巻号一覧
39 巻, 3 号
選択された号の論文の17件中1～17を表示しています
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関野 昌蔵, 藤島 敏行1975 年 39 巻 3 号 p. 213-220
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーTwo kinds of pure iron of commercial grade were heat-treated to have different grain size, hydrogen-treated and N or C charged, the content of which was measured by the Snoek peak height. Strain aging index (SAI) was measured by 7.5% straining and aging. In this case the aging conditions, strain rates, and N or C content were changed. The following conclusions were obtained. SAI increased sharply from zero when N content increased from zero to about 10 ppm, and became almost constant when N content was over 20∼40 ppm. On the other hand, SAI continued to increase with the increase of C content even when it was over 20 ppm. As regards the effect of aging temperature and time, SAI showed a maximum at 20 min at 100°C, no maximum being attained even at 300 hr at 50°C. SAI increased with strain rate, but the degree of increase was larger, the larger the grain size and the higher N or C content. When N or C content was less than 10 ppm, the grain size showed almost no effect on SAI, but in the range of higher N or C content, SAI was larger, the finer the grain size. As to the effect of annealing and furnace cooling on SAI in the case of only C, SAI was dependent largely on the interstitial C remaining in that state after the annealing and furnace cooling.抄録全体を表示PDF形式でダウンロード (668K) -
関野 昌蔵, 藤島 敏行1975 年 39 巻 3 号 p. 220-224
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーSteels containing Mn were heat-treated to have different grain size, hydrogen-treated and N or C charged, the content of which was measured by the Snoek peak height. Strain aging index (SAI) was measured by 7.5% straining and 100°C×1 hr aging. In this case, strain rates, and N or C content were changed. The following conclusions were obtained. SAI increased sharply from zero when N content increased from zero to about 10 ppm in 0.3%Mn steel, and it became almost constant when N content was over 20∼40 ppm. SAI increased sharply from zero, when C content increased from zero to under 5 ppm, and it continuously increased with increasing C content, and after passing through a maximum, decreased. The content corresponding to the maximum of SAI, shifted to lower C content when the grain size was larger and the strain rate lower. The effect of Mn content on SAI was small in N-charged 0.3%Mn steel. In the case of C, sometimes 2∼3 kg/mm2 SAI was observed even when the Snoek peak height was zero, and in a range of higher C content, SAI tended to decrease with increasing C content. This behavior was different from that observed in the pure iron.抄録全体を表示PDF形式でダウンロード (371K) -
関野 昌蔵, 藤島 敏行1975 年 39 巻 3 号 p. 224-232
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーTwo kinds of pure iron of commercial grade were heat-treated to have different grain size, hydrogen treated and N or C charged, the content of which was measured by the Snoek peak height. Keeping N and C in solid solution, the yield and flow stresses were measured at varying strain rate and temperature. The following conclusions were obtained. In the N-charged specimens, with a grain diameter of 60 μ, the yield stress increased sharply with the increase of N content from zero to 40 ppm, beyond which it increased slightly in proportion to N content. In the sample of grain diameter 700 μ, it increased nearly in proportion to N content from zero N. In the C-charged specimens, with a grain diameter of 30 μ, the yield stress showed a maximum at about 60 ppm, while with a grain diameter of 700 μ, it increased nearly in proportion to C content from zero C. The grain size dependency of yield stress increased sharply with the increase of N content from zero up to 30 ppm, beyond which it increased slightly. In the case of C, the dependency showed a maximum at about 50 ppm C content. As to the strain-rate dependency, both yield stress and flow stress increased with strain-rate, their absolute values decreasing with N or C content. As to the effect of temperature, these stresses increased greatly as the temperature decreased, the major portion of which was strain-rate dependent. Under 250°K, the effect of about 30 ppm N or C content was little. The data was analyzed by Conrad’s theory and the activation energy and pre-exponential term were determined.抄録全体を表示PDF形式でダウンロード (596K) -
白石 春樹, 坂入 英雄, 八木 栄一, 唐沢 孝, 橋口 隆吉, 渡辺 亮治1975 年 39 巻 3 号 p. 233-239
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーThe growth process of helium bubbles in α-particle bombarded pure aluminum during isothermal anneal ranging 200 to 645°C and 1 to 100 hr was observed by a transmission electron microscope and the possible growth mechanisms are discussed. The effects of helium concentration and cold work were investigated.
The helium bubbles are detectable only at the anneal above 550°C in both annealed and cold worked samples. The cold work does not cause any extra coarsening trend of bubbles. The observed types of bubble distribution in the grain interior are divided into two categories, irrespective of helium concentration and cold work; (1) the fine and uniform bubble distribution, in which case the average size is limited to about 200 Å or less in diameter even at the anneal just below the melting point, and (2) the coarsened and non-uniform bubble distribution ranging 500 to 4000 Å in diameter. The intermediate size bubbles are scarcely found in any cases.
In the above fine bubble distribution, the increase of helium concentration by a factor of two increases the density by the same factor of two, but does not change the mean size of bubbles.
Corresponding to the above two characteristic bubble distributions, it is concluded that two different mechanisms are operative in this experiment; (1) the growth of bubbles by the Brownian motion, in which the growth rate of bubbles is decreased to almost zero by bubble faceting and this results in the bubble size constancy during the prolonged annealing, and (2) the growth of bubbles by the grain boundary sweep-out mechanism, by which the abrupt coarsening of bubbles is caused. The lack of existence of the intermediate size bubble is explained in this way.抄録全体を表示PDF形式でダウンロード (789K) -
小林 正樹, 植田 安昭, 野口 文男1975 年 39 巻 3 号 p. 240-246
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーCuO pellet is chloridized with HCl-Ar mixture gas in the temperature range of 600 to 900°C and the rate of chlorination was measured by the thermobalance. On the other hand, the reaction process was analyzed by using the mass transfer model which was considered the controll mechanism of chloride volatilization. The experimental results were compared with the calculated values from the mass transfer models. The results obtained are summarized as follows.
(1) Under the small gas velocity and the low HCl partial pressure, the reaction of chlorination is controlled by transport of HCl through the gas film boundary layer at the surface of the sample. Calculated rate from the product of HCl partial pressure and the gas velocity agreed well with the results obtained experimentally.
(2) However, the reaction is controlled by the diffusion of HCl gas with an increase of chloridizing temperature. The experimental results could be analyzed by using the model which was considered only the forced convection.
(3) At the high HCl partical pressure and the large gas velocity, the rate is controlled by the vaporization of Cu2Cl2 (1). The rate was calculated by the mass transfer equation which was considered the forced convection and the natural convection of Cu3Cl3 (g). Activation energies obtained by each models agreed very well with the values obtained from experimental data. Calculated values were given 2.8 kcal/mol in the diffusion controlling step, 21.3 kcal/mol (at the forced convection) and 23.2 kcal/mol (at the natural convection) in the vaporization controlling step of Cu2Cl2 (1).抄録全体を表示PDF形式でダウンロード (591K) -
新井 透, 水谷 正義, 小松 登1975 年 39 巻 3 号 p. 247-255
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーTo investigate the surface layers of steels immersed in various kinds of borax baths, steels were kept in the borax bath containing powders of pure metals, alloys, carbides, oxides and nitrides of such elements as Ca, Si, Al, Mn, R are earth, Mg, Zr, Ti, V, Nb, Cr, Zn, Co, Ni and Cu, and their surfaces and cross sections were examined by microscopy, X-ray diffraction and electron probe microanalyses.
The results obtained are summarized as follows.
(1) Iron boride layers were formed on 0.1%C steel specimens treated in the bath containing pure metal powders of Ca, Si, Al, rare earth, Mg, Zr or alloys powders.
(2) In the bath containing a large amount of Fe-Ti or Fe-Mn powders, Ti or Mn carbide layers were formed on high C steel specimens, while iron boride layers were formed on low C steel specimens.
(3) In the bath containing Fe-V or Fe-Nb powders, V or Nb carbide layers were formed on 0.1%C steel specimens.
(4) In the bath containing Fe-Cr powders, double layers of Cr carbide (outer) and Fe-Cr solid solutions (inner) were formed on 0.1%C steel specimens.
It may be concluded from the results that the tendency to form boride layers is greater in a fused borax bath containing metal powder with a higher free energy change (−ΔG) of the oxide formation than that of boron oxidation.抄録全体を表示PDF形式でダウンロード (1174K) -
井口 信洋, 横田 清義, 三輪 敬之1975 年 39 巻 3 号 p. 255-261
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーIn the present study α+P→γ transformation behavior in the various carbon steels over the range of up to 107°C/sec super-rapid heating was investigated in the same method as previously employed for eutectoid steel.
The main results obtained are as follows:
(1) The increments of transformation temperatures from the equilibrium points (Ac1, Ac3) in various carbon steels with increasing heating rates (up to 107°C/sec) were determined. Ac3f transformation curves of varioud hypoeutectoid steels are disconteniously jumped in two steps (0.1%C: 150°C/sec, 0.3%C: 250°C/sec, 0.5%C: 1000°C/sec), and with increasing heating rate, the curve approximated to the Ac3f point of pure iron.
(2) A non-equilibrium phase diagram for less than 1.4%C steel was shown. In this diagram Ac3f line is flat (=1130°C) and independent of the carbon contents at the heating rate of 106°C/sec.
(3) In the α+P→γ super-rapid heating transformation of hypoeutectoid steels there takes place two processes; i.e. one is the P→γ diffusion process and the other is the α→γ diffusionless process, the former is the remained phase due to super-rapid heating.抄録全体を表示PDF形式でダウンロード (615K) -
吉岡 正三, 中山 豊, 伊藤 太一郎, 間渕 博1975 年 39 巻 3 号 p. 261-267
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーCu-Si alloy single crystals having various orientations were studied with respect to their deformation twinning behavior by tensile tests in the temperature range from −196 to 300°C. The results obtained are summarized as follows.
(1) The temperature and orientation dependences of the occurrence of twinning in Cu-Si alloy single crystals are in agreement with the previously known results of fcc crystals.
(2) When the stress for twinning is reached, a macroscopic band of twin forms, accompanied by an abrupt load drop on the stress-strain curve, and thereafter the band of twin grows jerkily (so-called serration) until the twinned region fills the specimen. The abrupt load drop and serrations vary with the deformation temperature and the composition in a way which is connected with the types of formation and propagation of the band of twin.
(3) In Cu-5.0 at%Si alloy single crystals of suitable orientation deformed at −196°C, twinning occurs even though the stress-strain curves do not show serrations, and in this case the onset of twinning is characterized by a knee in the stress-strain curve.
(4) It has been observed by transmission electron microscopy that the band of twin contains many individual fine twin lamellae, and the width of these lamellae is almost less than 0.2 μ.
(5) Twinning occurs on the primary or conjugate slip plane; and it appears that twinning predominantly takes place on the plane with higher resolved shear stress.抄録全体を表示PDF形式でダウンロード (676K) -
岩井 正雄1975 年 39 巻 3 号 p. 268-273
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーThe effect of halogen ion on the anodic dissolution of galena in dilute sulfulic acid solution was studied by means of the potentiodynamic and galvanostatic polarization method and electrondiffraction. The experimental results obtained are as follows:
(1) Galena shows an active-passive behavior similar to the lead electrode in sulfuric acid solution and the surface film formed on the galena electrode in the solution is a lead sulfate and shows a characteristic behavior of ionic conductors.
(2) The anodic dissolution of galena in the sulfuric acid solutipn containing halogen ion increases with increasing concentration of halogen ion in the solution in the following order Cl−>Br−>I−>no addition.
(3) The surface film formed on the galena electrode in the sulfuric acid solution containing Br− and Cl− is a lead sulfate and shows a characteristic behavior of ionic conductors.
(4) The acceleration of the reaction in anodic dissolution of galena in the solution containing halogen ion is caused by the “effect of anion” that the electrode interface is activated by halogen ion and the formation of halide complex.抄録全体を表示PDF形式でダウンロード (473K) -
増本 健, 木村 博1975 年 39 巻 3 号 p. 273-280
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーThe crystallization process of an iron-base amorphous alloy (Fe-P-C) was studied by means of electrical resistivity and differential specific heat measurements, transmission electron microscopy and X-ray diffraction, and the transformation sequence from the amorphous state to the crystalline state was clarified together with the precipitation morphology of the metastable and stable phases.
The main results obtained are as follows:
(1) The crystallization process of the amorphous Fe-P-C alloy is divided into four stages: (a) the stage of incipient crystallization where the short range ordering of atoms is considered to occur in the amorphous phase, (b) the formation of a metastable bcc phase (MS-I) with lattice constant a0=2.87 Å, (c) the formation of second metastable phase (MS-II) with complex structure, and (d) the formation of stable phase consisting of a mixture of α-Fe, Fe3P and Fe3C.
(2) A number of microcrystallites of the MS-I phase disperse homogeneously in the amorphous matrix. They have a cubic shape with the size 100 to 500 Å at temperatures above about 350°C. The precipitation is induced by the homogeneous nucleation and the crystal growth is extremely slow. After prolonged aging the size and number of the crystallites remain constant. The crystals of MS-II phase appear in the amorphous matrix with an oval shape at about 430°C and has a lath martensite-like internal structure. They grow rapidly from a few nuclei and completely spread over the amorphous matrix containing the MS-I phase. Above about 450°C, the MS-II phase transforms to the stable phase.
(3) The prolonged aging at a temperature lower than about 350°C or a relatively lower cooling rate from the liquid state changes the amorphous structure to a bcc structure.抄録全体を表示PDF形式でダウンロード (1044K) -
増本 量, 比内 正勝, 村上 雄悦1975 年 39 巻 3 号 p. 281-284
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーNi-Fe-Ta-Mo alloys were heated in hydrogen atmosphere at 1150°C for 3 hr and then cooled at rates of 0.75∼1400°C/hr from a temperature above order-disorder transformation point. The highest initial permeability of 120000 are obtained for the alloy of 74.35%Ni, 11.35%Fe, 13.85%Ta and 0.45%Mo cooled at the rate of 300°C/hr, and the highest maximum permeability of 610000 for the alloy of 74.20%Ni, 11.22%Fe, 13.96%Ta and 0.62%Mo cooled at 240°C/hr. The alloy with the highest initial permeability exhibited the electrical resistivity of 69.7 μΩ-cm, its Vickers hardness being 199. The high permeability Ni-Fe-Ta-Mo alloys showed the very low values of magnetostriction constant in a proper state of ordering.抄録全体を表示PDF形式でダウンロード (301K) -
辻本 得蔵1975 年 39 巻 3 号 p. 285-292
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーThe aging process in a Cu-4%Ti alloy during aging at 300∼600°C has been studied by means of X-ray small-angle scattering (SAS) and X-ray side-bands.
By the analysis of the SAS data, the aging process was subdivided into the four stages I∼IV: In stages I and II, the integrated intensity Q0 and Guinier’s radius of gyration Rg increased with aging time. For stage II the rates of increase in Q0 and Rg became larger than those observed for stage I. In stage III Q0 remained constant, but for stage IV it decreased with an increase in aging time. At aging temperatures above 400°C, stage I was not observed.
The corresponding behaviour of the main diffraction lines was as follows: In stage I the main diffraction lines did not move at all but in stage II they moved to a high angle side during aging. In stage III, they disappeared or coincided with the diffraction lines of the α2 phase.
Models of the concentration variation in the above-mentioned stages are discussed. The relationship between the stage I–II transition and the interdiffusion coefficient is described.抄録全体を表示PDF形式でダウンロード (674K) -
江島 辰彦, 小笠原 正俊1975 年 39 巻 3 号 p. 293-297
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーDensity of the MgCl2-KCl binary melt has been measured as accurately as possible by means of the Archimedean method with two spherical sinkers of different sizes made of platinum. The results obtained are summarized as follows:
(1) The density decreases monotonously with rising temperature at each composition. The temperature coefficient of density for MgCl2 is considerably low, but those for KCl and MgCl2-KCl mixtures are nearly the same.
(2) The variation of the density at liquidus temperature with composition is well corresponding to the liquidus line of the phase diagram except on the MgCl2-rich side.
(3) The molar volume calculated from the density at 800°C deviates negatively from the additivity for the compositions less than 30 mol%KCl, and shows a positive deviation in the remaining range.
(4) The excess molar volume at 800°C shows a minimum at about 17 mol%KCl and a maximum at about 67 mol%KCl.
(5) The values of the partial molar volume of KCl at 800°C are considerably low on the MgCl2-rich side, but are approximately constant on the KCl-rich side. On the other hand, the partial molar volume of MgCl2 changes monotonously on the MgCl2-rich side, but it begins to increase at about 60 mol%KCl and becomes constant in the range more than 80 mol%KCl.
These trends are explained by the change of the ionic constituents.抄録全体を表示PDF形式でダウンロード (408K) -
上村 正雄, 木川 泓, 川辺 秀昭, 山田 朝治1975 年 39 巻 3 号 p. 298-305
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーTo clarify the factor governing the directionality of fatigue behavior of 90% cold-rolled tough pitch copper, the surface structures are observed through optical and replica electron microscopy, and the fatigue phenomenon is discussed taking the {111} pole figure into consideration.
The following results are obtained:
(1) In the higher stress amplitude region with respect to the fatigue life about 106 cycles, the fatigue life of a test piece taken in the transverse direction to the rolling direction is longer than in the parallel direction. On the other hand, in the lower stress amplitude region the latter has a longer fatigue life than the former.
Due to the difference in fatigue lives, the structure of slip bands changes from coarse slip bands in the higher stress amplitude region to island-like slip bands in the lower stress amplitude region.
(2) In the higher stress amplitude region, the fatigue crack emerges as the slip band crack along the coarse slip band. In the lower stress amplitude region, however, fatigue crack emerges in the island-like slip band in the similar process as in the annealed specimen.
(3) Directions of the coarse slip band and the slip band crack correspond very well with those predicted from the {111} pole figure of rolled copper. Thus the directionality in the fatigue behavior in the higher stress amplitude region can be explained qualitatively from the {111} pole figure of the rolled specimen.
(4) On the other hand, in the island-like slip band very fine slip bands emerge in the direction predictable from the cube texture, so that in the process of crack emergence the directionality is not found. In this case the directionality of the fatigue strength can be explained mainly by the shape of grains elongated by rolling.抄録全体を表示PDF形式でダウンロード (1152K) -
姜 文圭, 内田 熊男, 井本 正介1975 年 39 巻 3 号 p. 305-311
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーThe hydrolytic behavior of Hafnium mononitride and monocarbide has been studied and compared with that of Titanium and Zirconium nitrides and carbides.
In the case of hydrolysis of HfN the gaseous products were H2, N2 and a small amount of NO, and the liquid product was NH3, as in the case of TiN and ZrN. In isothermal hydrolysis the principal product was NH3 at temperatures lower than 800°C, which was replaced by N2 at temperatures higher than 900°C. In this respect HfN was similar to ZrN, but not to TiN which produced mainly N2 even by hydrolysis at 800°C.
The products of hydrolysis of HfC were found to be CO, CO2, H2 and a small amount of CH4 also as in the case of TiC and ZrC. In the isothermal hydrolysis of HfC it was observed that a large amount of H2 evolved at the early stage of the hydrolysis while CO2 continued to evolve with some amount of H2 even after the ceasing of CO evolution. From analysis of the hydrolytic behavior the solid residue after the hydrolysis of HfC was considered to contain some waxes (CnHm).
It was suggested that the carbide of the element of smaller atomic number (Ti) would tend to form oxygen compounds (CO, CO2) while the carbide of the element of larger atomic number (Zr, Hf) hydrogen compounds (CnHm), since ThC and UC formed only hydrocarbons and H2 by hydrolysis. This suggestion was also valid to nitride.抄録全体を表示PDF形式でダウンロード (521K) -
石井 仁, 藤村 全戒1975 年 39 巻 3 号 p. 311-317
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーTo elucidate the brittleness observed in high Cr ferritic steels quenched from a high temperature, tensile behavior was studied on 11 kinds of specimens whose Cr contents ranged from 17 to 30% and were annealed at various temperatures between 700 and 1250°C for 1 hr, followed by water quenching or furnace cooling. Principal findings were as follows. (1) The specimens water-quenched from a temperature above 900°C showed an increase in tensile strength and a decrease in elongation as the annealing temperature increased, irrespective of the increase in grain diameter. This tendency was not so marked in specimens with very low (C+N) contents. Furthermore, in some of the specimens water-quenched from a temperature above 1100°C the tensile strength started decreasing as the annealing temperature increased, and there were cases where the above-mentioned two opposing tendencies were observed even in the same specimen. However, in the furnace-cooled specimens the change in tensile behavior due to annealing temperature was quite normal and the yield stress followed the Hall-Petch equation. (2) Water-quenched specimens showed larger yield stress increments to the same strain aging treatment and also a more pronounced P-L effect when deformed above room temperature than the furnace-cooled ones. (3) Tensile behavior of the water-quenched specimens came close to that of the furnace-cooled one when reheated at about 600°C. (4) Tensile behavior of high Cr steels can be interpreted in terms of solution hardening by C and N atoms.抄録全体を表示PDF形式でダウンロード (1107K) -
横堀 武夫, 沢木 洋三, 庄野 四郎, 熊谷 彰善1975 年 39 巻 3 号 p. 317-325
発行日: 1975年
公開日: 2008/04/04
ジャーナル フリーOne of the authors has made an investigation of the fatigue microcrack initiation and propagation leading to final fracture in plain carbon steel and low carbon tempered martensitic high strength steel using the plastic replication method and a scanning electron microscope. As a part of this study, the present investigation was undertaken to make clear the nature of fatigue crack in high strength eutectoid steel.
It is found that almost all the fatigue microcracks arise from the aluminum oxide-type inclusions. The initiation of these microcracks occurs at only 5∼20% of the total life and its behavior of propagation shows that the microcrack generated from severe stress concentrated inclusion joins the other originating from an other inclusion, but the former is preferentially grown to the degree of considerable size and finally leads to eventual fracture. The fatigue crack propagation towards the inside of the specimen is revealed to occur in the semicircular form with the inclusion as the center.
The fatigue crack propagation rate obeys the power relation, dc⁄dN=A(ΔK)δ where δ=1.8. Comparison between this result and that of plain low carbon steel and low carbon tempered martensitic high strength steel reveals that the strength level becomes higher the lower the fatigue crack propagation rate. As for the value of δ, it decreases with increasing strength level. This trend is in accord with the kinetic theory of fatigue crack propagation proposed by Yokobori.抄録全体を表示PDF形式でダウンロード (1019K)
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