Method of making textured ceramics

Abstract

The invention proposed a novel hot pressing flowing sintering method to fabricate textured ceramics. The perfectly 2-dimensional textured Si3N4 ceramics (Lotgering orientation factor fL 0.9975) were fabricated by this method. During the initial sintering stage, the specimen flowed along the plane which is perpendicular to the hot pressing direction under pressure, through the controlling of the graphite die movement. The rod-like -Si3N4 nuclei was easily to texture during the flowing process, due to the small size of the -Si3N4 nuclei and the high porosity of the flowing specimen. After aligned, the -Si3N4 grains grew along the materials flowing direction with little constraint. textured Si3N4 ceramics fabricated by this invention also showed high aspect ratio. Compared to the conventional hot-forging technique which contained the sintering and forging processes, hot pressing flowing sintering proposed is simpler and lower cost to fabricate textured Si3N4.

Claims

1. A method of making textured ceramics, comprising steps of: mixing ingredients, mixing and drying of the ingredients containing silicon nitride powder and sintering aids; b, forming a green part, the powder after drying being dry-pressed through steel die and then cold isostatic pressing to obtain a shaped body; c, making textured ceramic, using flowing hot pressing sintering method to make the green part obtained in above step b to flows in a one-dimensional or two-dimensional directions in order to achieve high-performance ceramics with preferred grain arrangement and anisotropy growth; wherein the hot press applied pressure is 10-50 MPa, and temperature is in the range of 1000-2000 C.

2. The method of making textured ceramics according to claim 1, wherein the sintering aid is selected from the group consisting of alkali metal oxides or rare earth metal oxides.

3. The method of making textured ceramics according to claim 1, wherein the processing steps comprises mixing the ingredients and drying the slurry; in a process of mixing the ingredients, the ceramic powders and the sintering aids are added to the solvent to form a slurry, and then the silicon nitride grinding balls are added, the weight ratio of silicon nitride grinding balls versus the ceramic powders is (1-5): 1, and followed by ultrasonic dispersion; wherein weight ratio of the sintering aid versus the a-phase silicon nitride powder is (0.5-35): 100.

4. The method of making textured ceramics according to claim 3, wherein the solvent is any one of water, ethanol, acetone, propanol, or more, the volume ratio of the mixed powders versus the solvent is 1: (1-3).

5. The method of making textured ceramics according to claim 3, the mixed slurry is poured into a rotary evaporator for drying, the drying temperature is 40-60 C.; after drying, the powder is sieved.

6. The method of making textured ceramics according to claim 5, wherein the dried powder is sieved through 30-200 mesh.

7. The method of making textured ceramics according to claim 5, wherein, a process of the step b to form a green part, comprises: the green part is dry-formed in the steel die, and then the green part is cold isostatic pressed for increased green density.

8. The method of making textured ceramics according to claim 7, wherein the cold isostatic pressure is 50-300 MPa.

9. The method of making textured ceramics according to claim 1, wherein the texturing process is performed in a graphite mold, and using flowing inert gas atmosphere for protection.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0018] FIG. 1 is a schematic illustration of temperature-time-pressure process for: (a) Hot-forging, (b) HPFS, (c) HP;

[0019] FIG. 2 is a XRD patterns of sintered samples by HPSF ((a) plane normal to the hot pressing direction, (b) plane parallel to the hot pressing direction) and HP (c);

[0020] FIGS. 3A and 3B are microstructures of specimens by HPSF ((a) plane normal to the hot pressing direction, (b) plane parallel to the hot pressing direction) and HP (c);

[0021] FIGS. 4A and 4B are schematic illustrations of texturing mechanisms of -Si3N4 ceramics by HPFS;

[0022] As shown in the Drawings: 1, a graphite mold; 2, the top punch; 3, lower punch; 4, ceramic blank; 5, the applied pressure; 6, the textured ceramics.

DETAILED DESCRIPTION OF THE INVENTION

[0023] The raw materials used in this study were 90wt % -Si3N4 powder (Ube Industries Ltd., Tokyo, Japan), 4 wt % La2O3, 4 wt % Yb2O3 (Beijing Fandecheng Corp., Beijing, China), and 2 wt % MgO (Hangzhou Wanjing Corp., Hangzhou, China). The powder mixtures were ball milled for 24 h in ethanol using Si3N4 balls. After drying, the powder was gently grounded and sieved 100 mesh. The powder mixtures were placed into a graphite die with specific tolerance between graphite punch and die (Shenyang Weitai Corp., Shenyang, China). The Si3N4 was fabricated by a new method (HPFS). Schematic illustration of temperature-time-pressure process for HPFS is shown in FIG. 1 (b). A low pressure of 5 MPa was applied ( ) on the sample before the start of sintering. The frictional force between the sample and graphite die was enough to keep the graphite die from falling down. When the sintering temperature reached 1500 C., the loading pressure was released and the graphite die would fall down. Then the pressure was increased to 30 MPa gradually before 1700 C. Finally, the sample was sintered at 1800 C. for 1 h under a pressure of 30 MPa in N2 atmosphere. In comparison with the HPFS, the mixed powder was also hot pressed (HP) at 1800 C. for 1 h under a pressure of 30 MPa in N2 atmosphere. Schematic illustration of temperature-time-pressure process for HP is shown in FIG. 1 (c), and the graphite die was stationary.

[0024] The crystallographic orientation (Lotgering orientation factor) in the sintered bodies was evaluated by X-ray diffraction (Bruker D8, Germany) on the surfaces parallel and perpendicular to the hot pressing direction, respectively. The polished surface of the sintered ceramics were plasma etched by CF4 containing 10% O2 (Structure Probe Corp, Pennsylvania, America). The textured microstructure of the etched surfaces were characterized by a scanning electron microscope (SEM, FEI Corp., Eindhoven, Dutch).

[0025] FIG. 2 shows the XRD patterns of sintered Si3N4 by HPFS and HP. Obviously, the diffraction peaks are different on the different planes of sintered samples by HPFS. On the planes perpendicular to the hot pressing direction, the diffraction peaks of the (hk0) planes were substantially stronger, especially the (200) and (210) planes, while the (101) and (002) planes disappeared, as shown in FIG. 2 (a). On the plane parallel to the hot pressing direction, the diffraction peaks of the (hk0) planes become relatively weak, whereas the diffraction peaks of the (101) plane appears with high intensity, and the (002) plane is the strongest, as shown in FIG. 2 (b). XRD pattern of the sample prepared by HP is shown in FIG. 2 (c). All the (hk1) peaks could be found, and the (101) plane is the strongest. According to the relative peak intensity of the two samples, it could be concluded that the Si3N4 prepared by HPFS was textured. The degree of orientation plane of textured Si3N4 can be intuitively evaluated from the relative peak intensity of the (101) plane in the XRD pattern of the top plane (perpendicular to the hot pressing direction).11 For the XRD pattern of samples prepared by HPFS, the disappearance of the (101) plane (perpendicular to the hot pressing direction) indicates the formation of a perfect 2-dimension texture.

[0026] The Lotgering orientation factor was used to evaluate the degree of texture in ceramics prepared by HPFS. The Lotgering orientation factor fL, according to the Lotgering reported, 12 can be expressed as,

[00001]$f_L=\frac{P-P_0}{1-P_0},P.Math..Math.\mathrm{and}.Math..Math.P_0=\frac{.Math..Math.l_{\left(\mathrm{hk}.Math..Math.0\right)}}{.Math..Math.l_{\left(\mathrm{hkl}\right)}}$

[0027] where (hk0) are the sums of peak intensities of the (hk0) planes perpendicular to the hot pressing direction, and (hk1) are the sums of peak intensities of all the (hk1) planes perpendicular to the hot pressing direction. The value of P was obtained from the sintered ceramic, and the value of P0 was obtained from the standard PDF card (No. 33-1160) of -Si3N4. As a result, the value of fL is 0.9975, which further confirmed that Si3N4 by HPFS had the perfect 2-dimensional texture.

[0028] Table I shows the textured Si3N4 by different texturing techniques. The texturing degree was evaluated by the following methods, such as fL, pole figure and I(101)/I(210). However, these methods have no comparability. It was well known that high texturing microstructure could be obtained in the strong magnetic field. In this work, the fL by HPFS was higher than that by strong magnetic field, which indicated that higher texturing degree can be obtained using HPFS method. Due to the appearance of the (101) peak on the XRD pattern,17 lower texturing degree was observed during the sintering-forging process compared to HPFS.

[0029] The top plane (plane normal to the hot pressing direction) and side plane (plane parallel to the hot pressing direction) microstructures of Si3N4 sintered by HPFS are shown in FIG. 3 (a) and (b), respectively. The elongated grains have planar orientation, but randomly distribute along the top plane. Thus, the microstructure is anisotropic with two-dimensional alignment, which is identified by XRD. FIG. 3 (c) shows the top plane (plane normal to the hot pressing direction) microstructure of the HP specimen. Obviously, all the grains were random and without texturing. In addition, HPFS specimen have higher aspect ratio than HP specimen.

[0030] The schematic illustration of texturing mechanisms of Si3N4 ceramics by HPFS is shown in FIG. 4. During the initial sintering stage, the equiaxed -Si3N4 particles changed into the rod-like -Si3N4 nuclei. After the graphite die falling down, the specimen flowed along the plane perpendicular to the hot pressing direction under pressure. The -Si3N4 nuclei was easily to texture under pressure, due to the small size nuclei and high porosity of the flowing specimen. After aligned, the -Si3N4 grains grew along the materials flowing direction with little constraint, which called dynamic grain growth. In the HP specimen, with the restriction of the graphite die, the -Si3N4 grains grew with high steric hindrance, due to grains impingement and coalesce into each other, which called static grain growth. Wu and Chen reported the dynamic grain growth was faster than static growth, 18 which may be the reason for the higher aspect ratio. Therefore, the HPFS not only can lead to texture of -Si3N4 ceramics, but also increase the aspect ratio of the elongated grains.

[0031] The texturing mechanism was different between HPFS and hot-forging. The sintering and texturing were finished by one step in HPFS. The texturing process was based on the flowing of the green compact, not superplasticity of Si3N4. With the wetting by the liquid phase, the green compact was flowing under the pressure. The phase transformation and texturing were happened almost in the same process. Due to the low steric hindrance in the initial sintering stage, it was easily to obtain high texturing degree. However, the hot-forging was based on the superplastic deformation of the Si3N4. It was hard to get the high texturing, due to the high steric hindrance after sintering. The HPFS was a more efficiency and easier method to fabricate high texturing Si3N4 than hot-forging.

TABLE-US-00001 TABLE I Examples of texturing techniques of Si.sub.3N.sub.4 Orientation Texture method type Degree of texture HPFS a,b-axis f.sub.L = 0.9975 aligned f.sub.L = 0.3* Hot a,b-axis pressing.sup.13 aligned Tape c-axis Pole figure: Max mrd = 15 casting.sup.14 aligned Strong c-axis f.sub.L = 0.97 magnetic field.sup.15 aligned Hot-forging.sup.16 a,b-axis Pole figure: Max mrd = 4.3 aligned Sintering-forging.sup.17 a,b-axis I(101)/I(210) = 0.05 aligned *Calculation based on the XRD results.