Journal of Materials Science

, Volume 42, Issue 1, pp 337–345 | Cite as

Sintering temperature depression in Al2O3 by mechanical milling

  • H. J. Goodshaw
  • J. S. Forrester
  • G. J. Suaning
  • E. H. Kisi


High-energy milling of Al2O3 with hardened steel milling media has confirmed that nanocrystalline powders are readily formed. At a ball to charge mass-ratio of 20:1, the crystallite size falls below 30 nm in just 2 h and below 15 nm in 4 h. The as-milled powders are contaminated with Fe which increases linearly with increased milling time, reaching ∼10 wt% after 16 h. The HCl leaching process of Karagedov and Lyakhov [Karagedov and Lyakhov (1999) Nanostruct Mater 11(5):559] was found to remove a large proportion of the Fe, but residual Fe was found with XRF analysis. Milled and leached samples show significant sintering temperature depression to approximately 1100 °C and produce sintered densities greater than 94% without the application of pressure. Milling induced lattice expansion of the Al2O3 is observed which we posit to be due to defect formation rather than Fe absorption. The respective roles of small crystallite size and lattice defects in reducing the sintering temperature are discussed.


Al2O3 Milling Milling Time Rietveld Refinement Mechanical Milling 
These keywords were added by machine and not by the authors. This process is experimental and the keywords may be updated as the learning algorithm improves.



The authors thank the Australian Research Council for financial support. We also thank Mr. David Phelan for assistance with the electron microscopy, and Mr. Peter Garfoot for his assistance with sample preparation.


  1. 1.
    Karagedov GR, Lyakhov NZ (1999) Nanostruct Mater 11(5):559CrossRefGoogle Scholar
  2. 2.
    Cutler IV, Bradshaw C, Christensen CJ, Hyatt EP (1957) J Am Ceram Soc 40:134CrossRefGoogle Scholar
  3. 3.
    Johnson WC, Coble RL (1978) J Am Ceram Soc 61:110CrossRefGoogle Scholar
  4. 4.
    Inada S, Kimura T, Yamaguchi T (1990) Ceram Int 16:369CrossRefGoogle Scholar
  5. 5.
    Sathiyakumar M, Gnanam FD (2002) Ceram Int 28:195CrossRefGoogle Scholar
  6. 6.
    Erkalfa H, Misirli Z, Baykara T (1995) Ceram Int 21:345CrossRefGoogle Scholar
  7. 7.
    Boccaccini AR, Kaya C (2002) Ceram Int 28:893CrossRefGoogle Scholar
  8. 8.
    Shiau F-S, Fang T-T (1999) Mater Chem Phys 60:91CrossRefGoogle Scholar
  9. 9.
    Pathak LC, Singh TB, Das S, Verma AK, Ramachandrarao P (2002) Mater Lett 57:380CrossRefGoogle Scholar
  10. 10.
    Ananthapadmanabhan PV, Thiyagarajan TK, Sreekumar KP, Venkatramani N (2004) Scripta Mater 50:143CrossRefGoogle Scholar
  11. 11.
    Park JH, Lee MK, Rhee CK, Kim WW (2004) Mater Sci Eng A 375–377:1263Google Scholar
  12. 12.
    Goldsby JC (2001) Ceram Int 27:701CrossRefGoogle Scholar
  13. 13.
    Karagedov GR, Lyakhov NZ (2003) KONA 21:76Google Scholar
  14. 14.
    Howard CJ, Hunter BA (1997) A computer program for Rietveld analysis of X-ray, neutron diffraction patterns. ANSTO Lucas Heights Research LaboratoriesGoogle Scholar
  15. 15.
    Klug HP, Alexander LE (1974) X-ray diffraction procedures for polycrystalline and amorphous materials, 2nd edn. J. Wiley and Sons, New York, p 662Google Scholar
  16. 16.
    Hill RJ, Howard CJ (1987) J Appl Cryst 20:467CrossRefGoogle Scholar
  17. 17.
    Alkebro J, Begin-Colin S, Mocellin A, Warren R (2000) J Europ Ceram Soc 20:2169CrossRefGoogle Scholar

Copyright information

© Springer Science+Business Media, LLC 2006

Authors and Affiliations

  • H. J. Goodshaw
    • 1
  • J. S. Forrester
    • 1
  • G. J. Suaning
    • 1
  • E. H. Kisi
    • 1
  1. 1.School of EngineeringUniversity of NewcastleCallaghanAustralia

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