巻号一覧
後続誌
57 巻, 7 号
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技術報告
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大西 脩嗣, 相沢 達志, 森本 庄吾, 岡田 千里1985 年 57 巻 7 号 p. 406-411
発行日: 1985/07/25
公開日: 2015/01/27
ジャーナル フリーA low pressure die casting machine has been developed to improve fluidity of the melt and to ensure sound aluminum alloy castings free from such casting defects as oxide inclusions and pinholes. A ladle and chamber enclosing a mold are automatically sealed, evacuated and filled with inert gas prior to castings, where evacuation is helpful for melt degassing. The rise of the melt into the mold is effected by gas pressure and controlled by a microcomputer at an optimum speed. Such parts as high speed turbo impellers with intricate shapes and light sections requiring high quality are successfully cast by the use of this machine.抄録全体を表示PDF形式でダウンロード (2943K)
研究論文
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李 鏞河, 川野 豊, 山本 悟, 豊島 康史1985 年 57 巻 7 号 p. 412-418
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーS- and Mg-treated malleable cast iron containing P, Cu, Ti, Al and Cr was tested. P lowers the melting point locally and forms a liquid phase both in S- and Mg-treated cast irons and prevents graphite spheroidization. Cu, Ti and Al in S-treated cast iron form sulphides and prevent graphite spheroidization. Cu in Mg-treated cast iron forms solid solution with Mg and prevents spheroidization. Cr in S-treated iron and Al and Cr in Mg-treated one have no effect on graphite spheroidization. The reason for inhibitation of graphite spheroidization is : Spherical pores formed by S- and Mg-treatments are indispensable for graphite spheroidization. These elements form liquid phases or consume S or Mg by forming compounds or solid solution and suppress pore formation by S- and Mg-treating, and prevent graphite spheroidization. Spheroidal graphite is not formed, if graphitization is promoted and graphite forms prior to pore formation in S-treated cast iron during annealing.抄録全体を表示PDF形式でダウンロード (888K) -
パリタッド ・パンチュバンヨン, 伊藤 政律, 梅田 高照, 木村 康夫, 栗林 一彦, 岸 輝雄1985 年 57 巻 7 号 p. 419-425
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーElastic-plastic fracture toughness was investigated by using electric potential (EP) and acoustic emission (AE) methods for cast irons with various types of graphite morphology including flake, CV and spheroidal and with various amounts of pearlite in matrix structure. Jin(AE) and Jin(EP) evaluated from the deflection points of AE event count and electric potential curves, and Jin(R) from cross point of blunting line and R curve in J-Δa(EP) plot are related by Jin(R)=1.34 Jin(AE)=1.34Jin(EP). And Jin(R) can be defined as JIC in cast irons used. JIC is expressed in regression equation with relation to nodularity n[%] and pearlite content in matrix P[%] as follows. JIC=16.614+0.500·n[%]−0.060·P[%]−0.004·n[%]·P[%]抄録全体を表示PDF形式でダウンロード (736K) -
近藤 靖彦, 西尾 敏幸, 安江 和夫, 柴田 周治1985 年 57 巻 7 号 p. 426-431
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーWear resistance and mechanical properties of eutectic graphite iron containing such additives as Al, Cu, Ni, P, Sn, B, Cr, Mo, W, V and Nb which accelerate pearlitization of the matrix were investigated. As-cast irons free from additives have a pearlite area about 67%. Iron containing Cu more than 0.96% has the pearlite area 98% in the matrix and tensile strength 48 kg/mm2 higher by 12 kg/mm2 than that of additive free iron. Tensile strength and hardness are controllable by addition of a required quantity of Cu. Iron containing Sn more than 0.1% has the pearlite area 98% or more, increased hardness and improved wear resistance. Mo and V in the iron enlarge the pearlite area more than 90%, harden the iron 30 in HRC or more and improve the wear resistance. Mo causes precipitation of acicular crystals. Cr, W and Nb enlarge the pearlite area more than 90% and permit HRC 25 to 30. Cr more than 0.5%, V more than 0.3% and V more than 0.02% cause a mottle structure. P and Al increase the pearlite area, but coarsen the graphite structure and lower the tensile strength. Ni improves tensile strength by refining the eutectic graphite, but reduces the pearlite area. The eutectic graphite iron containing Si and V cast into a metal mold has improved resistance to wear, but is inferior to the sand cast grey iron FC25.抄録全体を表示PDF形式でダウンロード (553K) -
陳 玉勇, 李 慶春1985 年 57 巻 7 号 p. 432-437
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーEffects of additional amount of a salt refiner, remelting and holding time on the grain structure of aluminum alloys were studied. The microstructure of aluminum alloys is considerably refined by the use of the salt grain refiner. An addition of the refiner 0.2 to 0.3% to Al-2%Cu alloy produces a finely dispersed equiaxial grain structure. An increase in quantity of the refiner from 0.05 to 0.4% causes remarkable refinement of grain size. The ultimate tensile strength, elongation and fracture toughness also increase. There would be a Ti and B enriched region around the salt as a result of the reaction of the salt to aluminum, forming a lot of TiAl3 and TiB2 particles which play nuclei of α-Al in the melt.抄録全体を表示PDF形式でダウンロード (780K) -
高柳 猛, 津田 昌利1985 年 57 巻 7 号 p. 438-443
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーMolten Ni-base super alloy (Alloy 454) was held in two kinds of Al2O3 type crucibles in vacuum 1.2 to 2×10−4 Torr for 0.5 to 3h at 1,540°C. A crucible containing 99.6%Al2O3 is stable to the molten alloy. When the alloy is melted in a crucible containing 95.3%Al2O3, Al in the molten alloy reacts to SiO2 in the glass phase of the crucible. Al2O3 is consequently detected as a product in the reacted layer of the melted ingot, and Si in the molten alloy slightly condenses. Such elements as Ni and Cr in the alloy probably constitute a reacted layer along with Al2O3. Cr in the melted ingot gradually decreases as the holding time is prolonged.抄録全体を表示PDF形式でダウンロード (741K) -
中沢 哲夫, 森本 庄吾, 酒井 淳次, 谷川 隆俊, 八重樫 盛1985 年 57 巻 7 号 p. 444-449
発行日: 1985/07/25
公開日: 2011/11/17
ジャーナル フリーThe mixture of silica sand, polyvinyl alcohol aqueous solution as a binder and Ca(OH)2 as a curing agent was kneaded and rapidly hardened by blowing CO2 gas. The mold in which PVA (polymerization degree ; 500, saponification degree ; 88mol%) is used shows superior properties to those with other types of PVA. An increase of Ca(OH)2 up to 2.5wt% in the silica sand mixture immediately strengthens the mold just CO2 gas blown, but lowers the mold dried at 100°C for 2h probably due to inadequate dispersion of Ca(OH)2 into PVA aqueous solution. The dispersion property of Ca(OH)2 should be improved. The mold prepared in this process is superior to the sodium-silicate CO2 process mold in low hygroscopicity and prefered collapsibility.抄録全体を表示PDF形式でダウンロード (699K)
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