_{1/3}Co

_{1/3}Mn

_{1/3})O

_{2}

2. University of Chinese Academy of Sciences, Beijing 100049, China

**Abstract**: After describing research status of super-structure for Li(Ni

_{1/3}Co

_{1/3}Mn

_{1/3})O

_{2}, diffraction patterns of Li(Ni

_{1/3}Co

_{1/3}Mn

_{1/3})O

_{2}in different order parameters have been researched by Powder-cell program, including crystal structure, X-ray and neutron diffraction pattern, anomalous diffraction pattern and comparison of Ni Co Mn in different positions. The influence of order parameters on intensity of matrix and super-lattice diffraction lines has also been analyzed and the summarization and prospect have been made lastly.

_{1/3}Co

_{1/3}Mn

_{1/3})O

_{2}order-disorder diffraction

Due to its high cost and toxicity, commercial cathode material LiCoO_{2} in lithium ion batteries is gradually replaced by Li(Ni, Co, Mn)O_{2}, among which Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} is the most competitive for its over-all properties^{[1-4]}. All of these cathode materials have a rhomboidal structure with trigonal symmetry (space group: R-3m, No.166), which is layer-structural with α-NaFeO_{2}. Usually, transition metal ions Me (Ni, Co, Mn) are located in octahedral 3*b* (0 0 1/2) sites and oxygen anions are in a cubic close-packing, occupying the 6*c*(0 0 *z*) sites. Lithium cations reside at Wyckoff 3*a*(0 0 0) sites, represented as [Li]_{3a}[Me]_{3b}[O_{2}]_{6c}. In addition, there are three symmetry operations in this structure, including (0, 0, 0), (1/3, 2/3, 2/3), (2/3, 1/3, 1/3).

Since the discovery of Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2}, the arrangement of transition metal in 3*b* is the key point of contention^{[5-10]}. At present, there are three supposed models for it. The first model, as illustrated in Fig. 1(a), consists of [Co_{1/3}Ni_{1/3}Mn_{1/3}]O_{2} slabs of the [_{2}, NiO_{2} and MnO_{2} slabs piled up regularly^{[11]}. In the third model, Ni, Co and Mn are randomly located in 3*b*, i.e. disorderly O3 structure.

The formation energy of the super-lattice model calculated by Koyama et al.^{[11]} was -0.17 eV per formula unit, and that of stacking model was +0.06 eV. So it is more possible that the super-lattice model exists, which restricts the volume change of cathode between charging and discharging and improves cycling life due to the stable lattice structure. Through XRD refinement, Yabuuchi et al.^{[11]} found that the [_{1}12, not simple R3m. Furthermore, electron diffraction study indicated that there exited the [

Although the arrangement of inner atom in Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} can be verified by calculation and detection, it cannot be proved that this material has the completely orderly arrangement^{[13-17]} in Fig. 1(a). Whitfield^{[18]} studied the structure of Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} by neutron(as shown in Fig. 3) and anomalous dispersion powder diffraction and found a random distribution of Mn, Ni, and Co over the R3m 3*b* sites. Rietveld analyses(as shown in Table 1) indicated that about 2% nickel migrated from 3*b* site to 3*a* site due to the similar atomic radius of Ni^{2+} (*r*_{Ni2+}=0.69 Å) and Li^{+} (*r*_{Li+}=0.76 Å), which was also called cation disorder. The more Ni^{2+}cations in Li^{+} layer, the harder deintercalate-intercalate of Li^{+}, so the electrochemical performances became worse.

The super lattice diffraction lines may appear after ordering treatment the order degree has an effect on the diffraction intensity of super lattice line; sometimes the super lattice diffraction lines do not appear but the diffraction intensity of matrix diffraction lines change^{[19-22]}. So we can calculate the order degree by diffraction intensity data, which depends on the crystal structure^{[23]}. In this paper Powder-cell was used to simulate diffraction patterns and intensity of the super and matrix lattices.

It was supposed that theorder degree *S*, was 0, 0.5 and 1. Space group was No.166, R3m, *a*=2.963, *c*=14.252, the atom positions^{[24]} are shown in Table 2. When *S* was 0, Ni, Co and Mn were randomly occupied in (0, 0, 1/2), (1/3, 2/3, 7/6) and (2/3, 1/3, 5/6), whose occupancy(SOF) were 1/3. When *S* was 1, Ni, Co and Mn were orderly occupied respectively in (0, 0, 1/2), (1/3, 2/3, 7/6) and (2/3, 1/3, 5/6), whose SOF were 1.0. When *S* was 0.5, it became complicated. Ni, Co and Mn were occupied in (0, 0, 1/2), (1/3, 2/3, 7/6) and (2/3, 1/3, 5/6) by order degree of 0.5. At the same time, they were occupied in 3*b* site by *SOF*=0.5×0.333=1/6. The crystal structure model was illustrated in Fig. 4.

3 X-ray and Neutron Diffraction Pattern

Figs. 5 and 6 show the diffraction patterns of X-ray and neutron at different *S*, and the specific data is listed in Table 3. As we can infer from the comparison data, there are obvious difference between the XRD pattern and neutron diffraction pattern. Three strength lines are distinct, the first strength line is different. The second strength lines decrease with the increase of *S*, but the third lines are almost constant. This is because that the scattering factors of Ni, Co, Mn have little difference for X-ray, while the difference for neutron is much larger. So the problem of order occupying position of neighboring atom is often studied by neutron diffraction^{[7]}.

4 Comparison of Ni, Co, Mn Occupied in Different Positions

The diffraction data was listed in Table 4 when *S*=1 and Ni, Co and Mn occupied in different position. It is known from the comparison that three strength distribution and relative intensities are the same and their structure amplitudes are similar.

5 Anomalous X-ray Diffraction Pattern

The anomalous diffraction is a diffraction experiment one using the radiation of some element's absorbing wavelength as incident ray, called as the anomalous scattering or anomalous diffraction, which is also called diffraction of choosing elements.

When there is anomalous diffraction, the total atomic scattering factor is given by:

$ {f_{\left( {S,\lambda } \right)}} = {f_{0\left( S \right)}} + {{f'}_{\left( {S,\lambda } \right)}} + {\rm{i}}{{f''}_{\left( {S,\lambda } \right)}} $ | (1) |

where *f*' and *f*" are the real and imaginary parts of anomalous diffraction correction, *f*' and *f*_{0} have the opposite phases, the phase of *f*" is 90°. And *f* is:

$ f = \sqrt {{{\left( {{f_0} + f'} \right)}^2} + {{\left( {f''} \right)}^2}} $ | (2a) |

The approximate form is:

$ f = {f_0} + f' + \frac{1}{2}\frac{{{{\left( {f''} \right)}^2}}}{{{f_0} + f'}} $ | (2b) |

The effects of anomalous diffraction on total scattering factor are as follows:

1) Anomalous diffraction can be ignored when the incident ray's wavelength is far from absorbing limit;

2) Near the absorption limit, anomalous scattering correction is quite large and increases with the scattering angle;

3) When the incident ray's wavelength is equal to absorption limit, anomalous diffraction can play a dominant position at high diffraction angles;

4) Anomalous diffraction correction is related to the atom number of the scattered due to different element has different absorbing limit.

So we can study the long range order of neighboring atoms by anomalous diffraction in principle. As seen from Table 5, the position of diffraction lines increases with the wavelength and moves to the high angle, while the relative intensity has no change. It seems that anomalous diffraction has no effect, but actually possible cause is that Powdercell could not carry out the correction of the anomalous scattering.

6 Influence of Order Degree on Intensity of Matrix Diffraction

The analysis shows that the order of Ni, Co and Mn in the 3*b* position has little effect on the matrix diffraction relative intensity for both the conventional and anomalous X-ray diffraction.

Under symmetric Bragg reflection geometry condition in the X-ray powder diffraction, the relative integral intensity for single-phase can be expressed as follows:

$ {I_{hkl}} = {P_{hkl}}{\left| {{F_{hkl}}} \right|^2}\frac{{1 + {{\cos }^2}2{\theta _{hkl}}}}{{{{\sin }^2}{\theta _{hkl}}\cos {\theta _{hkl}}}} $ | (3) |

where *P _{hkl}* is the multiplicity factor of crystal plane (

*hkl*),

*F*is structure factor, the last is angle factor. The formula of structure factor is:

_{hkl}$ \begin{array}{l} {F_{hkl}} = \sum\limits_{j = 1}^n {{f_j}{e^{2{\rm{ \mathsf{ π} i}}\left( {h{x_j} + h{y_j} + l{z_j}} \right)}}} = \sum\limits_{j = 1}^n {{f_j}\left[ {\cos 2{\rm{ \mathsf{ π} }}\left( {h{x_j} + k{y_j} + } \right.} \right.} \\ \;\;\;\;\;\;\;\;\;\left. {\left. {l{z_j}} \right) + {\rm{i}}\sin 2{\rm{ \mathsf{ π} }}\left( {h{x_j} + k{y_j} + l{z_j}} \right)} \right] \end{array} $ | (4) |

where *f _{j}* is the scattering factor of

*j*atom.

*x*,

_{j}*y*,

_{j}*z*is the coordinate of

_{j}*j*atom. Summation is for all atoms in single cell. Specifically for Li(Ni

_{1/3}Co

_{1/3}Mn

_{1/3})O

_{2}, they contain 3 Li atoms, 3 transition metal atoms and 6 oxygen atoms. The position parameters of main diffraction lines are listed in Table 6.

Suppose *f*_{3a}, *f*_{3b}, *f*_{6c} are the atom scattering factor of atoms on 3*a*, 3*b* and 6*c* position, then we get the following formula for Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2}:

$ \left\{ \begin{array}{l} {f_{3a}} = {f_{\left( {3a} \right)1}} + {f_{\left( {3a} \right)2}} + {f_{\left( {3a} \right)3}} = 3{f_{Li}}\\ {f_{6c}} = {f_{\left( {6c} \right)1}} + {f_{\left( {6c} \right)2}} + \cdots + {f_{\left( {3c} \right)6}} = 6{f_o} \end{array} \right. $ | (5) |

*f*_{3b} is complicated, when *S*=0,

$ {f_{3b}} = \frac{1}{2}\left( {{f_{{\rm{Ni}}}} + {f_{{\rm{Co}}}} + {f_{{\rm{Mn}}}}} \right) \times 3 $ | (6) |

when *S*=1

$ {f_{3b}} = {f_{{\rm{Ni}}}} + {f_{{\rm{Co}}}} + {f_{{\rm{Mn}}}} $ | (7) |

when 0 < *S* < 1

$ \begin{array}{l} {f_{3b}} = S \times \left( {{f_{{\rm{Ni}}}} + {f_{{\rm{Co}}}} + {f_{{\rm{Mn}}}}} \right) + \\ \;\;\;\;\;\;\;\;\left( {1 - S} \right) \times \frac{1}{3}\left( {{f_{{\rm{Ni}}}} + {f_{{\rm{Co}}}} + {f_{{\rm{Mn}}}}} \right) \times 3 \end{array} $ | (8) |

Eq.(8) shows that, when 0 < *S* < 1, atomic scattering factor of 3*b* position includes two parts. The first item describes the orderly occupying part, while the second item describes contribution of randomly occupied atoms remaining after orderly occupying. *f*_{Li}, *f*_{Ni}, *f*_{Co}, *f*_{Mn}, *f*_{o} are the scattering factor of Li, Ni, Co, Mn and O atoms respectively. They are all the functions of (sin*θ*)/*λ* and decrease with (sin*θ*)/*λ* increasing. For the same diffraction pattern, *λ* is constant, which means atom scattering factor decreases with 2*θ* increasing.

Similarly, the diffraction angle factor(1+cos^{2}2*θ _{hkl}*)/ (sin

^{2}

*θ*cos

_{hkl}*θ*) decreases with 2

_{hkl}*θ*increasing. The specific values can be calculated or obtained from professional books.

Thus, main characters of each diffraction lines of Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} can be summarized as follows:

(1) Considering the contribution of oxygen on 6*c* position to diffraction intensity, it can be divided into:

No contribution: 003, 101, 015, 009, 107, 018, 113;

The addition: 104, 110;

The subtraction: 006, 012.

(2) Considering the contribution of atoms on 3*a* and 3*b*, it can be divided into:

The addition: 006, 012, 104, 110, 018;

The subtraction: 003, 101, 015, 009, 107, 113.

(3) The"addition" and "subtraction" relationship reveals a very important rule. Take 003, 101 and 104 as examples, *F _{hkl}* is :

$ \left\{ \begin{array}{l} {F_{003}} = 3f_{{\rm{Li}}}^{003} - S \times \left( {f_{{\rm{Ni}}}^{003} + f_{{\rm{Co}}}^{003} + f_{{\rm{Mn}}}^{003}} \right) - \left( {1 - S} \right) \times \\ \;\;\;\;\;\;\;\;\;\frac{1}{3}\left( {f_{{\rm{Ni}}}^{003} + f_{{\rm{Co}}}^{003} + f_{{\rm{Mn}}}^{003}} \right) \times 3\\ {F_{101}} = 3f_{{\rm{Li}}}^{101} - S \times \left( {f_{{\rm{Ni}}}^{101} + f_{{\rm{Co}}}^{101} + f_{{\rm{Mn}}}^{101}} \right) - \left( {1 - S} \right) \times \\ \;\;\;\;\;\;\;\;\;\frac{1}{3}\left( {f_{{\rm{Ni}}}^{101} + f_{{\rm{Co}}}^{101} + f_{{\rm{Mn}}}^{101}} \right) \times 3\\ {F_{104}} = 3f_{{\rm{Li}}}^{104} + S \times \left( {f_{{\rm{Ni}}}^{104} + f_{{\rm{Co}}}^{104} + f_{{\rm{Mn}}}^{104}} \right) + \left( {1 - S} \right) \times \\ \;\;\;\;\;\;\;\;\;\frac{1}{3}\left( {f_{{\rm{Ni}}}^{104} + f_{{\rm{Co}}}^{104} + f_{{\rm{Mn}}}^{104}} \right) \times 3 + 6f_{\rm{O}}^{104} \end{array} \right. $ | (9) |

The diffraction line 104 is stronger than 101. The first part in the formula is the contribution of Li atoms; the second part is the contribution of orderly Ni, Co, Mn on 3*b*; the third part is the contribution of randomly Ni, Co, Mn on 3*b*; the fourth part is the contribution of oxygen on 6*c*. It can be inferred from Eq.(9) that the contribution of 3*a* and 3*b* to 003 and 101 is subtraction, for both 003 and 101 oxygen have not contribution. While contribution of 3*a* and 3*b* to 104 is addition.

With *S*=0, 0.2, 0.4, 0.6, 0.8, 1.0, the relative intensity of the calculation results (as shown in Table 8) and analysis results show that there is no influence of order degree on diffraction intensity matrix lines. In other words, the diffraction intensity of matrix lines has no relationship with order and disorder in the 3*b* site. Therefore the order degree, *S*, cannot be solved from the diffraction data of matrix lines.

7 Influence of Order Degree on Intensity of Super-lattice Diffraction Line

It is known from the above research that the ordering on 3*b* positions does not show diffraction lines of super-lattice for Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} belong to the No.166 space group structure. In order to prove whether it is right, the author has made a simulated study diffraction patterns of the classic AuCu_{3} super structure. The result shows that only when the use of crystallographic position are the same, but space group (extinction rule) is different, (No.225, Fm-3m and No.221, Pm-3m), diffraction pattern calculated can show the super-lattice lines. It can derive from his conclusion that above simulated diffraction patterns using No.166 space group do not appear super-lattice lines cannot prove that the diffraction pattern of Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} with super-structure cannot appear super lattice lines.

In the rhombohedral system with space group (No.143-No.167) was not found corresponding space group which *x*, *y*, *z* coordinates are the same with (3*b*) positions in No.166 space group and the extinction conditions are different. That No.166 after (3*b*) ordering has symmetry of P3_{1}12 (No.151)^{18} is questionable, because *x*, *y*, *z* coordinates of atoms are obviously different and extinction rule is similar between No.151 and No.166 space group.

To this end, wecalculated the crystallographic position parameters of space group No.166 may appear the super-lattice lines: 001, 002, 004, 111, as shown in Table 7.

We can conclude from analysis of Table 7:

(1) The 3*a* and 6*c* position atoms are no contribution to the diffraction intensity of 001, 002, 004 and 111.

(2) 3*b* position atoms contribution to the diffraction intensity are more complex; when disordered (*S*=0) occupation, the atomic scattering factors for each position are equal to (*f*_{Ni}+*f*_{Co}+*f*_{Mn})/3 the same, such as, factor scatter factor for each position, the contribution of three position is equal to zero; when totally ordered (*S*=1) occupation, the scattering factors of three position are different, the contribution of three positions is not zero, then the super-lattice lines can appear; and the larger the difference of atomic scattering factor between the three positions is, the stronger super-lattice line is. Therefore, using the anomalous diffraction techniques or/and neutron diffraction is beneficial to studying a super-lattice structure.

(3) When 0 < *S* < 1, structure factor is divided into two parts, ordered partials have contributed to intensity and the remaining disorder part has no contribution to intensity.

The effect of order degree on the diffraction intensity has calculated using the data given in Table 8, because 104 and 111 almost overlap, so only for four diffraction of 002, 003, 004, 101 was calculated. The results are given in Table 9.

We can see from analysis of Table 9:

(1) The matrix diffraction intensity does not change with *S*, in other words, the diffraction intensity of matrix line is not influenced by *S*;

(2) Diffraction intensity of super-lattice lines increases with the increase of *S*, which can solve an order degree, *S*, according to the intensity data super-lattice diffraction lines or super-lattice and matrix diffraction lines.

(3) The relative intensity of super-lattice lines is very weak, even *S*=1, the relative intensity of 002 and 004 super two points front is only 0.225% and 0.043%. So the general diffraction experiment is very difficult to detect the super-lattice lines.

For Li (Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2}, when Ni, Co, Mn ordered occupied in 3*b*, diffraction intensity of the matrix lines is not influenced by order degree *S*; but the diffraction intensity of super-lattice lines increase with the order degree. Theoretically, one can solve an ordering degree, *S*, according to the intensity data super-lattice diffraction lines or super-lattice and matrix diffraction lines, but it is very difficult because diffraction intensity of the super-lattice lines is very weak, in general diffraction experiments.

Therefore, whether orderly occupying is existed in 3*b* of Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} and forms of super structure still need further study in the following aspects:

1) To explore the optimal process of ordering treatment for Li(Ni_{1/3}Co_{1/3}Mn_{1/3})O_{2} material under the appropriate medium temperature;

2) To enhance the detection ability of diffraction experiment, use strong X-ray source, such as synchrotron radiation X-ray source, use high efficient detector, super fine experimental operation, such as slow speed scan and anomalous diffraction techniques or/and the neutron diffraction technique;

3) According to the relationship between diffraction intensity increases with the order degree increases, to determine the order degree of material; establish the relationship among ordering treatment process, order degree and materials (battery) performance.

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