Ceramic material and method for preparing the same

Abstract

A ceramic material including Co.sub.0.5Ti.sub.0.5TaO.sub.4. The ceramic material is prepared as follows: 1) weighting and mixing raw powders of Co.sub.2O.sub.3, TiO.sub.2 and Ta.sub.2O.sub.5 proportioned according to the chemical formula of Co.sub.0.5Ti.sub.0.5TaO.sub.4, to yield a mixture; 2) mixing the mixture obtained in 1), zirconia balls, and deionized water according to a mass ratio of 1:4-6:3-6, ball-milling for 6-8 h, drying at 80-120° C., sieving with a 60-200 mesh sieve, calcining in air atmosphere at 800-1100° C. for 3-5 h, to yield powders comprising a main crystalline phase of Co.sub.0.5Ti.sub.0.5TaO.sub.4; and 3) mixing the powders obtained in 2), zirconia balls, and deionized water according to a mass ratio of 1:3-5:2-4, ball-milling for 4-6 h, and drying at 80-100° C.; adding a 2-5 wt. % of polyvinyl alcohol solution to a resulting product, granulating, sintering resulting granules at 1000-1100° C. in air atmosphere for 4-6 h.

Claims

1. A ceramic material, comprising Co.sub.0.5Ti.sub.0.5TaO.sub.4 having a trirutile structure.

2. The ceramic material of claim 1, wherein the ceramic material is prepared through a method comprising: 1) weighting and mixing raw powders of Co.sub.2O.sub.3, TiO.sub.2 and Ta.sub.2O.sub.5 proportioned according to the chemical formula of CO.sub.0.5Ti.sub.0.5TaO.sub.4, to yield a mixture; 2) mixing the mixture obtained in 1), zirconia balls, and deionized water according to a mass ratio of 1: 4-6: 3-6, ball-milling for 6-8 h, drying at 80-120° C., sieving with a 60-200 mesh sieve, calcining in air atmosphere at 800-1100° C. for 3-5 h, to yield powders comprising a main crystalline phase of Co.sub.0.5Ti.sub.0.5TaO.sub.4; and 3) mixing the powders obtained in 2), zirconia balls, and deionized water according to a mass ratio of 1: 3-5: 2-4, ball-milling for 4-6 h, and drying at 80-100° C., adding a 2-5 wt. % of polyvinyl alcohol solution to a resulting product, granulating, sintering resulting granules at 1000-1100° C. in air atmosphere for 4-6 h, to yield the ceramic material.

3. The ceramic material of claim 2, wherein a dielectric constant of the ceramic material is between 36 and 41.

4. The ceramic material of claim 2, wherein a quality factor (Q×f) of the ceramic material is between 13135 and 17291 GHz.

5. The ceramic material of claim 2, wherein a temperature coefficient of resonant frequency of the ceramic material is between 113 and 116 ppm/° C.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

(1) FIG. 1 shows the X-ray diffraction patterns of ceramic materials in Examples 1 to 5 prepared in different sintering temperatures.

(2) FIG. 2 shows the scanning electron microscope images of the surface morphology of ceramic materials in Examples 1, 3, 4 and 5.

DETAILED DESCRIPTION OF THE IMPLEMENTATIONS

(3) To further illustrate, embodiments detailing a ceramic material are described below. It should be noted that the following embodiments are intended to describe and not to limit the disclosure.

(4) 1) Weighting raw powders of Co.sub.2O.sub.3, TiO.sub.2 and Ta.sub.2O.sub.5 proportioned according to the chemical formula of Co.sub.0.5Ti.sub.0.5TaO.sub.4.

(5) 2) Mixing and ball-milling the mixture obtained in 1), zirconia balls, and deionized water according to a mass ratio of 1:5:2. Thereafter, drying the slurry at 100° C. and then sieving the mixture with a 200-mesh sieve. Calcining the obtained mixture in air atmosphere at 1100° C. for 4 h to synthesize main crystalline phase of Co.sub.0.5Ti.sub.0.5TaO.sub.4.

(6) 3) Mixing the powders obtained in 2), zirconia balls, and deionized water according to a mass ratio of 1:5:2, ball-milling for 4 h, and then drying at 100° C. After drying, adding polyvinyl alcohol (2 wt. % PVA) solution into the obtained powder as a binder and putting into a cylinder mold at 20 megapascal for 30 s to form pellets. Thereafter, sintering the cylindrical samples at 1000-1100° C. in air atmosphere for 6 h to prepare Co.sub.0.5Ti.sub.0.5TaO.sub.4 ceramics.

(7) FIG. 1 shows the X-ray diffraction patterns of ceramic materials in Examples 1 to 5 prepared in different sintering temperatures, where the Si powder was used as an internal standard to calibrate the experiment and instrument errors. At different sintering temperatures, the diffraction peaks of samples matched with trirutile phase CoTa.sub.2O.sub.6 phase (JCPDS card No. 32-0314), indicating that trirutile solid solution Co.sub.0.5Ti.sub.0.5TaO.sub.4 was formed at this time. However, the position of actual diffraction peak shifted to higher angle. According to Bragg's law, the right shift of peak position was attributed to the decrease of cell volume. Compared with CoTa.sub.2O.sub.6, the ionic radius of Ti.sup.4+ ions in Co.sub.0.5Ti.sub.0.5TaO.sub.4 phase was smaller than that of Co.sup.2+ and Ta.sup.5+ ions at the same coordination number. Correspondingly, the cell volume decreases, and the diffraction peak shifted to higher angle.

(8) FIG. 2 shows the scanning electron microscope images of the surface morphology of ceramic materials in Examples 1, 3, 4 and 5. Obviously, with the increase of the sintering temperature, the amounts of micropores decreased, the densifications increased, and the grain size increased from 1.42 to 10.86 μm.

(9) TABLE-US-00001 TABLE 1 The raw materials of ceramic materials in Examples 1-5 Examples 1 2 3 4 5 Calcined temperature ° C. 1000 Sintering temperature 1000 1025 1050 1075 1100 Mass/g Co.sub.2O.sub.3 13.715 13.715 13.715 13.715 13.715 TiO.sub.2 13.208 13.208 13.208 13.208 13.208 Ta.sub.2O.sub.5 73.077 73.077 73.077 73.077 73.077

(10) TABLE-US-00002 TABLE 2 The properties of ceramic materials in Examples 1-5 External Dielectric τ.sub.f Exam- diameter Thickness constant Tanδ Q × f (ppm/ ples (mm) (mm) (∈.sub.r) (10.sup.−4) (GHz) ° C.) 1 10.48 5.30 36.51 5.89 13135 116.03 2 10.30 5.10 39.19 4.26 17068 113.06 3 10.20 5.13 39.43 4.62 17201 114.03 4 10.16 4.94 40.69 4.31 17291 114.54 5 10.30 5.04 39.38 4.32 17174 115.33

(11) From the above tables, it can be seen that the sample in Example 1 was not well-sintered because of its high loss, low dielectric and small shrinkage. With the further increase of sintering temperature, it can be seen from Examples 2-4 that the sample shrunk obviously, and the dielectric constant and quality factor were significantly improved. Combining with the scanning electron microscope images, the sample became densification. However, with the sintering temperature further increasing (Example 5), the shrinkages of samples decreased, the dielectric constant and the quality factor decreased as well. The abnormal growth of grain size in the scanning electron microscope image indicated that the sample had been over-burned at this time, and the excessive sintering temperature would be detrimental to the development of the dielectric properties of samples.

(12) It will be obvious to those skilled in the art that changes and modifications may be made, and therefore, the aim in the appended claims is to cover all such changes and modifications.