Journal articles: 'Austenitic stainless steel Cracking'

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Topolska, S., and J. Łabanowski. "Environmental Degradation of Dissimilar Austenitic 316L and Duplex 2205 Stainless Steels Welded Joints." Archives of Metallurgy and Materials 62, no. 4 (December 1, 2017): 2107–12. http://dx.doi.org/10.1515/amm-2017-0312.

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AbstractThe paper describes structure and properties of dissimilar stainless steels welded joints between duplex 2205 and austenitic 316L steels. Investigations were focused on environmentally assisted cracking of welded joints. The susceptibility to stress corrosion cracking (SCC) and hydrogen embrittlement was determined in slow strain rate tests (SSRT) with the strain rate of 2.2 × 10−6s−1. Chloride-inducted SCC was determined in the 35% boiling water solution of MgCl2environment at 125°C. Hydrogen assisted SCC tests were performed in synthetic sea water under cathodic polarization condition. It was shown that place of the lowest resistance to chloride stress corrosion cracking is heat affected zone at duplex steel side of dissimilar joins. That phenomenon was connected with undesirable structure of HAZ comprising of large fractions of ferrite grains with acicular austenite phase. Hydrogen assisted SCC tests showed significant reduction in ductility of duplex 2205 steel while austenitic 316L steel remains almost immune to degradation processes. SSR tests of dissimilar welded joints revealed a fracture in the area of austenitic steel.

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Wang, Wenbin, Li Xiong, Dan Wang, Qin Ma, Yan Hu, Guanzhi Hu, and Yucheng Lei. "A New Test Method for Evaluation of Solidification Cracking Susceptibility of Stainless Steel during Laser Welding." Materials 13, no. 14 (July 16, 2020): 3178. http://dx.doi.org/10.3390/ma13143178.

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A new test method named “Trapezoidal hot” cracking test was developed to evaluate solidification cracking susceptibility of stainless steel during laser welding. The new test method was used to obtain the solidification cracking directly, and the solidification cracking susceptibility could be evaluated by the solidification cracking rate, defined as the ratio of the solidification cracking length to the weld bead length under certain conditions. The results show that with the increase in the solidification cracking rate, the solidification cracking susceptibility of SUS310 stainless steel was much higher than that of SUS316 and SUS304 stainless steels during laser welding (at a welding speed of 1.0 m/min) because a fully austenite structure appeared in the weld joint of the former steel, while the others were ferrite and austenitic mixed structures during solidification. Besides, with an increase in welding speed from 1.0 to 2.0 m/min during laser welding, the solidification cracking susceptibility of SUS310 stainless steel decreased slightly; however, there was a tendency towards an increase in the solidification cracking susceptibility of SUS304 stainless steel due to the decrease in the amount of ferrite under a higher cooling rate.

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Shankar, V., T. P. S. Gill, S. L. Mannan, and S. Sundaresan. "Solidification cracking in austenitic stainless steel welds." Sadhana 28, no. 3-4 (June 2003): 359–82. http://dx.doi.org/10.1007/bf02706438.

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Setargew, Nega, and Daniel J. Parker. "Zinc diffusion induced precipitation of σ-phase in austenitic stainless steel." Metallurgical Research & Technology 116, no. 6 (2019): 618. http://dx.doi.org/10.1051/metal/2019040.

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Zinc diffusion-induced degradation of AISI 316LN austenitic stainless steel pot equipment used in 55%Al-Zn and Zn-Al-Mg coating metal baths is described. SEM/EDS analyses results showed that the diffused zinc reacts with nickel from the austenite matrix and results in the formation of Ni-Zn intermetallic compounds. The Ni-Zn intermetallic phase and the nickel depleted zones form a periodic and alternating layered structure and a mechanism for its formation is proposed. The role of cavities and interconnected porosity in zinc vapour diffusion-induced degradation and formation of Ni-Zn intermediate phases is also discussed. The formation of Ni-Zn intermediate phases and the depletion of nickel in the austenite matrix results in the precipitation of σ-phase and α-ferrite in the nickel depleted regions of the matrix. This reaction will lead to increased susceptibility to intergranular cracking and accelerated corrosion of immersed pot equipment in the coating bath. Zinc diffusion induced precipitation of σ-phase in austenitic stainless steels that we are reporting in this work is a new insight with important implications for the performance of austenitic stainless steels in zinc containing metal coating baths and other process industries. This new insight will further lead to improved understanding of the role of substitutional diffusion and the redistribution of alloying elements in the precipitation of σ-phase in austenitic stainless steels.

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Sundaresan, S. "Metallurgy of Welding Stainless Steels." Advanced Materials Research 794 (September 2013): 274–88. http://dx.doi.org/10.4028/www.scientific.net/amr.794.274.

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Based primarily on microstructure, five stainless steel types are recognized: ferritic, martensitic, austenitic, duplex and precipitation-hardening. The major problem in ferritic stainless steels is the tendency to embrittlement, aggravated by various causes. During welding, control of heat input is essential and, in some cases, also a postweld heat treatment. The austenitic type is the easiest to weld, but two important issues are involved in the welding of these steels: hot cracking and formation of chromium carbide and other secondary phases on thermal exposure. The nature of the problems and remedial measures are discussed from a metallurgical perspective. Duplex stainless steels contain approximately equal proportions of austenite and ferrite. The article discusses the upset in phase balance during welding both in the weld metal and heat-affected zone and the formation of embrittling secondary phases during any thermal treatment. Martensitic stainless steels are susceptible to hydrogen-induced cracking. Welding thus involves many precautions to prevent it through proper preheat selection, postweld heat treatment, etc. In the welding of precipitation-hardening stainless steels, it is usually necessary to develop in the weld metal strength levels matching those of the base metal. This is achieved by applying a postweld heat treatment appropriate to each type of alloy.

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Stradomski, G. "The Cracking Mechanism of Ferritic-Austenitic Cast Steel." Archives of Foundry Engineering 16, no. 4 (December 1, 2016): 153–56. http://dx.doi.org/10.1515/afe-2016-0101.

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Abstract In the high-alloy, ferritic - austenitic (duplex) stainless steels high tendency to cracking, mainly hot-is induced by micro segregation processes and change of crystallization mechanism in its final stage. The article is a continuation of the problems presented in earlier papers [1 - 4]. In the range of high temperature cracking appear one mechanism a decohesion - intergranular however, depending on the chemical composition of the steel, various structural factors decide of the occurrence of hot cracking. The low-carbon and low-alloy cast steel casting hot cracking cause are type II sulphide, in high carbon tool cast steel secondary cementite mesh and / or ledeburite segregated at the grain solidified grains boundaries, in the case of Hadfield steel phosphorus - carbide eutectic, which carrier is iron-manganese and low solubility of phosphorus in high manganese matrix. In duplex cast steel the additional factor increasing the risk of cracking it is very “rich” chemical composition and related with it processes of precipitation of many secondary phases.

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Truschner, Mathias, Jacqueline Deutsch, Gregor Mori, and Andreas Keplinger. "Cathodic and Anodic Stress Corrosion Cracking of a New High-Strength CrNiMnMoN Austenitic Stainless Steel." Metals 10, no. 11 (November 19, 2020): 1541. http://dx.doi.org/10.3390/met10111541.

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A new high-nitrogen austenitic stainless steel with excellent mechanical properties was tested for its resistance to stress corrosion cracking. The new conventional produced hybrid CrNiMnMoN stainless steel combines the excellent mechanical properties of CrMnN stainless steels with the good corrosion properties of CrNiMo stainless steels. Possible applications of such a high-strength material are wires in maritime environments. In principle, the material can come into direct contact with high chloride solutions as well as low pH containing media. The resistance against chloride-induced stress corrosion cracking was determined by slow strain rate tests and constant load tests in different chloride-containing solutions at elevated temperatures. Resistance to hydrogen-induced stress corrosion cracking was investigated by precharging and ongoing in-situ hydrogen charging in both slow strain rate test and constant load test. The hydrogen charging was carried out by cathodic charging in 3.5 wt.% NaCl solution with addition of 1 g/L thiourea as corrosion inhibitor and recombination inhibitor to ensure hydrogen absorption with negligible corrosive attack. Slow strain rate tests only lead to hydrogen induced stress corrosion cracking by in-situ charging, which leads to total hydrogen contents of more than 10 wt.-ppm and not by precharging alone. Excellent resistance to chloride-induced stress corrosion cracking in 43 wt.% CaCl2 at 120 °C and in 5 wt.% NaCl buffered pH 3.5 solution at 80 °C is obtained for the investigated austenitic stainless steel.

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Khoshnaw, Fuad Mohamed, and Hussein Bakir Rahmatalla. "Stress Corrosion Cracking Behaviour of Welded Duplex Stainless Steel." Advanced Materials Research 89-91 (January 2010): 709–14. http://dx.doi.org/10.4028/www.scientific.net/amr.89-91.709.

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This study investigated stress corrosion cracking of two welded stainless steel alloys, austenitic 304L and duplex 2205, in an acidic chloride solution. Different heat inputs are selected for welding the alloys, using tungsten inert gas, with and without filler metal. The slow strain rate technique is utilized to estimate the susceptibility of each weldment to stress corrosion cracking. Different strain rates are used, and the experiments showed that the strain rate equal to 1.66x10-6/sec is a critical value that can be used for assessing the susceptibility of the alloys to corrosion cracking. A numerical index used in this study to evaluate this susceptibility, which is based on a ratio between elongation percent of each alloy in the solution to that in the air. The results showed that the austenitic alloy has higher ductility than duplex in air, while there was not a big difference between both alloys in the solution. Increasing the heat input in autogenous welding caused a brittleness, i.e. less elongation, for both alloys. The results showed that the austenitic alloy is exposed to stress corrosion cracking in the solution, before and after welding, with or without filler metals. On the other hand, the duplex alloy showed higher resistance to stress corrosion cracking than the austenitic alloy due to the high chromium content, and it is dual phase.

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Correia, Maria J., and Manuela M. Salta. "Stress Corrosion Cracking of Austenitic Stainless Steel Alloys for Reinforced Concrete." Materials Science Forum 514-516 (May 2006): 1511–15. http://dx.doi.org/10.4028/www.scientific.net/msf.514-516.1511.

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The corrosion resistance under mechanical stress can be one of the most concerning types of localized corrosion for the application of stainless steel reinforcements in concrete. This paper will assess the stress corrosion cracking susceptibility, by the slow strain rate test method (SSRT), of three austenitic stainless steel alloys: one conventional Fe-Cr-Ni base alloy and two new composition Fe-Cr-Mn base alloys adequate to the manufacturing of ribbed bars for reinforcing concrete. The SSRT results show that only one of the austenitic Fe-Cr-Mn alloys is susceptible to stress corrosion cracking while the other shows a performance similar to that of the AISI 304 stainless steel alloy.

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Prabowo, Harris, Badrul Munir, Yudha Pratesa, and Johny W. Soedarsono. "Comparison of 2507 Duplex and 28 % Cr- Austenitic Stainless Steel Corrosion Behavior for High Pressure and High Temperature (HPHT) in Sour Service Condition with C-ring Experiment." Periodica Polytechnica Mechanical Engineering 65, no. 3 (July 5, 2021): 280–85. http://dx.doi.org/10.3311/ppme.17598.

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The scarcity of oil and gas resources made High Pressure and High Temperature (HPHT) reservoir attractive to be developed. The sour service environment gives an additional factor in material selection for HPHT reservoir. Austenitic 28 Cr and super duplex stainless steel 2507 (SS 2507) are proposed to be a potential materials candidate for such conditions. C-ring tests were performed to investigate their corrosion behavior, specifically sulfide stress cracking (SSC) and sulfide stress cracking susceptibility. The C-ring tests were done under 2.55 % H2S (31.48 psia) and 50 % CO2 (617.25 psia). The testing was done in static environment conditions. Regardless of good SSC resistance for both materials, different pitting resistance is seen in both materials. The pitting resistance did not follow the general Pitting Resistance Equivalent Number (PREN), since SS 2507 super duplex (PREN > 40) has more pitting density than 28 Cr austenitic stainless steel (PREN < 40). SS 2507 super duplex pit shape tends to be larger but shallower than 28 Cr austenitic stainless steel. 28 Cr austenitic stainless steel has a smaller pit density, yet deeper and isolated.

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Radhakrishnan, V. M. "Hot cracking in austenitic stainless steel weld metals." Science and Technology of Welding and Joining 5, no. 1 (February 2000): 40–44. http://dx.doi.org/10.1179/stw.2000.5.1.40.

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Zhang, Hui, Yanfeng Liu, Xian Zhai, and Wenkai Xiao. "Effects of High Temperature Aging Treatment on the Microstructure and Impact Toughness of Z2CND18-12N Austenitic Stainless Steel." Metals 10, no. 12 (December 18, 2020): 1691. http://dx.doi.org/10.3390/met10121691.

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During the casting cooling process or the forging process, austenitic stainless steel will remain at around 800 °C for some time. During this period, precipitate particle behaviors in austenitic stainless steel (containing ferrite) will cause a reduction in ductility, which can lead to material cracking. In this study, the effects of aging at 800 °C on the microstructure, impact toughness and microhardness of Z2CND18-12N austenitic stainless steel were systematically investigated. The precipitation processes of the χ and σ phases were characterized by color metallography and back scattered electron (BSE) signals. The toughness was investigated by the Charpy impact test. After the aging treatment, the χ and σ phases precipitated successively in the ferrite, and as the aging duration increased, the χ-phase dissolved and the σ-phase precipitated along the austenite grain boundaries. These all lead to a decrease in toughness and an increase in microhardness. Finally, the relationship between fracture morphology and aging time is discussed herein, and a crack mechanism is given.

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Yoo, Y. R., H. Y. Chang, Yong Bum Park, Y. S. Park, Tai Joo Chung, and Young Sik Kim. "Influence of Thermal Treatment on the Caustic SCC of Super Austenitic Stainless Steel." Materials Science Forum 475-479 (January 2005): 4227–30. http://dx.doi.org/10.4028/www.scientific.net/msf.475-479.4227.

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In general, thermal treatment at 500oC ~ 900oC ranges depending upon alloy composition of stainless steels can sensitize the steels and promote the intergranular cracking, and their intergranular corrosion resistance is decreased. These behaviors seem to be related to the change of microstructures. So, heat treatment at that temperature range should be avoided in fabrication, especially welding of stainless steels. In this work, it is focused on the effect of thermal treatment on caustic stress corrosion cracking of super austenitic stainless steel - S32050 The low temperature thermal treatment increased greatly the resistance to caustic SCC than those of annealed specimen. This enhancement might be closely related to the reduction of residual stress and slightly large grain, but its resistance was not affected by the anodic polarization behavior.

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Park, Ihho, Eun-Young Kim, and Won-Jon Yang. "Microstructural Investigation of Stress Corrosion Cracking in Cold-Formed AISI 304 Reactor." Metals 11, no. 1 (December 23, 2020): 7. http://dx.doi.org/10.3390/met11010007.

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The aim of this study was to investigate cracking behavior of AISI 304 stainless steel that had been exposed to a high temperature MgCl2 solution for several years. The microstructure of the cracked area of the reactor was studied by in-depth microstructural characterization. Transgranular stress corrosion cracking only occurred at the cold-formed part of the reactor. It was observed that approximately 10–20% of the austenite matrix was transformed into alpha prime martensite due to cold forming at the lower head of the reactor. The preferential path for crack propagation was found to be strain-induced alpha prime martensite. The present study reveals that strain-induced martensitic transformation in austenitic stainless steel has a negative effect on stress corrosion cracking.

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Wei, De Qiang, Xin Dong, and Shan Qiu Li. "Failure Analysis of Stress Corrosion Crack of 1Cr18Ni9 Stainless Steel Cylinder Body." Advanced Materials Research 591-593 (November 2012): 1094–97. http://dx.doi.org/10.4028/www.scientific.net/amr.591-593.1094.

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As a kind of corrosion resistant material, stainless steel is widely used in petroleum, chemical, pharmaceutical. Stress corrosion cracking is a main reason that why the stainless steel became disabled. Therefore, it is very necessary to research and study the stress corrosion cracking of stainless steel .The failure analysis to the sample is conducted aiming at the stress corrosion of the stainless steel piston cylinder in a factory. The analysis includes macro analysis, metallographic observation, scanning electron microscopy analysis and XRD analysis. The results of the study show that it is nonmetallic inclusion on the grain boundary, the chloridion in the industrial circulating water and the rough columnar austenitic grains in the organization of the samples that lead to the stress corrosion cracking of the piston cylinder.

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Penha, R. N., L. B. Silva, C. S. P. Mendonça, T. C. Moreira, and M. L. N. M. Melo. "Effect of ageing time on microstructure and mechanical properties of SAF 2205 duplex stainless steel." Archives of Materials Science and Engineering 1, no. 91 (May 1, 2018): 23–30. http://dx.doi.org/10.5604/01.3001.0012.1382.

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Purpose: SAF 2205 duplex stainless steels (DSSs) are materials characterized by a favourable combination of the properties of ferritic and austenitic stainless steels. This type of stainless steel presents good weldability, corrosion resistance especially for stress corrosion cracking (SCC). However, this steel presents an unavoidable disadvantage that is its potential microstructural instability. Although duplex stainless steels design idea is to present two main types of microstructure, other phases and carbides or nitrides can precipitate. In the case of DSS SAF 2205, in addition to austenitic and ferritic microstructure, during heat treatment processing, welding or use may occur precipitation of undesirable intermetallic phases such as chi, Widmanstätten austenite, sigma besides carbides and nitrides. The precipitation of s-phase is associated with effects that cause both reduction of toughness and decreases the corrosion resistance on austenitic, ferritic and duplex stainless steels. Design/methodology/approach: This study evaluated the aging treatment effect on hardness, impact toughness and ferrite content of a SAF 2205 duplex stainless steel. Samples were solubilized at 1150°C, quenched in water and aged at 850°C during 1, 5, 10, 30, 60 or 180 minutes. After aging, cooling was to room temperature in air. Findings: Aging time promoted s-phase precipitation and hardness increase. Hardness and ferrite volume measurements, microscopy and the prediction of sigma phase bases the discussion. Impact toughness decreased with time aging and intermetallic phase precipitation. Research limitations/implications: As future work could be performed some corrosion test, vary the cooling rate after aging, and using other techniques to identify phases. Focus the research at lower aging times to try the describe Cr partitioning process to form sigma phase. Practical implications: High aging time should be avoided for SAF 2205 DSS. Originality/value: Usually sigma-phase precipitation on DDS is correlated to welding process. This paper correlates it to aging heat treatment.

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Francis, Roger, and Glenn Byrne. "Duplex Stainless Steels—Alloys for the 21st Century." Metals 11, no. 5 (May 19, 2021): 836. http://dx.doi.org/10.3390/met11050836.

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Duplex stainless steels were first manufactured early in the 20th century, but it was the introduction in the 1970s of the argon-oxygen decarburisation (AOD) steel making process and the addition of nitrogen to these steels, that made the alloys stronger, more weldable and more corrosion resistant. Today, duplex stainless steels can be categorised into four main groups, i.e., “lean”, “standard”, “super”, and “hyper” duplex types. These groups cover a range of compositions and properties, but they all have in common a microstructure consisting of roughly equal proportions of austenite and ferrite, high strength, good toughness and good corrosion resistance, especially to stress corrosion cracking (SCC) compared with similar austenitic stainless steels. Moreover, the development of a duplex stainless-steel microstructure requires lower levels of nickel in the composition than for a corresponding austenitic stainless steel with comparable pitting and crevice corrosion resistance, hence they cost less. This makes duplex stainless steels a very versatile and attractive group of alloys both commercially and technically. There are applications where duplex grades can be used as lower cost through-life options, in preference to coated carbon steels, a range of other stainless steels, and in some cases nickel alloys. This cost benefit is further emphasised if the design engineer can use the higher strength of duplex grades to construct vessels and pipework of lower wall thickness than would be the case if an austenitic grade or nickel alloy was being used. Hence, we find duplex stainless steels are widely used in many industries. In this paper their use in three industrial applications is reviewed, namely marine, heat exchangers, and the chemical and process industries. The corrosion resistance in the relevant fluids is discussed and some case histories highlight both successes and potential problems with duplex alloys in these industries. The paper shows how duplex stainless steels can provide cost-effective solutions in corrosive environments, and why they will be a standard corrosion resistant alloy (CRA) for many industries through the 21st century.

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Neidel, A., T. Gädicke, V. Hartanto, S. Wallich, and E. Wöhl. "Austenitic Stainless Steel Bolt Failure by Stress Corrosion Cracking." Practical Metallography 55, no. 2 (February 15, 2018): 97–109. http://dx.doi.org/10.3139/147.110493.

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Neidel, Andreas, and Susanne Riesenbeck. "Hot Cracking in Inductively Bent Austenitic Stainless Steel Pipes." Journal of Failure Analysis and Prevention 11, no. 5 (October 2011): 473–77. http://dx.doi.org/10.1007/s11668-011-9478-4.

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Májlinger, Kornél, and Péter János Szabó. "Intercrystalline Cracking of Austenitic Steel during Brazing." Materials Science Forum 729 (November 2012): 442–47. http://dx.doi.org/10.4028/www.scientific.net/msf.729.442.

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During brazing of austenitic stainless steel with copper based brazing material a common failure occurs, namely that the brazing material solutes along grain boundaries, which look like cracks. This unfortunate effect occurred when AISI 304 steel is brazed. To avoid this unwanted effect since the cracks propagate mainly on high angle grain boundaries our goal was to enhance the number of special coincident site lattice type grain boundaries with thermomechanical treatment. Experiments were performed for 1, 48 and 72 hour heat treatments at different level of cold rolled materials. After the thermomechanical treatment significant decrease in the crack size was found in depth and width, respectively. The grain boundaries were investigated on electro polished samples in an electron microscope with electron backscattered diffraction technique. The brazing was made with Boehler SG-CuSi3 brazing material.

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Saida, Kazuyoshi, and Tomo Ogura. "Hot Cracking Susceptibility in Duplex Stainless Steel Welds." Materials Science Forum 941 (December 2018): 679–85. http://dx.doi.org/10.4028/www.scientific.net/msf.941.679.

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The hot cracking (solidification cracking) susceptibility in the weld metals of duplex stainless steels were quantitatively evaluated by Transverse-Varestraint test with gas tungsten arc welding (GTAW) and laser beam welding (LBW). Three kinds of duplex stainless steels (lean, standard and super duplex stainless steels) were used for evaluation. The solidification brittle temperature ranges (BTR) of duplex stainless steels were 58K, 60K and 76K for standard, lean and super duplex stainless steels, respectively, and were comparable to those of austenitic stainless steels with FA solidification mode. The BTRs in LBW were 10-15K lower than those in GTAW for any steels. In order to clarify the governing factors of solidification cracking in duplex stainless steels, the solidification segregation behaviours of alloying and impurity elements were numerically analysed during GTAW and LBW. Although the harmful elements to solidification cracking such as P, S and C were segregated in the residual liquid phase in any joints, the solidification segregation of P, S and C in LBW was inhibited compared with GTAW due to the rapid cooling rate in LBW. It followed that the decreased solidification cracking susceptibility of duplex stainless steels in LBW would be mainly attributed to the suppression of solidification segregation of P, S and C.

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Cao, Luo Wei, Chen Yang Du, and Guo Shan Xie. "Effects of Sensitization and Hydrogen on Stress Corrosion Cracking of 18-8 Type Stainless Steel." Applied Mechanics and Materials 853 (September 2016): 168–72. http://dx.doi.org/10.4028/www.scientific.net/amm.853.168.

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Austenitic stainless steels always failure in intergranular corrosion, stress corrosion cracking and their synthesis. Moreover, hydrogen also plays an important role in SCC. Effects of sensitization and hydrogen on stress corrosion cracking of 18-8 type stainless steel (304 and 304L) were investigated in this paper. Three states of specimens, including as-received, sensitization and hydrogen precharged, were prepared for this study. Two kinds of environment, involving air and 0.5mol H2SO4 +0.01mol KSCN solution, were selected to compare the SCC sensitivity of different condition of 304 and 304L by the slow strain rate tensile test (SSRT). Fracture morphology was observed by scanning electron microscope (SEM) to check the SCC fracture characteristic. In SEM, evident secondary cracks were found on the fracture surface of 304. Results showed that: 1) hydrogen precharged 304L has high SCC sensitivity (85.7% ) compared with low SCC sensitivity in solution (14.5%), which reveal that SCC of 304L is hydrogen-induced cracking type; 2) 304 stainless steel has high SCC sensitivity (60.8%); 3) sensitization increases the SCC sensitivity of 304 stainless steel (from 60.8% to 71.4%).

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Anaele, J. U., O. O. Onyemaobi, C. S. Nwobodo, and C. C. Ugwuegbu. "Effect of Electrode Types on the Solidification Cracking Susceptibility of Austenitic Stainless Steel Weld Metal." International Journal of Metals 2015 (August 12, 2015): 1–7. http://dx.doi.org/10.1155/2015/213258.

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The effect of electrode types on the solidification cracking susceptibility of austenitic stainless steel weld metal was studied. Manual metal arc welding method was used to produce the joints with the tungsten inert gas welding serving as the control. Metallographic and chemical analyses of the fusion zones of the joints were conducted. Results indicate that weldments produced from E 308-16 (rutile coated), E 308-16(lime-titania coated) electrodes, and TIG welded joints fall within the range of 1.5≤Creq./Nieq.≤1.9 and solidified with a duplex mode and were found to be resistant to solidification cracking. The E 308-16 weld metal had the greatest resistance to solidification cracking. Joints produced from E 310-16 had Creq./Nieq. ratio < 1.5 and solidified with austenite mode. It was found to be susceptible to solidification cracking. E 312-16 produced joints having Creq./Nieq. ratio > 1.9 and solidified with ferrite mode. It had a low resistance to solidification cracking.

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Kusmoko, Alain, D. Dunne, H. Li, and D. Nolan. "Laser Cladding of Stainless Steel Substrates with Stellite 6." Materials Science Forum 773-774 (November 2013): 573–89. http://dx.doi.org/10.4028/www.scientific.net/msf.773-774.573.

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Stellite 6 coatings were produced using laser cladding of two different steel substrates (martensitic and austenitic stainless steels). The chemical composition and microstructure of these coatings were characterized by atomic absorption spectroscopy, optical microscopy and scanning electron microscopy. The microhardness of the coatings was measured and the wear mechanism of the coatings was examined using a pin-on-plate (reciprocating) wear testing machine. The results showed less cracking and pore development for Stellite 6 coatings applied to the martensitic stainless steel (SS) substrate. The wear test results showed that the weight loss for the coating on martensitic SS was significantly lower than for the austenitic SS substrate. It is concluded that the higher hardness of the coating on the martensitic SS, together with the harder and more rigid substrate increase the wear resistance of the Stellite 6 coating.

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Kenik, E. A., J. T. Busby, M. K. Miller, A. M. Thuvander, and G. Was. "Grain Boundary Segregation and Irradiation-Assisted Stress Corrosion Cracking of Stainless Steels." Microscopy and Microanalysis 5, S2 (August 1999): 760–61. http://dx.doi.org/10.1017/s1431927600017128.

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Irradiation-assisted stress corrosion cracking (IASCC) of irradiated austenitic stainless steels has been attributed to both microchemical (radiation-induced segregation (RIS)) and microstructural (radiation hardening) effects. The flux of radiation-induced point defects to grain boundaries results in the depletion of Cr and Mo and the enrichment of Ni, Si, and P at the boundaries. Similar to the association of stress corrosion cracking with the depletion of Cr and Mo in thermally sensitized stainless steels, IASCC is attributed in part to similar depletion by RIS. However, in specific heats of irradiated stainless steel, “W-shaped” Cr profiles have been observed with localized enrichment of Cr, Mo and P at grain boundaries. It has been show that such profiles arise from pre-existing segregation associated with intermediate rate cooling from elevated temperatures. However, the exact mechanism responsible for the pre-existing segregation has not been identified.Two commercial heats of stainless steel (304CP and 316CP) were forced air cooled from elevated temperatures (∽1100°C) to produce pre-existing segregation.

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Bhandari, Deepak, Rahul Chhibber, Navneet Arora, and Rajeev Mehta. "Investigations on Design and Formulation of Buttering Layer Electrode Coatings for Bimetallic Welds." Materials Science Forum 880 (November 2016): 37–40. http://dx.doi.org/10.4028/www.scientific.net/msf.880.37.

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The bimetallic welds (BMWs) between ferritic low alloy steels and austenitic stainless steel are used widely in steam generators of the power plants. The adoption of these welds in wide industrial applications provides feasible solutions for the flexible design of the products by using each material efficiently and economically. The present paper is an effort towards studying the development of austenitic stainless steel buttering filler material for bimetallic weld joint. The work aims at the design and development of buttering layer electrode coatings for shielded metal arc welding process using extreme vertices design methodology suggested by McLean and Anderson to study the effect of electrode coating ingredients on the buttering layer metal composition and delta ferrite content to prevent solidification cracking.

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Negi, B. S. "Case Studies on Field Repairs of Stainless Steel Components in Refinery." Advanced Materials Research 794 (September 2013): 375–79. http://dx.doi.org/10.4028/www.scientific.net/amr.794.375.

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Stainless steels (SS) possess excellent corrosion, creep and high temperature oxidation resistance and are invariably used in refinery for construction of heater tubes, tube supports, Heat exchanger bundles, piping and internal lining of pressure vessels. Ferritic stainless steel type 405 is used for column strip-lining, martensitic stainless steel type 410 is used for column trays and heater tubes and austenitic stainless steel family is used very extensively for lining, piping, heat exchanger, heater tubes and tube supports. On-stream and turnaround condition monitoring of plant and equipment are carried out for health assessment and mitigation of premature failure. However, catastrophic failures of stainless steel due to stress corrosion cracking, thermal fatigue and stress relaxation cracking are encountered in addition to bulging and cracking of strip-lining. Field repairs of these components are required to be done. Stainless steels are difficult to weld due to low thermal conductivity, higher coefficient of thermal expansion, fissuring and solidification cracking problem during welding. Lower heat input and fast cooling facilitate the welding process. Welding of service exposed stainless steels is more challenging, as it has already undergone metallurgical degradation. Welding of stainless steels is carried out using TIG and SMAW process with matching electrode after establishing the welding specification procedures and welders qualification. Field repairs of stainless steels components are also attempted with original procedures and in case of difficulties, a buttering layer of inconel (ERNiCr3) or ER 309Mo is provided on the welding surface before using matching electrodes. Quality assurance of weld joint is ensured by stage-wise inspection and non-destructive testing. Dye penetrant test of root run and radiographic examination of final weld joint are most common. Post weld heat treatment is done as per code requirement. This Paper highlights three case studies on field repairs of stainless steel components in refinery. 1. Welding procedure followed for repair of bulged and cracked SS 316 strip-lining and cladding on carbon steel backing material. It is a dissimilar welding of SS 316L with degraded carbon steel. 2. Field welding of SS 347 Piping components, which has undergone thermal relaxation cracking at fillet joints. 3. Welding repair of SS 310 cast heater tube support conforming to A 297 Gr HK 40. The Paper also presents brief failure analysis with reasons and remedies.

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28

Alyousif, Osama M., and Rokuro Nishimura. "On the Stress Corrosion Cracking and Hydrogen Embrittlement Behavior of Austenitic Stainless Steels in Boiling Saturated Magnesium Chloride Solutions." International Journal of Corrosion 2012 (2012): 1–11. http://dx.doi.org/10.1155/2012/462945.

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The stress corrosion cracking (SCC) and hydrogen embrittlement (HE) behaviors for types 304, 310, and 316 austenitic stainless steels were investigated in boiling saturated magnesium chloride solutions using a constant load method under different conditions including test temperature, applied stress, and sensitization. Both of type 304 and type 316 stainless steels showed quite similar behavior characteristics, whereas type 310 stainless steel showed a different behavior. The time to failure (tf) parameter was used among other parameters to characterize the materials behavior in the test solution and to develop a mathematical model for predicting the time to failure in the chloride solution. The combination of corrosion curve parameters and fracture surface micrographs gave some explanation for the cracking modes as well as an indication for the cracking mechanisms. On the basis of the results obtained, it was estimated that intergranular cracking was resulted from hydrogen embrittlement due to strain-induced formation of martensite along the grain boundaries, while transgranular cracking took place by propagating cracks nucleated at slip steps by dissolution.

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29

MITANI, Susumu, Hisayoshi TAKAZAWA, Mitsumasa HISHIYAMA, and Mikio NISHIHATA. "Environmental cracking characteristics of deep-drawn austenitic stainless steel cases." Journal of the Society of Materials Science, Japan 39, no. 439 (1990): 432–37. http://dx.doi.org/10.2472/jsms.39.432.

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30

Al-Mukhtar, Ahmed M., and Qasim M. Doos. "Cracking Phenomenon in Spot Welded Joints of Austenitic Stainless Steel." Materials Sciences and Applications 04, no. 10 (2013): 656–62. http://dx.doi.org/10.4236/msa.2013.410081.

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31

Ogosi, E. I., U. B. Asim, M. A. Siddiq, and M. E. Kartal. "Modelling Hydrogen Induced Stress Corrosion Cracking in Austenitic Stainless Steel." Journal of Mechanics 36, no. 2 (February 21, 2020): 213–22. http://dx.doi.org/10.1017/jmech.2019.60.

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ABSTRACTA model has been developed which simulates the deformation of single crystal austenitic stainless steels and captures the effects of hydrogen on stress corrosion cracking. The model is based on the crystal plasticity theory which relates critical resolved shear stress to plastic strain and the strength of the crystal. We propose an analytical representation of hydrogen interactions with the material microstructure during deformation and simulate the effects hydrogen will have on void growth prior to fracture. Changes in the mechanical properties of the crystal prior to fracture are governed by the interaction of hydrogen atoms and ensembles of dislocations as the crystal plastically deforms and is based on the hydrogen enhanced localised plasticity (HELP) mechanism. The effects of hydrogen on void growth are considered by analysing the effect of hydrogen on the mechanical property of material bounding an embedded void. The model presented has been implemented numerically using the User Material (UMAT) subroutine in the finite element software (ABAQUS) and has been validated by comparing simulated results with experimental data. Influencing parameters have been varied to understand their effect and test sensitivities.

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32

Jeong, Jae-Yoon, Myeong-Woo Lee, Yun-Jae Kim, Poh-Sang Lam, and Andrew J. Duncan. "Chloride-Induced Stress Corrosion Cracking Tester for Austenitic Stainless Steel." Journal of Testing and Evaluation 49, no. 2 (August 3, 2020): 20200115. http://dx.doi.org/10.1520/jte20200115.

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33

Ravibharath, R., V. Muthupandi, P. Bala Srinivasan, and K. Devakumaran. "Characterization of Solidification Cracking in 304HCu Austenitic Stainless Steel Welds." Transactions of the Indian Institute of Metals 73, no. 9 (July 21, 2020): 2345–53. http://dx.doi.org/10.1007/s12666-020-02028-1.

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34

Vichytil, Clemens, G. Mori, Reinhard Pippan, M. Panzenböck, and Rainer Fluch. "Crack Growth Rates and Corrosion Fatigue of Austenitic Stainless Steels in High Chloride Solutions." Key Engineering Materials 488-489 (September 2011): 97–100. http://dx.doi.org/10.4028/www.scientific.net/kem.488-489.97.

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Purpose: Applications for highly corrosive environments and cyclic loading are often made out of austenitic stainless steels. Corrosion fatigue and crack propagation behaviour has been studied to determine failure processes and damage mechanisms. Approach: CrNiMo stabilized austenitic stainless steel and CrMnN austenitic stainless steel in solution annealed and cold worked condition are compared. S/N curves and crack propagation rate curves are recorded in 43 wt% CaCl2solution at 120 °C, which resembles most severe potential service conditions. For comparison these experiments are also performed in inert glycerine. Additionally, the electrochemical behaviour of these materials has been studied. Findings: The CrMnN steels have excellent mechanical properties but are very susceptible to stress corrosion cracking in the test solution. The fatigue limit as well as the threshold for long crack growth are significantly reduced in corrosive environment. Moreover these steels exhibit a remarkable increase in the propagation rate, which is extremely pronounced in the near threshold region. This effect is enhanced by cold working. CrNiMo steels also show a reduction in the fatigue limit, but it is less pronounced compared to CrMnN steels. The threshold is significantly reduced in corrosive environment, but propagation rate is lower in corrosive environment compared to inert glycerine. Possible explanations of this surprising behaviour are discussed.

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35

Islam, Mazharul M., Thierry Couvant, Philippe Marcus, and Boubakar Diawara. "Stress Concentration in the Bulk Cr2O3: Effects of Temperature and Point Defects." Journal of Chemistry 2017 (2017): 1–8. http://dx.doi.org/10.1155/2017/7039436.

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Modeling the growth and failure of passive oxide films formed on stainless steels is of general interest for the use of stainless steel as structural material and of special interest in the context of life time extension of light water reactors in nuclear power plants. Using the DFT+U approach, a theoretical investigation on the resistance to failure of the chromium-rich inner oxide layer formed at the surface of chromium-containing austenitic alloys (stainless steel and nickel based alloys) has been performed. The investigations were done for periodic bulk models. The data at the atomic scale were extrapolated by using the Universal Binding Energy Relationships (UBERs) model in order to estimate the mechanical behavior of a 10 μm thick oxide scale. The calculated stress values are in good agreement with experiments. Tensile stress for the bulk chromia was observed. The effects of temperature and structural defects on cracking were investigated. The possibility of cracking intensifies at high temperature compared to 0 K investigations. Higher susceptibility to cracking was observed in presence of defects compared to nondefective oxide, in agreement with experimental observation.

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36

Sasaki, Toshihiko, Kei Koda, Yohei Fujimoto, Shoichi Ejiri, Tamaki Suzuki, and Yuichi Kobayashi. "X-Ray Residual Stress Analysis of Stainless Steel Using cosα Method." Advanced Materials Research 922 (May 2014): 167–72. http://dx.doi.org/10.4028/www.scientific.net/amr.922.167.

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This paper shows X-ray residual stress analysis of stainless steel using 2-dimensional detection method. The 2-dimensional detection method of X-ray stress measurement will determine stress by conducting a 2-dimensional detecting of a Debye ring and analyzing the image data. The basic of typical austenitic stainless steel (JIS SUS304) was studied in this study, considering the fact that, at certain power plants, maintenance takes place to prevent stress corrosion cracking by adding compressive residual stress to the structure..

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37

Manwatkar, Sushant, S. V. S. Narayana Murty, and P. Ramesh Narayanan. "Fatigue Failure of Hydroformed AISI 316L Stainless Steel Bellows." Materials Science Forum 830-831 (September 2015): 713–16. http://dx.doi.org/10.4028/www.scientific.net/msf.830-831.713.

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Austenitic stainless steel AISI 316L is used for components of cryogenic engine in satellite launch vehicles due to its better mechanical properties at low temperatures. In one such application, AISI 316L stainless steel bellows are used in electro-pneumatic command valve of a cryogenic engine. This valve employs a hydro-formed bellow of 0.14mm thickness as an actuator element. When one of the electro-pneumatic command valve was vibrated without pressure, crack was noticed at the inner diameter of the bellow. Detailed metallurgical analysis indicated that the cracking to be due to fatigue.

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38

Chabaud-Reytier, M., L. Allais, C. Caes, P. Dubuisson, and A. Pineau. "Mechanisms of stress relief cracking in titanium stabilised austenitic stainless steel." Journal of Nuclear Materials 323, no. 1 (November 2003): 123–37. http://dx.doi.org/10.1016/j.jnucmat.2003.08.034.

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39

Brooks, J. A., and A. W. Thompson. "Microstructural development and solidification cracking susceptibility of austenitic stainless steel welds." International Materials Reviews 36, no. 1 (January 1991): 16–44. http://dx.doi.org/10.1179/imr.1991.36.1.16.

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40

FUJII, Tomoyuki, Keiichiro TOHGO, Yota MORI, and Yoshinobu SHIMAMURA. "Nucleation behavior of intergranular stress corrosion cracking in austenitic stainless steel." Proceedings of the Materials and Mechanics Conference 2017 (2017): OS1610. http://dx.doi.org/10.1299/jsmemm.2017.os1610.

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41

Lu, B. T., Z. K. Chen, J. L. Luo, B. M. Patchett, and Z. H. Xu. "Pitting and stress corrosion cracking behavior in welded austenitic stainless steel." Electrochimica Acta 50, no. 6 (January 2005): 1391–403. http://dx.doi.org/10.1016/j.electacta.2004.08.036.

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42

Yan, Yingjie, Yu Yan, Yang He, Jinxu Li, Yanjing Su, and Lijie Qiao. "Hydrogen-induced cracking mechanism of precipitation strengthened austenitic stainless steel weldment." International Journal of Hydrogen Energy 40, no. 5 (February 2015): 2404–14. http://dx.doi.org/10.1016/j.ijhydene.2014.12.020.

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43

Prabha, B., P. Sundaramoorthy, S. Suresh, S. Manimozhi, and B. Ravishankar. "Studies on Stress Corrosion Cracking of Super 304H Austenitic Stainless Steel." Journal of Materials Engineering and Performance 18, no. 9 (December 2009): 1294–99. http://dx.doi.org/10.1007/s11665-008-9347-9.

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44

Rozenak, P., and D. Eliezer. "Phase changes related to hydrogen-induced cracking in austenitic stainless steel." Acta Metallurgica 35, no. 9 (September 1987): 2329–40. http://dx.doi.org/10.1016/0001-6160(87)90081-2.

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45

Jayakumar, Tammana, A. K. Bhaduri, M. D. Mathew, Shaju K. Albert, and U. Kamachi Mudali. "Nitrogen Enhanced 316LN Austenitic Stainless Steel for Sodium Cooled Fast Reactors." Advanced Materials Research 794 (September 2013): 670–80. http://dx.doi.org/10.4028/www.scientific.net/amr.794.670.

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For the future sodium-cooled fast reactors (SFRs), which are envisaged with a design life of 60 years, nitrogen-enhanced 316LN austenitic stainless steel (SS) with improved high-temperature properties is being developed. To optimize the enhanced nitrogen content in 316LN SS, the effect of nitrogen on its tensile, creep and low cycle fatigue behavior has been investigated. For different heats of 316LN SS containing 0.07-0.22 wt% nitrogen, the tensile and creep properties increased with increase in nitrogen content, while low cycle fatigue properties peaked at 0.14 wt% nitrogen. Finally, based on the evaluation of the hot cracking susceptibility of the different heats of 316LN SS with varying nitrogen content, using the Varestraint and Gleeble hot-ductility tests, the nitrogen content for the nitrogen-enhanced 316LN SS has been optimized at a level of 0.14 wt%. The 0.14 wt% nitrogen content in this optimised composition shifts the solidification mode of the weld metal to fully austenitic region, including that due to dilution of nitrogen from the base metal, thereby increasing its hot cracking susceptibility. This necessitated development and qualification of welding electrodes for obtaining weld metal with 0.14 wt% nitrogen by optimising the weld metal chemistry so as to obtain the requisite delta ferrite content, tensile properties, and very importantly impact toughness both in the as-welded and aged conditions. Studies on localised corrosion behaviour of nitrogen-enhanced 316LN SS indicated the beneficial effect of nitrogen addition to sensitization, pitting, intergranular corrosion, stress corrosion cracking and corrosion fatigue.

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46

Dou, Yuchen, Hong Luo, and Jing Zhang. "Elastic Properties of FeCr20Ni8Xn (X = Mo, Nb, Ta, Ti, V, W and Zr) Austenitic Stainless Steels: A First Principles Study." Metals 9, no. 2 (January 29, 2019): 145. http://dx.doi.org/10.3390/met9020145.

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Austenitic stainless steels suffer from intergranular corrosion and stress corrosion cracking when exposed to elevated temperature (500–800 °C). Under these environments, Cr-carbides and Cr-carbontrides precipitate at the grain boundaries, which results in the formation of Cr-depleted zone. In practice, alloying elements could be added into austenitic stainless steels to modify the precipitation processes. Besides the precipitation processes, the elastic properties of the iron matrix would be influenced. Using the exact muffin-tin orbitals (EMTO) method, the solute effects on the elastic properties of FeCr20Ni8 austenitic stainless steels were studied. Based on the simulated shear modulus (G) and bulk modulus (B), we proposed a design map for FeCr20Ni8 based alloys, aiming to provide a basis for the design of high-performance austenitic stainless steels.

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47

Abass, M. H., M. S. Alali, W. S. Abbas, and A. A. Shehab. "Study of solidification behaviour and mechanical properties of arc stud welded AISI 316L stainless steel." Journal of Achievements in Materials and Manufacturing Engineering 1, no. 97 (November 3, 2019): 5–14. http://dx.doi.org/10.5604/01.3001.0013.7944.

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Purpose: This paper aims to investigate the impact of arc stud welding (ASW) process parameters on the microstructure and mechanical properties of AISI 316L stainless steel stud/plate joint. Design/methodology/approach: The weld performed using ASW machine. The influence of welding current and time on solidification mode and microstructure of the fusion zone (FZ) was investigated using optical microscope and scanning electron microscope (SEM). Microhardness and torque strength tests were utilised to evaluate the mechanical properties of the welding joint. Findings: The results showed that different solidification modes and microstructure were developed in the FZ. At 400 and 600 A welding currents with 0.2 s welding time, FZ microstructure characterised with single phase austenite or austenite as a primary phase. While with 800 A and 0.2 s, the microstructure consisted of ferrite as a primary phase. Highest hardness and maximum torque strength were recorded with 800 A. Solidification cracking was detected in the FZ at fully austenitic microstructure region. Research limitations/implications: The main challenge in this work was how to avoid the arc blow phenomenon, which is necessary to generate above 300 A. The formation of arc blow can affect negatively on mechanical and metallurgical properties of the weld. Practical implications: ASW of austenitic stainless steel are used in multiple industrial sectors such as heat exchangers, boilers, furnace, exhaust of nuclear power plant. Thus, controlling of solidification modes plays an important role in enhancing weld properties. Originality/value: Study the influence of welding current and time of ASW process on solidification modes, microstructure and mechanical properties of AISI 316 austenitic stainless steel stud/plate joint.

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48

YU, PING, JUSTIN MORROW, and SINDO KOU. "Resistance of Austenitic Stainless Steels to Ductility-Dip Cracking: Mechanisms." Welding Journal 100, no. 09 (September 1, 2021): 291–301. http://dx.doi.org/10.29391/2021.100.026.

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In Ni-based alloys, precipitates that form along grain boundaries (GBs) during terminal solidification have been shown to pin GBs and resist GB sliding, which can cause ductility-dip cracking (DDC). As a result, it is often suggested that the stainless steel skeletal/lacy  in a  matrix resists DDC because it pins GBs. In the present study, austenitic stainless steels 304, 316, 310, and 321 were quenched with liquid Wood’s metal (75˚C) during welding. Quenching captured the elevated-temperature micro-structure and simultaneously induced cracking, thus revealing the mechanisms of the resistance to DDC. In addition, DDC was much higher in 310 than 304, 316, and 321, which is consistent with results of conventional tests. Both 304 and 316 solidified as columnar  grains, with continuous  formed along GBs soon after solidification to resist DDC along the GBs. 321 solidified as equiaxed grains of  instead of columnar, and the tortuous GBs associated with equiaxed grains resisted DDC. 310, however, solidified as coarse, straight  grains with little  along the GBs, and solidification GBs migrated to become locally straight. The resulting GBs were long, straight, and naked, which is ideal for DDC. In 304, 316, or 321, skeletal/lacy  in a  matrix did not exist in the fusion zone near the mushy zone, where DDC occurs. This proved skeletal/lacy  cannot resist DDC as often suggested. Instead, the present study identified two new mechanisms of resistance to DDC: 1) formation of continuous or nearly continuous  along boundaries of columnar  grains and 2) solidification as equiaxed  grains.

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Ghosh Acharyya, Swati, M. Kiran Kumar, and Vivekanand Kain. "Studying the Mechanism behind Stress Corrosion Cracking of Non Sensitized 304L Austenitic Stainless Steel." Advanced Materials Research 794 (September 2013): 564–74. http://dx.doi.org/10.4028/www.scientific.net/amr.794.564.

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The susceptibility of non sensitized 304L stainless steel (SS) components towards stress corrosion cracking (SCC) has been studied here in the light of the significant role played bysurface working operations. The plant experience shows that the fracture surfaces of non sensitized 304L stainless steel components have no signs of carbide precipitation. However, heavy plastic deformation has been evidenced in the form of high density of slip bands on the surface up to a depth of about 100 μm with high tensile residual stresses near the surface. The present study has established that the primary cause of the increase in SCC susceptibility is the heavy plastic deformation near the surface and high magnitude of tensile residual stresses which is a consequence of the surface finishing operations like machining and grinding. In this study, solution annealed 304L stainless steel has been subjected to a) surface working operations like machining and grinding and b) bulk deformation operations such as 10 % cold rolling operation. The materials in different conditions where then subjected to detailed a) microstructural characterisation, b) electrochemical characterisation and c) tests for determining the stress corrosion cracking susceptibility. The distinct differences in the micro structure as a result of bulk deformation vs. surface deformation of 304L austenitic stainless steel were highlighted and correlated to the susceptibility towards stress corrosion cracking. The effect of surface working on the nature and composition of high temperature (300 °C and 10 MPa) oxide formed on 304L stainless steel has been studied in-situ by contact electric resistance (CER) and electrochemical impedance spectroscopy measurements using controlled distance electrochemistry technique in high purity water (conductivity < 0.1 μScm-1) at 300 °C and 10 MPa in an autoclave connected to a recirculation loop system. The results highlighted the distinct differences in the oxidation behaviour of surface worked material as compared to solution annealed material in terms of specific resistivity and low frequency Warburg impedance.

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50

Ziewiec, A. "Study of the Weldability of Austenitic PH Steel for Power Plants." Archives of Metallurgy and Materials 61, no. 2 (June 1, 2016): 1109–14. http://dx.doi.org/10.1515/amm-2016-0186.

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Abstract The article presents the results of Transvarestraint test of a modern precipitation hardened steel X10CrNiCuNb18-9-3 with copper. For comparison, the results of tests of conventional steel without the addition of copper X5CrNi18-10 are presented. The total length of all cracks and the maximum length of cracks were measured. The study of microstructure (LM, SEM) showed that the austenitic stainless steel X10CrNiCuNb18-9-3 is very prone to hot cracking. After performing the Transvarestraint tests three types of cracks were observed: solidification cracks occurring during crystallization, liquation cracks due to segregation in the heat affected zone (HAZ) and surface cracks. Niobium carbonitrides dispersed in the bands of segregation are the reason of high susceptibility to liquation cracking. Segregation of copper occurring during solidification causes of surface cracking. A combined effect of copper and stresses contributes to formation of hot microcracks. These microcracks propagate to a depth of 20-30 μm.

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Journal articles on the topic 'Austenitic stainless steel Cracking'

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