Relevant bibliographies by topics / Steel – Cracking

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  1. Journal articles
  2. Dissertations / Theses
  3. Books
  4. Book chapters
  5. Conference papers
  6. Reports

Academic literature on the topic 'Steel – Cracking'

Author: Grafiati
Published: 4 June 2021
Last updated: 1 February 2022

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Journal articles on the topic "Steel – Cracking"

1

Stradomski, Z., S. Stachura, and G. Stradomski. "Fracture Mechanisms in Steel Castings." Archives of Foundry Engineering 13, no. 3 (September 1, 2013): 88–91. http://dx.doi.org/10.2478/afe-2013-0066.

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Abstract The investigations were inspired with the problem of cracking of steel castings during the production process. A single mechanism of decohesion - the intergranular one - occurs in the case of hot cracking, while a variety of structural factors is decisive for hot cracking initiation, depending on chemical composition of the cast steel. The low-carbon and low-alloyed steel castings crack due to the presence of the type II sulphides, the cause of cracking of the high-carbon tool cast steels is the net of secondary cementite and/or ledeburite precipitated along the boundaries of solidified grains. Also the brittle phosphor and carbide eutectics precipitated in the final stage solidification are responsible for cracking of castings made of Hadfield steel. The examination of mechanical properties at 1050°C revealed low or very low strength of high-carbon cast steels.
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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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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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TUMULURU, MURALI. "Effect of Silicon and Retained Austenite on the Liquid Metal Embrittlement Cracking Behavior of GEN3 and High-Strength Automotive Steels." Welding Journal 98, no. 12 (December 1, 2019): 351s—364s. http://dx.doi.org/10.29391/2019.98.029.

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GEN3 steels are a new family of automotive sheet steels developed and commercialized in the last three years, specifically for body-in-white applications. The high ductility in GEN3 steels is typically achieved through the transformation-induced plasticity (TRIP) effect by the addition of silicon or aluminum. When these steels are formed into parts, the TRIP effect of austenite to martensite transformation provides enhanced ductility. Typically, 10 to 12 micrometers of zinc coating (known as galvanized coating) is applied to automotive steel sheets for corrosion protection. Liquid metal embrittlement (LME) cracking can occur during resistance spot welding (RSW) of galvanized steels. LME cracking occurs when molten zinc penetrates prior austenite grain boundaries of the steel substrate. The precise role of silicon in the LME cracking behavior in TRIP and GEN3 steels is unknown. Therefore, a study was undertaken to examine the role of silicon in LME cracking behavior of GEN3 steels. The purpose was also to examine if the presence of retained austenite is required for LME cracking to occur. In this study, laboratory heats were prepared using three silicon levels. Samples cut from galvanized panels were welded using a resistance spot welding machine, and weld areas were examined metallographically for the presence of LME cracks. Gleeble® simulations were done to study the LME behavior of the three steels prepared. Base materials were examined with a scanning electron microscope using the electron back-scattered diffraction (EBSD) method to examine the nature of grain boundaries found. The effect of retained austenite in LME cracking was studied using the Gleeble®. Both RSW and Gleeble® results showed silicon promotes LME cracking in steels, predominantly in the weld heat-affected zones(HAZs). More low-energy, low-coincidence site lattice (CSL) boundaries were found as the silicon content of the steel was decreased. These boundaries do not host cracks. Higher silicon appeared to shrink the safe temperature range over which LME cracks could be avoided, thus indicating heat in-put control to limit cracks has limited windows as the silicon in steel goes up. It was shown that the presence of retained austenite in steel is not a prerequisite for LME cracking to occur.
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Terasaki, F., H. Ohtani, A. Ikeda, and M. Nakanishi. "Steel Plates for Pressure Vessels in Sour Environment Applications." Proceedings of the Institution of Mechanical Engineers, Part A: Power and Process Engineering 200, no. 3 (August 1986): 141–58. http://dx.doi.org/10.1243/pime_proc_1986_200_021_02.

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It is well known that wet hydrogen sulphide (H2S) can cause embrittlement of steels, hydrogen induced cracking (HIC) and sulphide stress corrosion cracking (SSCC). Several fractures of pipelines handling sour crude oil or gas led to vigorous researches on these problems. As similar failures have also been experienced in petroleum refinery equipment, degradation of steel by hydrogen sulphide is now recognized as a serious environmental problem. The paper considers the mechanism and factors involved in HIC. This type of cracking occurs mainly in the parent steels. The susceptibility of steels to cracking is influenced strongly by inhomogeneities such as the shape and distribution of non-metallic inclusions, and segregation of alloying elements. These have a significant effect on HIC because they modify the microstructures in the segregated regions. With reference to environmental factors, these mainly concern the influence of H2S partial pressures, pH of the solutions and other phenomena relevant to the absorption of hydrogen by the steel. SSCC poses problems in weld zones. It can occur especially in heat affected zones (HAZ) with high hardnesses. Such cracking can be prevented by the control of hardness by a suitable selection of the chemical composition of the steel and the welding conditions. Nevertheless, countermeasures similar to those described for the prevention of HIC are necessary to prevent SSCC in HAZ even with relatively low hardness. Research on factors influencing HIC and SSCC has resulted in the development of steels which are highly resistant to wet H2S cracking. These steels have been supplied in plate form for pressure vessels. Experience has confirmed the good performance of welded constructions in aggressive service environments.
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Jones, R., and S. C. Forth. "Cracking in D6ac steel." Theoretical and Applied Fracture Mechanics 53, no. 1 (February 2010): 61–64. http://dx.doi.org/10.1016/j.tafmec.2009.12.005.

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Fydrych, Dariusz, Jerzy Łabanowski, and Grzegorz Rogalski. "Weldability of high strength steels in wet welding conditions." Polish Maritime Research 20, no. 2 (April 1, 2013): 67–73. http://dx.doi.org/10.2478/pomr-2013-0018.

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Abstract In this paper are characterized problems of high strength steel weldability in underwater wet welding conditions. Water as a welding environment intensifies action of unfavourable factors which influence susceptibility to cold cracking of welded steel joints. The susceptibility to cold cracking of S355J2G3 steel and S500M steel in wet conditions was experimentally estimated (by using Tekken test). It was concluded that the steels in question are characterized by a high susceptibility to formation of cracks in welds. Usefulness of the proposed Temper Bead Welding technique (TBW) was experimentally verified as a method for improving weldability of the steels in the analyzed conditions.
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Kong, Fan Yu. "Research on Test about Stress Corrosion Cracking of SPV50Q Spherical Tank." Advanced Materials Research 284-286 (July 2011): 2437–41. http://dx.doi.org/10.4028/www.scientific.net/amr.284-286.2437.

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SPV50Q steel belongs to high-alloyed steel that is widely used to fabricate storage tank for liquefied petroleum gas. However, it has a great tendency to the problem of environmental cracking under the service condition of LPG containing wet sulfide hydrogen surpassing the lowest allowance for steels. In order to quantitatively evaluate the cracking susceptibility on this steel in the wet H2S environment, the pre-fatigue crack M-WOL specimen stress corrosion cracking tests in three H2S concentrations were performed under the different welding conditions, and in safety performance analysis of equipment, and preventing countermeasure had been proposed. The method could be extended forecasting accident in LPG SCC.
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Joseline, Dyana, Radhakrishna G. Pillai, and Lakshman Neelakantan. "Initiation of Stress Corrosion Cracking in Cold-Drawn Prestressing Steel in Hardened Cement Mortar Exposed to Chlorides." Corrosion 77, no. 8 (May 28, 2021): 906–22. http://dx.doi.org/10.5006/3730.

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Cold-drawn, high-strength, prestressing (PS) steel strands are widely used in pretensioned concrete (PTC) structures. This paper discusses the stress corrosion cracking (SCC) of PS steel embedded in cement mortar and gradually exposed to chlorides. Various stages of the passive to active (P-to-A) transition, which marks the onset of SCC, were investigated using the electrochemical impedance spectroscopy technique. The key mechanisms were identified and confirmed using scanning electron microscopy/energy dispersive x-ray analysis, x-ray diffarction, and confocal Raman spectroscopy. It was found that the passive film on unstressed PS steel has better electrochemical characteristics than that on conventional steel rebars. However, the residual tensile stress at the surface of PS steels can assist passive film cracking after chloride attack—contrary to the pitting corrosion without cracking of passive film in conventional steels. Further, tests indicated that the concentration of chlorides required to crack the passive film in PS steels can reduce by about 50% when prestressed—as in field structures. Chemical composition, stress state, and microstructural features at the PS steel surface were identified as possible factors influencing the initiation of SCC in PTC structures.
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Cheng, Xiao Ying, Hong Yuan Chen, Wen Qing Liu, and Zhi Juan Zhang. "Influence of Mooring Chain Steel Strength on Stress Corrosion Cracking." Applied Mechanics and Materials 404 (September 2013): 32–39. http://dx.doi.org/10.4028/www.scientific.net/amm.404.32.

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Two strength mooring chain steels were used to investigate the stress corrosion cracking (SCC) in synthetic seawater. The resistance of both strength steels to SCC was similar in neutral synthetic seawater. But the failure mechanism was different. For lower strength steel, it is mainly induced by anodic dissolution, while for higher strength steel, by hydrogen embrittlement. The reason was elucidated from their microstructures and corrosion characteristics.
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Dissertations / Theses on the topic "Steel – Cracking"

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Raseroka, Mantsaye S. "Controlled chloride cracking of austenitic stainless steel." Pretoria : [s.n.], 2009. http://upetd.up.ac.za/thesis/available/etd-07032009-120615/.

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Wong, T. M. "Stress corrosion cracking in a high strength steel." Thesis, University of Canterbury. Engineering, 1986. http://hdl.handle.net/10092/6429.

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This thesis falls into four fields of study. The first is a survey of relevant literature concerning the many theories of stress corrosion cracking and hydrogen embritt1ement. This includes descriptions of the mechanisms of stress corrosion cracking (SCC) and outlines electromechanical processes and stress - sorption theory. Four widely accepted mechanisms for environment assisted cracking are also outlined. They are, 1) Embritt1ement resulting from accumulated hydrogen at embritt1ement sites, 2) Lowering of surface energy by adsorption of hydrogen, 3) Hydrogen interaction with dislocations, and 4) Lowering of the binding energy by interaction of hydrogen. The literature survey is a significant part of this thesis. The overall objective of the survey is to review a series of current SCC tests on high strength steels. The principal findings from these previous studies are summarized, they provide concrete evidence for the conclusion that SCC of high strength steels is due to hydrogen embrittlement. The second part of the project deals with the development of a stress corrosion loading clevis suitable for testing compact tension specimens. Three existing constant load rigs were developed, and equipment was designed for the successful operation of the rigs. Corrosive environment was applied to the standard compact tension specimen using a novel circulation system based on a magnetic plate stirrer. Corrosive solution (3.5% NaCl) was stirred by the magnetic plate, and the vortex created by the magnetic stirrer was used to create a pumping head. The third area of work dealt with the testing of compact tension specimens of ULTIMO 200 steel using the developed apparatus. The experimental procedures used are based on the application of linear elastic fracture mechanics to stress corrosion cracking. The fourth area of work carried out was to perform slot length calibration experiments on CT specimens by using strain gauges. The results indicated that the specimens pre-cracked in air with a higher dynamic load gave higher threshold stress intensities (KIscc ) than those pre-cracked in air with a lower dynamic load. An electron microscope study indicated evidence of a largely inter granular fatigue crack having occurred in the specimens pre-cracked with a high dynamic load.
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Gedeon, Steven Anthony. "Hydrogen assisted cracking of high strength steel welds." Thesis, Massachusetts Institute of Technology, 1987. http://hdl.handle.net/1721.1/14842.

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Saithala, Janardhan R. "Pitting and stress corrosion cracking of stainless steel." Thesis, Sheffield Hallam University, 2007. http://shura.shu.ac.uk/20311/.

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An investigation has been performed to determine the pitting resistance of stainless steels and stress corrosion cracking of super duplex stainless steels in water containing chloride ions from 25 - 170°C. The steels studied are 12% Cr, FV520B, FV566, 304L, Uranus65, 2205, Ferallium Alloy 255, and Zeron 100. All these commercial materials used in very significant industrial applications and suffer from pitting and stress corrosion failures. The design of a new experimental setup using an autoclave enabled potentiodynamic polarisation experiments and slow strain rate tests in dilute environments to be conducted at elevated temperatures. The corrosion potentials were controlled using a three electrode cell with computer controlled potentiostat. The experimental programme to determine pitting potentials was designed to simulate the service conditions experienced in most industrial plants and develop mathematical model equations to help a design engineer in material selection decision. Stress corrosion resistance of recently developed Zeron100 was evaluated in dilute environments to propose a mechanism in chloride solutions at high' temperatures useful for the nuclear and power generation industry. Results have shown the significance of the composition of alloying elements across a wide range of stainless steels and its influence on pitting. Nitrogen and molybdenum added to modern duplex stainless steels was found to be unstable at higher temperatures. The fractographic results obtained using the scanning electron microscope (SEM) has given insight in the initiation of pitting in modem duplex and super duplex stainless steels. A mathematical model has been proposed to predict pitting in stainless steels based on the effect of environmental factors (temperature, chloride concentration, and chemical composition). An attempt has been made to identify the mechanism of SCC in Zeron100 super duplex stainless steel. The proposed empirical models have shown good correlation between predicted pitting potential values with experimental results. It has been shown that the SCC mechanism in Zeron100 supports the slip assisted anodic dissolution model of SCC. The relationship between pitting and stress corrosion in dilute environments is established and empirical equations have been proposed to determine the damage region for wide range of stainless steels.
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Johnson, David H. "Lüders bands in RPV Steel." Thesis, Cranfield University, 2012. http://dspace.lib.cranfield.ac.uk/handle/1826/8039.

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The R6 procedure is used for the prevention and prediction of crack behaviour and other defects in the reactor pressure vessel(RPV). The RPV material is an upper-bainitic, low alloy steel structure, which deforms inhomogeneously when yielding. The current codes that are used to design and calculate the fracture, within an RPV, assume that the material yields continuously as the size of the L¨uders strain is less than 2%. However, the work of Wenman et al[1] has shown that the inclusion of a L¨uders band during calculations can reduce the residual stress in a material, when compared to standard work-hardening models and, consequently, reduces the amount of conservatism. The objective of the research was to determine whether Wenman’s finding could be generalised and therefore initiate a re-evaluation of R6 procedure, when looking into materials that yield discontinuously. This required further investigation into L¨uders bands, such as using failure assessment diagrams (FADs). The findings from FADs showed that at the temperature range for an RPV steel at -155±C for different micro-structures (assuming that the material deforms homogeneously), this reduced the amount of conservatism. However, at fracture toughness values more representative of room temperature behaviour, the converse was true. That is, assuming a discontinuous yield point reduced the amount of conservatism. It was also shown that the tempered martensite structure could be used as an alternative to the current upper bainitic, low alloy steel that is used in RPVs. Further insight is gained into the nature of a L¨uders band, by developing a theoretical model that showed explicit relations between L¨uders strain and the mean free-path(ferrite path), dislocation density and the grain-size. It was also shown that an explicit relation between the L¨uders strain and carbon content was possible from known data, which a new parameter Á was derived, and is the derivative of the work-hardening exponent with respect to the lower yield stress.
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Ghasemi, Rohollah. "Hydrogen-assisted stress corrosion cracking of high strength steel." Thesis, KTH, Skolan för kemivetenskap (CHE), 2011. http://urn.kb.se/resolve?urn=urn:nbn:se:kth:diva-50416.

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In this work, Slow Strain Rate Test (SSRT) testing, Light Optical Microscopy (LOM) and Scanning Electron Microscopy (SEM) were used to study the effect of micro-structure, corrosive environments and cathodic polarisation on stress corrosion cracking (SCC) of two grades of high strength steels, Type A and Type B. Type A is manufactured by quench and tempered (Q&T) method. Type B, a normalize steel was used as reference. This study also supports electrochemical polarisation resistance method as an effective testing technique for measuring the uniform corrosion rate. SSRT samples were chosen from base metal, weld metal and Heat Affected Zone (HAZ). SSRT tests were performed at room temperature under free corrosion potential and cathodic polarisation using 4 mA/cm2 in 1 wt% and 3.5 wt% NaCl solutions. From the obtained corrosion rate measurements performed in 1 wt% and 3.5 wt% NaCl solutions it was observed that increased chloride concentration and dissolved oxygen content enhanced the uniform corrosion for all tested materials. Moreover, the obtained results from SSRT tests demonstrate that both Q&T and normalized steels were not susceptible to SCC in certain strain rate(1×10-6s-1) in 1 wt% and 3.5 wt% NaCl solutions under free corrosion potential. It was con-firmed by a ductile fracture mode and high reduction in area. The weld metal of Type A with acicular ferrite (AF), pro-eutectoid (PF) and bainite microstructure showed higher susceptibility to hydrogen assisted stress corrosion cracking compared to base metal and HAZ. In addition, typical brittle intergranular cracking with small reduction in area was observed on the fracture surface of the Type A due to hydrogen charging.
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Singh, Preet Mohinder. "Stress corrosion cracking of carbon steel and inconel 600." Thesis, University of Newcastle Upon Tyne, 1989. http://ethos.bl.uk/OrderDetails.do?uin=uk.bl.ethos.328104.

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McNutt, Steven A. "Stress relief cracking in copper-precipitation strengthened HSLA-100 steel." Thesis, Monterey, California. Naval Postgraduate School, 1988. http://hdl.handle.net/10945/23410.

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Approved for public release; distribution is unlimited
The US Navy is currently developing a new family of high-strength , low-alloy steels which derive a significant portion of their strength from copper precipitation. These highly weldable steels require little or no preheat. resulting in substantial cost savings. The first of these steels. HSLA-80, has been certified for ship construction, but recent studies have indicated some susceptibility to stress relief cracking in weldments. HSLA-100, a modification of HSLA-80, is now being considered for several higher-strength naval structures. Stress-relief cracking has not been studied previously in this steel and is the subject of investigation in this work. The steel weldments were loaded below their yield strength, heated to temperatures of 550°-650° C, and permitted to stress relieve for one hour. At all temperatures, the steel exhibited susceptibility to stress relief cracking in certain stress ranges. Optical and scanning electron microscopy exhibited intergranular cracking which always traversed the coarse-grained region of the heat-affected zone. Auger and transmission electron microscopy indicated high concentrations of alloying elements at the grain boundaries. Stress-relief cracking was associated with the diffusion of alloying elements to the prior austenite grain boundaries.
http://archive.org/details/stressreliefcrac00mcnu
Captain, Canadian Forces
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Bhattacharya, Ananya. "Stress corrosion cracking of duplex stainless steels in caustic solutions." Diss., Atlanta, Ga. : Georgia Institute of Technology, 2008. http://hdl.handle.net/1853/26491.

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Thesis (Ph.D)--Materials Science and Engineering, Georgia Institute of Technology, 2009.
Committee Chair: Singh, Preet M.; Committee Member: Carter, W. Brent; Committee Member: Gokhale, Arun, M.; Committee Member: Neu, Richard; Committee Member: Sanders, Thomas H., Jr.. Part of the SMARTech Electronic Thesis and Dissertation Collection.
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Mozhi, T. Arul. "The effect of nitrogen on sensitization and stress corrosion cracking of AISI 304 stainless steels /." The Ohio State University, 1986. http://rave.ohiolink.edu/etdc/view?acc_num=osu1487265143147533.

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Books on the topic "Steel – Cracking"

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W, Fisher John. Fatigue cracking of steel bridge structures. McLean, Va: U.S. Dept. of Transportation, Federal Highway Administration, Research, Development, and Technology, Turner-Fairbank Highway Research Center, 1990.

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Norman, Bailey, ed. Welding steels without hydrogen cracking. 2nd ed. Abington, Cambridge: Abington Publishing, 1993.

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Lyle, Fred F. Stress-corrosion cracking susceptibility of weldments in duplex stainless steels. St. Louis, Missouri: Materials Technology Institute of the Chemical Process Industries, 1989.

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McNutt, Steven A. Stress relief cracking in copper-precipitation strengthened HSLA-100 steel. Monterey, Calif: Naval Postgraduate School, 1988.

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Hitch, Daniel C. A. Stress-corrosion cracking of duplex stainless steel in evaporating seawater. Manchester: UMIST, 1997.

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Vaidya, W. V. An experimental assessment of hysteresis in near-threshold fatigue crack propagation regime of a low alloy ferritic steel under closure-free testing conditions. Geesthacht: GKSS-Forschungszentrum Geesthacht GmbH, 1991.

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Fanous, Fouad. Impact of deck cracking on durability. Ames, Iowa: Center for Transportation Research and Education, Iowa State University, 2000.

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Irwin, G. R. Cleavage behaviors in nuclear vessel steels. Washington, DC: U.S. Nuclear Regulatory Commission, 1994.

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Toivonen, Aki. Stress corrosion crack growth rate measurement in high temperature water using small precracked bend specimens. Espoo [Finland]: VTT Technical Research Centre of Finland, 2004.

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Joyce, J. A. Comparison of J[subscript I][subscript c] and J-R curves for short crack and tensilely loaded specimen geometries of a high strength structural steel. Washington, DC: Division of Engineering, Office of Nuclear Regulatory Research, U.S. Nuclear Regulatory Commission, 1992.

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Book chapters on the topic "Steel – Cracking"

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Cross, Carl E., N. Coniglio, E. M. Westin, and A. Gumenyuk. "Laser Weldability of Stainless Steel." In Hot Cracking Phenomena in Welds III, 131–44. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-16864-2_8.

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Boellinghaus, Th, and D. Eliezer. "Hydrogen Trapping in Supermartensitic Stainless Steel TIG Welds." In Cracking Phenomena in Welds IV, 457–72. Cham: Springer International Publishing, 2016. http://dx.doi.org/10.1007/978-3-319-28434-7_20.

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Boellinghaus, Th, T. Mente, P. Wongpanya, E. Viyanit, and E. Steppan. "Numerical Modelling of Hydrogen Assisted Cracking in Steel Welds." In Cracking Phenomena in Welds IV, 383–439. Cham: Springer International Publishing, 2016. http://dx.doi.org/10.1007/978-3-319-28434-7_18.

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Saleh, Mofreh F., T. Yeow, G. MacRae, and A. Scott. "Effect of Steel Fibre Content on the Fatigue Behaviour of Steel Fibre Reinforced Concrete." In 7th RILEM International Conference on Cracking in Pavements, 815–25. Dordrecht: Springer Netherlands, 2012. http://dx.doi.org/10.1007/978-94-007-4566-7_79.

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Mente, T., and Th Boellinghaus. "Numerical Investigations on Hydrogen-Assisted Cracking in Duplex Stainless Steel Microstructures." In Cracking Phenomena in Welds IV, 329–59. Cham: Springer International Publishing, 2016. http://dx.doi.org/10.1007/978-3-319-28434-7_16.

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Hochanadel, P. W., T. J. Lienert, J. N. Martinez, R. J. Martinez, and M. Q. Johnson. "Weld Solidification Cracking in 304 to 304L Stainless Steel." In Hot Cracking Phenomena in Welds III, 145–60. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-16864-2_9.

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Gittos, M. F., S. M. I. Birch, and R. J. Pargeter. "Solidification Cracking Susceptibility in C-Mn Steel CO2 Laser Welds." In Hot Cracking Phenomena in Welds III, 225–62. Berlin, Heidelberg: Springer Berlin Heidelberg, 2011. http://dx.doi.org/10.1007/978-3-642-16864-2_13.

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Feng, Chai, Cai Fu Yang, Su Hang, Yong Quan Zhang, and Xu Zhou. "Cracking Resistance of Cu-Bearing Age-Hardening Steel." In Key Engineering Materials, 2015–20. Stafa: Trans Tech Publications Ltd., 2007. http://dx.doi.org/10.4028/0-87849-456-1.2015.

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Wang, Bin, Senfeng Zhang, Cui Zhou, Nan Liu, Liang Wang, and Xiaoyu Tian. "Cracking Failure Analysis of X70 Pipeline Steel Weld." In Springer Proceedings in Energy, 371–86. Singapore: Springer Singapore, 2018. http://dx.doi.org/10.1007/978-981-13-0158-2_40.

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Strader, Katherine, Boian T. Alexandrov, and John C. Lippold. "Stress-Relief Cracking in Simulated-Coarse-Grained Heat Affected Zone of a Creep-Resistant Steel." In Cracking Phenomena in Welds IV, 475–93. Cham: Springer International Publishing, 2016. http://dx.doi.org/10.1007/978-3-319-28434-7_21.

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Conference papers on the topic "Steel – Cracking"

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Lam, Poh-Sang, Changmin Cheng, Yuh J. Chao, Robert L. Sindelar, Tina M. Stefek, and James B. Elder. "Stress Corrosion Cracking of Carbon Steel Weldments." In ASME 2005 Pressure Vessels and Piping Conference. ASMEDC, 2005. http://dx.doi.org/10.1115/pvp2005-71327.

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An experiment was conducted to investigate the role of weld residual stress on stress corrosion cracking in welded carbon steel plates prototypic to those used for nuclear waste storage tanks. Carbon steel specimen plates were butt-joined with Gas Metal Arc Welding technique. Initial cracks (seed cracks) were machined across the weld and in the heat affected zone. These specimen plates were then submerged in a simulated high level radioactive waste chemistry environment. Stress corrosion cracking occurred in the as-welded plate but not in the stress-relieved duplicate. A detailed finite element analysis to simulate exactly the welding process was carried out, and the resulting temperature history was used to calculate the residual stress distribution in the plate for characterizing the observed stress corrosion cracking. It was shown that the cracking can be predicted for the through-thickness cracks perpendicular to the weld by comparing the experimental KISCC to the calculated stress intensity factors due to the welding residual stress. The predicted crack lengths agree reasonably well with the test data. The final crack lengths appear to be dependent on the details of welding and the sequence of machining the seed cracks, consistent with the prediction.
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Lebet, Jean-Paul, and Jean-Marc Ducret. "Early Concrete Cracking of Composite Bridges during Construction." In Composite Construction in Steel and Concrete IV Conference 2000. Reston, VA: American Society of Civil Engineers, 2002. http://dx.doi.org/10.1061/40616(281)2.

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Lebet, Jean-Paul, and Miguel Gómez Navarro. "Influence of Concrete Cracking on Composite Bridge Behaviour." In Fifth International Conference on Composite Construction in Steel and Concrete. Reston, VA: American Society of Civil Engineers, 2006. http://dx.doi.org/10.1061/40826(186)8.

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Al-Harthi, Sultan G., and Mohammad Obaid Mohammad Sameer. "Stress Corrosion Cracking in Low Temperature Carbon Steel." In ASME 2019 Pressure Vessels & Piping Conference. American Society of Mechanical Engineers, 2019. http://dx.doi.org/10.1115/pvp2019-93091.

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Abstract Repeated weld joints leaks were observed in newly commissioned non insulated low temperature carbon steel anhydrous ammonia pipes after few months of operations. A detailed investigation was carried out to identify the root cause which found to be usage of high strength filler wire which leads to stress corrosion cracking (SCC) and weld joints failure. Also, An Online advance inspection via Phased Array Ultrasonic Test (PAUT) was conducted to assess the condition of weld joints in anhydrous ammonia pipe loops. Moreover, three different samples of leaked weld joints were submitted for metallurgical failure analysis laboratory. The paper explains the root cause of the damage, Online PAUT inspection and the challenges faced during development of the rectification procedure and implementation.
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Rami´rez, J. A., and J. L. Gonza´lez. "Hydrogen Induced Cracking of Welds in Steel Pipelines." In ASME 2003 Pressure Vessels and Piping Conference. ASMEDC, 2003. http://dx.doi.org/10.1115/pvp2003-2182.

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The phenomenon of Hydrogen Induced Cracking (HIC) by the absorption of hydrogen from a sour fluid in carbon steel plates is well known, however the question if HIC cracks can penetrate weld deposits is still subject of controversy in both laboratory and field studies. In this research, plates containing Submerged Arc Welding, Resistance Seam Welding and Shield Metal Arc welds, were exposed to cathodic charging to induce HIC and to determine if HIC cracks can grow and pass through the weld materials. The HIC progress in the plates was detected and monitored by straight beam ultrasonic inspection in the A-Scan mode. The results showed that HIC can occur in the weld by the same mechanism as in normal plate in the case of SAW welds, while in the other two (RSEW, SMAW) the crack deviates from its original trajectory to form radial cracks when the HIC cracks penetrate into the weld material. The study is completed by metallographic and fractographic observations of the cracked specimens.
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Wu, Xiangyang, Zhiyi Zhang, Wen Li, Yongjing Wang, and Yue Liu. "Research on Cracking Sensitivity of Weathering Steel SMA490BW." In 2014 International Conference on Mechatronics, Control and Electronic Engineering (MCE-14). Paris, France: Atlantis Press, 2014. http://dx.doi.org/10.2991/mce-14.2014.86.

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Homrossukon, Samerjit, Sheldon Mostovoy, and Judith A. Todd. "Investigation of Hydrogen Assisted Cracking in Pressure Vessels." In ASME 2006 Pressure Vessels and Piping/ICPVT-11 Conference. ASMEDC, 2006. http://dx.doi.org/10.1115/pvp2006-icpvt-11-93923.

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Hydrogen assisted cracking (HAC) has been investigated in high strength 4140 and low strength Z17D pressure vessel steels, charged at −50 mA/cm2 in 1N H2SO4 + 25 mg/1 As2O3 and tested under three-point bend decreasing load. The HAC growth rate for Z17D steel (1.4×10−7 cm/s) was found to be approximately two orders of magnitude slower than that of 4140 steel (3.3×10−5 cm/s), while the threshold stress intensity factor for Z17D steel (∼37 MPa√m) was significantly higher than that of 4140 steel (∼7 MPa√m). This research will show that a single analytical model, based on the hypothesis that hydrogen both reduces crack resistance (R) and increases crack driving force (G), can explain HAC in 4140 and Z17D steels. The model predicts the hydrogen concentration required to initiate HAC as a function of the stress intensity factor and yield strength of the steel. Hydrogen-induced reduction of R was found to dominate HAC in 4140 steel, while hydrogen-induced reduction of R was combined with an increase in G for HAC cracking of Z17D steel.
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Gra˚berg, Stig, Lars Volden, and Anthonius Johannes Paauw. "Mid Thickness Delayed Cracking of Z-Quality Offshore Steel." In ASME 2011 30th International Conference on Ocean, Offshore and Arctic Engineering. ASMEDC, 2011. http://dx.doi.org/10.1115/omae2011-49003.

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During fabrication of a steel structure for an offshore modification project, delayed cracking was experienced in the mid plane or centre line of a 30 mm thick plate. The plate was part of a restraint box frame where 25 mm plates were welded to this 30 mm plate on both plate-surfaces. The applied 30 mm plate was a higher strength offshore steel (EN10225-S420 G2+M), with special through thickness properties and enhanced chemical composition as defined in material data sheet MDS Y30 of NORSOK M-120. Fracture mechanical testing including KV and CTOD in the mid plane confirmed that a very low toughness was present here with a brittle fracture type (cleavage). The plate was manufactured by the continuous casting process which due to centre line segregation resulted in high levels of manganese sulfide inclusions but also niobium carbides/nitrides. The plate manufacturer considered the documented toughness level as expected. Similar testing was performed on a 30 mm plate also delivered to the same material specification but of which the material certificate revealed a 10 times lower sulfur and phosphorus content indicating a much higher steel refinement. A significant higher toughness was obtained for this steel with high ductile behavior. Both steels showed a similar through thickness ductility, measured elongation for the through thickness tensile specimen, which implies that this property does not guaranty for the observed material behavior.
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Le, Minh, Olivier Asserin, Laurent Forest, Olivier Fandeur, and Philippe Pilvin. "Numerical Simulation of Hot Cracking Tests." In ASME 2013 Pressure Vessels and Piping Conference. American Society of Mechanical Engineers, 2013. http://dx.doi.org/10.1115/pvp2013-98170.

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One of the main nuclear materials is the austenitic stainless steels, which have good ductility and toughness, high thermal expansion coefficients and a thermal conductivity lower than that of martensitic or ferritic steels. The 316L(N) austenitic stainless steel (X2CrNiMo17-12-2 with controlled nitrogen) is evaluated for structures such as the vessels, which are steel enclosures surrounding the reactor core and its assemblies, in fourth generation nuclear systems. The RCC-MR code, which is used as a frame of reference in the manufacture of SFR (Sodium Fast Reactor concept), recommends the use of austenoferritic filler material for the welding of 316L(N) steel. These recommendations derive from past experience of working with fast neutron reactors (Phenix and Superphenix). In order to guarantee long-term properties at high temperatures, an austenoferritic and an austenitic filler metals are evaluated as filler metals. However, these materials are susceptible to hot cracking. Therefore, a study is conducted to ensure their weldability. The purpose of this work is to evaluate the susceptibility to hot cracking of the studied materials and to present a methodology applied to define a criterion called “laboratory” for each material and its transfer to a structure test. The relative susceptibility to hot cracking of these materials was evaluated using four tests: the Varestraint, the Gleeble, the trapezoid and the skew tests. Numerical simulation using Cast3M code and Sidolo software of these four tests were investigated in order to survey behavior laws of each studied material and solidification cracking thermomechanical criteria intrinsic to the materials. Some test and simulation results as well as hot cracking susceptibility ranking are presented and the transferability to real component welds of hot cracking criteria is discussed.
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Venegas, V., O. Herrera, F. Caleyo, J. M. Hallen, and T. Baudin. "Crystallographic Texture Control Helps Improve Pipeline Steel Resistance to Hydrogen-Induced Cracking." In 2010 8th International Pipeline Conference. ASMEDC, 2010. http://dx.doi.org/10.1115/ipc2010-31362.

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Low-carbon steel specimens, all within API (American Petroleum Institute) specifications, were produced following different thermomechanical paths. After austenization, the samples were rolled and recrystallized. The rolling process was carried out using different reduction-in-thickness degrees and finishing temperatures. The investigated steels showed similar microstructural features but differed considerably in their crystallographic textures and grain boundary distributions. After cathodic hydrogen charging, hydrogen-induced cracking (HIC) was detected in the hot-rolled recrystallized steels, whereas the cold and warm-rolled recrystallized steels proved resistant to this damage. Among the investigated specimens, the HIC-stricken show either the strongest {001}ND texture fiber, the smallest fraction of low-angle grain boundaries, or the weakest {111}ND (γ) texture fiber ({hkl}ND representing crystallographic orientations with {hkl} planes parallel to the steel rolling plane). In contrast, the HIC-resistant steels show the weakest {001}ND texture fiber, the largest fraction of low-angle grain boundaries, and the strongest γ fiber. These results support the hypothesis of this and previous works, that crystallographic texture control, through warm rolling schedules, helps improve pipeline steel resistance to hydrogen-induced cracking.
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Reports on the topic "Steel – Cracking"

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Gedeon, Steven A. Hydrogen Assisted Cracking of High Strength Steel Welds. Fort Belvoir, VA: Defense Technical Information Center, May 1988. http://dx.doi.org/10.21236/ada196738.

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Auten, T. A., and J. V. Monter. Temperature and environmentally assisted cracking in low alloy steel. Office of Scientific and Technical Information (OSTI), April 1995. http://dx.doi.org/10.2172/101185.

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Jackson, J. H., S. P. Teysseyre, and M. P. Heighes. Irradiation Assisted Stress Corrosion Cracking of Austenitic Stainless Steel in BWR Conditions. Office of Scientific and Technical Information (OSTI), June 2017. http://dx.doi.org/10.2172/1408502.

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Connor, Robert J., and Jason B. Lloyd. Maintenance Actions to Address Fatigue Cracking in Steel Bridge Structures: Proposed Guidelines and Commentary. Purdue University, October 2017. http://dx.doi.org/10.5703/1288284316552.

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Lam, P. INVESTIGATION OF THE POTENTIAL FOR CAUSTIC STRESS CORROSION CRACKING OF A537 CARBON STEEL NUCLEAR WASTE TANKS. Office of Scientific and Technical Information (OSTI), October 2009. http://dx.doi.org/10.2172/966687.

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Lam, P. INVESTIGATION OF THE POTENTIAL FOR CAUSTIC STRESS CORROSION CRACKING OF A537 CARBON STEEL NUCLEAR WASTE TANKS. Office of Scientific and Technical Information (OSTI), November 2009. http://dx.doi.org/10.2172/967385.

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Christine, Lozano, and Riveros Guillermo. Classical and innovative methods of fatigue and fracture repairs in navigation steel structures. Engineer Research and Development Center (U.S.), April 2021. http://dx.doi.org/10.21079/11681/40422.

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Most of the hydraulic steel structures (HSS) in the U.S. have reached or have past their design life, which leads to unsatisfactory performance. Welded connections with low fatigue resistance, poor weld quality, unanticipated structural behavior, or unexpected loading due to the deterioration of the design boundary conditions are the causes of fatigue cracking. The purpose of this report is to identify and evaluate the traditional and new methods used for fatigue and fracture repairs in navigation steel structures to restore their load carrying capacity and fatigue and fracture resistance. The final objective was to generate a guidance report comprising of recommended and more efficient repair methods for the different fatigue limit states observed in navigation steel structures.
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C. Stephen. Stress Corrosion Cracking of the Drip Shield, The Waste Package Outer Barrier and the Stainless Steel Structural Material. Office of Scientific and Technical Information (OSTI), April 2000. http://dx.doi.org/10.2172/837079.

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G. Gordon. Stress Corrosion Cracking of the Drip Shield, the Waste Package Outer Barrier, and the Stainless Steel Structural Material. Office of Scientific and Technical Information (OSTI), October 2004. http://dx.doi.org/10.2172/839515.

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Zhang, Y., A. Cook, C. Padovani, S. Zhou, and A. Turnbull. In situ crack growth measurements of atmospheric induced stress corrosion cracking of 316L stainless steel for HAW containers. National Physical Laboratory, September 2020. http://dx.doi.org/10.47120/npl.mat91.

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