Khanh Quoc Dang and Makoto Nanko
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AZojomo (ISSN 1833-122X) Volume 6 November 2010
Topics CoveredAbstract Keywords IntroductionExperimental ProcedureResults And DiscussionConclusionsReferences Contact Details
Al2O3 doped with a small amount of chromium is called ruby and is widely used in various applications. Al2O3-Cr2O3 powder mixture was prepared by drying Al2O3 aqueous slurry with Cr(NO3)3 and consolidated by pulsed electric current sintering (PECS) processing into Cr-doped Al2O3 polycrystals. The PECS process was performed in vacuum at sintering temperature of 1200°C with the heating rate ranging from 2 to 100 K/min under different applied uniaxial pressures of 40, 80 and 100 MPa. PECS with slow heating rate and high pressure leads to highly densified bodies and transparent Cr-doped Al2O3 polycrystals.
Cr-doped Al2O3, Ruby, Pulsed Electric Current Sintering (PECS), Density, Transparent, Microstructure
Pure corundum (Al2O3) is a rare mineral, perfectly colourless and transparent. Small amounts of metallic elements such as chromium, iron, titanium or vanadium can substitute for aluminium in the corundum crystal structure, giving rise to many colour variations. Ruby, this magnificent red variety from the multi-coloured corundum family, consists of aluminium oxide and chromium as well as very fine traces of other elements. The advantages of ruby are high heat-resistance, high melting point, high mechanical strength, high hardness and excellent chemical stability. Ruby is widely used for hydraulics, chemicals, airflow filters, solid-state lasers, solar energy, decorative products, optical components like prisms and wedges, etc. [1, 2].
Pulsed electric current sintering (referred to as PECS), also known as spark plasma sintering (SPS) or plasma activated sintering (PAS), is the latest pressure-sintering process to consolidate advanced materials such as ceramics, metallic materials and their composites. The sintering process consists of placing raw powder inside an electrically-conductive die, closing the unit with two punches pressed uniaxially, and applying a pulsed electric current momentarily through an electrically-conductive die, in some cases, through the sample to heat up the specimen [3-24]. PECS for producing transparent ceramics has also been reported [17-25]. Some reports described the successful sintering of transparent alumina polycrystals by PECS [17-22]. In particular, Kim et al. demonstrated that, for PECS processing of Al2O3, a slow heating rate is efficient for densification and transparency [17-19].
However, there are no reports on sintering of coloured Al2O3 with any doping by the PECS process. In the present study, Al2O3-Cr2O3 powder mixture was prepared by drying Al2O3 powder slurry with Cr(NO3)3. The powder mixture was reacted and sintered into transparent Cr-doped Al2O3 polycrystals by the PECS process with various conditions, particularly, different heating rates and applied pressures.
A commercial á-Al2O3 powder (99.99% purity, TM-DAR, Taimei Chemicals Co. Ltd., Japan) was mixed with Cr(NO3)3 (Nacalai Tesque Inc., Japan) as a source material of Cr2O3 in distilled water. The aqueous slurry was dried by dropping it into a glassware pot heated at 350°C. The mass of Cr2O3 concentration in the final samples was equalled to be 70 ppm. The Al2O3-Cr2O3 powder mixture was ground by a conventional dry milling process using an alumina mortar for 30 min. The sintering experiments were conducted by using Dr. Sinter Model SPS-1050 (Sumitomo Coal Mining Co.) with 12/2 in ON/OFF pulse pattern, which is recommended by the PECS supplier. The Al2O3-Cr2O3 powder mixture was put into the graphite die (ϕ30 in outer diameter, ϕ15.4 in inner diameter and 30 mm in height) with a ϕ1.8 x 3 mm hole for temperature measurement by a pyrometer. Sintering temperature was controlled by a preset heating program and it was measured by an optical pyrometer focused on the surface hole of the die during heating. The PECS process was conducted at sintering temperature of 1200°C for 20 min under various uniaxial pressures between 40 and 100 MPa in vacuum. Heating rate of 2 and 100 K/min was selected.
Bulk density of the sintered bodies was determined by the liquid-replacement technique with toluene. Phase identification of Al2O3-Cr2O3 powder mixture was conducted by using X-ray diffraction (XRD). The distribution of Cr, Al, and O was observed by the energy dispersive X-ray spectroscopy (EDX). Microstructure of as-sintered samples was observed by scanning electron microscopy (SEM) with EDX for element mapping. The average grain size was determined by using the linear intercept method with the compensation coefficient of 1.126 .
Results And Discussion
Figure 1 shows XRD pattern of the Al2O3-Cr2O3 powder mixture. Samples with the single corundum phase were obtained. No contamination or other chemical reaction has occurred. Figure 2 shows the microstructure of the Al2O3-Cr2O3 powder mixture after grinding with an alumina mortar. Strong agglomeration of the Al2O3 particles was observed.
Figure 1. XRD pattern of Al2O3-Cr2O3 powder mixture.
Figure 2. Microstructure of the Al2O3-Cr2O3 powder mixture after milling process.
Figure 3 shows EDX elemental maps of Al2O3-Cr2O3 powder mixture after the milling process. The element maps showed that the Cr and Al exist homogeneously throughout the powder mixture.
Figure 3. SEM and EDX images of Al2O3-Cr2O3 powder mixture after milling process.
The relationship between the relative density of sintered body and an applied uniaxial pressure is shown in Figure 4. The relative density is increased with increasing applied uniaxial pressure. The relative density of ruby polycrystals sintered by PECS with slow heating rate was higher than that in the rapid heating rate under same applied uniaxial pressure. All the samples sintered under 100 MPa attained nearly the theoretical density (>99%). With an applied uniaxial pressure of 80 MPa and higher, fully densified samples were obtained already at the slowest heating rate. An applied uniaxial pressure and the heating rate play important roles in the densification during the PECS process of Al2O3-Cr2O3 powder mixture.
Figure 4. Relationship between relative density, D, and an applied uniaxial pressure, P, in the PECS of Al2O3-Cr2O3 powder mixture.
Figure 5 represents SEM images of fractured surface of ruby polycrystals sintered by the PECS process under various conditions. With an applied uniaxial pressure of 40 MPa, the average grain size of all sintered samples exhibits smaller grain size and number of pores exists in samples. Increasing an applied uniaxial pressure to 100 MPa, the ruby polycrystals with a heating rate of 2 K/min was fully densified. Less pores at the grain boundary junction and the fine grains formed after sintering under higher pressure in slower heating rate. The relationship between average grain size and an applied uniaxial pressure with various heating rates is shown in Figure 6. The results show that an applied uniaxial pressure had little effect on average grain size but the heating rate significantly affected on average grain size. The grain size of ruby polycrystals with slower heating rate was smaller than ones formed by rapid heating rate. It appears that the heating rate plays a greater role in grain growth than an applied uniaxial pressure.
Figure 5. SEM images of the fractured surface of ruby polycrystals sintered at 1200°C: a) and b) the heating rate of 2 K/min and an applied uniaxial pressure were 40 and 100 MPa; c) and d) the heating rate of 100 K/min and an applied uniaxial pressures were 40, and 100 MPa, respectively. Arrows in a), c) and d) are represent the pores.
Figure 6. Relationship between average grain size, D, and an applied uniaxial pressure, P, in PECS of Al2O3-Cr2O3 powder mixture. The error bars show maximum and minimum values.
For the effect of the heating rate on the grain size, there have been conflicting results. Some researchers reported that the grain size of alumina decreased with increasing the heating rate [9, 10, 28]. Those reports mentioned a small grain size at rapid heating for the alumina, which was opposite to the results of the present study and other reports [18, 29]. Their mechanism is explained by using the conventional empirical equation of grain growth. The cause of their conflicting results has not been clarified. However, their respective PECS experiments were conducted under different sintering conditions with different Al2O3 powders. The different sintering conditions may provide a clue for understanding the conflicting results. To explain the reason for larger grain size at higher heating rate, Murayama and Shin mentioned the possibility that a high defect concentration was produced by rapid heating and associated rapid plastic deformation during densification . The defect produced by both heating and plastic deformation may therefore accelerate the grain growth during PECS processing. The initial defect concentration in the powder particles, which is different in different powder, should be also affected to sintering behaviour.
In order to achieve complete densification and fine grain size in pressure-sintering of alumina, Krell et al. emphasized the importance of homogeneous particle dispersion in the raw powder before sintering [30, 31]. They improved the final density and transparency by homogenizing the powder using such techniques as stirring, ultrasonification and milling. On the other hand, Kim et al. [17-19] considered that in addition to the low defect concentration, an effect similar to the precoarsening may act on the powder during slow heating rate at low temperature and the as-received Al2O3 powder was homogenized itself during PECS. Furthermore, some researchers reported that the Al2O3 powder with small amount doping element such as MgO or triple dopant combination of the 3 dopants: Mg, Y and La gave the fine grain size and the best transparency of samples [20, 21, 32]. Due to very limited solubility of elements in Al2O3, the grain size can be affected by segregation of dopants or impurities at grain boundary. As well as densification during the PECS process, the quality of the starting powder from powder preparation played a key role for grain growth during PECS processing.
As mentioned above, higher applied uniaxial pressure and slow heating rate resulted in complete densification and small grain size. The transparency of ruby polycrystals could be affected by both relative density and grain size. Transparency is inversely proportional to the grain size and the density [20, 27]. The difference in transparency of the ruby polycrystals sintered under high applied uniaxial pressure with various heating rates is shown in Figure 7. The ruby polycrystals with more porosity has lower apparent transparency than the dense ones. In addition to the effects of porosity, the grain size also influences transparency. Therefore, the ruby polycrystals changed gradually, the appearance from opaque to transparent with increasing applied uniaxial pressure and simultaneously decreasing heating rate. The transparency of ruby polycrystals is easily observed by the naked eyes.
Figure 7. Images of ruby polycrystals sintered by PECS at 1200°C under an applied uniaxial pressure of 100 MPa: a), b) the heating rates were 2 and 100 K/min, respectively. The thickness of these samples was approximately 2.5 mm.
However, some dots appeared inside the ruby polycrystals, as seen in Figure 7. These dots have high Cr concentration as shown by the EDX results. Figure 8 shows the SEM image and EDX elemental of fractured surface of sintered ruby polycrystals. Porous area, which is probably a black dot, shows high Cr concentration. Preparation of the homogeneous Al2O3-Cr2O3 powder mixture would be important for obtaining sintered ruby polycrystals with higher transparency without black dots. Powerful milling process such as high-speed milling may be effective in improving the homogeneity of the powder mixture.
Figure 8. SEM and EDX images of fractured surface of ruby polycrystals sintered at 1200°C with heating rate of 100 K/min under applied uniaxial pressure of 100 MPa.
Highly densified ruby polycrystals were successfully obtained with the PECS processing of Al2O3-Cr2O3 powder mixture prepared by drying aqueous Al2O3 slurry containing Cr(NO3)3. In present study, the PECS process with slow heating rate resulted in complete densification and small grain size. An applied uniaxial pressure had a little influence on microstructure, but had a significant effect on densification. The sintered ruby polycrystals with slow heating rate, e.g. 2 K/min, and high applied uniaxial pressure, e.g. 100 MPa, shows excellent transparency which is easily visible by the naked eyes. However, some dots appeared inside of ruby polycrystals. These dots are probably caused by heterogeneity in the Al2O3-Cr2O3 powder mixture.
References 1. A. Krell, T. Hutzler and J. Klimke, “Transmission physics and consequences for materials selection, manufacturing, and applications”, J. Euro. Ceram. Soc., 29 (2009) 207-221.
2. C. R. Beesley, “Guides for color grading faceted gemstones”, US Patent No. 4,534,644 (13 August 1985).
3. M. Tokita, “Trends in advanced SPS spark plasma sintering systems and technology”, J. Soc. Powder Technol. Jpn., 30 (1993) 790-804.
4. M. Nanko, T. Maruyama and H. Tomino, “Neck growth on initial stage of pulse current pressure sintering for coarse atomized powder made of cast-iron”, J. Jpn. Inst. Metals, 63 (1999) 917-923.
5. M. Nanko, T. Oyaidu and T. Maruyama, “Densification of Ni-20Cr alloy course-powder by pulse current pressure sintering”, J. Jpn. Inst. Metals, 66 (2002) 87-93.
6. T. Kondo, T. Kuramoto, Y. Kodera, M. Ohyanagi and Z. A. Munir, “Enhanced growth of Mo2C formed in Mo-C diffusion couple by pulse DC current”, J. Jpn. Soc. Powder Powder Metall., 55 (2008) 643-650.
7. M. Sato, M. Nanko, K. Matsumaru and K. Ishizaki, “Homogeneity in sintering of fine Ni-20Cr powder by pulsed electric current sintering (PECS) process”, Adv. Tech. Mat. and Mat. Proc. J., 8 (2006) 101-108.
8. G. D. Zhan, J. Kuntz, J. Wan, J. Garay and A. K. Mukherjee, “Alumina-based nanocomposites consolidated by spark plasma sintering”, Scripta Mater., 47 (2002) 737-741.
9. Z. Shen, M. Johnsson, Z. Zhao and M. Nygren, “Spark plasma sintering of alumina”, J. Am. Ceram. Soc., 85 (2002) 1921-1927.
10. Y. Zhou, K. Hirao, Y. Yamauchi and S. Kanzaki, “Densification and grain growth in pulse electric sintering of alumina”, J. Euro. Ceram. Soc., 24 (2004) 3465-3470.
11. S. W. Wang, L. D. Chen and T. Hirai, “Densification of Al2O3 powder using spark plasma sintering”, J. Mater. Res., 15 (2000) 982-987.
12. D. Jiang, D. M. Hulbert, J. D. Kuntz, U. Anselmi-Tamburini and A. K. Mukherjee, “Spark plasma sintering: A high strain rate low temperature forming tool for ceramics”, Mater. Sci. Eng. A, 463 (2007) 89-93.
13. F. Guillard, A. Allemand, J. Lulewicz and J. Galy, “Densification of SiC by SPS-effects of time, temperature and pressure”, J. Euro. Ceram. Soc., 27 (2007) 2725-2728.
14. M. Suganuma and Y. Kitagawa, “Pulsed electric current sintering of silicon nitride”, J. Am. Ceram. Soc., 86 (2003) 387-394.
15. S. W. Wang, L. D. Chen, T. Hirai and J. Guo, “Formation of Al2O3 grains with different sizes and morphologies during the pulse electric current sintering process”, J. Mater. Res., 16 (2001) 3514-3517.
16. D. M. Zhang, Z. Y. Fu, Y. C. Wang, Q. J. Zhang and J. K. Guo, “Heterogeneous of non-conductive materials sintering by pulse electric current”, Key Eng. Mater., 224-226 (2002) 729-734.
17. B. N. Kim, K. Hiraga, K. Morita and H. Yoshida, “Spark plasma sintering of transparent alumina”, Scripta Mater., 57 (2007) 607-610.
18. B. N. Kim, K. Hiraga, K. Morita and H. Yoshida, “Effects of heating rate on microstructure and transparency of spark plasma sintered alumina”, J. Euro. Ceram. Soc., 29 (2009) 323-327.
19. B. N. Kim, K. Hiraga, K. Morita, H. Yoshida, T. Miyazaki and Y. Kagawa, “Microstructure and optical properties of transparent alumina”, Acta Mater., 57 (2009) 1319-1326.
20. D. Jiang, D. M. Hulbert, U. Anselmi-Tamburini, T. Ng, D. Land and A. K. Mukherjee, “Optically transparent polycrystalline Al2O3 produced by spark plasma sintering”, J. Am. Ceram. Soc., 91 (2008) 151-154.
21. M. Stuer, Z. Zhao, U. Aschauer and P. Bowen, “Transparent polycrystalline alumina using spark plasma sintering: Effect of Mg, Y and La doping”, J. Euro. Ceram. Soc., 30 (2010) 1335-1343.
22. R. S. Dobedoe, G. D. West and M. H. Lewis, “Spark plasma sintering of ceramics”, Bull. Euro. Ceram. Soc., 1 (2003) 19-24.
23. R. Chaim, M. Kalina and J. Z. Shen, “Transparent yttrium garnet (YAG) ceramics by spark plasma sintering”, J. Euro. Ceram. Soc., 27 (2007) 3331-3337.
24. R. Chaim, M. Kalina and J. Z. Shen, “Transparent YAG ceramics by surface softening of nanoparticles in spark plasma sintering”, Mater. Sci. Eng. A, 429 (2006) 74-78.
25. K. Morita, B. N. Kim, K. Hiraga and H. Yoshida, “Fabrication of transparent MgAl2O4 spinel polycrystal by spark plasma sintering”, Scripta Mater., 58 (2008) 1114-1117.
26. M. I. Mendelson, “Average grain size in polycrystalline ceramics”, J. Am. Ceram. Soc., 52 (1969) 443-446.
27. R. Apetz and M. P. B. Bruggen, “Transparent alumina: a light-scattering model”, J. Am. Ceram. Soc., 86 (2003) 480-486.
28. L. A. Stanciu, V. Y. Kodash and J. R. Groza, “Effects of heating rate on densification and grain growth during field-assisted sintering of á-Al2O3 and MoSi2 powders”, Metall. Mater. Trans. A, 32 (2001) 2633-2638.
29. N. Murayama and W. Shin, “Effect of rapid heating on densification and grain growth in hot pressed alumina”, J. Ceram. Soc. Jpn, 108 (2000) 799-802.
30. A. Krell, P. Blank, H. Ma and T. Hutzler, “Transparent sintered corundum with high hardness and strength”, J. Am. Ceram. Soc., 86 (2003) 12-18.
31. A. Krell, P. Blank, H. Ma, T. Hutzler and M. Nebelung, “Processing of high-density submicrometer Al2O3 for new applications”, J. Am. Ceram. Soc., 86 (2003) 546-553.
32. D. S. Kim, J. H. Lee, R. J. Sung, S. W. Kim, H. S. Kim and J. S. Park, “Improvement of translucency in Al2O3 ceramics by two-step sintering technique”, J. Euro. Ceram. Soc., 27 (2007) 3629-3632.
Khanh Quoc Dang and Makoto Nanko
Department of Mechanical Engineering, Nagaoka University of Technology,
Nagaoka, Niigata 940-2188, Japan
E-mail : email@example.com
This paper was also published in print form in "Advances in Technology of Materials and Materials Processing", 12 (2010) 19-24.