巻号一覧
24 巻, 12 号
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網谷 俊男1960 年 24 巻 12 号 p. 765-769
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe problem of the anisotropic properties of aluminium sheets is regarded as of great importance to makers because of the “earing” phenomena which occur during deep drawing. Experiments were carried out to study the effect of preheating ingots on the anisotropy and recrystallization texture of the annealed aluminium sheets. By the present investigation the following results were obtained: (1) In the aluminium sheet which was hot- and cold-rolled from the ingot without any intermediate annealing treatment, the recrystallization texture and the anisotropy of the annealed sheet depend on the preheating temperature and time before rolling. (2) The above effect of preheating was not observed in high purity aluminium, but in commercial aluminium. This implies that the effects are concerned with the impurity elements in the aluminium ingots. (3) When a commercial purity aluminium ingot was preheated and rolled the recrystallization texture of the annealed sheet retained most of the main component of the rolling texture (123)[1\bar21], and this results in a 45° earing by deep drawing. When the ingot was not preheated, the second orientation (100)[001] appeared and a 90° earing was observed. (4) It was revealed by microscopic observation and electric resistance measurement that the precipitation of impurities is introduced by the preheating treatment of the ingot. It may be possible to conclude that the changes in the anisotropy and the recrystallizating texture are induced by the precipitation of the impurities when the ingot is preheated.抄録全体を表示PDF形式でダウンロード (902K) -
網谷 俊男1960 年 24 巻 12 号 p. 769-773
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーWhen rolled aluminium sheets of different purities were annealed at various temperature and time, the following results were obtained from the investigation of the relations among the recrystallized grain size, the change in the texture and the anisotropy. (1) Immediatly after the specimens have recrystallized, the texture of the small recrystallized grains of annealed high-purity aluminium contains most of the component of the (123)[1\bar21] rolling texture, so that earing appears at 45° to the rolling direction by deep drawing. When the recrystallized grains grow as the annealing proceeds, the second orientation (100)[001] develops and earings change from 45° to 90° with respect to the rolling direction. (2) In the case of commercial-purity aluminium, the impurity atoms restrict the growth of the recrystallized grains, so that the grains do not grow as the result of successive annealing, and, there is no change in the anisotropy. The most effective impurity element was iron (the content of iron should be more than 0.3 per cent), but silicon included as impurity had no effect on the growth of grains and the change in anisotropy. It may be inferred from the above results that when a small quantity of metalic elements is added to restrict the growth of recrystallized grains, the the texture and the anisotropy do not change.抄録全体を表示PDF形式でダウンロード (868K) -
藤原 達雄, 加藤 哲男1960 年 24 巻 12 号 p. 773-777
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーMagnetostrictions in Alnico 5 magnet were measured by means of a strain gauge. Magnetostriction remarkably depends on the direction of heat-treatment in magnetic field—tendency similar to that in other metals. Then by aging at 600°C, magnetostriction decreases on the whole at a direction perpendicular to the field of heat-treatment in magnetic field and in heat-treatment without magnetic field, and conversely, increases at a direction parallel to the field treatment. This is an interesting phenomenon for discussion of the structure of such materials. A faster cooling after fusion causes an increase in magnetostriction. The starting ponit of magnetostriction curve shifts to the side of lower magnetizing force, which is a property in soft magnetic material. In this state, powder patterns can be observed. A heating at 900°C, or a temperature between 1000° and 1200°C at which γ phase is produced, causes a magnetostriction curve distinctly different from that after heating at 950° or 1300°C which are solution temperatures.抄録全体を表示PDF形式でダウンロード (758K) -
森永 卓一, 後藤 武夫, 高橋 恒夫1960 年 24 巻 12 号 p. 777-781
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーIn order to clarify an unsatisfactory hardening characteristic observed in some melts of commercial Cu-Be alloys, four kinds of specimens of similar composition were prepared; three of them were arranged as industrial scale experiments under different procedures assigned, the other specimen was imported as a commercial strip from Beryllium Corp’n U.S.A. The hardness changes with aging time were examined together by microscopic observation, and then discontinuous precipitation at the initial stage was observed by electron micrography. The results were as follows: (1) When aged at 310°C the specimen “Z” showed considerable rapid hardening at the initial stage, followed by rapid softening, whereas in the imported Alloy B no such trend was observed up to 6 hrs, and in the other two specimens slight but not serious softening was observed. (2) Overaging is associated with rapid initial hardening rate and with subsequent development of the nodules, which appeared as small semi-spheres or narrow bands at grain boundaries. (3) As aging proceeds the nodules spread into the matrix as well as along grain boundaries, then several nodules join together forming continuous net works around the grains. (4) At the advancing interface lamellar precipitates in the nodule are continuous with undercomposed matrix, but they break away from the matrix and sometimes spheroidize at the location apart from the interface.抄録全体を表示PDF形式でダウンロード (1254K) -
立川 逸郎1960 年 24 巻 12 号 p. 782-785
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe length changes in hot-bath quenching both above and below the Ms temperature and aging at room temperature as well as in tempering of a 0.8%C steel were measured. The experiment has revealed the following: The expansion in hot-bath quenching at the martensitic range, of 200°C-1 hr or 180°C-5 hr, in which a mixed structure of lower-bainite and tempered martensite containing a lot of retained austenite is formed, is much smaller than that in ordinary quenching or martempering, and then, during the subsequent aging at room temperature a comparatively large expansion occurs with time in these hot-bath quenched specimens as a part of the retained austenite decomposes into martensite. The retained austenite is more stabilized in consequence of the proceeding of the lower-bainite reaction, but does not decompose at room temperature, causing little change in length.抄録全体を表示PDF形式でダウンロード (719K) -
栂野 秀夫, 大里 一夫1960 年 24 巻 12 号 p. 786-790
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーAssuming that shot-peening leaves compressional stress on metallic surface and may cancel out the harmful tensile stress, the effect of this operation against stress-corrosion cracking of stainless steels was investigated experimentally. A weak peening was practically ineffective, but beyond a degree of peening, stress-corrosion cracking was reduced. A fair success was achieved at the level of peening where “coverage” was 90∼100%, and “archeight” was 0.013∼0.015 A. It is supposed that the uneveness of shot-peened surface may be harmful from the standpoint of general corrosion, but the corrosion resistance of shot-peaned stainless steels did not deteriorate except in corrosive environments which were capable to activate stainless steels.抄録全体を表示PDF形式でダウンロード (731K) -
三戸 暁1960 年 24 巻 12 号 p. 790-794
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーKovar alloy now being used for glass sealing consists of a single γ phase at room temperature. But according to the phase diagram, two phases of α and γ may exist in the equiliburium state. Therefore when its Ms point is not so low under room temperature, the transformation from γ to α phase may take place during cold-working and may cause a decrease of workability by abnormal hardening. In this experiment the characteristics of work-hardening in unstable Kovar were examined by measuring the change of hardness with rolling and the stress-strain curve in tensile tests. An abnormal hardening was observed after about 40∼50% reduction in specimens with low nickel content. The hardening degree of such specimens was about 100%, while it was about a half in specimens with high nickel content, after about 80% reduction. The former specimens also showed about 40% increase of hardness by a low temperature annealing and a slight softening by a cold treatment. A nickel content over 29∼29.5% was necessary to prevent Kovar from hardening by transformation during cold-working.抄録全体を表示PDF形式でダウンロード (815K) -
加藤 栄一1960 年 24 巻 12 号 p. 794-797
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe extraction of hydrogen from white and high-silicon cast iron (Si∼14%) at 1000°, 1250° and 1650°C has been studied. The extracted hydrogen was separated from other gases by the aid of a palladium tube: this apparatus is capable of measuring both the evolution rate and total volume of hydrogen. Hydrogen diffused rapidly through the palladium tube at 800°, and most of the methane decomposed into carbon and hydrogen, the latter being able to diffuse through the tube. The diffusion rate of CO and N2 were negligible. It is showen that the vacuum heating technique at 1000°C can be applied to the determination of hydrogen in white and high-silicon cast iron. Addition of small amount of titanium (1.37%) or tellurium (0.3%) had no effect on the results.抄録全体を表示PDF形式でダウンロード (567K) -
西村 山治, 森山 徐一郎, 久島 亥三雄1960 年 24 巻 12 号 p. 798-802
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe behavior of the impurities, Sn, Ti, Fe, Si etc., in liquid-liquid solvent extraction of Ta and Nb with organic solvent is very important in the production of high purity Nb and Ta. The authors investigated the behavior of Sn in four systems of Ta and Nb solvent extraction, namely, with HF-hexone, HF-HCl-hexone, HF-H2SO4-hexone, and HF-HNO3-hexone. The results obtained can be summarized as follows: (1) By measuring the distribution coefficients of Sn, Ta, and Nb in each extractive system, it was found that Sn can be separated sufficiently from Nb and Ta. (2) The extractability of Sn heightens with a rise of mineral acid concentration in a constant HF acidity, especially, from 3.5 N HCl in HF-HCl-hexone system and from 7 N H2SO4 in HF-H2SO4-hexone system, while it gradually increases with a rise of HNO3 concentration or HF concentration in HF-HNO3-hexone system and HF-hexone system. (3) In a constant high HF acidity, 12.75 N, it decreases in the following order: HF-HCl system >HF-H2SO4 system>HF-HNO3 system. (4) Sn% of total organic extract rises with increasing number of times of extracting operation in HF-H2SO4 and especially in HF-HCl, but Sn% of four-times operated extract in HF-HNO3 was lower than that of three-times operated extract. In both HF-H2SO4 and HF-HNO3, the weight of Sn extracted a maximun in the second extraction, while the weight of extracted Sn in HF-HCl system increases with increasing number of extracting operations. (5) HF-hexone system is usually less efficient in extracting Sn than other HF-mineral acid-hexone systems, but HF-H2SO4 below 2.0 N H2SO4, HF-HCl below 0.65 N HCl, and HF-HNO3 below 2.7 N, in which HF acidity is 12.75 N, have similar efficiency in of Sn extraction as 12.75 N HF-hexone system and have larger coextraction efficiency of Nb and Ta than does the latter.抄録全体を表示PDF形式でダウンロード (781K) -
横山 友1960 年 24 巻 12 号 p. 802-805
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーA spectrographic method was studied to determine simultaneously microamounts of calcium and magnesium in cast iron. A sample were dissolved with acid, iron was removed by methyl-isobutyl-ketone extraction, then the solution containing calcium and magnesium was put in a porous-cup electrode and the spectra was excited with a condensed spark. Strontium and beryllium were added as the internal standard elements for calcium and magnesium, respectively, and Sr II 4215.52A/Ca II 3933.67A and Be II 3130.42A/Mg II 2802.70A were used as analytical line pairs. This method was applicable to the determination of calcium and magnesium in concentration above 0.005 per cent and the variation coefficients were 13.5 per cent for calcium and 9.7 per cent for magnesium at a concentration level of 0.01 per cent.抄録全体を表示PDF形式でダウンロード (596K) -
美馬 源次郎, 堀 茂徳, 中桐 明和1960 年 24 巻 12 号 p. 805-809
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe course of transformation of 0.68% carbon steel after rapid heating to austenizing temperatures has been investigated using hardness measurement and microscopic and dilatation techniques. The steel specimens used for the investigation have the structures with lamellar, and spheroidized pearlites and the structure consisting of spheroidized pearlite with graphite nodule. The rate of austenite formation for the lamellar pearlites is greater than the spheroidized pearlites and a finer pearlite gives a more rapid transformation than a coarse one, and when the spheroidized specimen contained graphite, a very long time is necessary for arriving at an austenite state of equilibrium. The austenizing curves obtained from hardness measurement of spheroidized specimens show a sigmoid shape, on the other hand, the austenizing for the lamellar specimens is completed more quickly after a certain incubation period. The explanation of time required to complete the transformation for the structural variables as a function of ferrite-cementite interfacial area is not sufficiently conclusive.抄録全体を表示PDF形式でダウンロード (1045K) -
作井 誠太, 武井 英雄1960 年 24 巻 12 号 p. 810-813
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe rigidity modulus, the electrical resistivity, the hardness and the internal friction in quench-hardened steel wires containing 0.08% and 0.12% of carbon were measured as functions of reduction in area and tempering temperature. The measurement were made on the specimens of wire of 0.6 mm diameter, using a torsion pendulum, a potentiometer and a micro-Vicker’s hardness tester. The result obtained were as follows: (1) The rigidity modulus of quench-hardened steel wire increases gradually by cold drawing, and the rate of increase is larger than that of annealled one. (2) The internal friction of the annealled steel wires decreases remarkably with the amount of cold-drawing up to the reduction of 30% in area, but at a heavy drawing above 30% reduction the change of internal friction is relatively small. The internal friction of the quenched steel wires did not change by cold drawing (But it must be taken care to measure the internal friction in wires aged more than one year at room temperature). (3) The rigidity modulus of steel wires cold-drawn after quenching increases slightly by tempering at 100∼500°C, but decreases remarkably above 550°C.抄録全体を表示PDF形式でダウンロード (664K) -
岡本 正三, 末永 勝郎, 正岡 功1960 年 24 巻 12 号 p. 814-818
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーSome complex structural changes in the alloys containing about 45%Cr, which had been considered as having the simple solubility change of Ni-rich solid solution, were found and discussed. When the alloys containing 43∼51%Cr are slowly cooled from 1250°C, both the fine granular structure and the lamellar structure are seen in the Ni-rich solid solution. The former structure corresponds to the phase change in the Ni solid solution at relatively higher temperatures and the latter structure corresponds to the phase change at lower temperatures, respectively. The alloys were cooled to several levels of temperature from 1050°C and then held at each of them, and the phase changes during the holdings were measured dilatometrically. The isothermal transformation was found to take place in the form like the S-curve of carbon steel, and it was also found that the small nose above 940°C corresponds to the fine granular precipitation and the large nose below 940°C corresponds to the formation of the lamellar one. The growth of the lamellar precipitation was conspicuous in 45%Cr, and at 860°C irrespective of the Cr-concentration of the alloys. However, it could not be clarified yet whether these phase changes are caused by the existence of the eutectoidal change of the Ni solid solution or not.抄録全体を表示PDF形式でダウンロード (944K) -
篠田 軍治, 佐野 忠雄, 桜井 忠一, 川崎 正, 泉 久司1960 年 24 巻 12 号 p. 818-822
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーCreep rupture tests were carried out at 600°C on plain specimens and two different types of notched specimens, and the changes of their microstructure after creep test were examined. The specimens used were AISI type 304, 304L and an iron-base high-chromium high-nickel alloys. The creep rupture strength was not much affected by the notches of the specimen. The microstructures of specimens, which were ruptured after comparatively short time under comparatively higher stresses, revealed a large number of slip bands in each grain and a drastic deformation of individual grain. In the specimens ruptured after longer time, on the other hand, there appeared great many voids at the grain boundaries and a large amount of twin bands instead of slip bands or deformation of grains. These results may inform that the deformations or ruptures of specimens in both cases (short time rupture and longer time rupture) are caused by essentially different causes. Nevertheless, all the rupture datas, in each specimen, fall on a single straight line when they are plotted on logarithmic section paper.抄録全体を表示PDF形式でダウンロード (1026K) -
秋園 幸一1960 年 24 巻 12 号 p. 822-825
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーTo study the impact fatigue, it is very important to know the value of the impact stresses. Usually U(energy)-N curves are used for the impact fatigue, so we cannot compare the results with other impact fatigue data or non-impact fatigue data. So, we studied the relation between the impact stress and the impact energy, using test pieces of various shapes and sizes, under five different impact conditions. The stresses were measured with wire-strain gages. The impact loads were obtained from the strain of supports of a modified Matsumuras impact fatigue-testing machine. The results obtained were as follows: (1) In the elastic region, the strains of the test pieces and the impact loads are proportional to \sqrtU. (U: impact energy) (2) The ratio of energy absorbed by the test pieces and the impact energy (ηT) decreases when the size of test pieces increases. (3) In the case of impact load, the effect of the modulus of section is smaller than in the case of static load, so we must consider the size effect in studying impact fatigue.抄録全体を表示PDF形式でダウンロード (551K) -
秋園 幸一1960 年 24 巻 12 号 p. 826-829
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーUsually, U(energy)-N curves are used to study the impact fatigue, so we cannot compare the results with other impact fatigue data or non-impact fatigue data. So we tried to show a few example of S(stress)-N curves of the impact fatigue, based on the results of our previous experiments in which the relation between impact stresses and impact energy were studied. And we carried out the experiments on the stand-point of the formation and the propagation of fatigue cracks, and whether the stresses applied are tensile, compressive or tensile-compressive stresses alternately is very important to study fatigue phenomena. We used Matsumura’s impact fatigue testing machine and notched test pieces (annealed 0.2% and 0.3% carbon steels). We can compare the fatigue data under two different conditions. From S-N curves for impact fatigue (S is stress at the bottom of notch), N0 (number of blows at which the fatigue crack begins to propagate) is the largest for the Case C, and the smallest for the Case T-C. (Case C means that the stresses at the bottom of the notches are compressive stress, Case T means tensile stresses, and Case T-C means tensile and compressive stresses alternately). For the Case C, the relation between l (length of fatigue cracks) and N (number of blows), and V (velocity of propagation of cracks) and I are as follows. l=K logN/N_0 V=0.4343 K/N K is constant and means tangent of l−logN curves. We applied the above formula to the results of the Cases T and T-C approximately, and compared K and V for each case. K in the Cases T and T-C were almost the same, and K in the Case C was smaller. V in the Case T-C was the largest and in the Case C was the smallest.抄録全体を表示PDF形式でダウンロード (523K) -
向坊 隆, 大島 恵一, 森 久, 長谷 泰治1960 年 24 巻 12 号 p. 829-832
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーThe corrosion rate of AISI 347 stainless steel in 5% sulfuric acid at 70∼97°C is divided into two regions, that is, the initial linear-rate law range (E\doteqdot20 kcal/mol) and the second one with the rate proportional to t0.5∼1.0. The irradiation of 60Co γ-ray affects only the 2nd region and increases the corrosion with the increase of the dose rate (10∼20% increase per 1×105 r/hr). The addition of hydrogen peroxide under no irradiation inhibits the corrosion. Therefore, the effect of the irradiation is believed to be caused by the reducing molecules which have a higher diffusion coefficient and a higher reactivity with the electrode than the oxidizing ones both of which are formed during the radiolysis of water. No change of the crystal structure was observed in the deposited film on the specimen with or without any irradiation.抄録全体を表示PDF形式でダウンロード (636K) -
古沢 浩一1960 年 24 巻 12 号 p. 833-836
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーIt has been suggested that the cause of banded structure in steel is the segregation of phosphorous. But no direct evidence has been offered nor the effect of the other elements cleared out. We prepared the thin segregated region by means of stump welding, and after various heat-treatments examined the change of microstructure. The results obtained were as follows: (1) By slow cooling, the ferrite band appeared in the region where phosphorous was rich and the pearlite band in the region rich in manganese, chromium and nickel. (2) By air cooling, these bands did not appear, or appeared only indistinctly. (3) These were the same as the actual banded structure of steel. The mechanism of these phenomena may be described as follows: If cooling takes place slowly, a small number of ferrites are first deposited in the region with a high phosphorous content, because Ar3 is higher in the region rich in phosphorous content than in P-poor one. This results in the concentration of carbon in the remaining austenite, and in the migration of carbon atoms away from the P-rich region into P-poor one. Thus ferrite band appears in the region with high phosphorous. If rapid cooling (as air cooling) is applied, a large number of ferrites nucleate, because of the large value of N/G at low temperature, in all regions, and the migration of carbon above mentioned does not take place. On account of these, the ferrite band does not appear or appears indistinctly. In the case of pearlite band caused by manganese, chromium or nickel, the same reasoning may be adduced.抄録全体を表示PDF形式でダウンロード (951K) -
金子 秀夫, 西沢 泰二, 玉置 維昭1960 年 24 巻 12 号 p. 837-841
発行日: 1960年
公開日: 2008/04/04
ジャーナル フリーIt is well known that the electrolytic isolation method has rendered a considerable service to the metallographic researches on carbides, oxides and other constituens in iron and steel. The present study was designed to establish the electrolytic conditions for the isolation of sulfides from low-carbon alloy steels using sodium citrate cells and hydrochloric acid cells, and to carry out some preliminary experiments by this procedure. The results obtained are as follows: (1) The sodium citrate cell with an electrolyte of 15% sodium citrate+1% potassium bromide solution is applicable to the isolation of almost every kinds of sulfides, except CrS and Al2S3. (2) The 0.5 N hydrochloric acid cell is applicable to the isolation of VS, ZrS, TiS, NbS and CrS with satisfactory results. (3) The microphotographs of various sulfides isolated from the steels show the charactaristic shapes, which provide new informations on the three dimensional structure of sulfides.抄録全体を表示PDF形式でダウンロード (887K)
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