巻号一覧
37 巻, 11 号
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岩井 正雄1973 年 37 巻 11 号 p. 1147-1152
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe interaction of sulfide particles of the zinc sulfide-lead sulfide system suspended in dilute sulfulic acid solutions was studied in order to obtain foundamental data on acid leaching processes. The experiments were carried out under the following conditions: temperature: 25∼70°C, pH value: 0.5∼2, amounts of sulfide: 5×10−1∼2×10−1 M/L, air pressure: 1∼2 L/min and agitation speed: 600 rpm. The experimental results were summarized as follows:
(1) The main dissolution reaction of ZnS in the solutions was the type of H2S formation and showed a parabolic behavior. The reaction was diffusion control.
(2) The main acid dissolution reaction of PbS in the solutions was the type of H2S formation. The reaction rate followed a linear law and the activation energy was 9.1 kcal·mol−1.
(3) The dissolution of ZnS and PbS in the ZnS-PbS system suspended in the solutions was observed in the following two types:
(i) The dissolution of ZnS proceeds during the measurement and the acid dissolution of coexisting PbS is repressed remarkably.
(ii) In the early stages of the reaction, the dissolution of ZnS proceeds and the acid dissolution of the coexisting PbS is repressed. After the lapse of a certain time, however, the dissolution of ZnS is repressed and the acid dissolution of the coexisting PbS starts.
(4) The repression of dissolution of ZnS in the ZnS-PbS system suspended in the solution can be explained by the effect of the S0 films produced at the ZnS surface.抄録全体を表示PDF形式でダウンロード (485K) -
貞廣 孟史1973 年 37 巻 11 号 p. 1153-1157
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーIndentation hardness of cemented carbides has been studied on the basis of Tabor’s theory. The surfaces of the specimens with 5∼25 wt% cobalt were finished by diamond paste-lapping after grinding with 150 mesh and 1500 mesh resin-bonded diamond wheels. Then, indentations were made by Rockwell cone, the Vickers cone and the ball indenter.
The results obtained are as follows:
(1) Tabor’s theory can be applied to indentation hardness of cemented carbides, and it is shown that the alloys have the general features of plastic materials.
(2) In the Rockwell hardness, it is necessary to improve the shape of the indenter and to choose a suitable load in order to minimize the crack formation around the indentation and the effect of curvature indentation.
(3) Vickers hardness is dependent on the applied load. With decreasing applied load, the hardness values shifts up and the fractuation of values increases. Thus, it is required to set a suitable load.
(4) If suitable ball diamond cone is used, the stress-strain characteristics of cemented carbides can be obtained from Meyer’s exponential relation by ball indentations.抄録全体を表示PDF形式でダウンロード (345K) -
須藤 一, 加賀 寿1973 年 37 巻 11 号 p. 1158-1165
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーIn order to investigate the fatigue properties of metastable austenitic steels, flat- and notch-fatigue tests of several kinds of high-nickel steels were carried out, and the following results were obtained:
(1) The effect of instability of austenite on the fatigue strength was not distinct, but the fatigue strength of metastable austenitic steels was a little higher than that of stable austenitic steels.
(2) With increasing the amount of martensite, the flat- and notch-tensile strength increased remarkably, but their fatigue strength was similar to that of a simple austenitic steel.
(3) By cold working, the flat- and notch-tensile strength and the flat-fatigue strength were increased remarkably, but the notch-fatigue strength was slightly decreased.
(4) The effects of cyclic transformation on the tensile and fatigue properties were smaller than those of heavy cold rolling.
(5) By replacing nickel with manganese, the tensile strength was increased, but the change in fatigue strength was small.
(6) As a most important reason for the results (1), it is considered that the transformation induced plasticity does not take place under a lower stress than a limiting value.
(7) As a most important reason for the results (2), it is considered that the fatigue cracks easily initiate and propergate along interfaces between austenite and martensite.抄録全体を表示PDF形式でダウンロード (987K) -
須藤 一, 松井 幸博1973 年 37 巻 11 号 p. 1166-1171
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe aging process in Fe-Cu alloys prepared by vacuum-deposition was investigated by means of transmission electron microscopy, X-ray diffraction, electric resistance and magnetic measurements.
The following results have been obtained:
(1) Apparent solubility limits of the alloys deposited on aluminum substrates, which were held on a cupper plaque chilled with liquid nitrogen, are 36% Cu in the BCC (α-Fe) phase and 33% Fe in the FCC (ε-Cu) phase respectively.
(2) Each phase in the two-phase alloy films has the composition nearly equal to that of the apparent solubility limit in the as-deposited state.
(3) By low temperature aging, the super-saturated solid solutions of the ε-Cu and α-Fe phases precipitate directly from the BCC and FCC solid solutions.抄録全体を表示PDF形式でダウンロード (533K) -
瀬尾 省逸, 宮崎 亨, 矢島 悦次郎, 森田 喜久男1973 年 37 巻 11 号 p. 1172-1179
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーDie dreizehn Stähle von Fe-Ni, Fe-Ni-C, Fe-Cr-Ni-C und Fe-Cr-Ni-Mn-C Legierungen wurden bei verschiedenen Temperaturen Zugversuch gemacht, deren Ms Temperaturen unter −30°C sind. Und davon wurde der Einfluß der Legierungselemente auf die mechanischen Eigenschaften bei der durch die Verformung induzierten Umwandlung von metastabiler Austenitstruktur versucht. Als metastabile Austenitstruktur wurde zuerst Fe-Ni Legierung gebraucht und dazu C, Cr und Mn beigefügt, um die Austenitstruktur zu stabilieren. Nachstehende Ergebnisse wurde erhalten.
(1) Um den TRIP Vorgang effektiv zu machen, ist es nötig, daß der sich bildende Martensit stark ist. Dafür ist wichtig die Entstehung kohlenstoffhaltigen Martensits. Chrom und Mangan, die Stapelfehlerenergie vermindern, sind auch wirksam. Die Zusätze dieser Elemente führen nicht direkte Erstarkung von Martensit herbei, sondern die große Verfestigung des Austenits. Daraus muß der stärkere, durch die Verformung induzierte Martensit gebildet werden.
(2) Für zähigen TRIP Stahl muß die Temperatur gewählt werden, bei der eine Steigung der Spannungs-Dehnungskurve entsteht. Das Maximum der Dehnung ist bei der Temperatur, bei der die Steigung erst entsteht. In diesem Fall ist “serration” keine nützliche Bedingung.
(3) Falls viel Mangan in der Legierung ist, bildets sich der ε-Martensit. Durch Verformung geschieht die γ→ε→α Umwandlung. Eine solche Legierung zeigt, daß Dehnung und Stärke betrifft einen niedrigen Wert als in einem Falle, in dem nur α-Martensit gebildet wird.
(4) Für den nützliche TRIP Stahl zur Industrie muß die Stapelfehlerenergie vermindert werden, ohne daß sich ε-Martensit bildet. Dadurch wird der Ms-Punkt leicht kontrolliert und es ist einfach, den Stahl mit großer Dehnung und Zähigkeit zu gebrauchen.抄録全体を表示PDF形式でダウンロード (672K) -
上舘 良興, 宮崎 亨, 矢島 悦次郎1973 年 37 巻 11 号 p. 1180-1187
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーIt is well known that alloys containing fine dispersed particles are superior in high temperature creep strength. The mechanism of the creep, however, has not been made clear.
In the present work, the mechanisms of the creep deformation of this kind of alloy are investigated, using the Nimonic type alloy, Ni-20% Cr-4% Al and Ni-20% Cr-35% C0-4% Al alloys containing fine rf particles. The results obtained are as follows:
(1) The steady state creep rate \dotε of the Ni-Cr-Al alloy is not linearly proportional to the applied stresses on the bilogarithmic scale. This is due to the presence of two different creep mechanisms corresponding to low and high applied stresses. The creep rate at low stress is controlled by the rate of climbing of edge dislocation and non-conservative motion of jog in screw dislocation, and at high stress cross slip of dislocation is a rate controlling process of the steady state creep. In the case of the former, the activation energy is nearly equal to that of the vacancy diffusion, while in the case of the latter the energy is much larger than the former. The thermally activated process of this cross slipping is considered to be due to the contraction of extended dislocation. In the highest stress region mechanical twins are observed.
(2) The cross slipping of dislocation is not observed in Ni-20 Cr-35 C0-4 Al alloy, with a low stacking fault energy, when crept under a high stress, and the activation energy is nearly equal to that of the vacancy diffusion. Therefore, the rate controlling process of creep deformation of the alloy is thought to be not cross slipping but climbing of dislocation.抄録全体を表示PDF形式でダウンロード (1374K) -
大森 正信, 若狭 邦男, 吉永 芳豊1973 年 37 巻 11 号 p. 1188-1194
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーIn order to study the intermediate temperature embrittlement behaviors of an OFHC copper and five α-brasses containing 1 to 30% zinc, tension tests were carried out with their round bars at temperatures ranging from room temperature to 700°C under two strain rates of 2×10−3 and 1.4×102/sec, respectively.
The results obtained are summarized as follows:
(1) All the specimens except for a 99-1 brass revealed a remarkable intermediate temperature embrittlement when they were deformed in the slow tension. In the rapid tension, however, the embrittlement disappeared completely in the OFHC copper and became less in the brasses than that in the slow tension. The embrittlement of the brasses increased with increasing zinc concentration.
(2) Specimens which revealed the intermediate temperature embrittlement were always accompanied by defects of cavities or cracks generated along grain boundaries during deformation. In a condition where the embrittlement appeared, it seemed very likely that the cavities were developed in the brass specimens even at a tensile strain of less than 3%.
(3) The embrittlement of copper and brass was probably attributable to a characteristic deformation behavior of grain boundaries rather than a diffusion-controlled behavior, in view of the facts that the temperature range in which the intermediate temperature embrittlement occurred did not shift to a higher temperature even when deformed at a high rete of strain and also the considerable embrittlement still appeared in the brasses with more than 10% zinc even when deformed in tension at a very high strain rate.
(4) The 99-1 brass had a very high ductility, showing no intermediate temperature embrittlement in both slow and rapid deformations. However, the cause of this high ductility behavior remained unknown.抄録全体を表示PDF形式でダウンロード (892K) -
大森 正信, 若狭 邦男1973 年 37 巻 11 号 p. 1195-1199
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーSingle crystals and coarse grained specimens grown from an OFHC copper and 70-30 brass were tested in tension at room temperature to 500°C under two strain rates of 2×10−3 and 1.4×102/sec to examine the ductility of the crystals and the grain boundary deformation behaviours of the coarse-grained specimens.
The results obtained were summarized as follows:
(1) The decrease of ductility corresponding to that revealed by the polycrystalline copper at intermediate temperatures was not found in the total elongation-temperature curves for the copper single crystals which were failured by complete rupture to a knife-edge in the present experimental conditions.
(2) A total elongation-temperature curve of the brass single crystal with a given axial orientation had a small dip around 300°C when the crystal was tested in the slow tension, but such a dip was absent in the curve when tested in the rapid tension. It was doubtful, however, whether the presence of this dip of elongation implied really a loss of ductility of the brass single crystal being deformed slowly around 300°C or not, since all the crystals were ruptured to a knife-edge in the present experimental conditions.
(3) When the coarse-grained specimens were tested in the slow tension at the intermediate temperatures, although grain boundary slidings appeared clearly prior to boundary crackings in the copper specimen, the boundaries in the brass specimen were observed to be cleaved suddenly after it was deformed to a certain degree without any appreciable boundary sliding.抄録全体を表示PDF形式でダウンロード (616K) -
北田 正弘1973 年 37 巻 11 号 p. 1200-1206
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーMicrostructures, morphology and electrical resistivity of Au-Ge and Au-Ge-Ni eutectic alloy films evaporated on the cleaved NaCl (100) substrate below the eutectic temperature are studied.
Au-12% Ge eutectic alloy films evaporated on the cleaved NaCl (100) show the structure composed of the matrix Au and the island-like Ge grains. The (111) planes of Au and Ge are parallel to the cleaved NaCl (100) surface, and the angles between ⟨110⟩ directions of Au and Ge are 3 to 10°. The average grain size of Ge in Au-12% Ge alloy films decreases with decreasing substrate temperature. The average grain size of Au in Au-Ge-Ni alloy films decrease with increasing concentration of Ni. The electrical resistivity of Au-Ge and Au-Ge-Ni alloy films increases with the increase in Ge or Ni concentration.抄録全体を表示PDF形式でダウンロード (902K) -
三浦 維四, 浅岡 憲三1973 年 37 巻 11 号 p. 1207-1212
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe tensile behavior of two-phase alloy containing a particle was studied by the finite element method which is a very useful computer simulation method for the solution of the problem of applied mechanics. This problem was carried out on the aluminium matrix with an elastic circular second phase whose Young’s modulus was 37000 kg/mm2, and was treated as the case of a two-dimensional plane stress model. The results of this simulation were as follows:
(1) The relation between the stress-strain curve and the development of the yielded zone of this two-phase alloy was obtained.
(2) Equivalent stress \barσ, stress in the tensile direction σx and stress in the transverse direction σy were calculated at various stages. It was found from the stress distribution that the matrix consisted of the following three parts;
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(3) The shear stress at the interface between particle and matrix was maximum in the elastic state (stage 1) at the 45° direction from the X axis. When the yielded zones, spreading outwards from the two parts, met first at a point on the longitudinal axis (stage 9), the shear stress peak moved to the 60° direction and the matrix near the particle was unloaded.抄録全体を表示PDF形式でダウンロード (437K) -
三浦 維四, 浅岡 憲三1973 年 37 巻 11 号 p. 1212-1216
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe tensile behavior of two-phase alloy containing a fiber was studied by the finite element method. This problem was carried out on the aluminium matrix with an elastic fiber whose Young’s modulus was 37000 kg/mm2, and was treated as the case of a two-dimensional plane stress model. The results of this simulation were as follows:
(1) The relation between the stress-strain curve and the development of the yielded zone of this two-phase alloy was obtained.
(2) It was found that the tensile stress in the second phase and the shear stress along the interface were affected remarkably by mechanical properties of the matrix and the second phase, particularly by the Young’s modulus ratio.
(3) A new approximate equation was proposed in consideration of the principal stress axis of this two-phase alloy, and this equation was in good agreement with the results calculated by means of the finite element method.抄録全体を表示PDF形式でダウンロード (390K) -
石原 只雄, 清水 義彦, 伊藤 伍郎1973 年 37 巻 11 号 p. 1217-1223
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーInvestigations were conducted to determine the effects of ferrite content, heat treatment and welding methods on the susceptibility of Fe-Cr-Ni stainless steel weld overlays to stress corrosion cracking in high temperature water. Specimens machined from the stainless steel weld overlays on a carbon steel were tested under the as-welded and the post-weld heat treated condition, respectively. These weld overlays contained about 1 to 13 percent ferrite in an austenite matrix.
Tests were conducted in a 3-liter autoclave containing high purity water or chloride-containing water. The stressed U-bends were exposed at 300°C for 300 hr under the undeaerated condition. The results were summarized as follows:
(1) No cracking was detected in any specimen of stainless steel weld overlays in high purity water.
(2) In contrast with the test in high purity water, cracking was observed for all of the specimens tested in chloride-containing water. The susceptibility to cracking, however, decreased with increasing amount of ferrite in their structure. This tendency was similar to that observed for the wrought alloys.
(3) There was no significant difference between the susceptibility to cracking of manual arc welded materials and that of submerged arc welded materials.
(4) The susceptibility to cracking of weld overlays was decreased by the post-weld heat treatment at 625°C for 20 hr.
(5) The types of cracking observed on the weld overlays were divided into three groups: (a) high austenite-containing alloys were subjected to transgranular cracking, (b) the austeno-ferritic duplex alloys containing about 6 to 9 percent of ferrite exhibited mixed cracks of trans- and inter-dendritic cracking, (c) the duplex alloys containing more than about 10 percent of ferrite were predominantly subjected to interdendritic cracking.
(6) These crack paths were discussed with respect to the geometry of the δ phase in their structure.抄録全体を表示PDF形式でダウンロード (802K) -
稲数 直次, 山本 久1973 年 37 巻 11 号 p. 1224-1229
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーIn order to find the relation between the drawing ratio and the process of fiber texture transition for drawn aluminium wire, an annealed aluminium rod was drawn up to 93 per cent, and the orientation changes occurring during drawing were investigated by a model of X-ray pole figures determined for various degrees of reduction in area.
The preferred orientation (112)[11\bar1], (112)[\bar1\bar11] and (110)[001] are developed by drawing up to about 72 per cent. As the drawing ratio increases, the normal plane to the compression axis around the wire axis ⟨111⟩ rotates toward {110}. These results are in accord with the rotation toward the slip plane having a higher relative resolved shear stress. Therefore, the {110} position can be expected to be the end-point having a certain compression plane around the wire axis. After severe drawing up to about 93 per cent, the ⟨100⟩ intermediate fiber texture rapidly decreases in intensity, leaving a single ⟨111⟩ fiber texture, and the drawn wire has random orientations around the wire axis ⟨111⟩.抄録全体を表示PDF形式でダウンロード (447K) -
荻野 喜清, Borgmann Fritz O., Frohberg Martin G.1973 年 37 巻 11 号 p. 1230-1235
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe viscosity of liquid iron has been measured by the oscillating crucible method. In a preliminary experiment, it was found that the equation suggested by Knappwost may be related to significant error in the case of liquid iron. In the present experiment, therefore, the analytic expression with three constants based on the Roscoe’s equation was used. The results showed that the temperature dependence of viscosity coefficient of liqiud iron changes at temperatures near 1600°C, i.e., below these temperatures, the viscosity coefficient showed the deviation from the extrapolated values in terms of the Arrhenius plot at higher temperatures. The temperature at which the deviation occurs depends on oxygen concentrations of liquid iron; i.e., this temperature rapidly decreases from 1630 to 1600°C with the increse of oxygen from 40 to 300 ppm.抄録全体を表示PDF形式でダウンロード (443K) -
川本 信, 新谷 進, 曽根 匠, 岡林 邦夫1973 年 37 巻 11 号 p. 1236-1242
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe wear characteristics of 0.42% C carbon steel and 17 Cr stainless steel rubbed against 17Cr stainless steel and 0.6% C carbon steel respectively were examined in relation to the temperature at the actual contact region (the flash temperature) and the mean temperature of the sliding surface. The wear tests were carried out by the pin-disc type machine under unlubricated condition. The flash temperature was obtained by measurement of the thermo-electromotive force developed between the sliding surfaces, and the mean temperature was calculated from the temperature gradient of the specimen measured by the thermo-couples.
In the condition where the flash temperature exceeded 300∼400°C, the wear of both materials decreased as the flash temperature was raised. At the flash temperatures in excess of 800°C, the wear was dominated by the mean temperature and increased as this temperature was raised. At the sliding speed more than that at which severe wear occurs, the wear was the smallest when the actual contact region reached the melting point or its neighborhood and the mean temperature was low. This cause may stem from the fact that the ruptures of the contact asperities occur in extremely thin layers, since only the interfaces of the asperities considerably soften or become viscous and the underlying metals have sufficient strength.
If the flash temperature and the mean temperature of the sliding surface are known, it will be possible to estimate any wear to occur. It is found that the temperature of the sliding surface is one of the most important factors which dominate wear.抄録全体を表示PDF形式でダウンロード (635K) -
吉岡 正三, 中山 豊, 伊藤 太一郎, 福永 健治1973 年 37 巻 11 号 p. 1243-1249
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe temperature dependence of stress-strain curves in Cu-Ni-Zn single crystals, especially of the critical resolved shear stress (CRSS), has been studied. Single crystals of composition close to Cu(1−2x)NixZnx and Cu(0.75−x)NixZn0.25 containing Cu2NiZn were prepared and deformed in tension between 77 and 1060°K.
The results obtained are as follows:
(1) The temperature dependence of stress-strain curves are similar to those of binary Cu alloys, though the concentration and ratio of Ni and Zn play important and delicate roles in them.
(2) There are three temperature ranges concerning the temperature dependence of CRSS. The range I corresponds to the low temperature range where CRSS decreases with increasing temperature. The temperature-dependent part of CRSS shows the activation energies of 0.66∼0.77 eV and is almost independent of alloy composition.
(3) The range II corresponds to the middle temperature range where CRSS depends little or reversely on the temperature. In Cu-20 Ni-20 Zn and Cu-25 Ni-25 Zn alloys, in addition, a maximum in CRSS exists between 500 and 600°K.
(4) The range III corresponds to the high temperature range where CRSS decreases with increasing temperature. In the temperature range T⁄Tm 0.7∼0.8 a relation \dotε∼τn holds (\dotε: strain rate, τ: CRSS). The activation energy for diffusion is found to be 1.9∼2.2 eV and is almost independent of the solute concentration.
(5) Like binary Cu alloys, the deformation substructures observed in the transmission electron microscope are composed of piled-up dislocation arrays below 773°K and a homogeneous dislocation arrangement at 873°K. In Cu-25 Ni-25 Zn deformed at 573°K, dislocation pairs of same sign are observed on the same slip plane. Then, the maximum on CRSS at 500∼600°K in Cu-20 Ni-20 Zn and Cu-25 Ni-25 Zn is considered to be closely related to the formation of long range order.抄録全体を表示PDF形式でダウンロード (868K) -
岡崎 謙二, 鹿子木 公春, Conrad Hans1973 年 37 巻 11 号 p. 1250-1258
発行日: 1973年
公開日: 2008/04/04
ジャーナル フリーThe deformation kinetics of Ti-O and Ti-C alloys (0.04∼0.45 at% O and 0.07∼0.36 at%C) with 2 to 15 μm grain size were investigated over the temperature range of 77 to 700°K employing strain rate cycling during an otherwise constant strain rate test. The value of the thermal component of the flow stress σ* was obtained directly from the strain rate cycling tests through the relation σ*=m*(∂σ⁄∂ln\dotε)T, where m* is the value of (∂ln\dotε⁄∂lnσ)T extrapolated to zero strain and infinite grain size. σ* was found to be proportional to the square root of the oxygen or carbon content, the proportionality constant at 0°K being 0.23 C66 or 0.17 C66 for Ti-O and Ti-C alloys respectively. The Gibbs free energy of activation (σ*=0, 0°K) for plastic flow of the Ti-O and Ti-C alloys are 1.1 and 0.8 eV respectively. The maximum iorces exerted by the obstacles on the dislocations are 63×10−6 and 52×10−6 dynes in Ti-O and Ti-C alloys respectiveiy and the distance at which the force first arises rapidly ∼2b, all independent of the interstitial content and grain size. These results are in accord with the overcoming of interstitial solute obstacles as the rate controlling mechanism of σ*.
The athermal component of the flow stress σμ increased with decrease in grain size according to the Hall-Petch relation. σμi(d−1⁄2=0) is equal to 0.05 C66 times the square root of the oxygen or carbon content, whereas the Hall-Petch constant K is relatively independent of the interstitial content. Based on previous work, it is concluded that the effects of grain size and interstitial content on σμ is through the dislocation density produced during straining.抄録全体を表示PDF形式でダウンロード (653K)
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