Pub Date : 1973-04-01DOI: 10.2320/JINSTMET1952.37.8_828
I. Kawakatsu, T. Osawa
{"title":"Wettability of Silver Brazing Alloy for Carbon Steel","authors":"I. Kawakatsu, T. Osawa","doi":"10.2320/JINSTMET1952.37.8_828","DOIUrl":"https://doi.org/10.2320/JINSTMET1952.37.8_828","url":null,"abstract":"","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"58 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1973-04-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"121642127","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1972-04-01DOI: 10.2207/QJJWS1943.40.1032
T. Ishida
A basic study on the dissolution of solid cobalt into molten copper was undertaken to obtain a fundamental knowledge in cobalt brazing. Cylinders were immersed in molten copper and then rotated under dynamic conditions of peripheral velocities from 19.0 to 61.5 cm/sec in the temperature range 1190°1340°C, the exposure time being from 45 sec to 120 sec. Rapid dissolvingof cobalt into molten copper occurred and the apperarnce of an etched surface after dissolution was observed. The rate of dissolution increased with an increase in temperature and rotational speed. A modified first-order kinetic equation was used to determine the dissolution-rate constants. These varied from 0.55 to 1.61 × 10-2 cm/sec depending on the temperature and the rotational speed, and were increased in proportion to 0.64-0.74 power of peripheral velocity. The activation energy for dissolution of solid cobalt into molten copper was estimated to be about 10.0 Kcal/mole. For a diffusion-controlled dissolution process, activation energy for dissolution is contributed to by the sum of activation energy for diffusion and some fraction of activation energy for viscosity. The dissolution rate of solid cobalt into molten copper is mixed-controlled.
{"title":"The Reaction of Solid Cobalt with Molten Copper (Report 1) : The Dissolution of Solid Cobalt into Liquid Copper","authors":"T. Ishida","doi":"10.2207/QJJWS1943.40.1032","DOIUrl":"https://doi.org/10.2207/QJJWS1943.40.1032","url":null,"abstract":"A basic study on the dissolution of solid cobalt into molten copper was undertaken to obtain a fundamental knowledge in cobalt brazing. Cylinders were immersed in molten copper and then rotated under dynamic conditions of peripheral velocities from 19.0 to 61.5 cm/sec in the temperature range 1190°1340°C, the exposure time being from 45 sec to 120 sec. Rapid dissolvingof cobalt into molten copper occurred and the apperarnce of an etched surface after dissolution was observed. The rate of dissolution increased with an increase in temperature and rotational speed. A modified first-order kinetic equation was used to determine the dissolution-rate constants. These varied from 0.55 to 1.61 × 10-2 cm/sec depending on the temperature and the rotational speed, and were increased in proportion to 0.64-0.74 power of peripheral velocity. The activation energy for dissolution of solid cobalt into molten copper was estimated to be about 10.0 Kcal/mole. For a diffusion-controlled dissolution process, activation energy for dissolution is contributed to by the sum of activation energy for diffusion and some fraction of activation energy for viscosity. The dissolution rate of solid cobalt into molten copper is mixed-controlled.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"4 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1972-04-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"115438659","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
{"title":"Some Metallurgical Observations on Heating of Explosive Austenitic Stainless Clad Steel","authors":"I. Tatsukawa, Akira Oda","doi":"10.2207/QJJWS1943.41.663","DOIUrl":"https://doi.org/10.2207/QJJWS1943.41.663","url":null,"abstract":"爆接18Cr-8Niステンレスクラッド鋼の加熱処理に伴う冶金的挙動を詳細に明らかにした.おもな結論はつぎのとおりである.i)500°～900℃の加熱により,ステンレス鋼合材の全断面にわたってCr炭化物が折出するが,これは爆接時に合材が受けた塑性ひずみにより促進される.ii)接合部では炭素の軟鋼からステンレス鋼への拡散移動が起こり,600°～700℃ではステンレス鋼境界に沿う約50μの深さにわたって,Cr7C3を主体とする異常に高い硬化層が生成する.加熱温度が900℃になると,炭化物はステンレス鋼内部に分散しかたさは低下する.同時にCr7C3のほかにCr23C6およびσ相が析出する.他方,Cr,およびNiが軟鋼側へ拡散し,ステンレス鋼境界には析出相のないステンレス鋼と軟鋼との中間組成をもつ合金層が生成する.1100℃ではこれらの析出物はオーステナイト素地中に再固溶する.iii)爆接時に境界部に生じた溶融層は,加熱によりしだいに軟化し,かつCr炭化物を析出する.iv)アークによる短時間加熱では,接合境界層の軟鋼およびステンレス鋼において脱炭と炭化物析出がそれぞれわずかに生起する。また,ステンレス鋼の熱影響部にはγ+α(δ)の共存域を生成する.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"24 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1972-04-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"121196303","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1970-09-01DOI: 10.2534/JJASNAOE1968.1970.128_A359
Masaki Watanabe, Y. Yoshino, I. Watanabe, H. Aoki
We obtained the following results from fatigue test on the welded joints of HT 80 with the reinforcements removed using the modified Schenck's test pieces.(1) The endurance limits of the welded joints were slightly lower than that of the base metal.(2) Most welded joints failed at the bonded zone or the softened zone in H. A. Z. In the case of the specimens failed at the bonded zone, the fatigue cracks started in the coarse grain zone.(3) The welded joints failed almost at the softened zone when the applied stress was comparatively high and failed slightly more at the bonded zone than the softened zone when the applied stress was near the endurance limit.(4) Considering the result (3), we had investigated the endurance limit (σ) from two points hardness (H) and grain diameter (D) and proposed the following formula, σ=a1H1/√D+b11/√D+a2H+b2, where a1, b1, a2, b2 are the constant values without concerning the material, and we proposed the following values : a1=0.0017, b1=0.54, a2=0.11, b2=3.5.(5) From one more experiment on the grain size dependence of the fatigue strength, we obtained the fact that the effect of the grain size on the fatigue strength decreases with increase of the applied stress.(6) The equation above mentioned shows the endurance limit, but when the applied stress is comparatively higher than the endurance limit, the values 'a1' and 'b1' must be smaller than 0.0017 and 0.54 judging from the result (5). In this case we can see that the fatigue strength of bonded zone is higher than that of the softened zone.
采用改进的Schenck试件对去掉增强后的ht80焊接接头进行了疲劳试验，结果表明:(1)焊接接头的耐久极限略低于母材的耐久极限;(2)大部分焊接接头在粘结区或H. A. z的软化区失效，试样在粘结区失效;(4)结合(3)的结果，从硬度(H)和晶粒直径(D)两个角度对疲劳极限σ进行了研究，提出了σ=a1H1/√D+b11/√D+a2H+b2的计算公式，其中a1, b1, a2，B2是不考虑材料的常数，我们提出如下值:a1=0.0017, b1=0.54, a2=0.11, b2=3.5.(5)再对疲劳强度的晶粒尺寸依赖性进行一次试验，得到晶粒尺寸对疲劳强度的影响随外加应力的增大而减小。(6)上述式表示的是疲劳极限，但当外加应力相对大于疲劳极限时，从结果(5)可以看出，a1和b1必须分别小于0.0017和0.54，此时粘结区的疲劳强度高于软化区的疲劳强度。
{"title":"Variation of the Positions where the Welded Joints of HT 80 failed in the Fatigue Test","authors":"Masaki Watanabe, Y. Yoshino, I. Watanabe, H. Aoki","doi":"10.2534/JJASNAOE1968.1970.128_A359","DOIUrl":"https://doi.org/10.2534/JJASNAOE1968.1970.128_A359","url":null,"abstract":"We obtained the following results from fatigue test on the welded joints of HT 80 with the reinforcements removed using the modified Schenck's test pieces.(1) The endurance limits of the welded joints were slightly lower than that of the base metal.(2) Most welded joints failed at the bonded zone or the softened zone in H. A. Z. In the case of the specimens failed at the bonded zone, the fatigue cracks started in the coarse grain zone.(3) The welded joints failed almost at the softened zone when the applied stress was comparatively high and failed slightly more at the bonded zone than the softened zone when the applied stress was near the endurance limit.(4) Considering the result (3), we had investigated the endurance limit (σ) from two points hardness (H) and grain diameter (D) and proposed the following formula, σ=a1H1/√D+b11/√D+a2H+b2, where a1, b1, a2, b2 are the constant values without concerning the material, and we proposed the following values : a1=0.0017, b1=0.54, a2=0.11, b2=3.5.(5) From one more experiment on the grain size dependence of the fatigue strength, we obtained the fact that the effect of the grain size on the fatigue strength decreases with increase of the applied stress.(6) The equation above mentioned shows the endurance limit, but when the applied stress is comparatively higher than the endurance limit, the values 'a1' and 'b1' must be smaller than 0.0017 and 0.54 judging from the result (5). In this case we can see that the fatigue strength of bonded zone is higher than that of the softened zone.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"61 6 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1970-09-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"134594949","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1970-09-01DOI: 10.2207/QJJWS1943.39.10_1075
I. Masumoto, T. Shinoda
This study was carried out directly to detect the constituent of gas in blowholes of weld metal by a microscopic micro-analysing and a mass spectrometer. Aluminum and its alloy, mild steel, high strength steel and austenitic stainless steel were used as base metals. And a bead - on - plate was deposited by the gas shielded metal arc welding under various shielding gases for each base metal. The diameter of a collected gas bubble from blowholes was measured by the microscope under a thin glass in absorbent step by step. The composition of the gas bubble was determined by calculation from the difference of diameters of the bubble before and after an absorbent solution. The quantity of hydrogen was determined from the loss of explosion by a special explosion pipet. The remainder gas after the microscopic micro-analysing was determined by the mass spectrometer (JMS-OISG).According to the results of analysis for aluminum deposit metal, a blowhole consists of the following gases; hydrogen about 75-85%, oxygen and argon several % and nitrogen 10-20%. In aluminum alloy deposit metal, oxygen could not be measured. Carbon dioxide, hydrogen sulphide, carbon monoxide and metahne were not recognized in both cases. Blowhole in mild steel deposit metal is full of carbon monoxide, hydrogen and nitrogen. Under the carbon dioxide shielding gas with a wire of insufficient deoxydation elements or carbon dioxide shielding gas with excess oxygen, blowholes consist mainly of carbon monoxide over 55% and nitrogen. Blowholes which were formed in a bead on rusted steel or on greased steel contained mainly 40-60% of hydrogen and 30-40% of carbon monoxide. In austenitic stainless steel deposit metal, the gas in blowhole is also carbon monoxide, hydrogen, nitrogen and argon in the case of argon and argon-nitrogen shielding.
{"title":"Chemical Analysis on Blowholes","authors":"I. Masumoto, T. Shinoda","doi":"10.2207/QJJWS1943.39.10_1075","DOIUrl":"https://doi.org/10.2207/QJJWS1943.39.10_1075","url":null,"abstract":"This study was carried out directly to detect the constituent of gas in blowholes of weld metal by a microscopic micro-analysing and a mass spectrometer. Aluminum and its alloy, mild steel, high strength steel and austenitic stainless steel were used as base metals. And a bead - on - plate was deposited by the gas shielded metal arc welding under various shielding gases for each base metal. The diameter of a collected gas bubble from blowholes was measured by the microscope under a thin glass in absorbent step by step. The composition of the gas bubble was determined by calculation from the difference of diameters of the bubble before and after an absorbent solution. The quantity of hydrogen was determined from the loss of explosion by a special explosion pipet. The remainder gas after the microscopic micro-analysing was determined by the mass spectrometer (JMS-OISG).According to the results of analysis for aluminum deposit metal, a blowhole consists of the following gases; hydrogen about 75-85%, oxygen and argon several % and nitrogen 10-20%. In aluminum alloy deposit metal, oxygen could not be measured. Carbon dioxide, hydrogen sulphide, carbon monoxide and metahne were not recognized in both cases. Blowhole in mild steel deposit metal is full of carbon monoxide, hydrogen and nitrogen. Under the carbon dioxide shielding gas with a wire of insufficient deoxydation elements or carbon dioxide shielding gas with excess oxygen, blowholes consist mainly of carbon monoxide over 55% and nitrogen. Blowholes which were formed in a bead on rusted steel or on greased steel contained mainly 40-60% of hydrogen and 30-40% of carbon monoxide. In austenitic stainless steel deposit metal, the gas in blowhole is also carbon monoxide, hydrogen, nitrogen and argon in the case of argon and argon-nitrogen shielding.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"3 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1970-09-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"133138628","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
{"title":"Effects of Nitrogen, Oxygen and Hydrogen Gases Added to Argon Gas on MIG-Welding of Aluminum Alloys","authors":"T. Fukui, Y. Sugiyama, S. Terai","doi":"10.2464/JILM.18.609","DOIUrl":"https://doi.org/10.2464/JILM.18.609","url":null,"abstract":"","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"17 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1970-04-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"116736822","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
The friction weldability of sintered high carbon-high chromium steel (PM) and S25C steel was investigated. The welded joint of the as-received PM and S25C steel, the quench-tempered joint after welding and the welded joint of the quench-tempered PM and the as-received S25C steel were made. They were labelled A, B and C joints. A continuous drive type friction welding machine was used. Welding was carried out in the range of the following conditions.Rotational speed: 2440 rpm, Friction pressure: 6.0, 8.0 Kgf/mm2, Upsetting pressure: 10.0, 14.0 Kgf/mm2, Friction time: 3.0, 5.0 s, Upsetting time: 10.0 s.Results of this study are summarized as follows:(1) The A joint are broken in the PM base metal or at the weld in tensile test. As the tensile strength of the as-received PM base metal itself is low, the joint is unsuited for practical use.(2) The C joints are broken at the weld interface or in the heat-affected zone of PM base metal in tensile test. The joint imperfection at the weld interface and the imperfection of joint between powder particles are the causes of fracture in each case.(3) The B joints are broken in the base metal in tensile test and have sufficient strength.(4) The B joint is superior to the quench-tempered PM base metal in bending ductility, impact value and fatigue limit.
{"title":"Friction Welding of Sintered Steel and Carbon Steel","authors":"A. Hasui, Lian Der-Ming, Y. Nishino, T. Kono","doi":"10.2207/QJJWS.3.696","DOIUrl":"https://doi.org/10.2207/QJJWS.3.696","url":null,"abstract":"The friction weldability of sintered high carbon-high chromium steel (PM) and S25C steel was investigated. The welded joint of the as-received PM and S25C steel, the quench-tempered joint after welding and the welded joint of the quench-tempered PM and the as-received S25C steel were made. They were labelled A, B and C joints. A continuous drive type friction welding machine was used. Welding was carried out in the range of the following conditions.Rotational speed: 2440 rpm, Friction pressure: 6.0, 8.0 Kgf/mm2, Upsetting pressure: 10.0, 14.0 Kgf/mm2, Friction time: 3.0, 5.0 s, Upsetting time: 10.0 s.Results of this study are summarized as follows:(1) The A joint are broken in the PM base metal or at the weld in tensile test. As the tensile strength of the as-received PM base metal itself is low, the joint is unsuited for practical use.(2) The C joints are broken at the weld interface or in the heat-affected zone of PM base metal in tensile test. The joint imperfection at the weld interface and the imperfection of joint between powder particles are the causes of fracture in each case.(3) The B joints are broken in the base metal in tensile test and have sufficient strength.(4) The B joint is superior to the quench-tempered PM base metal in bending ductility, impact value and fatigue limit.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"61 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1900-01-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"124902474","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
{"title":"Relation Between Fatigue Strength and Reinforcement Shape of Simulated Butt-Welded Joint","authors":"H. Nisitani, Hiroyuki Tanaka, T. Harada","doi":"10.2207/QJJWS.9.31","DOIUrl":"https://doi.org/10.2207/QJJWS.9.31","url":null,"abstract":"","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"181 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1900-01-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"126775077","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Influence of microstructure in the Heat-Affected-Zone on the reheat cracking susceptibility was studied.The reheat cracking tests on H.T. 80 steel were carried out by means of ring type specimens and three point bending test. Influence of microstructure of synthetic H.A.Z. at high temperature on the reheat treatment process were investigated by high temperature hardness measurements, X-ray analysis and scanning electron microscopic observations. The results are summarized as follows. 1) The reheat cracking's critical stress of Martensite structure specimens (Water Quenched) were generally double than that of Bainite and Ferrite structure specimens (Air Cooled). But, the reheat cracking susceptibility of A.C. specimens were little by the difference of forms in microstructure. 2) The reheat cracking susceptibility were estimated by the relation of the deformability of a material and the precipitate of alloying carbides. Accordingly, alloying carbides of A.C. specimens precipitated to M3C type carbides during cooling process of synthetic H.A.Z., but that of W.Q. specimens precipitated to M3C type carbides as well as A.C specimens and M2C type carbides during reheat treatment process. W.Q. specimens of the lower reheat' cracking susceptibility are affected mainly by the precipitate of M2C type carbides in the matrix. 3) It is seemed that the precipitation of M2C and M3C type carbides during reheat treatment process from W.Q. specimens decreased the alloying elements concentration in the matrix, and showed a good deformability of a material. As a consequence, the reheat cracking susceptibility of W.Q. specimens were lower than that of A.C. specimens.
{"title":"Influence of Microstructure in the Heat-Affected-Zone on the Reheat Cracking Susceptibility","authors":"Mitsuru Nakamura, T. Enjo, Y. Kikuchi","doi":"10.2207/QJJWS.3.560","DOIUrl":"https://doi.org/10.2207/QJJWS.3.560","url":null,"abstract":"Influence of microstructure in the Heat-Affected-Zone on the reheat cracking susceptibility was studied.The reheat cracking tests on H.T. 80 steel were carried out by means of ring type specimens and three point bending test. Influence of microstructure of synthetic H.A.Z. at high temperature on the reheat treatment process were investigated by high temperature hardness measurements, X-ray analysis and scanning electron microscopic observations. The results are summarized as follows. 1) The reheat cracking's critical stress of Martensite structure specimens (Water Quenched) were generally double than that of Bainite and Ferrite structure specimens (Air Cooled). But, the reheat cracking susceptibility of A.C. specimens were little by the difference of forms in microstructure. 2) The reheat cracking susceptibility were estimated by the relation of the deformability of a material and the precipitate of alloying carbides. Accordingly, alloying carbides of A.C. specimens precipitated to M3C type carbides during cooling process of synthetic H.A.Z., but that of W.Q. specimens precipitated to M3C type carbides as well as A.C specimens and M2C type carbides during reheat treatment process. W.Q. specimens of the lower reheat' cracking susceptibility are affected mainly by the precipitate of M2C type carbides in the matrix. 3) It is seemed that the precipitation of M2C and M3C type carbides during reheat treatment process from W.Q. specimens decreased the alloying elements concentration in the matrix, and showed a good deformability of a material. As a consequence, the reheat cracking susceptibility of W.Q. specimens were lower than that of A.C. specimens.","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"8 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1900-01-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"124573031","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 1900-01-01DOI: 10.2207/qjjws1943.50.147
H. Kihara, K. Satoh, M. Endoh, Mamoru Hirose, T. Shimoyama, G. Takano
For pressure hulls of Deep Submergence Vehicle (DSV) operating in seas of 2000 m depth, the most important point is the maximum load carrying capacity under the minimum weight. For this reason, spherical shell made of high strength steel is adopted for pressure hulls. Spherical shape is an optimum shape for external hydrostatic pressure loading and the most suitable steel for this shape is HT100 steel
{"title":"Study on Welding of High Strength Steel with High Toughness for Pressure Hull of Deep Submergence Vehicle (1st report)","authors":"H. Kihara, K. Satoh, M. Endoh, Mamoru Hirose, T. Shimoyama, G. Takano","doi":"10.2207/qjjws1943.50.147","DOIUrl":"https://doi.org/10.2207/qjjws1943.50.147","url":null,"abstract":"For pressure hulls of Deep Submergence Vehicle (DSV) operating in seas of 2000 m depth, the most important point is the maximum load carrying capacity under the minimum weight. For this reason, spherical shell made of high strength steel is adopted for pressure hulls. Spherical shape is an optimum shape for external hydrostatic pressure loading and the most suitable steel for this shape is HT100 steel","PeriodicalId":273687,"journal":{"name":"Transactions of the Japan Welding Society","volume":"67 1","pages":"0"},"PeriodicalIF":0.0,"publicationDate":"1900-01-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"124086302","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":0,"RegionCategory":"","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
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