DOCSLIB.ORG

NYS00484B-00-BD01 Identified: 11/5/2015 Admitted: 11/5/2015 Withdrawn: Rejected: Stricken: Other

Total Page：16

File Type：pdf, Size：1020Kb

Download full-text PDF Read full-text
NYS00484B-00-BD01 Identified: 11/5/2015 Admitted: 11/5/2015 Withdrawn: Rejected: Stricken: Other United States Nuclear Regulatory Commission Official Hearing Exhibit In the Matter of: Entergy Nuclear Operations, Inc. (Indian Point Nuclear Generating Units 2 and 3) ASLBP #: 07-858-03-LR-BD01 Docket #: 05000247 | 05000286 Exhibit #: NYS00484B-00-BD01 Identified: 11/5/2015 Admitted: 11/5/2015 Withdrawn: Rejected: Stricken: Other: 5. CARBON AND LOW ALLOY STEELS Peter Ford General Electric Global Research, Niskayuna, New York – Retired 5.1 OVERALL INTRODUCTION AND CURRENT CONCERNS Carbon and low alloys steels serve in a variety of locations within the nuclear power generating fleet. These ductile structural materials are used as pressure boundary materials in pressure vessels and piping in the RCS, ECCS, secondary water and service water systems of LWRs. These alloys are attractive for this use due to their relatively low cost, good mechanical properties in thick sections and good weldability. In reactor coolant system components, such as the pressure vessel, pressurizer and some piping, the carbon and low alloy steels are clad on the inside wetted surface with corrosion resistant materials such as austenitic stainless steels or nickel-base alloys. This background paper covers stress corrosion cracking (SCC) of ductile carbon and low alloy steel components and their associated weldments, with a special focus on extended operation degradation. Stress corrosion cracking, corrosion fatigue cracking, and flow-accelerated corrosion (FAC) are the primary modes of degradation discussed and presented. Specific areas of concern for extended service are identified. Irradiation effects and thermal aging for these alloys are also covered in considerably more detail in Volume III of this EMDA report (i.e., NUREG/CR-7153). 5.1.1 Steel Compositions and Applications Carbon and low alloy steels (Table 5.1) are used for pressure-retaining components in the primary, secondary, and tertiary systems of both BWRs and PWRs. These steels are used in the reactor in a variety of forms, including seamless piping, forgings, castings, plate, and bolting. The specific carbon or low alloy steel/component combinations that are used in a particular reactor vary between reactor designs and manufacturers, but in general, the reactor components include the following: • Reactor pressure vessel vertical sections in both PWRs and BWRs are manufactured from rolled low alloy steel A533 Gr. B Class 1 plates, which are then welded to form a cylinder. The cylinder is clad on the internal surface with a 5 mm layer of Type 308 SS, and then tempered during a post weld heat treatment (PWHT) at 595 °C (1,103 °F) to 620 °C (1,148 °F) for one hour per 25 mm thickness of steel. The composition of this C-Mn-Mo low alloy steel has more severe limitations on the Cu, S, P, and V contents for plates in the high-flux beltline region since these elements increase the extent of irradiation embrittlement. • The top and bottom heads of the pressure vessel in BWRs and PWRs are generally clad* low alloy steel A508 Gr. 2 Class 1 forgings using the same cladding/heat treatment conditions as for the vertical sections. After the vertical sections and the top and bottom * Note that in some BWR designs the top head may be unclad. heads are fabricated, all three subassemblies are welded together to form the primary pressure vessel and are then given a further PWHT. • Steam generator shells of PWRs are low alloy steel A533 Gr. A Class 1 or Class 2 plates, which, like the pressure vessel, are heat-treated after subassembly. The secondary side of the steam generator is not usually clad. • Steam generator tube sheets in PWRs are generally A508 Gr. 2 Class 1 or A508 Gr. 2 Class 2, with cladding on the primary side of the bottom head. • Steam generator channel heads in PWRs are generally A216 Gr. • The pressurizer shells in PWRs are generally low alloy steel A516 Gr.70 or A533 Gr. B plate with internal stainless steel cladding. Table 5.1. ASTM compositional specifications for ferritic and bainitic carbon and low alloy steel concentrations given as weight percentages. Balance is Fe. ASME/ASTM C max Mn P max S max Si Cu max Ni Cr Mo V max Ferritic Steels A105 0.035 0.6–1.05 0.035 0.04 0.1–0.35 0.4(1) 0.4 maxa 0.3 0.12 0.05 maxa maxa A106 GrB 0.3 0.29– 0.035 0.035 0.1 min 0.4 (2) 0.4 maxb 0.4 0.15 0.08b 1.06 maxb maxb A216 Gr WCB 0.3 1.0 max 0.04 0.045 0.6 max 0.3(3) 0.5 maxc 0.5 0.2 maxc 0.03c maxc A302 GrB 0.25 1.15– 0.035 0.035 0.15–0.4 0.45–0.6 1.50 A333 Gr6 0.3 0.29– 0.035 0.035 0.1 max 1.06 A508 Gr3 0.25 1.2–1.5 0.025 0.025 0.15–0.4 0.4–1.0 0.25 0.45–0.6 0.05 max A516 Gr70 d 0.85–1.2 0.035 0.035 0.15–0.4 A533 Type A 0.25 1.15–1.5 0.035e 0.035 0.15–0.4 0.45–0.6 A533 Type B 0.25 1.15–1.5 0.035 0.035 0.15–0.4 0.4–0.7 0.45–0.6 Bainitic Steels 1Cr1Mo0.25V 0.33 0.85 0.25 1.0 1.25 0.25 2Cr1Mo Gr22 0.026 0.49 0.012 0.009 0.28 0.05 2.42 0.98 NiCrMoV 0.28 0.6 0.015 0.018 0.15–0.3 3.25–4.0 1.25– 0.3–0.6 0.15 (A469 Cl8) 2.0 NiCrMoV 0.35 1.0 0.015 0.018 0.15– 0.75 0.9–1.5 1.0–1.5 0.3 (A470 Cl8) 0.35 NiCrMoV 0.28 0.7 0.015 0.015 0.15– 2.0–4.0 0.7–2.0 0.2–0.7 0.05 (A471 Cl8) 0.35 a Sum of Cu, Ni, Cr, and Mo shall be <1.00%; sum of Cr and Mo shall not exceed 0.32%. b Limits for V and Nb may be increased to 0.1% and 0.05%, respectively. c Sum of Cr and Ni shall not exceed 0.32%. d Carbon max. varies with thickness of plate; 0.5–2 in., 0.28% max; 2–4 in., 0.30% max; 4–8 in., 0.31% max. e For reactor beltline: Cu < 0.1% max, P < 0.012% max, S < 0.015% max, and V < 0.05% max. 100 • Reactor coolant piping for PWR primary circuits may be seamless carbon steel with, in some designs, austenitic stainless steel cladding. Alternatively, a higher-cost option of using cast stainless steel (CF8M) has been used for the main coolant piping. The recirculation piping in BWRs is usually stainless steel (Types 304 SS, 316 SS, 304L SS, 316L SS), although unclad A333 Gr. 6 carbon steel piping may be used in the main steam and the feedwater lines. The piping in the lower-temperature emergency core cooling and auxiliary/support systems is usually seamless A105 or A106 Gr. B carbon steel. 5.1.2 Initial Concerns It was recognized initially by the reactor designers that two problems could occur if carbon steels and low alloy steels were used in water-cooled nuclear reactors. First, irradiation embrittlement of the pressure vessel steel would occur in high-neutron-flux regions over time, and, second, corrosion products could be irradiated during passage through the core region and would create radioactive “crud” that could hamper maintenance operations. The first problem was addressed by monitoring the extent of irradiation embrittlement in low alloy steel surveillance samples placed adjacent to a reactor pressure vessel (RPV) wall in the high neutron flux “beltline” region. This embrittlement is, along with fatigue usage calculations, an input to the regulatory “time limited aging analyses” (TLAA) required for license renewal (sometimes referred to more commonly as “life extension”) for up to 60 years. The crud/radioactivity issue was addressed by cladding the inside of the RPV with stainless steel (e.g., Type 308 SS), thereby reducing the inventory of corrosion product that could become irradiated. 5.1.3 Subsequent Concerns Unfortunately, environmentally assisted degradation has been observed [1–8] in carbon and low alloy steel components of LWRs by degradation modes that were not assessed at the early design stage. The degradation modes were: • “High-cycle” (i.e., low strain amplitude/high frequency) fatigue due to flow-induced vibration or thermal stress cycles (e.g., in dead legs and in feedwater nozzles). • “Low-cycle” (i.e., high strain amplitude/low frequency) fatigue (e.g., due to start-up and shutdown cycles). • Pitting of carbon steel components, usually under oxidizing conditions at temperatures <150 °C (302 °F). Such degradation often acts as a precursor to stress corrosion cracking (SCC) and corrosion fatigue (CF) during subsequent operation at higher temperatures. • Corrosion of carbon steel tube support plates in the secondary side of PWR steam generators due to complex concentrated environments occurring at heat transfer surfaces in the tube/support plate crevice. • Transgranular stress corrosion cracking (TGSCC) of BWR carbon steel piping and low alloy steel PWR steam generator shells in situations involving dynamic loading, oxidizing environments, and high service stress. 101 • Intergranular stress corrosion cracking (IGSCC) at elevated temperatures of components such as Canada Deuterium Uranium (CANDU) PWR steam generator inlet piping that had been cold formed. • IGSCC of welded carbon steel piping in low-temperature [<90 °C (194 °F)], closed-coolant water (CCW) systems containing inhibitors.
Load more

Recommended publications
  • Corrosion Fatigue: Type 304 Stainless Steel in Acid-Chloride and Implant Metals in Biological Fluid
    76-9939 BOWERS, Davtd Francis, 1937- CORROSION FATIGUE: TYPE 304 STAINLESS STEEL IN ACID-CHLORIDE AND IMPLANT METALS IN BIOLOGICAL FLUID. The Ohio State University, Ph.D., 1975 Engineering, metallurgy Xerox University Microfilms, Ann Arbor, Michigan 48ioe CORROSION FATIGUE: TYPE 304 STAINLESS STEEL IN ACID-CHLORIDE AND IMPLANT METALS IN BIOLOGICAL FLUID Dissertation Presented in Partial Fulfillment of the Requirements for the Degree Doctor of Philosophy in the Graduate School of The Ohio State University by David Francis Bowers, B.S., M.S. Metallurgical Engineering The Ohio State University 1975 Approved by (dviser Department of Metallurgical Engineering Reading Committee: Dr. Mars G. Fontana Dr. Frank Beck Dr. John P. Hirth To My Wife and Daughter TABLE OF CONTENTS Page ACKNOWLEDGEMENTS.......................................... iv VITA........................................................ vi LIST OF TABLES............................................. viii LIST OF FIGURES... ...................... x INTRODUCTION.................. .. ......................... 1 I. LITERATURE SURVEY..................... 4 1.1 Concepts and Theory of Fatigue Crack Growth.. 4 1.2 Fracture Mechanics Approach to Crack Growth in Engineering Structures..................... 18 1.3 Effect of Microstructure on Fatigue Cracking Growth................................ 24 1.4 Mechanical Variables in Corrosion Fatigue.... 41 1.5 Environmental Interaction with Fatigue Crack Growth.................................... 59 II. EXPERIMENTAL DETAILS...............................
    [Show full text]
  • Corrosion-Fatigue Evaluation of Uncoated Weathering Steel Bridges
    applied sciences Article Corrosion-Fatigue Evaluation of Uncoated Weathering Steel Bridges Yu Zhang, Kaifeng Zheng, Junlin Heng * and Jin Zhu Department of Bridge Engineering, School of Civil Engineering, Southwest Jiaotong University, Chengdu 610031, China * Correspondence: [email protected]; Tel.: +86-182-8017-6652 Received: 19 July 2019; Accepted: 19 August 2019; Published: 22 August 2019 Featured Application: The new findings highlight the enhancement in corrosion-fatigue performance of steel bridges by using the uncoated weathering steel. Besides, an innovative approach has been established to simulate the corrosion-fatigue process in uncoated weathering steel bridges, providing deep insights into the service life of the bridges. The approaches suggested in the article can be used (not limited to) as a reference for the research and design of uncoated weathering steel bridges. Abstract: Uncoated weathering steel (UWS) bridges have been extensively used to reduce the lifecycle cost since they are maintenance-free and eco-friendly. However, the fatigue issue becomes significant in UWS bridges due to the intended corrosion process utilized to form the corrodent-proof rust layer instead of the coating process. In this paper, an innovative model is proposed to simulate the corrosion-fatigue (C-F) process in UWS bridges. Generally, the C-F process could be considered as two relatively independent stages in a time series, including the pitting process of flaw-initiation and the fatigue crack propagation of the critical pitting flaw. In the proposed C-F model, Faraday’s law has been employed at the critical flaw-initiation stage to describe the pitting process, in which the pitting current is applied to reflect the pitting rate in different corrosive environments.
    [Show full text]
  • Corrosion Fatigue of Austenitic Stainless Steels for Nuclear Power Engineering
    metals Article Corrosion Fatigue of Austenitic Stainless Steels for Nuclear Power Engineering Irena Vlˇcková 1,*, Petr Jonšta 2, ZdenˇekJonšta 2, Petra Vá ˇnová 2 and Tat’ána Kulová 2 1 RMTSC, Material & Metallurgical Research Ltd., Remote Site Ostrava, VÚHŽ a.s., Dobrá 739 51, Czech Republic 2 Department of Materials Engineering, VŠB-Technical University of Ostrava, Ostrava 708 33, Czech Republic; [email protected] (P.J.); [email protected] (Z.J.); [email protected] (P.V.); [email protected] (T.K.) * Correspondence: [email protected]; Tel.: +420-558601257 Academic Editor: Hugo F. Lopez Received: 21 September 2016; Accepted: 8 December 2016; Published: 16 December 2016 Abstract: Significant structural steels for nuclear power engineering are chromium-nickel austenitic stainless steels. The presented paper evaluates the kinetics of the fatigue crack growth of AISI 304L and AISI 316L stainless steels in air and in corrosive environments of 3.5% aqueous NaCl solution after the application of solution annealing, stabilizing annealing, and sensitization annealing. Comparisons were made between the fatigue crack growth rate after each heat treatment regime, and a comparison between the fatigue crack growth rate in both types of steels was made. For individual heat treatment regimes, the possibility of the development of intergranular corrosion was also considered. Evaluations resulted in very favourable corrosion fatigue characteristics of the 316L steel. After application of solution and stabilizing annealing at a comparable DK level, the fatigue crack growth rate was about one half compared to 304L steel. After sensitization annealing of 316L steel, compared to stabilizing annealing, the increase of crack growth rate during corrosion fatigue was slightly higher.
    [Show full text]
  • The Environmental Effect on Corrosion Fatigue Behavior of Austenitic Stainless Steels
    The Environmental Effect on Corrosion Fatigue Behavior of Austenitic Stainless Steels by Lun Yu B.S. Nuclear Engineering (2013) Shanghai Jiao Tong University SUBMITTED TO THE DEPARTMENT OF NUCLEAR SCIENCE AND ENGINEERING IN PARTIAL FULFILLMENT OF THE REQUIREMENTS FOR THE DEGREE OF DOCTOR OF PHILOSOPHY IN NUCLEAR SCIENCE AND ENGINEERING AT THE MASSACHUSETTS INSTITUTE OF TECHNOLOGY September, 2017 © 2017 Massachusetts Institute of Technology. All rights reserved. Signature of Author: _____________________________________________________________ Lun Yu Department of Nuclear Science and Engineering August 25, 2017 Certified by: __________________________________________________________________ Ronald G. Ballinger Professor of Nuclear Science and Engineering, Materials Science and Engineering Thesis Supervisor Certified by: ___________________________________________________________________ Michael P. Short Assistant Professor of Nuclear Science and Engineering Thesis Reader Accepted by: ___________________________________________________________________ Ju Li Battelle Energy Alliance Professor of Nuclear Science and Engineering, Professor of Materials Science and Engineering Chair, Department Committee on Graduate Students This page was left blank intentionally The Environmental Effect on Corrosion Fatigue Behavior of Austenitic Stainless Steels by Lun Yu Submitted to the Department of Nuclear Science and Engineering on September 1, 2017 in Partial Fulfillment of the Requirements for the Degree of Doctor of Philosophy in Nuclear Science and
    [Show full text]
  • 10Th International Congress on Marine Corrosion and Fouling, University of Melbourne, February 1999
    10th International Congress on Marine Corrosion and Fouling, University of Melbourne, February 1999 Additional Papers John A Lewis (Editor) Maritime Platforms Division Aeronautical and Maritime Research Laboratory DSTO-GD-0287 ABSTRACT This volume contains nineteen papers from the 10th International Congress on Marine Corrosion and Fouling, held at the University of Melbourne in Melbourne, Australia, in February 1999. The scope of the congress was to enhance scientific understanding of the processes and prevention of chemical and biological degradation of materials in the sea. Papers in this volume range across the themes of marine biofilms and bioadhesion, macrofouling processes and effects, methods for prevention of marine fouling, biocides in the marine environment, biodeterioration of wood in the sea, and marine corrosion. RELEASE LIMITATION Approved for public release Published by DSTO Aeronautical and Maritime Research Laboratory 506 Lorimer St Fishermans Bend, Victoria 3207 Australia Telephone: (03) 9626 7000 Fax: (03) 9626 7999 © Commonwealth of Australia 2001 AR-011-880 May 2001 APPROVED FOR PUBLIC RELEASE 10th International Congress on Marine Corrosion and Fouling, University of Melbourne, February 1999 Additional Papers Executive Summary The fouling and corrosion of vessels and structures immersed in the sea continues to pose significant economic and operational costs to the owner. Fouling growth can interfere with the operation of submerged equipment, impose increased loading stresses and accelerate corrosion on marine structures, and adversely affect the performance of ships by increasing hydrodynamic drag, which necessitates the use of more power and fuel to move the ship through the water. Similarly, marine corrosion and biodegradation of materials can compromise the operation and structural integrity of vessels, structures and other immersed equipment.
    [Show full text]
  • Four Types of Heat Exchanger Failures
    Four Types of Heat Exchanger Failures . mechanical, chemically induced corrosion, combination of mechanical and chemically induced corrosion, and scale, mud, and algae fouling By MARVIN P. SCHWARTZ, Chief Product Engineer, ITT Bell & Gossett a unit of Fluid Handling Div., International Telephone & Telegraph Corp , Skokie IL Hcat exchangers usually provide a long service life with Maximum recommended velocity in the tubes and little or no maintenance because they do not contain any entrance nozzle is a function of many variables, including moving parts. However, there are four types of heat tube material, fluid handled, and temperature. Materials exchanger failures that can occur, and can usually be such as steel, stainless steel, and copper-nickel withstand prevented: mechanical, chemically induced corrosion, higher tube velocities than copper. Copper is normally combination of mechanical and chemically induced limited to 7.5 fps; the other materials can handle 10 or 11 corrosion, and scale, mud. and algae fouling. fps. If water is flowing through copper tubing, the velocity This article provides the plant engineer with a detailed should be less than 7.5 fps when it contains suspended look at the problems that can develop and describes the solids or is softened. corrective actions that should be taken to prevent them. Erosion problems on the outside of tubes usually result Mechanical-These failures can take seven different from impingement of wet, high-velocity gases, such as forms: metal erosion, steam or water hammer, vibration, steam. Wet gas impingement is controlled by oversizing thermal fatigue, freeze-up, thermal expansion. and loss of inlet nozzles, or by placing impingement baffles in the cooling water.
    [Show full text]
  • Investigation of Corrosion Fatigue Phenomena in Transient Zone of Mechanical Drive Steam Turbines and Its Preventive Measures
    Proceedings of the Second Middle East Turbomachinery Symposium 17 – 20 March 2013, Doha, Qatar Investigation of Corrosion Fatigue Phenomena in Transient Zone of Mechanical Drive Steam Turbines and its Preventive Measures by Satoshi Hata Engineering and Design Division Mitsubishi Heavy Industries, Compressor Corporation Naoyuki Nagai Hiroshima Research & Development Center Mitsubishi Heavy Industries, Ltd. Norihito Fujimura MCO Saudi Arabia, LCC. (MCOSA) Mitsubishi Heavy Industries, Compressor Corporation Satoshi Hata ABSTRACT Satoshi Hata is a Group Manager For mechanical drive steam turbines, the investigation within the Turbo Machinery results of corrosion fatigue phenomena in the transient zone Engineering Department, Mitsubishi are introduced, including basic phenomena on expansion Heavy Industries, Ltd., in Hiroshima, line and actual design and damage experience. These results Japan. He has 30 year experience in were analyzed from the standpoint of stress intensity during R&D for nuclear uranium centrifuges, turbomolecular pumps, heavy-duty the start of cracking. In order to resolve such problems, gas turbines, steam turbines and preventive coating and blade design methods against fouling compressors. Mr. Hata has B.S., M.S. and corrosive environments are developed. Detailed and Ph.D. degrees (in Mechanical evaluation test results are given for coating performance Engineering) from Kyusyu Institute of using a unique test procedure simulating fouling phenomena Technology. and washing conditions. Finally, the results of the Naoyuki
    [Show full text]
  • Corrosion-Fatigue Testing on Steel Grades with Different Heat and Surface Treatments Used in Rock-Drilling Applications
    DEGREE PROJECT IN MATERIALS SCIENCE AND ENGINEERING, SECOND CYCLE, 30 CREDITS STOCKHOLM, SWEDEN 2016 CORROSION-FATIGUE TESTING ON STEEL GRADES WITH DIFFERENT HEAT AND SURFACE TREATMENTS USED IN ROCK-DRILLING APPLICATIONS LUIS MIGUEL BÉJAR INFANTE KTH ROYAL INSTITUTE OF TECHNOLOGY SCHOOL OF INDUSTRIAL ENGINEERING AND MANAGEMENT Abstract Corrosion fatigue is a common failure mechanism in rock drilling components and many other mechanical parts subjected to cyclic loads in corrosive environments. A crucial part in the design of such components resides in the selection of the right materials for the application, which ideally involves testing and comparison of their performance under working conditions. The present work was performed with the purpose of designing a corrosion-fatigue testing method that would allow the designer to compare the performance of different materials exposed to corrosion fatigue, permitting also the comparison with results from dry fatigue testing. The method was designed for rotating-bending machines. Two different steel grades were used during the work, one through hardened and one case hardened. The effect of these heat treatments and of shot peening over corrosion-fatigue behaviour were studied using the proposed method. It was proven that the testing speed has a strong impact on the fatigue life of steel. It was found that, at a fixed stress level, the case hardened and shot peened steel reached 3X10^6 cycles at 2300 rpm, while it failed at only 5X10^5 cycles with a testing speed of 500 rpm. A large beneficial influence of the shot peening was demonstrated. It was also observed that, at fixed testing speed, the shot peening on the through hardened steel can increase its fatigue strength from 190 MPa to 600 MPa under corrosion fatigue.
    [Show full text]
  • Mechanical Fatigue of Metals
    354.pdf A SunCam online continuing education course Mechanical Fatigue of Metals by Gerald O. Davis, P.E. 354.pdf Mechanical Fatigue of Metals A SunCam online continuing education course 1. Introduction - Overview of Mechanical Fatigue of Metals Among the several ways that metallic engineering materials may fail in service, mechanical fatigue is typically the most common. The percentages of the total mechanical failures that are due to fatigue vary by different sources from 50% to as much as 80 to 90 %. Some examples of applications in which fatigue failures occur include rotating shafts, bearings, gears, the wings and pressurized fuselages of aircraft, pipelines and tubes in shell-and-tube heat exchangers. There are many other examples. The variable loads and changing stresses that occur in fatigue have unique effects on the services lives of engineering alloys that don’t apply in situations where the only stresses acting are static. In situations where loading and resulting stresses don’t vary, resistance to failures becomes relatively straight forward. They can be adequately addressed by assuring working stresses, i.e., allowable stresses, are less than the yield, or ultimate tensile strength or ultimate shear strength (depending on the application) of the metal selected after applying a factor of safety to cover unknown aspects. Mechanical fatigue is significantly more complex. It is essential to realize that metal mechanical properties generated from standard, constant load tests should never be applied directly to fatigue applications. Fatigue often produces failure and complete metal separation when the maximum, fluctuating stress is well below the yield or ultimate tensile strength of the metal.
    [Show full text]
  • Literature Survey on the Stress Corrosion Cracking of Low-Alloy Steels in High-Temperature Water
    CH0200021 O o hi Q> PAUL SCHERRER INSTITUT PSI Bericht Nr. 02-06 CQ February 2002 5) ISSN 1019-0643 a Nuclear Energy and Safety Division Laboratory for Materials Behaviour Literature Survey on the Stress Corrosion Cracking of Low-Alloy Steels in High-Temperature Water H.P. Seifert Paul Scherrer Institut CH - 5232 Villigen PSI 33/13 Telefon 056 310 21 11 Telefax 056 310 21 99 Literature Survey on the Stress Corrosion Cracking of Low-Alloy Steels in High-Temperature Water H.P. Seifert Nuclear Energy and Safety Division Laboratory for Materials Behaviour Structural Integrity Group Abstract The present report is a summary of a literature survey on the stress corrosion cracking (SCC) behaviour/ mechanisms in low-alloy steels (LAS) in high-temperature water with special emphasis to primary-pressure-boundary components of boiling water reactors (BWR). A brief overview on the current state of knowledge concerning SCC of low-alloy reactor pressure vessel and piping steels under BWR conditions is given. After a short introduction on general aspects of SCC, the main influence parameter and available quantitative literature data concerning SCC of LAS in high-temperature water are discussed on a phenomenological basis followed by a summary of the most popular SCC models for this corrosion system. The BWR operating experience and service cracking incidents are discussed with respect to the existing laboratory data and background knowledge. Finally, the most important open questions and topics for further experimental investigations are outlined. TABLE OF CONTENTS ABSTRACT 2 INDEX 4 0. ABBREVIATIONS 6 1. INTRODUCTION 8 1.1 REPORT OUTLINE 8 1.2 REFERENCES 9 2.
    [Show full text]
  • By J. W. Montan0 Astronautics Laboratory
    I- x- By J. W. Montan0 Astronautics Laboratory May 10, 1971 MSFC Fopm 3190 (September 1968) A MECHANICAL PROPERTY AND STRESS CORROSION EVALUATION OF MP35N MULTIPHASE ALLOY George C. Marshall Space Flight Center Marshall Space Flight Center, AL 35812 Technic a1 Me mo randurn National Aeronautics and Space Administration Washington, D. C. 20546 15. SUPPLEMENTARY NOTES Astronautics Laboratory, Science and Engineering I$. ABSTRACT This report presents the mechanical properties of solution treated, York strengthened, and age hardened, MP35N Multiphase alloy bar stock manu- factured by the Latrobe Steel Company under license from the Standard Pressed Steel Company. Test specimens manufactured from approximately 1.0 inch (2.54 cm) diameter bar stock were tested at temperatures of 75°F (23.9OC) to -423°F (-253°C). The test data indicated excellent tensile strength, ductility, and impact properties. Results of the alternate immersion stress corrosion tests on stressed and unstressed tensile specimens 0.125-inch (.3175 cm) diameter and transverse "C"-ring specimens machined from 1.0 inch (2.54 cm) diameter bar indicated that the material is unsusceptible to stress corrosion cracking when tested in 3.5 percent NaCl solution for 180 days. 17. KEY WORDS I 18. DISTRIBUTION STATEMENT Cryogenic Temperature Unclassified - unlimited Alternate Immersion Unclassified Unclassified ACKNOWLEDGEMENT Acknowledgement is given to the following personnel of the Astronautics Laboratory; Mr. Wendell Deweese, S&E-ASTN-MMA - Brown Engineering Company Metallography Mr. Samuel H. Hunter, S&E-ASTN-MMA Assistance in ambient and cryogenic temperature tensile and impact testing . Mr. Daniel S. Kinkle, Jr., Sa-ASTN-MCS Fractographs and fractogtaphic analysis Mr.
    [Show full text]
  • Corrosion Types
    EN380 Naval Materials Science and Engineering Course Notes, U.S. Naval Academy CHAPTER 5 CORROSION TYPES 5.1 Uniform Corrosion 5.2 Galvanic Corrosion 5.3 Crevice Corrosion 5.4 Pitting Corrosion 5.5 Other Localized Corrosion 5.6 Selective Leaching aka Dealloying 5.7 Erosion-Corrosion 5.8 Stress-Corrosion-Cracking (S.C.C.) 5.9 Intergranular Corrosion 5.10 Fretting 5.11 Biological corrosion 5.12 Stray current corrosion The diagram on the following page illustrates the main types of corrosion which will be discussed in this chapter. 5 - 1 EN380 Naval Materials Science and Engineering Course Notes, U.S. Naval Academy Corrosion types [from Jones (1996)]. 5 - 2 EN380 Naval Materials Science and Engineering Course Notes, U.S. Naval Academy 5.1 Uniform Corrosion This corrosion results from the continual shifting of anode and cathode regions of the surface of a metal in contact with the electrolyte and leads to a nearly uniform corrosive attack on the entire surface. An example of such corrosion is the rusting of steel plate in seawater. If the rate of metal loss is known, allowances can be made in design and maintenance to accommodate the corrosion. Although it is termed uniform corrosion, it is characterized by the average surface loss. Uniform corrosion of storage tanks [from Jones (1996)]. 5.2 Galvanic Corrosion When two different metals are exposed to a corrosive environment, an electrical potential difference will exist. If the two metals are electrically connected, the more active metal will become the anode in the resulting galvanic cell and its corrosion will be increased.
    [Show full text]