All issues
Volume 31, Issue 2
Displaying 1-20 of 20 articles from this issue
- |<
- <
- 1
- >
- >|
-
Iwao Muchi, Akira Moriyama, Junichiro Yagi, Kenji Tamura1967 Volume 31 Issue 2 Pages 97-103
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSIn order to evaluate the variations of the concentration of sulfur in molten iron in the hearth of the blast furnace, a methematical model has been derived. And the reductions of silica in slag in the upper zone from the tuyere level have been analysed in consideration of the temperature distribution of descending molten materials.
Variations of the level of molten iron and the depth of the layer of slag in the hearth can be calculated by Eqs. (12)∼(19), and those results obtained on the basis of the data of actual operations are shown in Figs. 2 and 3.
The relations between temperature of molten materials in the hearth and time are determined by Eq. (22), and an instance of the results is given in Fig. 4.
Changes of the concentration of sulfur in molten iron flowing through the layer of slag and that of sulfur in the molten iron bath can be calculated by use of Eqs. (30)∼(32) under isothermal conditions and of Eqs. (33) and (34) under non-isothermal conditions, and those results are illustrated in Figs. 4 and 5.
According to the temperature distribution along the furnace shaft, which has been described in the previous report, longitudinal variations of the concentrations of silica in slag and silicon in iron from the position of melting-down to the tuyere level are calculated by use of Eq. (40) and those results are given in Fig. 6.View full abstractDownload PDF (449K) -
Junichiro Yagi, Kenji Tamura, Iwao Muchi1967 Volume 31 Issue 2 Pages 103-109
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSTaking account of the diffusion through gaseous film, intraparticle diffusion and chemical reaction, the over-all decomposition rate of limestone is determined as the function of operating conditions. The volume rate of flow and volume fractions of CO, CO2, N2 and H2 in top gas and productions of pig iron and slag are calculated from the over-all mathematical balances of a blast furnace.
Adding to the fractional conversion of limestone and gaseous pressure as new variables, an improved mathematical model of a blast furnace is established. Basing on this mathematical model, the axial distributions of process variables such as the temperatures of gas and particles, fractional conversions of iron and limestone, volume rate of flow of gas, molar fractions of CO, CO2, N2 and H2, bulk density of burdens and gaseous pressure can be computed.
The computed results of our mathematical model applied to the actual operations of different blast furnaces are illustrated in Figs. 3∼5.View full abstractDownload PDF (1055K) -
Toyota Narita, Yasunobu Tsuji1967 Volume 31 Issue 2 Pages 109-113
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSAn attempt was made to identify oxides on 0∼2.5 wt%Be-elinvars at 800°C and 1100°C in a dissociated-ammonia gas and in air. For this, electron and X-ray diffraction methods were adopted. An X-ray microanalyser and an optical microscope were employed complementally in the observation of the oxides. The results obtained are as follows;
(1) BeO was formed selectively on the surfaces of 0.5∼2.5 wt%Be-elinvars heated in a dissociated-ammonia gas at 800°C and 1100°C for a few minutes.
(2) On the surfaces of 1.2∼2.5 wt%Be-elinvars heated in air at 1100°C for 1 hour, BeO was formed predominantly.
(3) The surfaces of 0∼1.2 wt%Be-elinvars exposed in air at 1100°C for 1 hour were covered with layer oxides—α-Fe2O3 (outer layer), spinel type oxide or (Fe, Ni, Cr)3O4 (inner layer).
(4) A thin BeCr2O4 film, in the same condition as above, spread itself on the surface of 2.5 wt%Be-elinvar, in pores of which the patches of oxides with layer structures were dispersed.View full abstractDownload PDF (947K) -
Mitsuhisa Hino, Tatsuhiko Ejima, Mitsuo Kameda1967 Volume 31 Issue 2 Pages 113-119
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe surface tension and density of liquid lead silicate have been measured as accurately as possible in the temperature range from 800° to 1200°C by means of a modified dipping cylinder method and the Archimedean method, respectively. The results obtained are summarized as follows:
The surface tension of liquid lead silicate increases with decreasing content of PbO, and the slope of the curve showing the relation between surface tension and composition changes at about the stoichiometric compositions, 2PbO·SiO2 and PbO·SiO2. The temperature coefficient of surface tension is positive in the composition range of less than about 50 mole%SiO2. However, it becomes negative when the content of SiO2 is more than the above composition range.
The negative deviation from the additivity in molar volume indicates the occurrence of the bond breaking and the production of discrete silicate anions, and minimum values are also found at about 33 and 50 mole%SiO2 in the plots of molar volume and composition.View full abstractDownload PDF (1884K) -
Tatsuhiko Ejima, Mitsuo Kameda1967 Volume 31 Issue 2 Pages 120-125
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSViscosity coefficients of liquid lead silicate and lead borate have been measured in the temperature range from 800° to 1200°C by means of the counterbalanced sphere method. The results obtained are summarized as follows:
\ oindent(1) PbO-SiO2 system
A linear relation is observed between log viscosity and 1⁄T2 isocomposition rather than the Arrhenius type plots between log viscosity and 1⁄T. The activation energy for viscous flow decreases with increasing content of PbO.
\ oindent(2) PbO-B2O3 system
A linear relation is observed between log viscosity and 1⁄T2 isocomposition as in the case of the PbO-SiO2 system. The activation energy of viscous flow slowly decreases with increasing content of PbO up to about 33 mole%PbO and then more rapidly with increasing concentration.
The density of liquid lead borate decreases with increasing temperature by a linear relation. At about 33 mole%PbO, a minimum is found in the plots of molar volume and composition.View full abstractDownload PDF (1136K) -
Toshisuke Shioya, Senichi Yamada, Yutaka Tarutani1967 Volume 31 Issue 2 Pages 126-132
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSRecently, the “Deform-quenching” method, in which steel is quenched immediately after hot working in the stable phase of austenite, has been high-lighted for its industrial application because of the resulting better mechanical properties and higher heat efficiency.
It is investigated how the “Deform-quenching” method works on the mechanical properties of steel and how its process will be. The materials used as specimens were three plain carbon steels with 0.26, 0.45 and 1.07%C. The specimens were prepared by (i) the “Deform-quenching” method, (ii) quenched and tempered after the treatments of hot working and keeping at the forge-finishing temperature for 15, 30 and 120 minutes, or (iii) normal quenching.
It was found that the steels which were subjected to the “Deform-quenching” method were much superier in hardness and mechanical properties after tempering, and the carbides were more uniformly dispersed than the steels treated by other methods for all the specimens. When the “Deform-quenched” steel was kept longer in the as-forged condition at about 900°C, the hardenability became inferior and almost disappeared in the case of quenching after keeping two hours at that temperature. It seems that the stress in forging promotes the martensite transformation and improves the hardenability of steel. That is the reason why mechanical properties in the tempered steels in the “Deform-quenching” method are improved, although the grain size of austenite grows.
When applied the same method to 99.9%Ni, the effect of work hardening remained for 15∼20 min even at a temperature of about 900°C which is higher than the recrystalization temperature. Namely, it has been found that forging effect can be retained for a fairly long time.View full abstractDownload PDF (2041K) -
Michitomo Kato1967 Volume 31 Issue 2 Pages 132-137
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSGrain boundary sliding during a constant rate heating under various constant compressive stresses of 20 kg/cm2 to 35 kg/cm2 were observed in high purity aluminium bicrystals with boundary misorientation angles of 33°37′ and 33°19′. The bicrystal specimens were prepared by the Bridgemann method. Grain boundaries were situated parallel and normal to the compressive direction. The main results obtained were as follows. (1) When grain boundaries were situated parallel to the compressive direction, grain boundary sliding increased with increasing compressive stress up to 25 kg/cm2, but when the stress increased to 30 kg/cm2, the amount of grain boundary sliding became smaller than that for the compressive stress of 25 kg/cm2. In the case of normal compression, grain boundary sliding increased with increasing compressive stress up to 30 kg/cm2. (2) Grain boundary sliding during the free compressive deformation was caused by the misorientation of component crystal for external stress. (3) Grain boundary situated normal to the compressive direction migrated well. (4) The behaviour of the deformation layer in the region adjacent to the grain boundary affected strongly the difference in activation energy for grain boundary sliding by the compressive direction.View full abstractDownload PDF (1752K) -
Ryoichi Nozato1967 Volume 31 Issue 2 Pages 137-142
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe electrical resistivity (ρ) versus temperature (T) curves have been obtained during the re-heating of Pb-0.4 wt%Mg alloys aged for various times at room temperature. The isothermal resistivity changes of the alloys have also been observed at various aging temperatures (0°∼140°C). (1) At the aging-temperatures lower than 100°C, ρ decreases in two distinct stages with aging time (t). The first and second stages of decrease of ρ can be interpreted to the formations of a G-P zone and a stable precipitate, respectively. At the aging-temperatures higher than 100°C, ρ decreases in a single stage. The decrease of ρ in this case is considered due to the formation of the stable precipitate. (2) The temperature coefficients of the resistivity dρ⁄dT versus T curves have been obtained from the ρ versus T curves, and discussed referring to the specific heat versus temperature curves obtained in the previous paper. The reversion phenomena can be detected by increase in dρ⁄dT at about 100°C on the dρ⁄dT versus T curve. (3) The activation energies for the first and second stages of the low-temperature aging are found to be about 10 and 16 kcal/mol, respectively. The activation energy for the high-temperature aging is found to be the same as the value for the second stage of the low-temperature aging. (4) The fractional change (f) of ρ with t seems to be represented by Johnson-Mehl’s equation: f=1−exp(−btn), where b and n are the constants.View full abstractDownload PDF (1683K) -
Ren Obata1967 Volume 31 Issue 2 Pages 143-147
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe relation between freezing process and shape of castings is quite important in considering the mould plan, especially in dimensioning the risers.
Studies were made on solidification of tin castings with some fundamental shapes in sand moulds by observing their cooling curves and the results of the pour-out test.
Experiments were carried out on seven castings.
The shapes of castings were as follows: (a) square bar, (b) rectangular block, (c) L shape, (d) T shape, (e) cross shape, (f) wedge shape, and (g) two rectangular blocks placed in parallel and separated by a thin core.
The results obtained were as follows.
(1) On the square, rectangular, L, T and cross shapes (each having the length/thickness ratio L/T=2∼4) the solidified volume per unit surface area of casting increased proportionally with the square root of time after pouring, but on the cross shape whose surface is a little more irregular than others, the solidification was slightly retarded. But, for these shapes, Chvorinov’s rule is considered to be applicable practically.
(2) On the wedge shape, the latent heat dissipates in the direction normal to the face of casting. As the latent heat scarecely flows out from the surface of those portions already solidified to its full thickness, the increase of solidification does not follow the square root of time, and the rate of solidification reduces gradually, and the perfunctory application of Chvorinov’s rule to the wedge shape leads to a considerable underestimation of the solidification time.
(3) On twin block casting (g) having a separation core whose thickness is sufficiently thin compared with the thickness of the block, the skin formation on the core surface was retarded by the heat from the opposite block and the square root of the solidification time of each block linearly increased with the decreasing of core thickness.View full abstractDownload PDF (961K) -
Isao Gokyu, Junji Kihara, Ikuo Ochiai1967 Volume 31 Issue 2 Pages 148-153
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSIn the previous report, it has been concluded that the hot-rolling simulation by counter-blow forging may be a successful one. The hot-worked specimens of 0.05%C-rimmed steel are 80% cold-rolled and annealed for 1 hr at 680°C. Effects of the holding time after hot working, cooling conditions and aging treatment prior to cold rolling on properties of annealed specimens are investigated.
The main results are as follows:
(1) A specimen held for some time at the hot-working temperature and water-quenched, the (222) component of the annealed specimen gradually increases with hot-working temperature, as reported by Whiteley et al.
(2) A specimen water-quenched just after hot worked, the (222) component of both cold-rolled and annealed specimen is the greatest when the hot-working temperature is about 800°∼860°C. With this condition, the hot worked specimens have a very fine grain of 8 μ.
(3) The other low index components of the annealed specimen are a little affected by the aging treatment of holding at 100°C for 40∼80 min prior to cold rolling.
(4) The Hv hardness of the annealed specimens is largely affected by the hot-working temperature and the thermal treatment after hot working. That of the specimen buenched just and non-aged after hot working or air-cooled is as low as 100 and does not depends on the hot-working temperature. On the other hand, if the specimens are held for some time at the hot-working temperature or quench-aged prior to cold-rolling, the Hv hardness of the specimens hot-worked at 860°∼910°C becomes 10∼20 higher than that of other specimens.
(5) If it is possible to cool the hot-strip coil rapidly just after passing through the final pass, the finishing temperature should be set at 800°∼860°C. If impossible, it should be set at higher temperatures than the A3 point.View full abstractDownload PDF (1492K) -
Isao Gokyu, Junji Kihara1967 Volume 31 Issue 2 Pages 154-159
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSUsing the counter-blowing type forging tester by which it is possible to compress metal specimens at various temperatures above room temperature at high strain sates of 2×102∼103/sec, the flow stress behaviours of hexagonal closed packed metals and alloys, i.e., Mg, Mg-Cd alloys, AZ-31 alloy, Ti and Zr are investigated.
The main experimental results are as follows:
(1) Flow stresses of Mg and its alloys largely depend on both temperature and strain rate from room temperature to 250°C above the strain of 0.10, on the other hand, the temperature and strain-rate dependence of flow stress is as small as that of Al below the strain of 0.10.
(2) Yielding point phenomenon occurs by dynamic recovery when Mg alloys are rapidly deformed by the strain of about 0.15 and further deformed slowly.
(3) The temperature and strain-rate dependence of flow stress for Ti and Zr is much larger than that for Al, Cu and Mg. The difference increases with strain. In the differential test (changing strain rate) at room temperature, no yield point phenomenon is observed.
(4) It is concluded that the flow stress is determined by the amount of the possible dynamic recovery during deformation in the case of Mg and its alloys (from room temperature to 250°C) and, on the other hand, determined by the frictional resistance to moving dislocation in the case of Ti and Zr (from room temperature to 600°∼800°C).View full abstractDownload PDF (928K) -
Hisashi Suzuki, Kozi Hayashi, Ichiro Kawakatu1967 Volume 31 Issue 2 Pages 160-164
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSWC-TiC-10%(Co+Ni) alloys having various contents of TiC and carbon and various ratios of Co/Ni were vacuum-sintered over a definite temperature range from 1400° to 1430°C. Their fundamental properties were studied and the results obtained were as follows.
(1) The alloys formed a three or two-phase region depending on the TiC content, in a way similar to WC-TiC-Co alloys. The width of the three-phase region for a constant TiC content, however, increased slightly with increasing Ni content in the binder. (2) Lattice parameters of the binder phase and the β phase reached constant values in the four-phase regions adjacent to the three-phase region. In the three-phase region, the former decreased and the latter increased with increasing carbon content in the alloys. (3) The amount of dissolved tungsten in the binder phase increased with decreasing carbon content and with increasing Ni content. Titanium carbide hardly dissolved in the binder phase, as observed in WC-TiC(TaC)-Co alloys. (4) Rupture strength of each three-phase alloy showed a maximum at the high carbon side. The alloys with high TiC contents were markedly strengthened with increasing Ni content in the binder. (5) Magnetic saturation of the alloys decreased with increasing Ni content. In the case of pure Ni or extremely high Ni binder, the alloys with lower carbon contents transformed to be non-magnetic. Such phenomenon had been observed also in WC-Ni alloy. (6) In short, the properties of WC-TiC-Co-Ni alloys can easily be understood in consideration of the properties of WC-TiC-Co and WC-TiC-Ni alloys.View full abstractDownload PDF (466K) -
Shogo Kanazawa, Akira Nakashima, Kentaro Okamoto, Koji Tanabe, Susumu ...1967 Volume 31 Issue 2 Pages 165-171
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe heat treated Nb-Mo steel with 80 kg/mm2 strength level, reported here, is a new type of steel which has been developed to replace the conventional T-1 type steel plate. The important feature of this steel is in the reduction of alloying elements in kind and amount. By such reduction, carbon equivalent (Ceq) in welding is much reduced and the improvement of weldability is achieved. It is rather surprising that this steel has sufficiently high strength and toughness as the 80 kg/mm2 level high strength steel in spite of such reduction of the alloying elements. It is found that this is caused by the coexistence of proper amounts of Nb and Mo. In this paper, the effects of Nb and Mo upon the mechanical properties and hardenability of new steel are evaluated.View full abstractDownload PDF (1351K) -
Shogo Kanazawa, Akira Nakashima, Kentaro Okamoto, Koji Tanabe, Susumu ...1967 Volume 31 Issue 2 Pages 171-176
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSAs already reported in the previous paper, this new steel containing about 0.03%Nb & 0.55%Mo is very unique among Nb treated steels, because it can achieve sufficiently high strength by tempering even after quenching from a rather low austenitizing temperature in the range of about 900°C. In this paper, the strengthening effect of this unique Nb-Mo steel has been analyzed and its mechanism is discussed from the view point of its precipitate.
The strengthening is found to be mainly caused by the precipitation of (Nb, Mo)(C, N), NaCl type NbC (N) containing Mo, in the process of tempering. It is also found that the amount of precipitation is greater in Nb-Mo steel than in Nb steel or Mo steel and the size of the precipitate is smaller in this new steel.View full abstractDownload PDF (1354K) -
Katsuya Kudaka, Hiroshi Konno, Toshio Matoba1967 Volume 31 Issue 2 Pages 177-182
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSWC powder and WC-Co mixed powder (Co 1.5 and 6 wt%) were sintered at 15∼45 kbar and 800°∼1800°C under high pressure and temperature, respectively. As sintering temperature increases, the hardness of the sintered bodies increases and then decreases after attaining a maximum value. The obtained hardness was an appreciably high value of 2500∼3000 kg/mm2 in micro-Vicker’s hardness. The increase in hardness is mainly due to the adhesion between particles, the inhibition of grain growth and the increase of microstrain in crystals, whereas the decrease in hardness is mainly due to grain growth and the relaxation of strain by high temperature.
Sintering processes of WC powder and WC-Co mixed powder under high pressure are divided into the following three sintering temperature stages. In the 1st stage, no adhesion between partices nor grain growth occurs and consequently no increase in hardness is observed. In the 2nd stage, the adhesion between particles proceeds, but grains hardly grow and the hardness increases to attain a maximum value. In the 3rd stage, grains considerably grow and the hardness decreases. In the sintering of WC-Co mixed powder, the 3rd stage is above the eutectic temperature of about 1350°C, which is almost independent of the Co content and pressure. Sintering of WC-Co mixed powder proceeds mainly by plastic flow in the 2nd stage and by solution-precipitation in the 3rd stage. In the sintering of WC powder, the 3rd stage remarkably shifts to high temperature with pressure. The sintering proceeds mainly by plastic flow in the 2nd stage and by diffusion in the 3rd stage.View full abstractDownload PDF (1108K) -
Isao Gokyu, Kunio Ito1967 Volume 31 Issue 2 Pages 183-189
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSStrips which were cut out obliquely with respect to the first rolling direction from the straightly rolled sheets were rolled further after intermediate annealing or directly without intermediate annealing.
The intensities of X-ray diffractions were measered to study the changes in the textures of the finally annealed sheets. X-ray pole figures were determined for the typical textures. The height of ears developed by a cupping test and the conical cup values were also measured.
The textures produced by the oblique rolling can be explained with the data known for the rotation of the orientation of single crystals during rolling, when the textures formed by the treatments prior to the oblique rolling are considered as the initial orientations.
In the annealing textures of the sheets which are obliquely rolled without intermediate annealing, the components of which (100) planes are parallel to a sheet surface are poor, while the components of which (100) planes are tilted by 15∼20 deg from a sheet surface are rich.
The pole concentrations near (110)[001]∼(210)[001] orientations in the final annealing texture are dispersed widely by the oblique rolling with intermediate annealing.
Corresponding to the changes in the annealing textures, the developement of the ears by the cupping test is markedly lowered by the oblique rolling with intermediate annealing. The conical cup values are, however, not improved by the oblique rolling in the range of the present treatments.View full abstractDownload PDF (512K) -
Shigeo Horiuchi, Tadatsune Okubo, Isao Gokyu1967 Volume 31 Issue 2 Pages 189-194
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe variation of the texture during annealing of 7-3 brass cold rolled by 93% was examined by quantitative pole figures. The {225}⟨734⟩ major and the {110}⟨110⟩ minor components were formed on annealing at about 300°C due to the primary recrystallization, the {110}⟨110⟩ major and the {110}⟨112⟩ minor components on annealing at 600°C, and the {110}⟨112⟩ major and the {110}⟨110⟩ minor components on annealing at 800°C due to the grain growth.
The rotation relationships between growing grains and consumed matrix were calculated by an electronic computer. The variation of the texture can be accounted for on the assumption that ⟨111⟩ 30° rotation relationship gives rise to the preferential growth of the grain and also in consideration of the loss of grain boundary energy.View full abstractDownload PDF (948K) -
Shigeo Horiuchi, Tadatsune Okubo, Isao Gokyu1967 Volume 31 Issue 2 Pages 195-199
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSQuantitative X-ray pole figures of α and β phases in 6-4 brass cold-rolled 93% and annealed at the temperature less than 800°C were obtained. Pole figures of the α phase were similar to those of 7-3 brass under the same treatment, that is, the orientations were {110}⟨112⟩ after rolling, {225}⟨734⟩+{110}⟨110⟩+{210}⟨121⟩+{110}⟨112⟩ after annealing for 30 min at 300°C and {110}⟨110⟩+{110}⟨112⟩ after annealing for 30 min at 600°C. The β phase had a sharp {111}⟨112⟩ orientation after rolling and kept almost the same orientation after annealing for 30 min at 300°C, even after the softening due to recovery. It recrystallized on further annealing for 30 min at 600°C and had the double components, {112}⟨110⟩ with a rotational spread of ±15° about R. D. and {111}⟨112⟩.
It was confirmed by use of a computer that there always existed the rotation relationships of high angle about the axes near ⟨110⟩, ⟨111⟩ and ⟨100⟩ between {111}⟨112⟩ of the deformed matrix and {112}⟨110⟩ with the rotational spread of ±15° about R. D. of the recrystallized grains.View full abstractDownload PDF (360K) -
Yoshimoto Wanibe, Kôkichi Sano1967 Volume 31 Issue 2 Pages 199-203
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSThe present work attempts to investigate the comprehensive effect of the initial oxygen content in liquid iron on the formation of the layer-like inclusions group. Therefore, the experiments were carried out by dropping an aluminum bar onto the static liquid iron, containing the variously controlled oxygen content. The oxygen content in the liquid iron was also reduced by additions of carbon and chromium and the effects of both elements on the formation of the group was investigated with the naked eye and by the microscope. The results obtained are as follows:
(1) It is now confirmed that when the initial oxygen content is reduced, the inclusions group is not formed as expected in the previous report.
(2) The effects of carbon and chromium on the formation of the inclusions group were investigated. Though the oxygen content, controlled with chromium, is relatively high, this group is not formed. This phenomenon was discussed in the light of the effect of chromium on the activity of oxygen dissolved in liquid iron. The activity of oxygen needed for the formation of this group is shown to be more than 0.03.
(3) Then, the phenomenon that the inclusions group is not formed in the specimens of low oxygen content was discussed from the viewpoint of the V-W-B-D theory of nucleation. With decreasing oxygen content, the interfacial energy between liquid iron and solid alumina is increased remarkablely and the supersaturation necessary for the nucleation of the alumina inclusion is so great that the group cannot be formed.View full abstractDownload PDF (474K) -
Seita Sakui, Nobuhiko Abe, Kimiko Sato1967 Volume 31 Issue 2 Pages 204-205
Published: 1967
Released on J-STAGE: April 04, 2008
JOURNAL FREE ACCESSDownload PDF (131K)
- |<
- <
- 1
- >
- >|