Handbook Corrosion (1992) WW Part 4 pptx

Source: Ref 107 (a) 1.0% maximum present, but not determined analytically. Fig. 11 Internal surface of carbon steel pipe section damaged by cavitation Fretting is erosion-corrosion that occurs at the contact area between two metals under load and subject to slight relative movement by vibration or some other force (Ref 108, 109, 110). Damage begins with local adhesion between mating surfaces and progresses when adhered particles are ripped from a surface and react with air or other corrosive environment. Affected surfaces show pits or grooves with surrounding corrosion products. On ferrous metals, corrosion product is usually a very fine, reddish iron oxide; on aluminum, it is usually black. Fretting is detrimental not only because of the destruction of metallic surfaces but also because of a severe effect on the fatigue life. It has been shown that fretting can reduce the endurance limit of a metal by 50 to 70% (Ref 109). The relative motion necessary to produce fretting is very small. Displacements as small as 10 -8 cm have produced fretting. Fretting generally does not occur on contacting surfaces in continuous motion, such as ball or sleeve bearings. Fretting can be minimized or eliminated in many cases by one or more of the following: • Increasing the hardness of contacting surfaces. This may mean increasing the hardness of bother just one of the components. Surface- hardening treatments such as shot peening, nitriding, chrome plating, and carburizing are beneficial • Increasing the friction between the mating members by roughening or by plating (lead, copper, nickel, silver, gold) • Applying phosphate coatings to exclude air or applying anaerobic sealants or adhesives to increase the tightness of the fit • Increasing the fit interference, which reduces slippage by increasing the force on mating components • Switching to materials with more fretting resistance, as shown in Table 6 Table 6 Relative fretting resistance of various material combinations Combination Fretting resistance Aluminum on cast iron Poor Aluminum on stainless steel Poor Bakelite on cast iron Poor Cast iron on cast iron, with shellac coating Poor Cast iron on chromium plating Poor Cast iron on tin plating Poor Chromium plating on chromium plating Poor Hard tool steel on stainless steel Poor Laminated plastic on cast iron Poor Magnesium on cast iron Poor Brass on cast iron Average Cast iron on amalgamated copper plate Average Cast iron on cast iron Average Cast iron on cast iron, rough surface Average Cast iron on copper plating Average Cast iron on silver plating Average Copper on cast iron Average Magnesium on copper plating Average Zinc on cast iron Average Zirconium on zirconium Average Cast iron on cast iron with coating of rubber cement Good Cast iron on cast iron with Molykote lubricant Good Cast iron on cast iron with phosphate conversion coating Good Cast iron on cast iron with rubber gasket Good Cast iron on cast iron with tungsten sulfide coating Good Cast iron on stainless steel with Molykote lubricant Good Cold-rolled steel on cold-rolled steel Good Hard tool steel on tool steel Good Laminated plastic on gold plating Good Source: Ref 11 Abrasive wear is damage that results from the action of hard particles on a surface under the influence of a force that is oblique to the surface (Ref 112, 113, 114, 115, 116, 117). This is not, strictly speaking, a form of erosion-corrosion, but will be briefly discussed for comparison with the forms of erosion-corrosion mentioned above. Three common forms of abrasive wear are erosion abrasion, grinding abrasion, and gouging abrasion. Erosion abrasion usually involves low velocities and weak support of the abrasive material. Examples are wear on a plowshare in sandy soil and polishing of a metal surface with an abrasive held in a soft cloth. Thus, the energy of the abrasive is quite low, and impact is absent. Grinding abrasion is the fragmentation of the abrasive, usually between two strong surfaces. Examples are a lapping operation in a machine shop and ball/rod mill grinding. Thus, impact is low to moderate, but the gross stress may be quite high, at least on a microscopic scale. Gouging abrasion is recognized by the prominent grooves or gouges that are present on the wearing surfaces. Examples are abrasive disk grinding, machine tool cutting, and wear of power shovel bucket teeth. Heavy impact is generally associated with this type of abrasion, along with gross stress. To alleviate these forms of abrasion, a careful study of the type of abrasion and an understanding of the service conditions are required. The material selection should be based on the known properties of materials versus service requirements. More information on metal wear and corrosion is available in the article "Mechanically Assisted Degradation" in this Volume; the article "Wear Failures" in Failure Analysis and Prevention, Volume 11 of ASM Handbook, formerly 9th Edition Metals Handbook contains information on abrasion and wear. Other Forms of Corrosion. Selective leaching, also known as dealloying or parting corrosion, occurs when one element is preferentially removed from an alloy, leaving an often porous residue of an element that is more resistant to the environment. It is a problem of commercial significance in copper alloy systems (Ref 118), primarily copper-zinc and copper-aluminum and, to a lesser extent, copper-nickel. The terms dezincification, dealuminization, and denickelification describe the selective leaching of zinc, aluminum, and nickel, respectively, from the alloys. In these cases, a porous residue of copper remains, either as a fairly uniform layer or in plugs. The latter is more damaging in that the effect is similar to pitting corrosion. Selective leaching in copper alloy systems occurs primarily in certain waters, especially under deposits in stagnant areas in heat exchangers. Alloy additions of arsenic, antimony, or phosphorus are effective in inhibiting this attack, but only in copper-zinc alloys. Thus, arsenical or antimonial admiralty brass (UNS C44300 and C44400, respectively) is specified, for example, where this alloy is required for water service. Graphitic corrosion of cast iron is another commercially important form of selective leaching. In this case, the iron matrix corrodes, leaving behind a porous graphite mass that can be carved with a pocket knife. Cast iron underground municipal watermains (Ref 119) and fire watermains at petrochemical plant sites are affected by graphitic corrosion from both the soil and water sides. Internal cement linings and external protective coatings, with cathodic protection in severely corrosive soils, are relatively low-cost solutions to watermain corrosion problems. The section "Dealloying Corrosion" of the article "Metallurgically Influenced Corrosion" in this Volume contains more information on the phenomenon of dealloying. Exfoliation is a form of localized corrosion that primarily affects aluminum alloys. Corrosion proceeds laterally from initiation sites on the surface and generally proceeds intergranularly along planes parallel to the surface. The corrosion products that form in the grain boundaries force metal away from the underlying base material, resulting in a layered or flakelike appearance. Extruded products from the 2000-series copper-magnesium alloys, the 7000-series zinc-copper- magnesium alloys, and, to a lesser extent, the 5000-series alloys are particularly susceptible to exfoliation in both marine and industrial environments. Also, at least one case affecting 6000-series magnesium-silicon alloys in freshwater service has been reported (Ref 120). This attack is generally associated with the alloy fabrication method and temper, impurities in the alloy matrix, and the distribution of intermetallic compounds at the surface and in grain boundaries. Aluminum alloys 1100, 3003, and 5052 are resistant. Standard test methods for determining susceptibility to exfoliation corrosion in aluminum alloys are covered in ASTM standards G 34 and G 66. Liquid-metal embrittlement (LME), also known as liquid metal assisted cracking, is not considered to be a corrosion phenomenon, except in cases involving aqueous mercury compounds (Ref 121). However, LME is discussed here because it is a problem frequently encountered by materials engineers. Liquid-metal embrittlement is the penetration, usually along grain boundaries, of metals and alloys by such metals as mercury, which are liquid at room temperature, and metals that have relatively low melting points, such as bismuth, tin, lead, cadmium, zinc, aluminum, and copper. Stress, temperature, and time are the factors that facilitate and accelerate LME. Virtually all metal and alloy systems are subject to LME by one or more of these metals at or above their melting points. Zinc is a prime offender because of widespread use throughout industry in the form of corrosion-resistant coatings applied to carbon steels by hot-dip galvanizing, electroplating, tumbling, and spray painting. Plain carbon steels are embrittled by zinc at temperatures above 370 °C (700 °F) for long periods of time, especially when the steel is heavily stressed or cold worked. Austenitic stainless steels and nickel-base alloys will also crack in the presence of molten zinc. These alloys usually crack instantly when welded to galvanized steel, a fairly common occurrence in the chemical-processing industry. In addition, austenitic alloy failures have occurred: • In high-temperature bolting fastened with galvanized steel nuts • During welding or heat treating of components contaminated by grinding with zinc-loaded gr inding wheels, contact with zinc-coated structurals or slings, or exposure to zinc paint overspray • During process industry plant fires involving piping and vessels (thin- wall expansion joint bellows are especially susceptible) sprayed with molten zinc from coated steel structures Thus, it is imperative that all traces of zinc be removed from coated steel members before welding to austenitic alloys and before intimate contact with these alloys at temperatures above 370 °C (700 °F). Also, austenitic stainless steels and nickel-base alloys should be handled with non-coated steel hoist chains, cables, and structurals; they should be dressed and cleaned with new grinding wheels and stainless steel brushes, and they should be marked with materials (paints, crayons, and so on) free from zinc and other low-melting metals. Cadmium is probably second to zinc in importance as an agent of liquid-metal embrittlement, because of its application as a corrosion-resistant coating to a variety of hardware, particularly fasteners. Failures by cadmium LME of bolting operating at temperatures above 300 °C (570 °F) and fabricated from such high-strength alloy steels as AISI 4140 and 4340 and austenitic stainless steels are fairly common. In fact, some high-strength steels and high-strength titanium alloys are embrittled by cadmium at temperatures below its melting point by mechanisms not yet understood. The solution to LME by cadmium is similar to that of zinc, that is, avoidance of contact with, and contamination of, susceptible metal and alloy systems at temperatures above the 321 °C (610 °F) melting point of cadmium (and at all temperatures at which high- strength steels and titanium alloys are involved). Metal systems that are embrittled by contact with mercury include copper and its alloys, aluminum and its alloys, Nickel 200 (at elevated temperatures) and Monel alloy 400, and titanium and zirconium and their alloys. Cracking is intergranular except in zirconium alloys; in these alloys, cracking is transgranular. Mercury LME of aluminum and copper alloys was more common years ago in the petrochemical industry when mercury-filled manometers and thermometers were extensively used. Failures or upsets would release mercury into process or service (steam, cooling water, and so on) streams, causing widespread cracking of piping, heat exchanger tube bundles, and other equipment. Under these conditions, even pure aluminum and pure copper are susceptible. With regard to the titanium system, the commercially pure grades used in the chemical-processing industry are less sensitive than the alloys. In addition, LME in aqueous solutions of mercurous salts, such as mercurous nitrate, is possible because the mercurous ion can be reduced to its elemental form at local cathodic sites. Although not a metal, sulfur will penetrate the grain boundaries of nickel and nickel alloys at elevated temperatures in much the same way as in the low-melting metals mentioned above. Sulfur forms a very aggressive nickel-nickel sulfide eutectic alloy that metals at about 625 °C (1157 °F). Sources other than elemental sulfur include organic compounds (greases, oils, cutting fluids) and sulfates. Thus, contamination from these sources before welding, hot forming, annealing, and other heating operations must be avoided (see the section "Liquid-Metal Embrittlement" of the article "Environmentally Induced Cracking" in this Volume). Economics Cost-Effective Materials Selection. The two extremes for selecting materials on an economic basis without consideration of other factors are (Ref 122): • Minimum cost: Selection of the least expensive material, followed by scheduled periodic replacements or correction of problems as they arise • Minimum corrosion: Selection of the most corrosion-resistan t material regardless of installed cost or life of the equipment Cost-effective selection generally falls somewhere between these extremes and includes consideration of other factors, such as availability and safety. For example, critical components in a large single-train chemical-processing plant should be fabricated from materials that tend toward the minimum corrosion extreme because failure could shut down the entire operation. However, component materials for a multitrain or batch operation, especially one that processes a relatively short-lived product, might tend toward the minimum cost extreme, even to the point of purchasing used equipment at a fraction of the cost of new fabrication. Thus, different strategies are appropriate for different situations. Additional information is available in the article "Corrosion Economic Calculations" in this Volume. References 1. R.J. Landrum, Designing for Corrosion Resistance, Chem. Eng., 24 Feb 1969, p 118- 124; 24 March 1969, p 172-180 2. Corrosion Abstracts, National Association of Corrosion Engineers 3. Corrosion Data Survey Metals Section, 6th ed., 1985; Corrosion Data Survey Nonmetals Section, National Association of Corrosion Engineers, 1975 4. C. Westcott et al., "The Development and Application of Integrated Expert Systems and Data Bases for Corrosion Consultancy," Paper 54, presented at Corrosion/8 6, Houston, TX, National Association of Corrosion Engineers, March 1986 5. E.H. Schmauch et al., "Expert Systems for Personal Computers," Paper 55, presented at Corrosion/86, Houston, TX, National Association of Corrosion Engineers, March 1986 6. S.E. Marschand et al., "Expert Systems Developed by Corrosion Specialists," Paper 56, presented at Corrosion/86, Houston, TX, National Association of Corrosion Engineers, March 1986 7. W.F. Bogaerts et al., "Artificial Intelligence, Expert Systems and Computer-A ided Engineering In Corrosion Control," Paper 58, presented at Corrosion/86, Houston, TX, National Association of Corrosion Engineers, March 1986 8. R.B. Puyear, Material Selection Criteria for Chemical Processing Equipment, Met. Prog., Feb 1978, p 40- 46 9. "Laboratory Corrosion Testing of Metals for the Process Industries," NACE TM-01- 69 (1976 Revision); "Method of Conducting Controlled Velocity Laboratory Corrosion Tests," NACE TM-02- 70, National Association of Corrosion Engineers 10. Metal Corrosion, Erosion, and Wear, Vol 03.02, Section 3, Annual Book of ASTM Standards, American Society for Testing and Materials, 1986 11. G. Kobrin, Evaluate Equipment Condition by Field Inspection and Tests, Hydrocarbon Process., Jan 1970, p 115-120 12. B.J. Moniz, Field Identification of Metals, in Process Industries Corrosion The Theory and Practice, National Association of Corrosion Engineers, 1986, p 839 13. B.J. Moniz, Field Identification of Metals, in Process Industries Corrosion The Theory and Practice, National Association of Corrosion Engineers, 1986, p 842 14. Monitoring Internal Corrosion in Oil and Gas Production Operations With Hydrogen Probes, NACE Publication 1C 184, Mater. Perform., June 1984, p 49-56 15. J.C. Bovankovich, On-Line Corrosion Monitoring, Mater. Prot. Perform., June 1973, p 20-23 16. G. Kobrin, Reflections on Microbiologically Induced Corrosion of Stainless Steels, in Biologically Induced Corrosion, NACE-8, S.C. Dexter, Ed., National Association of Corrosion Engineers, 1986, p 33- 46 17. Guide to Engineered Materials, Vol 1, ASM INTERNATIONAL, June 1986, p 79 18. R. Baboian, New Methods for Controlling Galvanic Corrosion, Mach. Des., 11 Oct 1979, p 78-85 19. R.M. Davison, H.E. Deverell, and J.D. Redmond, Ferritic and Duplex Stainless Steels, in Process Industries Corrosion The Theory and Practice, National Association of Corrosion Engineers, 1986, p 427-443 20. "Intergranular Corrosion of Chromium-Nickel Stainless Steels Final Report," Bulletin 138, Welding Research Council, 1969 21. M.A. Streicher, Tests for Detecting Susceptibility to Intergranular Corrosion, in Process Industries Corrosion The Theory and Practice, National Association of Corrosion Engineers, 1986, p 123-159 22. J.S. Armijo, Intergranular Corrosion of Nonsensitized Austenitic Stainless Steels, Corrosion, Jan 1968, p 24-30 23. W.H. Herrnstein, J.W. Cangi, and M.G. Fontana, Effect of Carbon Pickup on the Serviceability of Stainless Steel Alloy Castings, Mater. Perform., Oct 1975, p 21-27 24. Corrosion Data Survey Metals Section, 5th ed., National Association of Corrosion Engineers, 1974, p 268-269 25. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Inst itute of the Chemical Process Industries, 1985, p 8-14 26. The Role of Stainless Steels in Petroleum Refining, American Iron and Steel Institute, 1977, p 41 27. D.R. McIntyre and C.P. Dillon Guidelines for Preventing Stress Corrosion Cracking in the Chem ical Process Industries, Publication 15, Materials Technology Institute of the Chemical Process Industries, 1985, p 21-22 28. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publicatio n 15, Materials Technology Institute of the Chemical Process Industries, 1985, p 208-209 29. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Instit ute of the Chemical Process Industries, 1985, p 216-217 30. R.M. Davison, H.E. Deverell, and J.D. Redmond, Ferritic and Duplex Stainless Steels, in Process Industries Corrosion The Theory and Practice, National Association of Corrosion Engineers, 1986, p 434-435 31. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute of the Chemical Process Industries, 1985, p 150-151 32. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute of the Chemical Process Industries, 1985, p 179 33. D.R. McIntyre, Factors Affecting the Stress Corrosion Cr acking of Austenitic Stainless Steels Under Thermal Insulation, in Corrosion of Metals Under Thermal Insulation, STP 880, American Society for Testing and Materials, 1985, p 29-33 34. J.A. Richardson and T. Fitzsimmons, Use of Aluminum Foil for Prevention of Stress Corrosion Cracking of Austenitic Stainless Steel Under Thermal Insulation, in Corrosion of Metals Under Thermal Insulation, STP 880, American Society for Testing and Materials, 1985, p 188-198 35. D.R. McIntyre and C.P. Dillon, Guidelines for P reventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute of the Chemical Process Industries, 1985, p 69 36. The Role of Stainless Steels in Petroleum Refining, American Iron and Steel Institute, 1977, p 42-44 37. "Protection of Austenitic Stainless Steels in Refineries Against Stress Corrosion Cracking by Use of Neutralizing Solutions During Shutdown," NACE RP-01- 70, (1970 Revision), National Association of Corrosion Engineers 38. M.G. Fontana , F.H. Beck, and J.W. Flowers, Cast Chromium Nickel Stainless Steels for Superior Resistance to Stress Corrosion, Met. Prog., Dec 1961 39. J.W. Flowers, F.H. Beck, and M.G. Fontana, Corrosion and Age Hardening Studies of Some Cast Stainless Alloys Containing Ferrite, Corrosion, May 1963, p 194t-195t 40. J.W. Flowers, F.H. Beck, and M.G. Fontana, Corrosion and Age Hardening Studies of Some Cast Stainless Alloys Containing Ferrite, Corrosion, May 1963, p 195t-196t 41. W.H. Friske, Shot Peening to Prevent the Corrosion of Austenitic Stainless Steels, AI-75- 52, Rockwell International, 1975 42. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute o f the Chemical Process Industries, 1985, p 164 43. Internal Report, Accession No. 15925, E.I. Du Pont de Nemours & Company, Inc., p 6, 7 44. Corrosion Data Survey Metals Section, 6th ed., National Association of Corrosion Engineers, 1985, p 176 45. O.L. Towers, SCC in Welded Ammonia Vessels, Met. Constr., Aug 1984, p 479-485 46. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute of the Che mical Process Industries, 1985, p 53 47. J.D. Jackson and W.K. Boyd, "Stress- Corrosion Cracking of Aluminum Alloys," DMIC Memorandum 202, Battelle Memorial Institute, 1965, p 2, 3 48. J.R. Myers, H.B. Bomberger, and F.H. Froes, Corrosion Behavior and Use of Titanium and Its Alloys, J. Met., Oct 1984, p 52, 53 49. D.R. McIntyre and C.P. Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process Industries, Publication 15, Materials Technology Institute of the Chemical Process Indu stries, 1985, p 88 50. R.A. Page, Stress Corrosion Cracking of Alloys 600 and 690 and Nos. 82 and 182 Weld Metals in High Temperature Water, Corrosion, Vol 39 (No. 10), Oct 1983, p 409-421 51. A.R. McIlree and H.T. Michels, Stress Corrosion Behavior of Fe-Cr- Ni and Other Alloys in High Temperature Caustic Solutions, Corrosion, Vol 33 (No. 2), Feb 1977, p 60-67 52. Ph. Berge et al., Caustic Stress Corrosion of Fe-Cr-Ni-Austenitic Alloys, Corrosion, Vol 33 (No. 12), Dec 1977, p 425-435 53. R.S. Pathania, Caustic Cracking of Steam Generator Tube Materials, Corrosion, Vol 34 (No. 5), May 1978, p 149-156 54. R.S. Pathania and J.A. Chitty, Stress Corrosion Cracking of Steam Generator Tube Materials in Sodium Hydroxide Solutions, Corrosion, Vol 34 (No. 11), Nov 1978, p 369-378 55. K.H. Lee et al., Effect of Heat Treatment Applied Potential on the Caustic Stress Corrosion Cracking of Inconel 600, Corrosion, Vol 41 (No. 9). Sept 1985, p 540-553 56. R.S. Pathania and R.D. Cleland, The Effect of Thermal Treatment s on Stress Corrosion Cracking of Alloy-800 in a Caustic Environment, Corrosion, Vol 41 (No. 10), Oct 1985, p 575-581 57. J.R. Crum, Stress Corrosion Cracking Testing of Inconel Alloys 600 and 690 Under High Temperature Caustic Conditions, Corrosion, Vol 42 (No. 6), June 1986, p 368-372 58. Summary of Questionnaire Replies on Corrosion in HF Alkylation Units, Corrosion, Vol 15, May 1959, p 237t-240t 59. Materials for Receiving, Handling and Storing Hydrofluoric Acid, NACE Publication 5A171 (1983 Revision), Mater. Perform., Nov 1983, p 9-12 60. F.W. Billmeyer, Textbook of Polymer Science, 2nd ed., John Wiley & Sons, 1971, p 133 61. R.B. Seymour, Plastics vs Corrosives, John Wiley & Sons, 1982, p 46 62. D.R. McIntyre, Environmental Cracking, in Process Industries Corrosion, National Association of Corrosion Engineers, 1986, p 21-30 63. D. Warren, Hydrogen Effects on Steel, in Process Industries Corrosion, National Association of Corrosion Engineers, 1986, p 31-43 64. J. McBreen et al., The Electrochemical Introduction of Hydrogen Into Metals, in Fundamental Aspects of Stress Corrosion Cracking, National Association of Corrosion Engineers, 1967, p 51-63 65. W. Beck et al., Hydrogen Permeation in Metals as a Function of Stress, Temperature, and Dissolved Hydrogen Concentration, in Hydrogen Damage, American Society for Metals, 1977, p 191-206 66. R. Gibala, "Internal Friction in Hydrogen-Charged Iron," Case Institute of Technology, 1967 67. R. Gibala, AIME Abstract Bull. (Inst. of Metals Div.), Vol 1, 1966, p 36 68. R. Gibala, Hydrogen-Dislocation Interaction in Iron, Trans. Met. Soc. AIME, Vol 239, 1967, p 1574 69. R. Gibala, "On the Mechanism of the Köster Relaxation Peak," Case Institute of Technology, Department of Metallurgy, 1967 70. A. Szummer, Bull. Acad. Polon Ser. Sci. Chem., Vol 12, 1964, p 651 71. D.A. Vaughan et al., Corrosion, Vol 19. 1963, p 315t 72. M.L. Holzworth et al., Corrosion, Vol 24, 1968, p 110-124 73. N.A. Nielsen, Observations and Thoughts on Stress Corrosion Mechanisms, in Hydrogen Damage, American Society for Metals, 1977, p 219-254 74. M.O. Spiedel, Hydrogen Embrittlement of Aluminum Alloys?, in Hydrogen Damage, American Society for Metals, 1977, p 329-351 75. L.S. Darken et al., Behavior of Hydrogen in Steel During and After Immersion in Acid, in Hydrogen Damage, American Society for Metals, 1977, p 60-75 76. H.H. Johnson et al., Hydrogen Crack Initiation and Delayed Failure in Steel, Trans. AIME, Vol 212, 1958, p 526-536 77. K. Farrell et al., Hydrogen Embrittlement of an Ultra-High-Tensile Steel, J. Iron Steel Inst., Dec 1964, p 1002-1011 78. C.D. Kim et al., Techniques for Investigating Hydrogen- Induced Cracking of Steels With High Yield Strength, Corrosion, Vol 24, 1968, p 313-318 79. K. Farrell, Cathodic Hydrogen Absorption and Severe Embrittlement in a High Strength Steel, Corrosion, Vol 26, 1970, p 105-110 80. W.M. Baldwin, Jr. et al., Hydrogen Embrittlement of Steels, Trans. AIME (J. Met.), Vol 200, 1954, p 298-303 81. P. Blanchard et al., "La Fragilisation de s Metaus par L'hydrogen. Influence de la Structure Cristallographic et Electronique," Paper presented before the Societe Francaise de Metallurgie, Oct 1959 82. G.G. Hancock et al., Hydrogen Cracking and Subcritical Crack Growth in a High Strength Steel, T rans. AIME, Vol 236, 1966, p 447 83. D.P. Williams et al., Embrittlement of 4130 Steel by Low-Pressure Gaseous Hydrogen, Metall. Trans., Vol 1, 1970, p 63 84. G.E. Kerns et al., Slow Crack Growth of a High Strength Steel in Chlorine and Hydrogen Sulfide Gas Environments, Scr. Metall., Vol 6, 1972, p 631-634 85. G.E. Kerns et al., Slow Crack Growth of a High Strength Steel in Chlorine and Hydrogen Halide Gas Environments, Scr. Metall., Vol 6, 1972, p 1189-1194 86. R.M. Hudson, Corrosion, Vol 20, 1969, p 24t 87. T.P. Radhakrishnan et al., Electrochim. Acta, Vol 11, 1966, p 1007 88. G.E. Kerns, Effects of Sulfur and Sulfur Compounds on Aqueous Corrosion, in Process Industries Corrosion, National Association of Corrosion Engineers, 1986, p 353-365 89. M.T. Wang et al., Effect of Heat Treatment and Stress Intensity Parameters on Crack Velocity and Fractography of AISI 4340 Steel, in Hydrogen in Metals, International Conference in Paris, 1972, p 342 90. V. Sawicki, Ph.D. dissertation, Cornell University, 1972 91. G.E. Kerns, Ph.D. dissertation, Ohio State University, 1973 92. P. McIntyre et al., "Accelerated Test Technique for the Determination of K ISCC in Steels," Corporate Laboratories Report MG/31/72, British Steel Corporation, 1972 93. Bulletin 191, Welding Research Council, March 1978 94. N. Bailey, Welding Carbon Manganese Steels, Met. Constr., Vol 2, 1970, p 442-446 95. R.L. Schuyler, III, Hydrogen Blistering of Steel in Anhydrous Hydrofluoric Acid, Mater. Perform., Vol 18 (No 8), 1979, p 9-16 96. G. Herbsleb et al., Occurrence and Prevention of Hydrogen Induced Stepwise Cracking and Stress Corrosion Cracking of Low Alloy Pipeline Steels, Corrosion, Vol 37 (No. 5), 1981, p 247-255 97. S.A. Golovanenko et al., Effect of Alloying Elements and Struc ture on the Resistance of Structural Steels to Hydrogen Embrittlement, in H 2 S Corrosion in Oil and Gas Production A Compilation of Classic Papers, National Association of Corrosion Engineers, 1981, p 198 98. J. Watanabe et al., "Hydrogen-Induced Disbondi ng of Stainless Weld Overlay Found in Hydrodesulfurizing Reactor," Paper presented at ASME Conference on Performance of Pressure Vessels with Clad and Overlaid Stainless Steel Linings, Denver, CO, American Society of Mechanical Engineers, 1981 99. J. Watanabe et al., "Hydrogen Induced Disbonding of Stainless Steel Overlay Weld," Paper presented at the Pressure Vessel Research Committee Meeting, New York, NY, 1980 100. M.G. Fontana and N.D. Greene, Corrosion Engineering, McGraw-Hill, 1967, p 72-91 101. F.J. Heymann, Erosion by Liquids The Mysterious Murderer of Metals, Mach. Des., Dec 1970 102. I.M. Hutchings, The Erosion of Materials by Liquid Flow, Publication 25, Materials Technology Institute of the Chemical Process Industries, 1986 103. P. Eisenbery et al., How to Protect Materials Against Cavitation Damage, Mater. Des. Eng., March 1967 104. T.E. Backstrom, "A Suggested Metallurgical Parameter in Alloy Selection for Cavitation Resistance," Report CHE 72, Department of the Interior, Dec 1972 105. R.W. Hinton, "Cavitation Damage of Alloys Relationship to Microstructure," Paper presented at NACE [...]... 317L 18 14 3.2 34L 17 15 4. 3 34LN 18 14 4.7 1 .44 39 18 14 4.3 0.13 Nitronic 50 21 14 2.2 0.20 20Cb-3 20 33 2 .4 Alloy 904L 20 25 4. 2 2RK65 20 25 4. 5 JS700 21 25 4. 5 19/25LC 20 25 4. 8 Al-6X 20 24 6.6 254SMO 20 18 6.1 0.20 19/25HMO 21 25 5.9 0.15 Type 316L 19 12 2.3 Type 317L 19 13 3.8 Base metals Filler metals 309MoL 23 14 2.5 Batox Cu 19 24 4.6 254SLX 20 24 5.0 SP-281 20 25 4. 6 Jungo 45 00... Behavior of Mild Steel Under Conditions of Fretting Corrosion, Wear, Vol 5, 1962, p 235- 244 110 Fretting and Fretting Corrosion, Lubrication, Vol 52 (No 4) , 1966 111 J.R McDowell in Symposium of Fretting Corrosion, STP 144 , American Society for Testing and Materials, 1952 112 H.S Avery, Abrasive Wear The Nature of the Abrasive, Publication RCR CR 340 , Abex Corporation 113 H.S Avery, "Hard Facing Alloys,"... Design and Corrosion Control, Macmillan, 1977 2 R.N Parkins and K.A Chandler, Corrosion Control in Engineering Design, Department of Industry, Her Majesty's Stationery Office, 1978 3 L.D Perrigo and G.A Jensen, Fundamentals of Corrosion Control Design, North Eng., Vol 13, 1982, p 16 34 4 P Elliott, Corrosion Survey, supplement to The Chemical Engineer, Sept 1973 5 P Elliott and J.S Llewyn-Leach, Corrosion. .. Mechanism of the Dealloying Phenomenon, Corrosion, Feb 1968, p 38 -44 119 R.A Gummow, The Corrosion of Municipal Iron Watermains, Mater Perform., March 19 84, p39 -42 120 J Zahavi and J Yahalom, Exfoliation Corrosion of Al Mg Si Alloys in Water, J Electrochem Soc., Vol 129 (No 6), June 1982, p 1181-1185 121 D.R McIntyre and C.P Dillon, Guidelines for Preventing Stress Corrosion Cracking in the Chemical Process... Prog., May 1960, p 80-88, 1 34, 166-1 74 P.A Schweitzer, Ed., Corrosion and Corrosion Protection Handbook, Marcel Dekker, 1983 H.H Uhlig and R.W Revie, Corrosion and Corrosion Control, 3rd ed., John Wiley & Sons, 1985 F.L Whitney, Jr., Factors in the Selection of Corrosion Resistant Materials, Met Prog., June 1957, p 90-95 Design Details to Minimize Corrosion Peter Elliott, Cortest Engineering Services Inc... Llewyn-Leach, Corrosion Control Checklist for Design Offices, Department of Industry, Her Majesty's Stationery Office, 1981 6 C.J Smithells, Ed., Corrosion Control, in Metals Reference Book, Butterworths, 1977 7 J Jelinek and B Studman, Inspection Offshore, Gas Eng Mgmt., Nov-Dec 1983, p 395 -40 4 Corrosion of Weldments The ASM Committee on Corrosion of Weldments Introduction IT IS NOT UNUSUAL to find... calomel electrode (SCE) Source: Ref 4 Tables are available in Ref 4 that summarize filler alloy selection recommended for welding various combinations of base metal alloys to obtain maximum properties, including corrosion resistance Care must be taken not to extrapolate the corrosion performance ratings indiscriminately Corrosion behavior ratings generally pertain only to the particular environment tested,... immersion in fresh or salt water For example, the highest corrosion rating (A) is listed for use of filler alloy 40 43 to join 3003 alloy to 6061 alloy In strong (99%) nitric acid (HNO3) service, however, a weldment made with 40 43 filler alloy would experience more rapid attack than a weldment made using 5556 filler metal With certain alloys, particularly those of the heat-treatable 7xxx series, thermal... Alloy Weldment in H2SO4 Service A 76-mm (3-in.) diameter tantalum alloy tee removed from the bottom of an H2SO4 absorber that visually showed areas of severe etching attack was examined The absorber had operated over a period of several months, during which time about 11 ,40 0 kg (25,000 lb) of H2SO4 was handled The absorber was operated at 60 °C ( 140 °F) with nominally 98% H2SO4 There was a possibility...Conference, National Association of Corrosion Engineers, March 1963 106 R.E.A Arndt, "Cavitation and Erosion: An Overview," Paper presented at NACE Conference, National Association of Corrosion Engineers, March 1977 107 Trans ASME, Vol 59, 1937 108 R.B Waterhouse and M Allery, The Effect of Non-Metallic Coatings on the Fretting Corrosion of Mild Steel, Wear, Vol 8, 1965, p 42 1 -44 7 109 R.B Waterhouse et al., . 44 . Corrosion Data Survey Metals Section, 6th ed., National Association of Corrosion Engineers, 1985, p 176 45 . O.L. Towers, SCC in Welded Ammonia Vessels, Met. Constr., Aug 19 84, p 47 9 -48 5. Fretting Corrosion, Wear, Vol 5, 1962, p 235- 244 110. Fretting and Fretting Corrosion, Lubrication, Vol 52 (No. 4) , 1966 111. J.R. McDowell in Symposium of Fretting Corrosion, STP 144 , American. Fe-Cr-Ni-Austenitic Alloys, Corrosion, Vol 33 (No. 12), Dec 1977, p 42 5 -43 5 53. R.S. Pathania, Caustic Cracking of Steam Generator Tube Materials, Corrosion, Vol 34 (No. 5), May 1978, p 149 -156 54. R.S.