nanoclay

Nanoscale Research Letters201712:411

  • Received: 15 May 2017
  • Accepted: 5 June 2017
  • Published:


In this work, a series of transition metal (Cr, Mn, Fe, and Co) doped kaolinite nanoclays were investigated by density functional theory (DFT) calculations. The influence of metal doping on geometric structure and electronic structure of kaolinite was analyzed. The ferromagnetic (FM), antiferromagnetic (AFM), and nonmagnetic (NM) states of transition metal (TM) doped kaolinite structures were studied. The crystal volume, lattice parameters, bond length, charge, and spin were calculated by dispersion-corrected density functional theory (DFT-D2). The results indicated that Cr3+ and Fe3+ dopants showed more stable under AFM state, while Mn3+ preferred both AFM and FM states, and Co3+ dopant preferred NM state. Also, the transition metal doping could induce lattice volume expansion and some dopant states in the band gap.


  • Kaolinite nanoclay
  • Transition metal
  • Doping
  • Electronic structure
  • Dispersion-corrected density functional theory


Kaolin-group nanoclay minerals, as a result of hydrothermal alteration and/or weathering processes, have unique physical properties because of their layered structure, small grain size, and most importantly the hydrated surface with plenty of hydroxyl groups. It has attracted the attention of researchers in materials chemistry, environmental chemistry, and mineral physics [111]. Kaolinite, one of the most abundant nanoclay minerals on Earth, has been wildly used in plastics, catalysis, and the cement industry. Further functionalization of kaolinite as novel support materials has attracted more and more attentions in various fields. Kaolinite can simply serve as support materials to mix with other nanoparticles to form phase change materials for solar energy utility [4, 5] or coated with doped oxide to form conductive powders for applications in conductive fields [9, 12]. The hybridization of kaolinite with functional nanoparticles was found to enhance the photocatalytic activity of Pd–ZnO and the luminescence properties of CdS through a synergistic effect [6, 7]. The surface properties of kaolinite were modified by anchoring some functional groups at the surface [13, 14] or by acid activation pretreatment for further improvement [2].

The structures and energetics of kaolin-group minerals have been extensively investigated experimentally [1517] and theoretically [1822]. Theoretical study of heavy metal adsorption on the kaolinite surface were studied for Cd, Cu, Hg, and Ni(II) adsorption [23], in which adsorption ability of kaolinite clay for ions were found in the order of Ni > Cu > Cd > Hg(II). The adsorption and diffusion of Pb(II) [24, 25] and uranyl [26] on the kaolinite (001) surface were studied [2426], and the adsorption behavior in aqueous system was also reported later [27, 28]. The influence of Mg, Ca, and Fe doping on kaolinite surface, and the subsequent adsorption and penetration of H2O into the interlayer were studied [29]. The adsorption energies of H2O on doped kaolinites (001) were found less than undoped surface. The electronic structure of kaolinite with and without intrinsic defects has been studied by the standard density functional theory (DFT) functionals and hybrid functionals [30]. However, not until recently have the structure evolutions during the dehydroxylation, dealumination, and silica condensation process of kaolinite are modeled by DFT calculations [1, 31, 32]. The removal of Al in kaolin-group materials greatly altered the geometry and electronic properties of these layer materials and improved their support effect [1, 2].

Metal doping, as a well-known method to modify the structure and properties of compounds, has been theoretically studied for Al2O3 [33], TiO2 [34], MOF [35], and other solids [36]. To explore the changes in structure and properties of kaolinite nanoclay upon transition metal (TM) doping would be interesting for this layered clay material. In this work, a series of Cr, Mn, Fe, and Co doped kaolinite nanoclay were studied by DFT calculations and focused on the influence of metal doping on geometric structure and electronic structure of kaolinite nanoclay. The possible ferromagnetic (FM), antiferromagnetic (AFM), and nonmagnetic (NM) states of these transition metal doped kaolinite structures were studied. The lattice parameters, bond length, charge, and spin were optimized and calculated by dispersion-corrected density functional theory (DFT-D2).


All calculations were performed with the program CASTEP (Cambridge Sequential Total Energy Package) code [37], based on first-principle DFT. Generalized gradient approximation (GGA) with the exchange-correlation potential by Perdew, Burke, and Ernzerhof (PBE) was used for the calculations [38]. Grimme’s DFT-D2 dispersion corrections were included to account for Van der Waals dispersion interactions [39]. An energy cutoff of 500 eV was applied using the ultrasoft pseudo-potential plane-wave formalism [40]. The Monkhorst–Pack [41] grid with 2 × 2 × 3 k-point mesh was used for geometrical relaxation and electronic structure calculations. The self-consistent total energy in the ground state was effectively obtained by the density-mixing scheme [42]. For the geometry optimizations, the convergence threshold for self-consistent field (SCF) tolerance was set to 1.0 × 10−6 eV/atom, all forces on the atoms were converged to less than 0.03 eV/Å, the total stress tensor was reduced to the order of 0.05 GPa, and the maximum ionic displacement was within 0.001 Å. The elements investigated in valence states were O(2s22p4), Al(3s23p1), Cr(3s23p63d54s1), Mn(3d54s2), Fe(3d64s2), and Co(3d74s2). Uspcc pseudo-potentials were used for Mn, Fe, and Co, and usp pseudo-potentials for the rest of the elements. The cell parameters and atomic coordination were fully relaxed during the geometry optimization using a Broyden–Fletcher–Goldfarb–Shanno (BFGS) minimization algorithm. The crystal symmetry was removed by imposing different initial magnetic moments on TM ions so that the electronic ground state could adopt lower symmetry.

Results and Discussion

The initial kaolinite structure was taken for our previous work [1]. Figure 1 shows the relaxed 2 × 2 × 1 crystal structure of kaolinite (4 kaolinite units). The kaolinite layer structure, Al2Si2O5(OH)4, is composed by an octahedral Al–O sheet and a tetrahedral Si–O sheet, connected by apical O atom (Oa). The Si–O tetrahedron is constructed by one central Si atom and four surrounding O atom, in which one is the Oa atom and the other three are the basal O atoms (Ob). The Al–O octahedron is constructed by one central Al and six surrounding O, in which two are Oa atom and the other four are O atoms (in OH groups) shared with other Al–O octahedron. Besides, these OH groups can be divided into two kinds: the inter-layer OH (OHinter) at the surface of the layer structure and the inner OH (OHinner) inside the layer structure between the Al sheet and the Si sheet. Hence, there are two kinds of Si–O bonds, Si–Oa and Si–Ob (black dot line), and three kinds of Al–O bonds, Al–Ointer (red dot line), Al–Oinner (green dot line), and Al–O (black dot line) in kaolinite bulk structure.
Fig. 1
Fig. 1

Top (up) and side (down) views of kaolinite. The Si–Oa (black), Si–Ob (black), M–OHinter (red), M–OHinner (green), and M–O (blue) bonds are indicated by dot lines

The dispersion energy always plays a major role in the structure stabilization of clay mineral due to the interaction between the layers [21, 43]. Among the several hybrid functionals, PBE-D2 [21], B3LYP [22], B3LYP-D [18], and RPBE-D2 [18, 21], which was used to obtain the experimental lattice structure of kaolinite [44, 45], PBE-D2 functional was found both accurate and less time consuming. The overestimation of PBE functional for bond lengths are overcome by dispersion correction compared to experimental results, as briefly reported previously [1]. In order to distinguish the effect of TM doping on the structure of kaolinite, here, we first revisit the lattice structure and the optimized bond distances between central cations (Si and Al) and oxygen atoms, Oa, Ob, and OHinn.

As shown in Table 1, for kaolinite, the calculated unit cell volume optimized using dispersion-corrected PBE-D2 functional is close to the experimental value, which gives significantly lowered relative error (0.4%) compared to PBE functional (3.4%). For lattice vectors a and b, the relative error using PBE-D2 (0.4%) is much lower than PBE (1.1%). And, under dispersion corrections of PBE-D2, the layer distance (vector c) of kaolinite is decreased by 0.17 Å (2%). Notably, the lattice angles after dispersion correction are very close to experimental results, especially for α. As for bond length distributions in kaolinite, although PBE-D2 gives little improvement for Si–Oa, Al–OHinner, and Al–O bonds compared with experimental results, a huge improvement is made for Al–OHinter bond at Al–O surface (which is important for surface chemistry) and slight improvement for Si–Ob bond at Si–O surface. Notably, for Al–OHinter bond, the dispersion correction from PBE-D2 seems to accurately describe the bonding environment at outmost layer of the Al–O surface, which is strongly influenced by the dispersion force from the Si–O surface of another kaolinite layer that lies above. Another point to mention here is that there are actually two splitted Al–O bonds (Fig. 1, blue dot line) with significantly different bond lengths of about 1.95 and 2.00 Å [45], which shows the lattice distortion of the Al–O octahedron originated from the lattice mismatch between Si–O sheet and Al–O sheet. As a major error in the calculation of kaolinite structure compared to experimental results, these Al–O bonds are overestimated by both PBE and PBE-D2, with similar averaged bond length (Table 1). PBE-D2 gives two Al–O bonds of approximately 1.96 and 2.04 Å, with the second one overestimated by 0.04 Å (Fig. 2, blue dot line).
Table 1

Calculated and experimental unit cell parameters (Å) and averaged bond lengths (Å) of kaolinite and the most stable TM–kaolinite structure with AFM, FM, and NM states. The M–O bond represents the Al–O bond for kaolinite or the TM–O bond for TM–kaolinite. The average charge and spin of M atoms are also given

















Exp [45]


V (Å3)











a (Å)











b (Å)











c (Å)











α (deg)











β (deg)











γ (deg)



































































































Fig. 2
Fig. 2

The bond distribution of Cr–, Mn–, Fe–, and Co–kaolinite. Multi-magnetic states are given for each TM–kaolinite. The averaged different types of O–H (black), Si–Oa (black), Si–Ob (black), M–OHinter (red), M–OHinner (green), and M–O (blue) bonds in kaolinite are indicated by dot lines. The M–OHinter (red), M–OHinner (green), and M–O (blue) bonds in Cr–kaolinite (AFM), Mn–kaolinite (FM), Fe–kaolinite (AFM), and Co–kaolinite (NM) are indicated by solid lines

The transition metals (Cr, Mn, Fe, and Co) doped kaolinites were constructed by replacing Al atom with Cr, Mn, Fe, or Co atom. Only the equivalent substitution of Al3+ ion with TM3+ ion was considered since nonequivalent substitution of TM ions with chemical state other than +3 will cause additional vacancies or impurities for charge balance. From structure point of view, PBE and PBE-D2 functionals of TM–kaolinite give similar structure difference as observed for kaolinite. Considering that PBE-D2 functional describes better for lattice vectors and bond lengths of the two basal surfaces of kaolinite, following discussion on TM–kaolinite, mainly depended on the results obtained by PBE-D2 functional. The lattice parameters, bond length, charge, and spin of TM doped kaolinite and their magnetic states were summarized in Table 1. The energy differences (per TM atom) between AFM and FM states for Cr–kaolinite, Mn–kaolinite, and Fe–kaolinite are 0.022, −0.006, and 0.094 eV, respectively. Since Co–kaolinite structure is only stable at a nonmagnetic state, only NM structure of Co–kaolinite is shown.

The unit cell volumes of TM–kaolinite are expanded compared to kaolinite, with a trend of Mn–kaolinite > Fe–kaolinite >> Cr–kaolinite >> kaolinite > Co–kaolinite. The cell expansions are mainly caused by the longer M–O bonds compared to Al–O bonds, leading to the major expansion in lattice vectors a and b. Meanwhile, the Si–Ob bonds at the Si–O sheet are elongated simultaneously, and the crystal lattice angles of α and β are distorted accordingly. The cell volume of Mn–kaolinite with FM state is increased by 1.4% compared to AFM state, while in contrast little influence of magnetic ordering on cell volumes is found for Cr–kaolinite and Fe–kaolinite. The magnetic moments of Cr, Mn, Fe, and Co are close to that in TM doped Al2O3 [33], while the Mulliken charge are slightly higher which implies stronger reactivity.

The bond length distributions of TM–kaolinite are analyzed in Fig. 2, with different types of Si–O and M–O bonds in TM–kaolinite indicated by solid lines for each doping element. Overall speaking, there is an increase of the bond lengths of M–O and Si–Ob after TM doping, and meanwhile there is a reorganization of the bond distribution of the splitted M–O bonds for M–OHinter (red), M–OHinner (green), and M–O (blue) bonds. Notably, the splitted Al–O bonds (blue dot line) disappeared after Cr and Co doping. Furthermore, the bond length distributions are highly dependent on the magnetic ordering for Mn atoms but are only slightly influenced for Cr and Fe atoms.

The PDOS results for Cr3+(d3), Mn3+(d4), Fe3+(d5), and Co3+(d6) and the corresponding charge density distributions are shown in Figs. 3 and 4. According to the Jahn–Teller theorem, any degenerate electronic system will spontaneously distort in such a way as to remove the degeneracy [46], which is affected by the surrounding bonding environment [47]. For TM3+ doping in octahedral Al site of kaolinite with plenty of hydroxyl groups, the five d-shell orbitals of TM3+ will split into a triplet t2g state and a doublet eg state under Oh symmetry. The electrons in the triplet state are localized in the middle region between the ligands and further hybridized with the nearest O states. Those in the doublet state point directly at the ligands and thus lie higher in energy than the t2g electrons. Generally, the presence of electrons in the eg orbitals tends to destabilize the octahedral bonding, and the degeneracy is removed by lengthening the bonds opposite the filled orbital and shortening the bonds opposite the empty orbital. The d–d transition of TM3+(Oh) species is always from the occupied t2g orbitals (dxy, dyz, and dzx) to unoccupied eg orbital (dx2-y2 or dz2, depending on their occupancy). The orbital splitting between eg orbitals and t2g orbitals of Cr3+(d3), Mn3+(d4), Fe3+ (d5), and Co3+ (d6) in TM–kaolinite is similar with that in Al2O3 and TiO2 [33, 48, 49], but the splitting energies between 3d orbitals are slightly larger than in their own oxides (Fig. 3), possibly due to the hybridization with the surrounding hydroxyl groups.
Fig. 3
Fig. 3

Total density of states (DOS) and atom-projected density of states (PDOS) of the most stable states for TM doped kaolinite are given. The highest occupied 3d orbitals (yellow) and the first (brown) and second (purple) lowest unoccupied 3d orbitals around Fermi level are pointed by colored arrows

Fig. 4
Fig. 4

Partial charge density of TM 3d orbitals in TM–kaolinite, corresponding to the states pointed by arrows in PDOS results. The isosurface levels are 0.02 e/Å3

The difference of splitting energies between FM and AFM states of Mn–kaolinite is small, and the distributions of density of states are similar except the spin directions are different. Hence, for simplicity, only the results for AFM state are shown. For the high-spin Mn3+(d4) ion in Mn–kaolinite with AFM state, only one of the two eg orbitals is occupied at the valence band maximum (VBM) (Fig. 3, yellow arrow). The occupation of dz2 orbital which is lower in energy gives a strong repulsion on the bonding electrons of the two ligands along the z axis and elongates the M–O bonding in that direction. This effect is the well-known Jahn–Teller effect. The states at the bottom of the conduction band minimum (CBM) are composed by the lowest unoccupied dz2 orbital (brown arrow) and the higher dx2y2 orbital (purple arrow) of Mn3+(d4). For Cr3+(d3), Fe3+ (d5), and Co3+ (d6) doped case, where the t2g and eg orbitals are occupied evenly, the influence of Jahn–Teller distortion effect is small, which only caused slight deviation of the M–O bonds in TM–kaolinite (Fig. 2). Such modification of structure and electronic properties by TM doping might improve the application of kaolin in the field of catalysis [50, 51], CO capture [52, 53], drug loading [54], and energy storage [5557]. And, it can also be applied to other minerals, such as montmorillonite [50, 58], perlite [55], and talc [59] to alter their electronic properties.


The influence of transition metal (Cr, Mn, Fe, and Co) doping on geometric structure and electronic structure of kaolinite nanoclay are investigated by DFT calculations. The crystal volume, lattice parameters, bond length, charge and spin, and possible magnetic states are calculated and studied. The Cr3+ and Fe3+ dopants show more stable under AFM state, Mn3+ prefer FM state, and Co3+ dopants prefer NM state. The transition metal doping induces lattice volume expansion and some reorganization of the M–O bond distributions. Meanwhile, the TM dopants introduce some 3d states with larger splitting energies in the band gap of kaolinite.







Cambridge Sequential Total Energy Package


Conduction band minimum


Density functional theory


Dispersion-corrected density functional theory




Generalized gradient approximation




Perdew, Burke, and Ernzerhof


Self-consistent field


Transition metal


Valence band maximum



This work was supported by the National Science Fund for distinguished Young Scholars (51225403), the Strategic Priority Research Program of Central South University (ZLXD2017005), the National “Ten Thousand Talents Program” in China, the Hunan Provincial Science and Technology Project (2016RS2004, 2015TP1006), and the Postdoctoral Science Foundation of Central South University (201507). Computing resources were provided by High Performance Computing Centre of Central South University and the National Supercomputing Centre of China in Shenzhen.

Authors’ Contributions

HY conceived the project and wrote the final paper. LF carried out the calculations and wrote the initial drafts of the work. LF and HY analyzed the data, discussed the results, and commented on the manuscript. Both authors read and approved the final manuscript.

Competing Interests

The authors declare that they have no competing interests.

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Authors’ Affiliations

Centre for Mineral Materials, School of Minerals Processing and Bioengineering, Central South University, Changsha, 410083, China
Peter A. Rock Thermochemistry Laboratory and NEAT ORU, University of California Davis, One Shields Avenue, Davis, CA 95616, USA
Hunan Key Lab of Mineral Materials and Application, Central South University, Changsha, 410083, China


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