巻号一覧
32 巻, 11 号
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中村 衛, 浅村 均, 山中 久彦1968 年 32 巻 11 号 p. 1043-1046
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーIn this report, to find out the reasons why the worked, quenched and subsequently tempered steel has a higher strength than that of the conventionally heat treated one, 0.47%C steel was chosen as the specimen, after tempering at 200°∼600°C for 1 hr, the specimen was investigated by an optical microscope and a transmission electron microscope. The results may be summarized as follows: (1) The sorbite structure of the worked, quenched and subsequently tempered steel was found to be extremely fine and uniform as compared with the conventionally quenched one. (2) On tempering of the worked and quenched martensite at 600°C for 1 hr, the cell structure and fine subgrains were observed and these forms were quite isotropic rather than a prolonged parallel shape of the conventional martensite. Its dislocation density was estimated to be the order of 1011/cm2. Those configurations built up by the unique shape and size of cells and the high dislocation density are considered to contribute to the strengthening of this steel.抄録全体を表示PDF形式でダウンロード (1380K) -
中村 衛, 浅村 均, 山中 久彦1968 年 32 巻 11 号 p. 1047-1052
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーIn this experiment, pure iron was used to explain the cause of strengthening by hot worked quenching. The structures of hot worked and quenched iron were mainly observed by means of optical and transmission electron microscope, and these structures were compared with that of unworked and quenched iron. The obtained results were as follows: (1) Pure iron was worked at 1000°∼1200°C and immediately quenched, into water. It was found that the hardness of the pure iron was Hv 10 higher than that of the unworked and quenched specimens. (2) The worked and quenched iron was reheated at the temperature of 200°∼800°C, then its increment of hardness was decreased as the temperature rose, and the hardness difference between worked and unworked diminished and was consistent at 600°C. (3) It was observed by optical microscope that the new fine subgrain as network existed in the larger grain of worked and quenched iron. (4) From the results of the transmission electron microscopic observation, the density of dislocations in worked and quenched was about 2.2×109/cm2, and its value was twice the unworked and quenched.抄録全体を表示PDF形式でダウンロード (2683K) -
中村 衛, 浅村 均, 山中 久彦1968 年 32 巻 11 号 p. 1052-1056
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーA 0.7% carbon steel was used to investigate the strengthening ratio and the mode of strengthening in the worked and quenched steel, as compared with the conventionally heat treated steel. The 0.7% carbon steel was worked over the temperature range 800°∼1200°C and immediately quenched into water. Then, the hardness of the workeda nd quenched steel and the variation of hardness after subsequent tempering treatment were measured by the Rockwell hardness tester. And the effect of hot working prior to quenching upon the thermal dilatation of the worked and quenched steel was investigated by means of a differential dilatometer. The results obtained are summarized as follows:
(1) Hardness of the worked specimens of austenite at 900°∼1200°C increased gradually as the working ratio increased.
(2) By tempering the worked and quenched steel for 1 hr at the temperature range 100°∼700°C, its hardness began to decrease at the tempering temperature of 110°C. However, the hardness of the worked and quenched steel after tempering was higher than that of the unworked and quenched steel.
(3) The amount of contraction in the dilatation curves at 180°C decreased gradually as the working ratio increased in the worked and quenched steel.
(4) It was observed that the contraction ratio in the dilatation curves of the worked and quenched steel was smaller than that of the unworked and quenched steel after isothermal heating at 122°, 150° and 200°C respectively.抄録全体を表示PDF形式でダウンロード (1756K) -
飛田 守孝, 幸田 成康1968 年 32 巻 11 号 p. 1057-1061
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーResistivity measurements were carried out on Cu-Ge (0.86, 2.41, 4.41, 7.02, 8.68 at%) solid solution alloys, especially containing 4.41, 7.02, 8.68, at%Ge. The results were compared with those for Cu-Al (10.37 at%) and Cu-Ni (20.77 at%) solid solution alloys.
Concentration dependence of the resistivity in Cu-Ge alloys has an anomality between 4.41 and 7.02 at%Ge. The change of internal microstructures in the Cu-Ge alloys is recognized from the temperature dependence curves that the first fold points on the curve are at 800°C in 7.02 at%Ge and 8.68 at%Ge, and at 650°C in 4.41 at%Ge solid solution alloy.
Isochronal annealing curves of quenched Cu-Ge, Cu-Al, Cu-Ni alloys show that 7.02 at% and 8.68 at%Ge alloys are similar to the Cu-10.37 at%Al alloy in resistivity change and that Cu-4.41 at%Ge alloy is similar to the Cu-20.77 at%Ni alloy. It is considered that some short range order is formed in 7.02 and 8.68 at%Ge alloys.
Decreasing of the resistivity is caused by quenching Cu-8.68 at%Ge alloy from 100°∼170°C. It seems that at these temperatures the short range order zones which are formed during slow cooling grow to some extent whereby effective electron scattering centers are formed.抄録全体を表示PDF形式でダウンロード (2278K) -
川原 浩司1968 年 32 巻 11 号 p. 1062-1067
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーHardness measurement, dilatation measurement, transmission-electron microscopy, and electron diffraction observation are used to study the mechanism of age hardening in the alloy. Some phenomena difficult to explain in terms of precipitation processes are observed, examples of which are as follows: (1) The structural observations and the diffraction patterns obtained from the martensitic solid solution before aging showed the presence of clusters consisting of Ni3Ti-like phase. (2) The increment of hardness was very rapid; e.g. age hardening occurred quickly at about 550°C in the course of heating even with the highest rate of heating in this experiment. (3) The peak hardness on 600°C-and 700°C-aging was almost independent of the heating rates. (4) The overagings in the martensitic phase indicated deep shrinkages without increasing austenite. (5) The behaviors of softening and of transformation in heating at 700°C showed abnormal phenomena.
Although age hardening of this alloy has been interpreted in terms of precipitation, i.e. of diffusion processes, but in view of the above results it is suggested that there is a mechanism of non diffusional processes, that is, the presence of the clusters and the change in coherency of the clusters/matrix relationship may govern the behaviors of hardening and softening in the alloy.抄録全体を表示PDF形式でダウンロード (2684K) -
大矢根 守哉, 関口 秀夫1968 年 32 巻 11 号 p. 1068-1073
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーCompressive tests have been performed on specimens of a steel containing 1.0%C and 1.4%Cr, heat treated so as to have lamellar perlite or spheroidized pearlite. The effects of strain rate on flow stress and compressive formabilities have been studied at various temperatures. The behavior of carbides in a plastically deformed ferrite matrix has been investigated by means of an electron microscope in order to elucidate the strength conferred by dispersion hardening.
In spheroidized pearlite, the significant work hardening rate observed at small strain cannot be explained by Fisher’s theory of work hardening, which accounts for the extra flow stress at a given strain in terms of the back stress due to dislocations around carbides. It is suggested that the increment of work hardening is due to the increase of dislocation density affected by the size and volume fraction of carbide particles.抄録全体を表示PDF形式でダウンロード (2871K) -
久保田 広行, 小指 軍夫, 清水 輝彦1968 年 32 巻 11 号 p. 1074-1078
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーA low alloy steel of 0.2%C was quenched directly after rolling at low temperature (a treatment similar to ausforming). The resulting martensite gave rise to a distinct texture which was presumed to originate from the preferred orientation of unrecrystallized austenite. This texture in turn resulted in an anisotropy of plastic flow in the tesile test. In the Charpy impact test, the ductile-brittle transition temperature showed a marked decrease. This improvement was attributed to the relaxation of plastic constraint due to delamination along elongated prior austenitic grain boundaries.抄録全体を表示PDF形式でダウンロード (1750K) -
木下 智見, 友清 芳二, 松田 日出彦, 江口 鉄男1968 年 32 巻 11 号 p. 1078-1084
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe anomalous specific heat of quenched α Cu-Al alloys with 15.5 at%Al has been investigated together with anomalies in electrical resistivity and micro vickers hardness. The former anomalies take place in three stages, namely, the first two (stage I and II) are heat evolution occurring below and above 150°C, and the other (stage III) is heat absorption in the temperature range between 240° and 300°C.
In the present work an attempt is made to elucidate the experimental results obtained from the measurements of the specific heat, electrical resistivity and micro Vickers hardness.
The experimental results are interpreted as follows:
(1) The anomaly in stage I is due to the formation of the short range order in the process of disappearance of quenched-in vacancies, and to the aggregation of solute atoms around defects.
(2) The anomaly in stage II is due to the further development of the short range order associated with dispersion of solute atoms trapped by defects in stage I.
(3) The anomaly in stage III is due to the destruction of the short range order formed in stages I and II and also in the quenching process.
Furthermore we have observed a slight of heat in the temperature range above 300°C, but could not obtain any definite information about it.抄録全体を表示PDF形式でダウンロード (2349K) -
岡本 昌文, 長谷川 正義1968 年 32 巻 11 号 p. 1085-1090
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーIn order to find the properties of carbon-free iron-nitrogen alloys (0.035∼0.11 wt%N), investigations have been made on the microstructures, hardness, structural changes in quenching, tempering properties and mechanical properties. The specimens pressure-melted in nitrogen atmosphere are Fe-N binary alloys, ternary alloys containing 1 at%Mn, Mo and V, and multi-component alloys consisting of Cr-Mo, Cr-Mn, Mo-Mn, Ni-Cr, etc. The results are summarized as follows: (1) The hardness of normalized Fe-N binary and ternary alloys shows a linear increase with the nitrogen content. (2) Fe-N alloys (0.07∼0.1%N) shows an increase in hardness with the quenching temperature and reaches a nearly constant hardness in the range of Hv 300∼350 above 1000°C (30 min), except for alloys containing V. (3) The structures of quenched Fe-N alloys (0.07∼0.1%N) are massive martensite, though their shapes are a little different depending on the alloying elements added. (4) After tempering, the quenched Fe-N alloys containing Mo and Cr exhibit high resistance to softening, accompanied by the secondary hardening at 400°∼500°C. (5) The strength and ductility of Fe-N binary alloys are lower, but those of multi-component alloys containing Cr, Mn or Mo are high; e.g. Fe-0.0745N-1.2Cr-1.6Mn alloy exhibits a tensile strength of 55.2 kg/mm2 and an elongation of 22.6%.抄録全体を表示PDF形式でダウンロード (2477K) -
太田 陸奥雄, 橋本 文雄, 谷本 雅1968 年 32 巻 11 号 p. 1091-1097
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーAl-rich Al-Zn-Mg-Si and Al-Zn-Mg-Ge quaternary alloys were studied by the measurement of electrical resistivity. The results may be summarized as follows: (1) The isothermal aging curves of electrical resistivity in the Al-Zn-Mg-Si and Al-Zn-Mg-Ge quaternary alloys seemed to be composed of two stages when electrical resistivity was plotted against logarithm of aging time. (2) When Mg:Si=2:1, the maximum increase of resistivity, ΔρM, in the Al-Zn-Mg-Si and Al-Zn-Mg-Ge quaternary alloys was nearly equal to that in Al-Zn binary alloy, with the same amount of Zn with quaternary alloys under the same aging condition. But when Mg:Si>2:1, ΔρM, in the quaternary alloys was larger than that in the binary alloy. (3) The times, tMs, required to reach the maximum in electrical resistivity in the Al-Zn-Mg-Si and Al-Zn-Mg-Ge quaternary alloys were much longer than that in the Al-Zn binary alloy or Al-Zn-Mg ternary alloy. (4) It might be concluded that the increase of electrical resistivity was mainly dependent upon the spherical G.P.zones which were similar to those in Al-Zn binary alloy (Zn-G.P.zones), when Mg:Si=2:1. The clusters containing Mg and Si in the ratio of 2:1 ((Mg2Si) clusters) might be formed during the aging. However, it seems that these clusters do not contribute to the increase of electrical resistivity. (5) The shape of isothermal aging curves and the very large value of tMs in the quaternary alloys may be explained, if it is assumed that (Mg2Si) clusters may absorb more vacancies when clusters are formed and consequently the rate of growth of Zn-G.P.zones is decreased. (6) It seems that (Mg2Si) clusters can absorb much more vacancies than those absorbed by isolated atoms of Mg and Si in solid solution.抄録全体を表示PDF形式でダウンロード (2610K) -
太田 陸奥雄, 橋本 文雄, 前田 裕宣1968 年 32 巻 11 号 p. 1097-1103
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーAl-Zn alloys containing 0.84∼4.4 at%Zn were studied by the measurement of electrical resistivity and small angle scattering of X-ray. The results may be summarized as follows: (1) After isothermal aging below a certain temperature, the electrical resistivity of each alloy increases initially, reaches a maximum value and then decreases corresponding to the formation and growth of G.P.zones. But when isothermally aged above a certain temperature, the electrical resistivity shows a slight increase in a short time (about 30 sec) and then decreases very slowly for a long time, with no distinct maximum in the isothermal aging curves. In this case, it seems that G.P.zones are not formed and the small increase of electrical resistivity is related to some behaviour of supersaturated zinc. Therefore, these certain temperatures seems to be the maximum temperature at which G.P.zones can be formed in Al-Zn alloys. (2) The quantity of zinc consumed for the formation and growth of G.P.zones may be proportional to the difference between the total atomic concentration of zinc and the atomic concentration which can be estimated from the solvus for G.P.zones at the aging temperature. (3) Reversion was incomplete when aged for a long time. (5) Plots of time, tM, required to reach the maximum resistivity against the reciprocal of absolute temperature are approximated by a straight line at lower temperatures. But tMs are fairly longer than that expected from the extension of a straight line at higher temperatures. The plots cannot be approximated by a straight line in a wide temperature range. These phenomena might be explained as follows: The quantity of zinc consumed for the formation and growth of G.P.zones decreases rapidly as the aging temperature rises.抄録全体を表示PDF形式でダウンロード (1890K) -
太田 陸奥雄, 橋本 文雄, 谷本 雅, 前田 裕宣1968 年 32 巻 11 号 p. 1103-1109
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーAl-Zn-Ag ternary alloys and several other alloys were studied by the measurement of electrical resistivity and small angle scattering of X-ray. The results may be summarized as follows: (1) The highest temperature at which G.P.zones can be formed in alloys containing a small amount of silver is higher than that in the Al-Zn binary alloy containing the same amount of zinc. Namely, G.P.zones become stable at the initial stage when a small amount of silver is added. (2) This effect become remarkable when the concentration of silver increases. (3) When zinc concentration is the same, the radius of G.P.zones formed in the Al-Zn-Ag ternary alloy at room temperature is larger than that in the Al-Zn binary alloy. (4) Stability of G.P.zones is nearly constant, even when a small amount of copper or germanium is added to the Al-Zn binary alloy. (5) It seems that G.P.zones in the Al-Zn-Ag alloys consist of both Zn and Ag atoms.抄録全体を表示PDF形式でダウンロード (1877K) -
財満 鎮雄, 広野 雅道1968 年 32 巻 11 号 p. 1109-1115
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーUp to this time, it has been reported that the silumin (AC3A) has good castability and poor machinability. So, in order to improve the machinability of silumin, the turning test was carried out by adding a few elements. The results showed that the silumin is a material with a fairly large cutting resistance, and tool wear and is not easy to obtain good cutting surface. The machinability was examined by adding calcium and natrium effective for improvement of aluminium-silicon system eutectic alloys and phosphorus effective for refinement of the primary silicon in hyper eutectic alloys. By the addition of natrium, the machinability was improved considerably; for example, the cutting resistance decreased, the surface roughness and the tool wear was improved. On the other hand, by the addition of calcium, the cutting resistance increased slightly, but there was no favorable effect on the surface or the tool wear. And, by the addition of phosphorus, the tool wear increased, but there was no improvement in the cutting resistance, surface roughness and other properties.抄録全体を表示PDF形式でダウンロード (2947K) -
増本 剛, 磯村 滋宏1968 年 32 巻 11 号 p. 1116-1120
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe semiconducting solid solutions of the Cd3As2-Cd3P2 system were prepared directly from high purity elements in a quartz tube filled with Argon gas by the aid of an internal heating high-pressure resistance furnace. The physical, electrical and thermal properties of these specimens were measured.
The Cd3As2-Cd3P2 system consists of a continuous series of solid solution and shows n-type conductivities over the whole composition range. At room temperature, the electrical properties of this system show the following orders of magnitude; the resistivity: 10−2∼10−4 Ω-cm, the carrier concentration: 1017∼1018 cm−3, the carrier mobility: 900∼9000 cm2/V-sec. The total thermal conductivities show values as low as 0.014∼0.35 W/cm-deg at room temperature. The thermoelectric figure of merit for the Cd3As2-Cd3P2 system is rather large, especially the value for 30 mol%Cd3As2-70 mol%Cd3P2 solid solution attaining 1.1×10−3 deg−1 at room temperature.抄録全体を表示PDF形式でダウンロード (1808K) -
増本 剛, 田村 良雄1968 年 32 巻 11 号 p. 1121-1127
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーAn electron bombardment floating zone melting apparatus for the refractory metals, which was first built-up on trial in Japan (1960), is described. The operation and the performance are further described for the floating zone melting of W, Mo, Ta, Nb, Pt, Pd and Fe rods. The results obtained are as follows:
(1) By using emission control, by which the bombardment current is kept constant by automatically adjusting the filament temperature and bombardment voltage in “Temperature Limited characteristics”, the floating zone melting of sintered specimens incurring a great deal of outgassing during melting was performed successfully.
(2) The purifying effect of floating zone melting was confirmed by residual resistance ratio measurements and, from the ratio values, it was made clear that the zone melted rods have been purified by vacuum distillation and zone refining. Namely, in the cases of 5 mmφ W and Mo rods three zone passed at zoning rate 3 mm/min in 1×10−5 torr, the ratio values have been decreased to 1/400 for W rod and to 1/150 for Mo rod respectively against the values of starting materials.
(3) By only one zoning, 5 mmφ W, Mo, Ta, Nb, Pt and Pd rods were found to be single crystals at 1∼4 mm/min without seed crystals.
Moreover, 4 mmφ Nb single crystal was produced by using ⟨100⟩ seed crystal. Therefore, this apparatus could be used as a single crystal growing apparatus for refractory metals.抄録全体を表示PDF形式でダウンロード (2882K) -
三宅 一男, 冨士原 由雄, 西垣 賢一1968 年 32 巻 11 号 p. 1128-1131
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe influence of cobalt content on the fatigue strength and fatigue phenomena in tungsten carbide-cobalt alloys were investigated. The test was done at 8000 rpm by using a rotating beam fatigue machine.
The results obtained are as follows:
(1) The S-N curves in WC-Co alloys do not show flat portions which are observed in the case of iron and steel materials. Taking N=108 rpm for the fatigue limit, the fatigue strength increases with cobalt contents. There is a linear relation between fatigue strength and tensile strength.
(2) Enlarged pictures of the fatigue fracture surface indicate that the crack runs emissively, with the stress concentration source as the central figure. Electromicrographs of the crack source neighborhood exihibit a kind of fusional structure. This fusional part may be due to the excessive stress concentration.
(3) According to the results of X-ray diffraction, the binder phase transforms from γ Co (fcc) to ε Co (hcp) by fatigue and it’s ε content increases with fatigue degree.
(4) The coercive force increases with increasing fatigue and stress.抄録全体を表示PDF形式でダウンロード (1822K) -
幸塚 善作, 鈴木 康治, 大石 敏雄, 森山 徐一郎1968 年 32 巻 11 号 p. 1132-1137
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe e.m.f. measurements were carried out at the temperature range of 1100°∼1250°C by means of the following galvanic cells employing solid electrolytes, Ni, NiO/ZrO_2(+CaO)/O(in Cu).
From these experimental resalts, it was found that:
(1) The oxygen contents in molten copper could be estimated from the e.m.f. of cell. In particular, at the low oxygen content the above electrochemical method was highly sensitive for the determination of oxygen contents.
(2) Henry’s law was obeyed from the low oxygen content of 100 ppm to such a high content that Cu2O precipitated, and the activity coefficient of oxygen was 0.120 at 1100°C, 0.150 at 1150°C and 0.195 at 1200°C.
(3) The present results were in good agreement with the data based on the equilibrium experiments using a mixing gas of CO and CO2.抄録全体を表示PDF形式でダウンロード (1957K) -
一ノ瀬 幸雄, 山下 武夫, 谷口 哲, 菱山 定夫, 小林 勝1968 年 32 巻 11 号 p. 1137-1142
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe effects of processing conditions were investigated on the magnetic and switching properties of a fine Mo-permalloy ribbon and a twistor which were manufactured by the following processes.
(This article is not displayable. Please see full text pdf.)
Magnetic and switching properties of the ribbon and the twistor are remarkably influenced by these processing conditions, especially by the degree of cold reduction (R2) and the aging (A1) in the fine wire before cold rolling to the ribbon. The higher degree of cold reduction in the process R2 and the lower aging temperature in the process A1 result in the better magnetic and switching properties of the ribbon and the twistor. The reason is that the processing conditions in the above two processes strongly influence the roll-anisotropy and dispersion relating to the magnetic and switching properties of the ribbon and the twistor. Further, as to the twistor, it is found that the aging in the ribbon (A2) before winding and the stabilizing in the twistor (A3) after winding are both of very importance to the magnetic and switching properties. That is why the process A2 is necessary to reduce the stress sensitivity relating to the magnetostriction and the process A3 to eliminate the internal stress induced by winding.抄録全体を表示PDF形式でダウンロード (1258K) -
向井 楠宏, 坂尾 弘, 佐野 幸吉1968 年 32 巻 11 号 p. 1143-1149
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe deoxidation reaction zone at an early stage of the deoxidation process of liquid iron and at its reoxidation was investigated, and the following results were obtained. At the dissolving stage of the deoxidizer, a non-metallic phase rich in FeO would be able to nucleate homogeneously for a low supersaturation of the Fe-Mn-Si-Al-O system. This shows that the deoxidation reaction begins in the vicinity of the top of diffusion of deoxidizing elements. At the growth stage of the inclusion, activities of the deoxidizing elements at the surface of the inclusion will depend on the supply velocity of each element to the surface of the inclusion. So in the above-mentioned reaction zone, the composition of the inclusion, which can be determined by the activities will be greatly influenced by the diffusion of each element. The experimental data obtained by other investigators appear to support our predictions.
An experimental apparatus satisfying the conditions of the above-mentioned reaction zone was described. From the experimental results it has been concluded that the FeO-rich inclusions produced in the reaction zone change their compositions and sizes by the various types of reactions with liquid iron containing Si and Mn during floating up in the liquid iron.抄録全体を表示PDF形式でダウンロード (2535K) -
向井 楠宏, 坂尾 弘, 佐野 幸吉1968 年 32 巻 11 号 p. 1149-1154
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe size and the composition of inclusions produced in the liquid iron containing Si and Mn were examined by the same method as described in the previous report. The results obtained are as follows:
(1) The compositions of inclusions in each iron specimen lie on a line bending to the MnO corner on the FeO-MnO-SiO2 diagram. (2) This line can be regarded as a locus of variation of composition of the inclusion by dissolution of FeO and MnO of the inclusion into the liquid iron and direct or “indirect” substitutional reaction between the inclusion and the liquid iron. (3) The composition at the end of this line is equal to the one equilibrated with the liquid iron. (4) From the above results, the desirable concentration area of liquid iron for the Si and Mn preliminary complex-deoxidation was estimated in terms of the ability of coalescence of inclusions.抄録全体を表示PDF形式でダウンロード (1368K) -
向井 楠宏, 坂尾 弘, 佐野 幸吉1968 年 32 巻 11 号 p. 1155-1160
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe size and the composition of inclusions produced in the liquid iron containing Si, Mn, and Al were examined by the same method as described in the previous report. The results obtained are as follows:
(1) The compositions of inclusions in each iron specimen lie on a line bending to the SiO2 corner on the (FeO+MnO)-SiO2-Al2O3 diagram. The extent of this bending decreases with increasing Al content in liquid iron.
(2) This line can be regarded as a locus of variation of composition of the inclusion by dissolution of FeO and MnO in the inclusion into the liquid iron and direct or indirect substitutional reaction between the inclusion and the liquid iron in the same manner as mentioned in the previous report.
(3) From the above results and the optimum composition area of the inclusion in the MnO-SiO2-Al2O3 system obtained previously, the optimum concentration area of liquid iron was estimated for Si, Mn, and Al complex-deoxidation and for reoxidation of liquid iron. The experimental results of Si, Mn, and Al complex-deoxidation obtained by other investigators confirmed the existence of the optimum concentration area.抄録全体を表示PDF形式でダウンロード (2559K) -
椙山 正孝, 福迫 達一, 佐藤 彰1968 年 32 巻 11 号 p. 1161-1166
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーRegarding the process of direct-rolling of molten metals for manufacturing finished products directly from molten metals as the developed one of continious casting, we made a study of producing half-made products with the process of direct-rolling of molten metals. An experimental work of the direct-rolling of molten metals by our laboratory machine No.2 was carried out with Al-Si alloys which have a low plasticity and solidify in a manner of the eutectic type. Producing-conditions and properties of direct-rolled plates were examined. The main results obtained were as follows:
(1) The upper limit of the direct-rollable speed of molten Al-Si alloys related to the pouring temperature were much lower than that of pure Al and became slower as the silicon content increases.
(2) In the case of hypoeutectic and hypereutectic alloys, at a lower direct-rolling speed silicon atoms normally segregated very strongly in the middle of the thickness of plates. On the other hand, in the case of hypoeutectic and eutectic alloys, silicon atoms segregated inversely at a higher direct-rolling speed in the vicinity of the surface of direct-rolled plates.
(3) We recognized swell, transversal wrinkles and round dimples as defects of the surface of direct-rolled molten Al-Si alloys. These defects decreased as the direct-rolling speed became slower.
(4) Mechanical properties of direct-rolled molten Al-Si alloys were higher than those of the plates solidified in a water-cooled book mold.抄録全体を表示PDF形式でダウンロード (2956K) -
沢谷 精, 室田 昭治1968 年 32 巻 11 号 p. 1167-1171
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーThe atomic number effect in quantitative electron microprobe analysis is discussed. The computer method of Archard and Mulvey is modified using (1) the Webster’s law in order to calculate the energy loss suffered by the electron passing through the solid target, (2) Green and Cosslett’s expression for the relation between electron energy and ionization cross section and (3) Cosslett’s expression for the difusion range. A comparision between calculated results and experimentally determined values has been made for Au-Cu alloy, and after the good agreement between them is confirmed, the correction factors of the atomic number effect are calculated for several iron-base binary alloys. Quantitative electron probe microanalysis has been performed on Fe-Al, Fe-Si, Fe-Mo and Fe-W alloys and compared with the computed values.抄録全体を表示PDF形式でダウンロード (1582K) -
鈴木 隆志, 長谷川 博一, 渡辺 三雄1968 年 32 巻 11 号 p. 1171-1177
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーWe studied low carbon Fe-Cr-Ni alloys in order to develop the steel which has two phases, austenite and ferrite, and the resistance to stress corrosion cracking in the chloride environment.
The martensitic hardening occurs when the (Cr+Ni) content is less than 24% and the (Cr-Ni) content is more than 18%. And the characteristic intergranular corrosion of the ferritic steel can be arrested when the austenite phase is precipitated more than 10%.
The quantities of the two phases, austenite and ferrite, are equal when the (Cr-1.5Ni) content is about 14∼15%, and in this case it has the maximum resistance to stress corrosion cracking. We consider that the advance of ferrite precipitation is to arrest the propagation of cracks and to strengthen its matrix.
It is concluded that the optimum composition of these steels is about 22%Cr and 5%Ni.抄録全体を表示PDF形式でダウンロード (1707K) -
渡辺 亨, 佐藤 有一, 依田 連平1968 年 32 巻 11 号 p. 1177-1183
発行日: 1968年
公開日: 2008/04/04
ジャーナル フリーIn order to obtain the fundamental data on heat resistivity of nickel-base and chromium-base alloys, the recrystallization of nickel-chromium binary alloy has been investigated. The main experimental results obtained are as follows:
(1) Chromium-base alloys containing 10∼40% nickel can hardly be fabricated by hot and cold working.
(2) The hardening of nickel rich alloys up to the amealing temperature for the softening by recrystallization becomes remarkable with increasing chromium content.
(3) The temperature for 60% recrystallization of specimens having the γ single phase increases with increasing chromium content from 390°C in pure nickel to 675°C in 30% chromium-nickel alloy.
(4) The recrystallization temperature of the alloy with precipitation of the α phase from γ single phase decreases by the reaction of discontinuous precipitation, while that of the alloy with precipitation of the γ phase from the α single phase increases by the reaction of general precipitation.
(5) The temperature curve of 60% recrystallization in nickel-chromium binary alloy was made out.
(6) The recrystallization temperature of specimens solution treated, annealed, and then cold rolled becomes slightly lower than that of specimens without the annealing.抄録全体を表示PDF形式でダウンロード (2796K)
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