巻号一覧
30 巻, 11 号
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三浦 維四, 本間 久夫1966 年 30 巻 11 号 p. 1001-1005
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーIt has been described in a previous report that the strength of the composite containing continuous fiber is improved to a great extent when the fiber itself has a large strength. As the strengthening element, many other substances can be expected for use instead of the fiber. In the present study, the concentrated parts of the solute atom in solid solution have been experimented as a strengthening element which is distributed in the continuous state. The experiment was carried as follows. 195 sheets of aluminum foils (7 μ thickness) and 4 sheets of silver foils (6 μ thickness) are laminated in the composite arrangement of Al 39-Ag 1-Al 39-Ag 1-Al 39-Ag 1-Al 39-Ag 1-Al 39 and are bounded each other by hot rolling at 500°C. When these specimens are heated, silver atoms diffuse into the aluminum matrix and the process of diffusion during the heating at 550°C for 3 min is discussed on the basis of Fick’s second law. It has been predicted that the total strength in this type of alloys will be an integral value of strength in each part in the cross section. This is because the strength of the alloy strengthened by continuous fiber is about the algebraic average of the strength of the fiber and the stress on the matrix at the breaking strain of the composite as discovered in the another paper. The results of the tensile test of these alloys are well fitted to the interpretation relating to the strength stated above.抄録全体を表示PDF形式でダウンロード (1490K) -
三浦 維四, 岩出 章, 太田 守1966 年 30 巻 11 号 p. 1005-1010
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThe authors and their co-workers have studied the relation between structures of composite alloys and their mechanical properties by use of the specimens prepared by foil metallurgy. In this paper, an attempt has been made to prepare special and controlled structures of the Al-CuAl2 eutectic and Al-Si eutectic alloys by means of unidirectional solidification. The solidification rate is 0.5, 3.5 and 5.0 cm/hr in the air, and in the case of using water as cooling atmosphere, the rate of lowering the specimen into water is 0.3, 3 and 30 m/hr. As the vessels for melting the specimens, a cylindrical envelope made of titanium foil (20 μ thickness) and a sheath made of stainless steel sheet are employed.
The main results are as follows: (1) For Al-CuAl2 eutectic alloys, a cellular structure is found in each specimen, and its solid model shows a lotus-root structure. (2) Unidirectional solidification into water also reveals a cellular structure, where the spacing between the alligned CuAl2 platelets is very small (0.4∼0.5 μ). (3) In the solidification of Al-Si eutectic alloys into water, the eutectic structure is very fine and its mean free path λ is 1.8∼3.0 μ, while the value of λ in the modified structure by addition of sodium is 3.3 μ. Further, the value of λ in the specimen solidified in water after modification by sodium is 1.0 μ.抄録全体を表示PDF形式でダウンロード (2243K) -
添野 浩, 土屋 正利1966 年 30 巻 11 号 p. 1011-1017
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーNitrogen diffusion peaks in iron chromium alloys containing less than 1.5 atomic pct chromium were measured at the frequencies of 1.0 and 102 c/s. Two abnormal peaks were observed on both temperature sides of the usual nitrogen peak in unalloyed iron. From peak shifts, activation energies for the low and the high temperature peak were calculated as 16 kcal/mol and 20 kcal/mol, respectively. The high temperature peak is put down as being due to nitrogen atoms in the vicinity of chromium atoms, while the mechanism of the low temperature peak is interpreted as jumps of nitrogen atoms in strained Fe-Fe interstices which are produced by the addition of chromium atoms. Although it is not obvious whether the high temperature peak is describable in terms of a single relaxation time or not, it is reasonable for the low temperature peak to introduce a distribution of relaxation times.
Precipitation of nitride phases, Fe8N, Fe4N and CrN, from Fe-Cr-N alloys were investigated by measuring electrical resistivity. Internal friction peaks were also measured after the precipitation of the chromium nitride as a function of chromium contents. Precipitation of the chromium nitride was clearly observed even in 0.2 atomic pct chromium alloy. Consequently, soluble nitrogen atoms in alpha iron-chromium alloys are decreased due to the precipitation of the chromium nitride.抄録全体を表示PDF形式でダウンロード (2180K) -
鷹合 徹也1966 年 30 巻 11 号 p. 1017-1021
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーAn electron beam floating zone melting apparatus has been assembled after A. Calverley’s(1). The apparatus consists of four components; vacuum system, power supply, anode supports and traversing cathode. The acceleration voltage of maximum 10 kV is supplied to the specimen (anode), while the W-filament (cathode) is nearly earth potential. Electron beam concentrators made of tantalum disks were found to be effective for obtaining higher temperatures in specimen rods. For example, the use of a single concentrator or paired concentrators resulted in a rise of the specimen temperature which was about 250°∼450°C higher than the cases with no concentrators.
The substantial heat quantities required for actual zone melting experiments aggreed well with the values calculated from the equation by Donald(3).
In the zone melting process of titanium and zirconium, the vacuum in the melting chamber and the firing wattage given to the W-filament showed unique changes.抄録全体を表示PDF形式でダウンロード (1339K) -
鷹合 徹也1966 年 30 巻 11 号 p. 1022-1026
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThe refining effect of floating zone melting on molybdenum, tungsten and tantalum were investigated from their mechanical properties and chemical analysis. Floating zone melted tungsten and molybdenum rods showed excellent bent ductility at room temperature. By the floating zone melting method, tungsten and molybdenum grew to single crystals rather easily, and their crystal orientations were almost near the (111) direction. By tensile tests, zone melted molybdenum and tantalum rods showed fracturs of the chiseltype break pattern, and no yielding was observed.
Compression strain hardening exponents of the floating zone melted molybdenum and tungsten rods were smaller than those of the starting materials, but in the case of the tantalum rod, the strain hardening exponent of the zone melted part was somewhat larger than that of the starting rod.
The resistance ratio of the zone melted molybdenum rod was 2.8×10−4 against 4.0×10−2 in the starting rod and 3.2×10−2 in the recrystallization zone.抄録全体を表示PDF形式でダウンロード (2214K) -
鷹合 徹也1966 年 30 巻 11 号 p. 1027-1031
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーElectron beam melting of tungsten has been studied mainly by spectroscopic analysis, X-ray diffraction of columnar crystal grains and considerations of recrystallization behaviours.
The actually required power for tungsten ingot melting was about twice as large as that estimated by E. B. Boas, probably due to the better thermal conductivity of metallic tungsten. The evaporation rate of tungsten during the electron beam melting is about 10∼25% of the charged weight. The actual melting operation temperature is estimated to be about 4100°∼4200°K from the measured evaporation rates. The electron-beam melted tungsten ingot consists of well-collimated long columnar crystal grains. The crystal orientations of these columnar crystal grains are distributed near (011)-(223) zone of the stereographic triangle. The orientation relationship between the upper and lower columnar grains in the electron-beam melted tungsten ingot reveals that the growth of the upper columnar crystal grains takes place almost epitaxially along the crystal orientation of the lower columnar crystal grains.
From the changes in elongation and ultimate tensile strength due to annealing, the recrystallization temperature of the electron-beam melted tungsten has been measured to be 900°∼1000°C, in a way consistent with the sintered tungsten. However, there is a marked difference in the recrystallized microstructure between the electron-beam melted and the sintered tungsten.抄録全体を表示PDF形式でダウンロード (1792K) -
山崎 道夫1966 年 30 巻 11 号 p. 1032-1036
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーA high carbon 18Cr-12Ni stainless steel was two-step solution treated and was found to show excellent creep rupture properties. This two-step solution treatment comprises (1) homogenizing of the steel above the solid solubility line of carbide (Cr23C6), (2) subsequent cooling directly to intermediate temperatures (970°∼1120°C) below the solubility line, and (3) preferential precipitation of the carbide at grain boundaries. The grain boundary precipitation occurred in corrugated fashion, and it was considered that this corrugation minimized grain boundary sliding and hence Zener’s triple point cracking. Stroh’s equation was utilized to explain this.
The effects of the temperatures of the first and second steps and the holding time at the second step were studied.
Comparison in a 1000 hr rupture stress at 600°C revealed that the best two-step solution treatment within this investigation gave 26 kg/mm2, nearly a 50% increase in stress, against the highest value of 17.5 kg/mm2 in the conventional one-step solution treatment.抄録全体を表示PDF形式でダウンロード (1423K) -
美馬 源次郎, 佐治 重興1966 年 30 巻 11 号 p. 1037-1041
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThe changes in internal friction, hardness, electrical resistivity, magnetic properties and microscopic structure of 2.3, 5.4 and 9.6 wt% iron-copper alloys by aging at the temperatures from 600° to 750°C, were studied.
During the aging process, the hardness change shows a single peak, while the electrical resistivity decreases in the stage of age-hardening and reaches an equilibrium state before the hardness reaches a maximum. In 2.3 wt% iron-copper alloys, there is no change of internal friction in the stage of age-hardening, but in the stage of over-aging, the internal friction increases remarkably. At the same time, the amplitude dependence appears and the break-away point shifts to the lower amplitude side with aging time. In the 5.4 and 9.6 wt% iron-copper alloys, the internal friction decreases in the stage of age-hardening and the change of internal friction in the stage of over-ageing is similar to that of the 2.3 wt% iron-copper alloys. The above change of internal friction in the stage of over-ageing begins at a shorter aging time with rising aging temperature and increasing iron concentration. This change of internal friction is related to the growth of the precipitate particles.
Internal friction of copper-iron alloys in this study is neither a relaxation-type of energy loss nor a magnetomechanical hysteresis energy loss due to the precipitate, but it is a hysteresis energy loss of vibrating dislocation.
On the basis of these results, the change of coherency between the matrix and the precipitate and hardening mechanism in these alloys have been discussed.抄録全体を表示PDF形式でダウンロード (2243K) -
美馬 源次郎, 中桐 明和1966 年 30 巻 11 号 p. 1042-1047
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThe isothermal softening processes occuring in a undoped tungsten wire (0.38 mmφ) which was prepared through the usual industrial production process for the present investigation has been studied mainly by the tensile test and microscopic observations in the temperature range of 1100°∼1800°C.
The tensile strength changes during isothermal annealing was compared with the microscopic structure changes and the results of X-ray measurements, and it is shown that they are in good agreement with each other.
It has been found that the softening takes place in several stages and that a large fraction of softening and a rapid decrease in elongation (nearly to zero) are observed in the final stage of softening. On the other hand, during the stage second to the last a marked increase in elongation takes place and any noticeable tensile strength change is not observed.
The activation energies for the last stage and the other stages of softening are found to be 66,000 cal/g-atom and 73,770 and 73,500 cal/g-atom.
The characteristic microscopic structure corresponding to the last stage of softening is a coarse equiaxed grain structure, while the elongated grain structure is characteristic in the stage second to the last.
The coarse equiaxed grain structure is markedly differs from the ordinary recrystallization structure observed in the moderately or heavily cold drawn metals.
It is considered that the coarse equiaxed grain structure corresponds to the microstructure which results from migration of small or medium angle boundary rather than the so called recrystallization structure (primary recrystallization structure).抄録全体を表示PDF形式でダウンロード (1589K) -
美馬 源次郎, 西田 和彦1966 年 30 巻 11 号 p. 1047-1051
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーChanges in the configuration of dislocations of the undoped tungsten wire (0.38 mmφ) during isothermal annealing at 1180°C have been studied by transmission electron microscopic observations, the results of which almost coincide with those by optical and replica electron microscopic observations.
The microstructure of the drawn tungsten wire consists of highly elongated grains called fibers or fiberish grains.
Although characteristic boundary fringes are observed on these fiberish grain boundaries and the barrelled subgrain boundaries in the annealed specimens, their boundaries do not seem to be high angle boundaries.
During isothermal annealing, the grains surrounded by high-angle boundaries have not been observed. Accordingly, the authors can not find the so-called recrystallization nuclei through this work.
It is observed generally that the width of the fiberish grain increases with increasing annealing time. The mean width of the fiberish grain \barWt can be experessed as
\barW_t = 0.27 (t-1) ^0.15, where t is the annealing time.抄録全体を表示PDF形式でダウンロード (1145K) -
一ノ瀬 幸雄1966 年 30 巻 11 号 p. 1052-1057
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーIt can be presumed thermodynamically that Si forms a stable gaseous monoxide and increases the refining effect under vacuum in a way consistent with Ge, and the addition of Si should be also thought to be effective for improvement of the magnetic properties of Fe-Ni alloys because of decreasing the gas content and non-metallic inclusions. In the present paper, on the basis of the above prediction, effect of a small amounts of Si addition to 50Ni-Fe alloys was investigated thermodynamically and magnetically. The results obtained are summarized as follows:
(1) It is theoretically induced that Si becomes more easily to form a gaseous monoxide under vacuum and its vapor pressure attains about 102 mmHg at 1600°C. And it is presumable therefore that Si is useful as an refining agent similar to Ge. The reults of gas analysis are comparable with the curve of the theoretical calculation as PSiO=5 mmHg.
(2) The addition of Si induces a remarkable decrease in coercive force and a remarkable increase in initial permeability. The maximum permeability is the highest near 1%Si, and the effective permeability becomes larger in high frequency because of high resistivity by the addition of Si.
(3) The addition of Si, as well as Ge, promotes remarkably the grain growth, which is particularly effective in the initial addition of only a few %Si. The grain size dependence of the coercive force and the initial permeability are respectively expressed by the following equations:
(This article is not displayable. Please see full text pdf.)
\ oindentThe above relations are always seen no matter what amounts of Si are added.抄録全体を表示PDF形式でダウンロード (2428K) -
木村 高夫1966 年 30 巻 11 号 p. 1058-1062
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーInvestigations were carried out on the recovery and recrystallization of Cu-0.225 wt% Al alloy internally oxidized and cold rolled by electron microscopy and X-rays. The results obtained were summarized as follows.
(1) The Cu-0.225 wt%Al alloy of 0.2-mm thickness internally oxidized at 1000°C and cold rolled by 50% shows recovery but no recrystallization even annealed for 6 hr at 1000°C. A very small amount of recrystallization was observed after annealing the specimen for 1 hr at 1030°C.
(2) The recovery and recrystallization process of the alloy seems to be the disentanglement of tangled dislocations, the formation of subgrains by polygonization, the coalescence of subgrains into recrystallization nuclei and the growth of the formed nuclei.
(3) The unusual retardation of recrystallization of the alloy can be explained in terms of the pinning of dislocations by the dispersed particles, the invalidity of old boundary upon recrystallization, the sluggish growth of the recrystallization nuclei by the coalescence of subgrains due to the small misorientation among subgrains, and the impingement effect of the dispersed particles upon grain boundary migration.抄録全体を表示PDF形式でダウンロード (1562K) -
今野 熙, 久高 克也, 的場 敏夫, 安藤 正久1966 年 30 巻 11 号 p. 1063-1068
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーUsing a modified girdle-type ultra high-pressure apparatus, WC-Co alloys containing 1.5 and 6 wt% in cobalt were loaded up to 20∼70 kbars at room temperature and 1000°∼1800°C. From the measurement of microhardness, electron microscopic observation and X-ray diffraction, the following results were obtained.
(1) Generally, with increasing pressure, the hardness increases above a certain pressure and reaches a maximum value, and then decreases rapidly. The increase in hardness is mainly due to the hardening of WC crystals or the microstress induced in WC crystals and the decrease in hardness is owing to local formation of micro-cracks by stress concentration in WC grains under high pressure.
(2) Stresses generated in the high pressure apparatus are divided into the environmental hydrostatic pressure component and the compressive stress component and the ratio of the two components depends on the coefficient of internal friction of the pressure medium.
(3) Generally, the hardness decreases by the annealing effect with increasing compression temperature. However, in the case of the hard metals whose the hardness has decreased as a whole by the local fracture at room temperature, the hardness increases in a certain range of temperature because of contributions of the binder to the binding of the fractured grains at high temperatures.抄録全体を表示PDF形式でダウンロード (1788K) -
茨木 正雄, 岡本 平, 岸武 勝彦1966 年 30 巻 11 号 p. 1068-1074
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーA study was performed, using aluminum-rich Al-Cu and Al-Si alloys frozen unidirectionally, to make clear the effects of growth condition and solute elements on the morphology, the size of dendrite cells and the arms spacing of cellular dendrites formed in columnar crystals of binary alloys. The primary branches, which grow perpendicular to the freezing direction from the dendrite stalk, become platelike as shown previously. The dendrite cell size or dendrite width, Z, is given by the following formula:
(This article is not displayable. Please see full text pdf.)
\ oindentwhere m is the liquidus slope, k0 the equillibrium distribution coefficient, D the diffusion coefficient of solute in liquid phase, C0 the solute content and Vs the cooling rate in the coexisting region of liquid and solid phases, and a0 a constant. The dendrite arms spacing, Za, is proportional inversely to Vs\frac14, and independent of the solute elements.抄録全体を表示PDF形式でダウンロード (1715K) -
吉岡 正三, 中山 豊, 伊藤 太一郎1966 年 30 巻 11 号 p. 1074-1080
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThe pre-yield micro-plastic deformation in α Cu-Al and Cu-Ni solid solution single crystals was studied at room temperature by means of the etch pit technique. The motion and multiplication of dislocations are detectable from shape and size of etch pits. Some of the specimens were deformed in tension at a strain rate of 4×10−4 sec−1, and others were deformed with a four-points bending jig under a stress pulse of 1 sec. The frictional stress against dislocation motion of two alloy systems are calculated from an equation for dislocation pile-ups with the measurement of etch pits arrays. The “10−6 yield stress” was studied with a strain indicator which had a strain sensitivity of 2×10−6, and compared with the result of the etch pit observation.
The results obtained are as follows:
(1) Dislocation motion is observed at a much lower stress than the yield stress, and the ratio of the number of moved dislocations to that of total grown-in dislocations decreases as the solute concentration increases.
(2) Dislocation multiplication stresses detected by etch pit observation in the bending test is higher than those in the tension test. The multiplication stress corresponds to the “10−6 yield stress” which is detected by the strain indicator having a sensitivity of 2×10−6.
(3) From the observation of etch pits, it would be assumed that the multiplication stress corresponded to the stress at which the moved dislocations cut through the forest dislocations.
(4) Frictional stress deduced from the pile-up dislocation arrays increases with solute concentration. For Cu-2.5 at%Al 0.060±0.030 kg/mm2, for Cu-5.0 at%Al 0.085±0.025 kg/mm2, for Cu-10 at%Al 0.20±0.04 kg/mm2, for Cu-15 at%Al 0.28±0.08 kg/mm2, for Cu-2.5 at%Ni 0.065±0.035 kg/mm2, and for Cu-5 at% Ni 0.075±0.015 kg/mm2 are obtained.抄録全体を表示PDF形式でダウンロード (2223K) -
田村 今男, 大山 徹1966 年 30 巻 11 号 p. 1081-1085
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーA series of Fe-Ni-C martensites having transformation twins and an Fe-Cr-Ni-C martensite having no transformation twins but dislocations were rolled at 200°C, room temperature and −196°C (boiling point of liquid nitrogen). The hardness change and the deformation mode of the martensites were examined. The martensites having transformation twins (Fe-Ni-C) were deformed by slip, if the carbon content of the martensite was low or the deformation temperature was high. In this case, the hardness change with reduction in deformation showed usual curve of work-hardening. However, when the carbon content was high or the deformation temperature was low, the martensite was deformed by twinning. In this case, the martensite showed work-softening at a few percent reduction, and then hardened rapidly beyond the minimum hardness with increase in reduction. The martensite having no transformation twins but dislocations (Fe-Cr-Ni-C) was deformed by slip, and the hardness change with reduction showed a usual work-hardening curve throughout in this investigation.抄録全体を表示PDF形式でダウンロード (2436K) -
榊 隆1966 年 30 巻 11 号 p. 1086-1092
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーThis experiment was carried out to establish a simple and accurate method for the determination of the bismuth content in high alloy steel.
The bismuth was separated as thionalide complex from the iron and other elements in an ammoniacal solution in which were masked those elements by use of ammonium tartrate, sodium cyanide and sodium sulfite.
By means of this separation method with thionalide, the bismuth can be separated easily and accuratlly from large amounts of iron, manganese, nickel, chromium, molybdenum, copper, tungsten, vanadium, cobalt, titanium, aluminium, zirconium and others.
The separated bismuth was determined by the spectrophotmetric method with xylenol orange.
As a result of the experiment, the author succeeded in establishing a method in which 0.01 to 0.3% of bismuth in high alloy steel can precisaly be measured without difficulty.
The bismuth contents in synthetic samples were measured by this method with satisfactory results.抄録全体を表示PDF形式でダウンロード (1941K) -
村井 三郎, 芳賀 武, 平山 恵一1966 年 30 巻 11 号 p. 1092-1098
発行日: 1966年
公開日: 2008/04/04
ジャーナル フリーAs shown in the isothermal transformation diagram, the β′→μ transformation begins easily around the decomposition temperature; for example at 350°C, the μ-phase formation is observed after heating for 100 hr. The above-mentioned μ-fromation process both in the alloys with β′ of different Al compositions which were directly quenched from the β-range and in those which were quenched from the α+β, γ2+β range are observed mainly on the basis of the microstructure and X-ray analysis, with the following results:
(1) The μ-formation processes proceed rapidly with decreasing Al content.
(2) Both the α and γ2 phases coexist with the μ-phase in the hypo and hyper-eutectoid alloys.
(3) Eutectoid transformation by subsequent temperature rising occurs more easily in the μ-phase than in the residual β′ martensite matrix.抄録全体を表示PDF形式でダウンロード (2169K)
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