Hardness of Covalent Crystals

  • Faming Gao, Julong He, Erdong Wu, Shimin Liu, Dongli Yu, Dongchun Li, Siyuan Zhang, and Yongjun Tian, Key Laboratory of Metastable Materials Science and Technology, College of Materials Science and Engineering, Yanshan University, Qinhuangdao 066004, China, Shenyang National Laboratory for Materials Science, Chinese Academy of Sciences, Shenyang 110016, China, Laboratory of Rare Earth Chemistry and Physics, Changchun Institute of Applied Chemistry, Chinese Academy of Sciences, Changchun 130022, China, and Laboratory of Solid State Microstructures, Nanjing University, Nanjing 210008, China
Phys. Rev. Lett. 91, 015502
Hv/EhNa as a function of ionicity fi. The solid line is from Eq. (7). Hv/EhNa as a function of ionicity fi. The solid line is from Eq. (7). Show more

Superhard materials are of primary importance in modern science and technology. Intense theoretical and experimental efforts have been focused on the possibility of finding new low compressibility materials with hardness comparable to diamond. In order to design the new superhard materials, clarifying the meaning of hardness is of utmost importance [1–3]. Over the last two decades, material scientists have aimed at finding materials with high values of bulk modulus E and shear modulus G [4–7]. In fact, bulk modulus measures resistance to volume change, which has little direct connection with hardness, as is well known from dislocation theory [8]. A better correlation has been observed between hardness and G, although, in this case too, the dependence is not unequivocal and monotonic. For example, the bulk and shear moduli of tungsten carbide which are as high as 439 and 282 GPa, respectively, are among the highest as known, but its hardness is only 30 GPa [1]. This implies that it is difficult to describe hardness quantitatively only by macroscopic physical properties of E and G.

In simple metals and ionic substances, the bonding is delocalized, and hardness is determined by extrinsic factors such as impurities, precipitates, grain boundaries, and the like. However, in covalent substances, the bonding is localized in electron spin pairs, thus hardness is intrinsic. Gilman’s theory indicates that chemical hardness and mechanical hardness have the same reaction barrier, which is the difference between energy of the lowest unoccupied electronic orbital and the highest occupied orbital [7]. Recently, Jhi et al. have investigated the correlation between valence electron concentration and hardness [9]. Their work has given a clue that hardness could be understood in terms of their electronic band structure. In our opinion, the hardness of covalent crystals is intrinsic and equivalent to the sum of resistance of each bond per unit area to indenter. This resistant force of bond can be characterized by energy gap, and the number of bond per unit area is determined by valence electron density. Based on this assumption, we represent a semiempirical method for the evaluation of hardness in covalent crystals.

Hardness was defined as the resistance offered by a given material to external mechanical action. Vickers and Knoop scales are frequently used. In static indentation tests, pyramid is forced into a surface and the load per unit area of impression is taken as the measure of hardness. Therefore, it is not surprising that the resistant force per unit area could play a key role in determining hardness of materials.

Generally speaking, hardness depends strongly on plastic deformation, which is related to the creation and motion of dislocations [1]. In a covalent crystal, bonding is highly stereospecific and dislocation energy depends strongly on its position. Regardless of details, a basic fact remains that, in order to plastically shear such a crystal, electron-pair bonds must first be broken and then remade, resulting in two unpaired electrons when an atomic shear process is half completed. Energetically breaking an electron-pair bond inside a crystal means that two electrons become excited from the valence band to the conduction band so the activation energy required for plastic glide is twice the band gap, Eg [10]. Thus, the resistant force of bond can be evaluated by energy gap Eg and the hardness of overly covalent crystals should have a following form:

where Na is the covalent bond number per unit area and A is a proportional coefficient. For a crystal with cell volume V, Na can be expressed as

where ni is the number of i atom in the cell, Zi is the valence electron number of i atom. Ne is the electron density expressed in number of valence electrons per cubic angstroms.

Equation (1) is suitable only for pure covalent crystals. For polar covalent crystals, besides the covalent component, a partial ionic component has to be considered. The average energy gap Eg for a binary polar covalent ABm type crystal can be separated into both of covalent or homopolar gap Eh and ionic or heteropolar gap C by Phillips [11]

where C represents the ionic or charge-transfer contribution, Eh represents the pure covalent contribution, and is equal to Eg in the case of a purely covalent Group IV crystal such as diamond or Si. Ionic bonding results from long-range electrostatic force which is not directly related to hardness [8]. Recent work also indicates that the activation energies of dislocation glide in polar covalent crystals are proportional to Phillips’s homopolar band gap Eh [12], which characterizes the strength of the covalent bond. Therefore, we can deduct the ionic contribution C from the factor Eg, leave only a homopolar component Eh for the hardness of polar covalent crystals, which is given as follows [11] :

where d is the bond length in angstroms, Eh is in electronvolts. However, the partly ionic bonding results in the loss of covalent bond charge [13]. In other words, an electron-pair localized on a chosen bond is screened due to partly ionic bonding and results in a smaller effective covalent bond number per unit area in comparison with that of Na for pure covalent crystals. Here we introduce a correction factor exp(-αfi) to describe this screening effect of many bonds, i.e., use Naexp(-αfi) for polar covalent crystals instead of Na for pure covalent crystals in Eq. (1), where α is a constant, fi is ionicity of chemical bond in crystal scaled by Phillips [11]:

In order to determine the correlation between the hardness Hv and ionicity fi, we plot Hv/EhNa against fi for some typical crystals from Table I as shown in Fig. 1. The exponential regression equation is obtained as follows:

For practical calculation of hardness, Eq. (6) can be expressed as

In order to confirm the practicability of Eq. (7), we calculated the Vickers hardness of typical covalent and polar covalent crystals and listed the results in Table I. The good agreements between the experimental and calculated values for the crystals with Vickers hardness above 10 GPa demonstrate the predictive power of Eq. (7). From the data in Table I, it can be deduced that the unexpected smaller hardness of tungsten carbide results from its larger bond length and smaller bond density.

Martin has revealed that the elastic properties of the sphalerite structure crystals, especially the shear modulus G, follow approximately linear trends as functions of the ionicity fi [22]. However, if we take into account polar covalent crystals with different structures, the shear modulus G does not show a systematic variation trends with fi, and no direct relation between hardness and shear modulus G can be established. Whereas as shown in Fig. 1, the hardness can be approximately described by an exponential function of ionicity.

It should be noticed that some secondary factors [7] affecting hardness have not been considered in our present model. As shown in Table I, α-SiO2 is such an example. Its experimental hardness is only 11 GPa, remarkably lower than its calculated value of 30.6 GPa. This is due to its open crystal structure, which is built up of SiO4 tetrahedra. These tetrahedra are linked only by their corners and can easily tilt. Under pressure of the indenter, the mechanism for plastic deformation and volume change in α- SiO2 is the rotation and bending of the framework tetrahedra about their shared oxygen atoms rather than the broken of the bonds of the frameworks [1,23].

Equation (7) will also be useful in predicting the trends of hardness for new materials. Since multicomponent compound systems are dominant in new materials, it is necessary to extend Eq. (7) to these systems. Based on Phillips scheme [11,14], a theory describing the chemical bond of complex crystals has been developed by Zhang et al. [15,16,24,25]. In the theory, “crystal formula” is a combination of subformula of chemical bond. The subformula of any type of chemical bond A-B in the multibond crystal AaBb can be expressed by the following formula:

where A,B, represent different elements or different sites of the same element in the crystal formula, and a,b, represent numbers of the corresponding element, N(B-A) represents the number of B ions in the coordination group of A ion, and NCA represents the nearest coordination number of A ion.

Similarly, the hardness of muticomponent compound systems can be expressed as an average of hardness of all binary systems in the solid [26,27]. When there are differences in the strength among different types of bonds, the trend of breaking the bonds will start from a softer one. Therefore, the hardness Hv of complex crystals should be calculated by a geometric average of all bonds as follow:

where Hvμ=350(Neμ)2/3e-1.191fiμ/(dμ)2.5 is the hardness of binary compound composed by μ-type bond, nμ is the number of bond of type μ composing the actual complex crystal, fiμ is the ionicity of binary compound composed by μ-type bond, which can be calculated according to the literature [15,16,24,25], Neμ is the number of valence electrons of type μ per cubic angstroms and is expressed as follows [15,16,24,25]:

where (neμ)* is the number of valence electrons per μ bond, (ZAμ)* or (ZBμ)* is the valence electron number of the A or B atom constructing μ bond, respectively, vbμ is the bond volume, and Nbν is the bond number of type ν per unit volume.

Ternary B-C-N compounds have also been considered as potential superhard materials. Cubic BC2N has been synthesized [28], whereas there have been no corresponding data of atom positions for cubic BC2N in the literature. In order to calculate the hardness Hv, we have carried out first principles calculation using the GGA approach of density functional theory with the Material studio [29]. In the calculations, geometry optimization for BC2N was performed with the same procedure as in the literature [5], a β-BC2N type structure is derived from the optimization. According to the calculated crystal structure of β-BC2N, and the chemical bond theory [15,16,24,25], we can write its bond-valence equation as follows:

The parameters of each type of chemical bond are calculated and listed in Table II. Based on this information and Eq. (9), the Vickers hardness of β-BC2N crystal is calculated and listed also in Table II. It can be seen that the calculated Vickers hardness value for β-BC2N crystal is very close to the experimental value of the synthesized cubic BC2N crystal [28].

In conclusion, three conditions should be met for a superhard material: higher bond density or electronic density, shorter bond length, and greater degree of covalent bonding. Our method presented here has satisfactorily predicted the trend of hardness for polar covalent solids. It has also built up a link between hardness and first principles calculation, and thus could play an important role in the design of new superhard materials.


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About the Authors

Image of Faming Gao
Image of Julong He
Image of Erdong Wu
Image of Shimin Liu
Image of Dongli Yu
Image of Dongchun Li
Image of Siyuan Zhang
Image of Yongjun Tian

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