田中 武雄

Mechanical alloying (MA) has been performed for a mixture of elemental iron and graphite powders by the conventional type ball-mill. Solid state reaction of Fe₃C formation has been studied for Fe₈₃C₁₇, Fe₇₅C₂₅ and Fe₇₁C₂₉ powders by transmission electron microscopy, X-ray diffractometry, ⁵⁷Fe Mössbauer spectroscopy and differential scanning calorimetry. The amorphous phase coexistent with α-Fe has been formed after 200 hour MA. After subsequent milling, these phases have been transformed into Fe₃C carbide through Fe₇C₃-like carbide. While, the successive reaction from Fe₅C₂ to Fe₃C has been also confirmed in the process of heating the amorhous phase coexistent with α-Fe.

Mechanical alloying (MA) and mechanical grinding (MG) have been performed for Fe₈₆C₁₄ powders by a conventional ball-mill. MA has been carried out on a mixture of elemental iron and graphite powders and MG on a pre-alloyed iron-cementite powder. Ball-milled powders have been examined by scanning electron microscopy, transmission electron microscopy, X-ray diffractometry, ⁵⁷Fe Mössbauer spectroscopy and differential scanning calorimetry. Super-saturated solid solution of α-iron has been formed by a cold-welding of the pulverized iron particles on the MA process. By subsequent milling and/or heating, carbide has been formed from the solid solution. While, ultra-fine structure with capital size of few nano-meter has been formed for MG powder of the white cast iron. Amorphous phase has been formed by both MA and MG.

Mechanical alloying (MA) and mechanical grinding (MG) have been performed for Fe₈₆C₁₄ powders by a conventional ball-mill. MA has been carried out on a mixture of elemental iron and graphite powders and MG on a pre-alloyed iron-cementite powder. Ball-milled powders have been examined by scanning electron microscopy, transmission electron microscopy, X-ray diffractometry, ⁵⁷Fe Mössbauer spectroscopy and differential scanning calorimetry. Super-saturated solid solution of α-iron has been formed by a cold-welding of the pulverized iron particles on the MA process. By subsequent milling and/or heating, carbide has been formed from the solid solution. While, ultra-fine structure with capital size of few nano-meter has been formed for MG powder of the white cast iron. Amorphous phase has been formed by both MA and MG.

Mechanical alloying (MA) has been performed for a mixture of elemental iron and graphite powders by the conventional type ball-mill. Solid state reaction of Fe₃C formation has been studied for Fe₈₃C₁₇, Fe₇₅C₂₅ and Fe₇₁C₂₉ powders by transmission electron microscopy, X-ray diffractometry, ⁵⁷Fe Mössbauer spectroscopy and differential scanning calorimetry. The amorphous phase coexistent with α-Fe has been formed after 200 hour MA. After subsequent milling, these phases have been transformed into Fe₃C carbide through Fe₇C₃-like carbide. While, the successive reaction from Fe₅C₂ to Fe₃C has been also confirmed in the process of heating the amorhous phase coexistent with α-Fe.

Mechanical alloying (MA) and mechanical grinding (MG) have been performed for Fe₈₆C₁₄ powders by a conventional ball-mill. MA has been carried out on a mixture of elemental iron and graphite powders and MG on a pre-alloyed iron-cementite powder. Ball-milled powders have been examined by scanning electron microscopy, transmission electron microscopy, X-ray diffractometry, ⁵⁷Fe Mössbauer spectroscopy and differential scanning calorimetry. Super-saturated solid solution of α-iron has been formed by a cold-welding of the pulverized iron particles on the MA process. By subsequent milling and/or heating, carbide has been formed from the solid solution. While, ultra-fine structure with capital size of few nano-meter has been formed for MG powder of the white cast iron. Amorphous phase has been formed by both MA and MG.