Volume 01 - Properties and Selection Irons, Steels, and High-Performance Alloys Episode 11 pdf

• Machine tools should be rigid and in good condition. Any factors that encourage chatter are undesirable • Tools should be sharp. Dull tools cause excessive work hardening of the cut surface and accentuate the difficulty in machining • Low speeds of about 9 to 12 m/min (30 to 40 sfm) should be used. High speeds are likely to create red- hot chips and to cause rapid tool breakdown • Cobalt high-speed steel tools or tools with cemented carbide and ceramic inserts can be used. The latter are preferred • The liberal use of a good grade of sulfur-bearing cutting oil is beneficial but not essential • In castings, holes should be formed by cores in the foundry, rather than by machining, whenever possible • Coolants are recommended for surface grinding operations Various sources provide statements in favor of both positive-rake and negative-rake tools and both dry cutting and liquid coolants. Because high temperatures at the cutting edge are a large part of the problem, effective cooling seems desirable. Negative-rake tools are likely to require more force and thus to produce more heat. However, the thinner edge of a positive-rake tool is more vulnerable to heat. Comparative machining data are presented in Table 17. Table 17 Feed forces required in lathe turning of austenitic manganese steels Specimens were 31.7 mm (1.25 in.) diam bars, toughened by water quenching. Roughing cuts 2.5 mm (0.098 in.) deep were taken using complex-carbide tools c ontaining about 15% TiC + TaC (predominantly TiC) and about 7 to 10% Co. New cutting edges were used for each positive or negative rake. Cutting speed was 0.19 to 0.20 m/s (37 to 39 sfm). Feed forces Negative 7° rake Flat tool Positive 6° rake Horizontal Vertical Horizontal Vertical Horizontal Vertical Type of steel N lbf kN lbf N lbf kN lbf kN lbf kN lbf 1.12C-13Mn 670 150 1.58 355 780 175 1.58 355 1.13 255 1.67 375 3Ni-13Mn 620 140 1.53 345 . . . . . . . . . . . . 1.25 280 1.69 380 1Mo-13Mn 800 180 1.65 370 . . . . . . . . . . . . 1.09 245 1.71 385 1.12C-13Mn leaded (a) 580 130 1.49 335 490 110 1.38 310 1.25 280 1.69 380 Wrought type 304 stainless (b) 690 155 1.16 260 890 200 1.25 280 Welded to tool Welded to tool Cast CF-8 stainless (b) 670 150 1.13 255 . . . . . . . . . . . . 2.25 505 2.56 575 Source: Ref 3 (a) Recovery of 0.20% Pb from 0.35% added in ladle. The effect on machinability is inclusive. (b) Stainless steels suffer in comparison at this speed. They are more machinable at higher speeds and permit certain operations, such as drilling of 6.4 mm ( 1 4 -in.) diam holes, which are very difficult with austenitic manganese steel. The type 304 stainless steel was cold finished. Machinability is increased by the embrittlement that develops with reheating between about 540 and 650 °C (1000 and 1200 °F). Although not usually practicable, such a treatment may be useful if the part can subsequently be properly toughened. Milling usually is not considered practicable. Machinable Grade. A 20Mn-0.6C steel was developed specifically for improved machinability. Table 18 gives the mechanical properties of this material. Even though the yield strength was deliberately reduced from 360 MPa (52 ksi) to a value between 240 and 310 MPa (35 and 45 ksi) to obtain improved machinability, the ultimate tensile strength exceeds 620 MPa (90 ksi), and elongation in small castings may reach 40%. The heat treatment of this steel involves water quenching from 1040 °C (1900 °F). As-cast properties are lower but are probably adequate for many applications. Table 18 Typical room-temperature properties of machinable manganese steel Tensile strength Yield strength Type Treatment MPa ksi MPa ksi Elongation, % Reduction in area, % Hardness HB Magnetic permeability, Standard 13% Mn Toughened 825 120 360 52 40 35 200 1.01 Toughened 640- 855 93- 124 275- 310 40- 45 39-65 26-44 159-170 1.003 Machinable grade A, 20 Mn-0.6 C As-cast 380- 580 55-84 275- 305 40- 44 13-22 24 159-170 1.003 Source: Abex Research Center This nonmagnetic modified grade can be lathe turned, drilled, tapped, and threaded; even holes 6.4 mm ( 1 4 in.) in diameter can be drilled and tapped in this metal. In some machine shops, it is rated only slightly more difficult to drill than plain 1020 steel, and the quality of the tapped threads is considered very good. Typical machining data for this steel are presented in Table 19. Wear resistance has been sacrificed for machinability, and this grade has significantly less abrasion resistance than do the various types in ASTM A 128. Table 19 Force requirements for single-point lathe turning of austenitic manganese steel Feed force (a) Horizontal Vertical Type Condition N lbf N lbf Friction coefficient Standard 13% Mn As-cast 535-670 120-150 1225 275 0.64 Toughened 690 155 1310 295 0.76 As-cast 155-290 35-65 890-980 200-220 0.31-0.48 Machinable grade A (20% Mn) Toughened 180-380 40-85 955-1000 215-225 0.33-0.57 Source: Abex Research Center (a) Depth of cut, 3 mm (0.1 in.) on radius; feed, 0.16 mm/rev (0.0062 in./rev); turning speed, 1.35 m/s (265 ft/min); 6° positive-rake tool. Reference cited in this section 3. H.S. Avery, Austenitic Manganese Steel, Metals Handbook, Vol 1, 8th ed., American Society for Metals, 1961 Austenitic Manganese Steels Revised by D.K. Subramanyam, * Ergenics Inc.; A.E. Swansiger, ABC Rail Corporation; and H.S. Avery, Consultant References 1. E.C. Bain, E.S Davenport, and W.S.N. Waring, The Equilibrium Diagram of Iron-Manganese- Carbon Alloys of Commercial Purity, Trans. AIME, Vol 100, 1932, p 228 2. C.H. Shih, B.L. Averbach, and M. Cohen, Work Hardeni ng and Martensite Formation in Austenitic Manganese Alloys, Research Report, Massachusetts Institute of Technology, 1953 3. H.S. Avery, Austenitic Manganese Steel, Metals Handbook, Vol 1, 8th ed., American Society for Metals, 1961 4. H.S. Avery, Work Hardening in Relation to Abrasion Resistance, in Proceedings of the Symposium on Materials for the Mining Industry, published by Climax Molybdenum Company, 1974, p 43 5. Manganese Steel, Oliver and Boyd, for Hadfields Ltd., 1956 6. H.S. Avery and H.J. Chapin, Austenitic Manganese Steel Welding Electrodes, Weld. J., Vol 33, 1954, p 459 7. F. Borik and W.G. Scholz, Gouging Abrasion Test for Materials Used in Ore and Rock Crushing, Part II, J. Mater., Vol 6 (No. 3), Sept 1971, p 590 8. M. Fujikura, Recent Developments of Austenitic Manganese Steels for Non- Magnetic and Cryogenic Applications in Japan, The Manganese Center, Paris 1984 9. D.J. Schmatz, Structure and Properties of Austenitic Alloys Containing Aluminum and Silicon, Trans. ASM, Vol 52, 1960, p 898 10. J. Charles and A. Berghezan, Nickel-Free Austenitic Steels for Cryogenic Applications: The Fe-23% Mn- 5% Al-0.2% C Alloys, Cryogenics, May 1981, p 278 11. R. Wang and F.H. Beck, New Stainless Steel Without Nickel or Chromium for Marine Applications, Met. Prog., March 1983, p 72 12. J.C. Benz and H.W. Leavenworth, Jr., An Assessment of Fe-Mn- Al Alloys as Substitutes for Stainless Steels, J. Met., March 1985, p 36 13. W.J. Jackson and M.W. Hubbard, Steelmaking for Steelfounders, Steel Castings Researc h and Trade Association, 1979, p 106 14. R. Castro and P. Garnier, Some Decomposition Structures of Austenitic Manganese Steels, Rev. Métall., Cah. Inf. Tech., Vol 55, Jan 1958, p 17 15. D. Rittel and I. Roman, Tensile Fracture of Coarse-Grained Cast Austenitic Manganese Steels, Metall. Trans. A, Vol 19A, Sept 1988, p 2269-2277 16. P.H. Adler, G.B. Olson, and W.S. Owen, Strain Hardening of Hadfield Manganese Steel, Metall. Trans. A, Vol 17A, Oct 1986, p 1725 17. H.C. Doepken, Tensile Properties of Wroug ht Austenitic Manganese Steel in the Temperature Range from +100 °C to -196 °C, J. Met., Trans. AIME, Feb 1952, p 166 18. K.S. Raghavan, A.S. Sastri, and M.J. Marcinkowski, Nature of the Work Hardening Behaviour in Hadfield's Manganese Steel, Trans. TSM-AIME, Vol 245, July 1969, p 1569 19. Y.N. Dastur and W.C. Leslie, Mechanism of Work Hardening in Hadfield Manganese Steel, Metall. Trans. A., Vol 12A, May 1981, p 749 20. B.K. Zuidema, D.K. Subramanyam, and W.C. Leslie, The Effect of Aluminum on the Work Hardening and Wear Resistance of Hadfield Manganese Steel, Metall. Trans. A, Vol 18A, Sept 1987, p 1629 21. Abex Research Center, Abex Corporation, unpublished research, 1981-1983 22. H.S. Avery, Austenitic Manganese Steel, American Brakeshoe Company, 19 49, condensed version in Metals Handbook, American Society for Metals, 1948, p 526-534 23. T.E. Norman, Eng. Mining J., July, 1957, p 102 24. R. Blickensderfer, B.W. Madsen, and J.H. Tylczak, Comparison of Several Types of Abrasive Wear Tests, in Wear of Materials 1985, K.C. Ludema, Ed., American Society of Mechanical Engineers, p 313 25. D.E. Diesburg and F. Borik, Optimizing Abrasion Resistance and Toughness in Steels and Irons for the Mining Industry, in Proceedings of the Symposium on Materials for the Mining Industry, Climax Molybdenum Company, 1974, p 15 26. U. Bryggman, S. Hogmark, and O. Vingsbo, Abrasive Wear Studied in a Modified Impact Testing Machine, Wear of Materials, 1979, p 292 27. "The Physical Properties of a Series of Steels, Part II, " Special Report 23, Alloy Steels Research Committee, British Iron and Steel Institute, Sept 1946 28. Metals and Their Weldability, Vol 4, 7th ed., Welding Handbook, American Welding Society, 1982, p 195 Wrought Stainless Steels Revised by S.D. Washko and G. Aggen, Allegheny Ludlum Steel, Division of Allegheny Ludlum Corporation Introduction STAINLESS STEELS are iron-base alloys containing at least 10.5% Cr. Few stainless steels contain more than 30% Cr or less than 50% Fe. They achieve their stainless characteristics through the formation of an invisible and adherent chromium-rich oxide surface film. This oxide forms and heals itself in the presence of oxygen. Other elements added to improve particular characteristics include nickel, molybdenum, copper, titanium, aluminum, silicon, niobium, nitrogen, sulfur, and selenium. Carbon is normally present in amounts ranging from less than 0.03% to over 1.0% in certain martensitic grades. The selection of stainless steels may be based on corrosion resistance, fabrication characteristics, availability, mechanical properties in specific temperature ranges and product cost. However, corrosion resistance and mechanical properties are usually the most important factors in selecting a grade for a given application. Original discoveries and developments in stainless steel technology began in England and Germany about 1910. The commercial production and use of stainless steels in the United States began in the 1920s, with Allegheny, Armco, Carpenter, Crucible, Firth-Sterling, Jessop, Ludlum, Republic, Rustless, and U.S. Steel being among the early producers. Only modest tonnages of stainless steel were produced in the United States in the mid-1920s, but annual production has risen steadily since that time. Even so, tonnage has never exceeded about 1.5% of total production for the steel industry. Table 1 shows shipments of stainless steel over a recent 10-year period. Production tonnages are listed only for U.S. domestic production. France, Italy, Japan, Sweden, the United Kingdom, and West Germany produce substantial tonnages of steel, and data on production in these countries are also available. However, other free-world countries do not make their figures public, and production statistics are not available from the U.S.S.R. or other Communist nations, which makes it impossible to estimate accurately the total world production of stainless steel. Table 1 Total U.S. shipments of stainless steel over the 10-year period from 1979 to 1988 Shipments Year kt 1000 tons 1979 1234 1361 1980 (a) 1022 1127 1981 (a) 1055 1163 1982 (a) 811 894 1983 (a) 1032 1137 1984 (a) 1132 1248 1985 (a) 1135 1251 1986 (a) 1077 1187 1987 (a) 1287 1418 1988 (b) 1439 1586 (a) Ref 1. (b) Ref 2 The development of precipitation-hardenable stainless steels was spearheaded by the successful production of Stainless W by U.S. Steel in 1945. Since then, Armco, Allegheny-Ludlum, and Carpenter Technology have developed a series of precipitation-hardenable alloys. The problem of obtaining raw materials has been a real one, particularly in regard to nickel during the 1950s when civil wars raged in Africa and Asia, prime sources of nickel, and Cold War politics played a role because Eastern-bloc nations were also prime sources of the element. This led to the development of a series of alloys (AISI 200 type) in which manganese and nitrogen are partially substituted for nickel. These stainless steels are still produced today. New refining techniques were adopted in the early 1970s that revolutionized stainless steel melting. Most important was the argon-oxygen-decarburization (AOD) process. The AOD and related processes, with different gas injections or partial pressure systems, permitted the ready removal of carbon without substantial loss of chromium to the slag. Furthermore, low carbon contents were readily achieved in 18% Cr alloys when using high-carbon ferrochromium in furnace charges in place of the much more expensive low-carbon ferrochromium. Major alloying elements could also be controlled more precisely, nitrogen became an easily controlled intentional alloying element, and sulfur could be reduced to exceptionally low levels when desired. Oxygen could also be reduced to low levels and, when coupled with low sulfur, resulted in marked improvements in steel cleanliness. During the same period, continuous casting grew in popularity throughout the steel industry, particularly in the stainless steel segment. The incentive for continuous casting was primarily economic. Piping can be confined to the last segment to be cast such that yield improvements of approximately 10% are commonly achieved. Improvements in homogeneity are also attained. Over the years, stainless steels have become firmly established as materials for cooking utensils, fasteners cutlery, flatware, decorative architectural hardware, and equipment for use in chemical plants, dairy and food-processing plants, health and sanitation applications, petroleum and petrochemical plants, textile plants, and the pharmaceutical and transportation industries. Some of these applications involve exposure to either elevated or cryogenic temperatures; austenitic stainless steels are well suited to either type of service. Properties of stainless steels at elevated temperatures are discussed in the section "Elevated-Temperature Properties" of this article and more detailed information is available in the article "Elevated-Temperature Properties of Stainless Steels" in this Volume. Properties at cryogenic temperatures are discussed in the section "Subzero-Temperature Properties" of this article. Modifications in composition are sometimes made to facilitate production. For instance, basic compositions are altered to make it easier to produce stainless steel tubing and castings. Similar modifications are made for the manufacture of stainless steel welding electrodes; here, combinations of electrode coating and wire composition are used to produce desired compositions in deposited weld metal. References 1. Metal Statistics: 1988, American Metal Market, Fairchild Publications, 1988 2. 1988 Annual Statistical Report, American Iron and Steel Institute, 1989 Wrought Stainless Steels Revised by S.D. Washko and G. Aggen, Allegheny Ludlum Steel, Division of Allegheny Ludlum Corporation Classification of Stainless Steels Stainless steels are commonly divided into five groups: martensitic stainless steels, ferritic stainless steels, austenitic stainless steels, duplex (ferritic-austenitic) stainless steels, and precipitation-hardening stainless steels. Martensitic stainless steels are essentially alloys of chromium and carbon that possess a distorted body-centered cubic (bcc) crystal structure (martensitic) in the hardened condition. They are ferromagnetic, hardenable by heat treatments, and are generally resistant to corrosion only to relatively mild environments. Chromium content is generally in the range of 10.5 to 18%, and carbon content may exceed 1.2%. The chromium and carbon contents are balanced to ensure a martensitic structure after hardening. Excess carbides may be present to increase wear resistance or to maintain cutting edges, as in the case of knife blades. Elements such as niobium, silicon, tungsten, and vanadium may be added to modify the tempering response after hardening. Small amounts of nickel may be added to improve corrosion resistance in some media and to improve toughness. Sulfur or selenium is added to some grades to improve machinability. Ferritic stainless steels are essentially chromium containing alloys with bcc crystal structures. Chromium content is usually in the range of 10.5 to 30%. Some grades may contain molybdenum, silicon, aluminum, titanium, and niobium to confer particular characteristics. Sulfur or selenium may be added, as in the case of the austenitic grades, to improve machinability. The ferritic alloys are ferromagnetic. They can have good ductility and formability, but high-temperature strengths are relatively poor compared to the austenitic grades. Toughness may be somewhat limited at low temperatures and in heavy sections. Austenitic stainless steels have a face-centered cubic (fcc) structure. This structure is attained through the liberal use of austenitizing elements such as nickel, manganese, and nitrogen. These steels are essentially nonmagnetic in the annealed condition and can be hardened only by cold working. They usually possess excellent cryogenic properties and good high-temperature strength. Chromium content generally varies from 16 to 26%; nickel, up to about 35%; and manganese, up to 15%. The 2xx series steels contain nitrogen, 4 to 15.5% Mn, and up to 7% Ni. The 3xx types contain larger amounts of nickel and up to 2% Mn. Molybdenum, copper, silicon, aluminum, titanium, and niobium may be added to confer certain characteristics such as halide pitting resistance or oxidation resistance. Sulfur or selenium may be added to certain grades to improve machinability. Duplex stainless steels have a mixed structure of bcc ferrite and fcc austenite. The exact amount of each phase is a function of composition and heat treatment (see the article "Cast Stainless Steels" in this Volume). Most alloys are designed to contain about equal amounts of each phase in the annealed condition. The principal alloying elements are chromium and nickel, but nitrogen, molybdenum, copper, silicon, and tungsten may be added to control structural balance and to impart certain corrosion-resistance characteristics. The corrosion resistance of duplex stainless steels is like that of austenitic stainless steels with similar alloying contents. However, duplex stainless steels possess higher tensile and yield strengths and improved resistance to stress-corrosion cracking than their austenitic counterparts. The toughness of duplex stainless steels is between that of austenitic and ferritic stainless steels. Precipitation-hardening stainless steels are chromium-nickel alloys containing precipitation-hardening elements such as copper, aluminum, or titanium. Precipitation-hardening stainless steels may be either austenitic or martensitic in the annealed condition. Those that are austenitic in the annealed condition are frequently transformable to martensite through conditioning heat treatments, sometimes with a subzero treatment. In most cases, these stainless steels attain high strength by precipitation hardening of the martensitic structure. Standard Types. A list of standard types of stainless steels, similar to those originally published by the American Iron and Steel Institute (AISI), appears in Table 2. The criteria used to decide which types of stainless steel are standard types have been rather loosely defined but include tonnage produced during a specific period, availability (number of producers), and compositional limits. Specification-writing organizations such as ASTM and SAE include these standard types in their specifications. In referring to specific compositions, the term type is preferred over the term grade. Some specifications establish a series of grades within a given type, which makes it possible to specify properties more precisely for a given nominal composition. Table 2 Compositions of standard stainless steels Composition, % (a) Type UNS designation C Mn Si Cr Ni P S Other Austenitic Types 201 S20100 0.15 5.5-7.5 1.00 16.0- 18.0 3.5-5.5 0.06 0.03 0.25 N 202 S20200 0.15 7.5- 10.0 1.00 17.0- 19.0 4.0-6.0 0.06 0.03 0.25 N 205 S20500 0.12-14.0-1.00 16.5-1.0-0.06 0.03 0.32-0.40 N 0.25 15.5 18.0 1.75 301 S30100 0.15 2.00 1.00 16.0- 18.0 6.0-8.0 0.045 0.03 . . . 302 S30200 0.15 2.00 1.00 17.0- 19.0 8.0- 10.0 0.045 0.03 . . . 302B S30215 0.15 2.00 2.0- 3.0 17.0- 19.0 8.0- 10.0 0.045 0.03 . . . 303 S30300 0.15 2.00 1.00 17.0- 19.0 8.0- 10.0 0.20 0.15 min 0.6 Mo (b) 303Se S30323 0.15 2.00 1.00 17.0- 19.0 8.0- 10.0 0.20 0.06 0.15 min Se 304 S30400 0.08 2.00 1.00 18.0- 20.0 8.0- 10.5 0.045 0.03 . . . 304H S30409 0.04- 0.10 2.00 1.00 18.0- 20.0 8.0- 10.5 0.045 0.03 . . . 304L S30403 0.03 2.00 1.00 18.0- 20.0 8.0- 12.0 0.045 0.03 . . . 304LN S30453 0.03 2.00 1.00 18.0- 20.0 8.0- 12.0 0.045 0.03 0.10-0.16 N 302Cu S30430 0.08 2.00 1.00 17.0- 19.0 8.0- 10.0 0.045 0.03 3.0-4.0 Cu 304N S30451 0.08 2.00 1.00 18.0- 20.0 8.0- 10.5 0.045 0.03 0.10-0.16 N 305 S30500 0.12 2.00 1.00 17.0- 19.0 10.5- 13.0 0.045 0.03 . . . 308 S30800 0.08 2.00 1.00 19.0- 21.0 10.0- 12.0 0.045 0.03 . . . 309 S30900 0.20 2.00 1.00 22.0- 24.0 12.0- 15.0 0.045 0.03 . . . 309S S30908 0.08 2.00 1.00 22.0- 24.0 12.0- 15.0 0.045 0.03 . . . 310 S31000 0.25 2.00 1.50 24.0- 26.0 19.0- 22.0 0.045 0.03 . . . 310S S31008 0.08 2.00 1.50 24.0- 26.0 19.0- 22.0 0.045 0.03 . . . 314 S31400 0.25 2.00 1.5- 3.0 23.0- 26.0 19.0- 22.0 0.045 0.03 . . . 316 S31600 0.08 2.00 1.00 16.0- 18.0 10.0- 14.0 0.045 0.03 2.0-3.0 Mo 316F S31620 0.08 2.00 1.00 16.0- 18.0 10.0- 14.0 0.20 0.10 min 1.75-2.5 Mo 316H S31609 0.04- 0.10 2.00 1.00 16.0- 18.0 10.0- 14.0 0.045 0.03 2.0-3.0 Mo 316L S31603 0.03 2.00 1.00 16.0- 18.0 10.0- 14.0 0.045 0.03 2.0-3.0 Mo 316LN S31653 0.03 2.00 1.00 16.0- 18.0 10.0- 14.0 0.045 0.03 2.0-3.0 Mo; 0.10-0.16 N 316N S31651 0.08 2.00 1.00 16.0- 18.0 10.0- 14.0 0.045 0.03 2.0-3.0 Mo; 0.10-0.16 N 317 S31700 0.08 2.00 1.00 18.0- 20.0 11.0- 15.0 0.045 0.03 3.0-4.0 Mo 317L S31703 0.03 2.00 1.00 18.0- 20.0 11.0- 15.0 0.045 0.03 3.0-4.0 Mo 321 S32100 0.08 2.00 1.00 17.0- 19.0 9.0- 12.0 0.045 0.03 5 × %C min Ti 321H S32109 0.04- 0.10 2.00 1.00 17.0- 19.0 9.0- 12.0 0.045 0.03 5 × %C min Ti 330 N08330 0.08 2.00 0.75- 1.5 17.0- 20.0 34.0- 37.0 0.04 0.03 . . . 347 S34700 0.08 2.00 1.00 17.0- 19.0 9.0- 13.0 0.045 0.03 10 × %C min Nb 347H S34709 0.04- 0.10 2.00 1.00 17.0- 19.0 9.0- 13.0 0.045 0.03 8 × %C min - 1.0 max Nb 348 S34800 0.08 2.00 1.00 17.0- 19.0 9.0- 13.0 0.045 0.03 0.2 Co; 10 × %C min Nb; 0.10 Ta 348H S34809 0.04- 0.10 2.00 1.00 17.0- 19.0 9.0- 13.0 0.045 0.03 0.2 Co; 8 × %C min - 1.0 max Nb; 0.10 Ta 384 S38400 0.08 2.00 1.00 15.0- 17.0 17.0- 19.0 0.045 0.03 . . . Ferritic types 405 S40500 0.08 1.00 1.00 11.5- 14.5 . . . 0.04 0.03 0.10-0.30 Al 409 S40900 0.08 1.00 1.00 10.5- 11.75 0.50 0.045 0.045 6 × %C min - 0.75 max Ti 429 S42900 0.12 1.00 1.00 14.0- 16.0 . . . 0.04 0.03 . . . 430 S43000 0.12 1.00 1.00 16.0- 18.0 . . . 0.04 0.03 . . . 430F S43020 0.12 1.25 1.00 16.0- 18.0 . . . 0.06 0.15 min 0.6 Mo (b) 430FSe S43023 0.12 1.25 1.00 16.0- 18.0 . . . 0.06 0.06 0.15 min Se 434 S43400 0.12 1.00 1.00 16.0- 18.0 . . . 0.04 0.03 0.75-1.25 Mo 436 S43600 0.12 1.00 1.00 16.0- 18.0 . . . 0.04 0.03 0.75-1.25 Mo; 5 × %C min - 0.70 max Nb 439 S43035 0.07 1.00 1.00 17.0- 19.0 0.50 0.04 0.03 0.15 Al; 12 × %C min - 1.10 Ti 442 S44200 0.20 1.00 1.00 18.0- 23.0 . . . 0.04 0.03 . . . 444 S44400 0.025 1.00 1.00 17.5- 19.5 1.00 0.04 0.03 1.75-2.50 Mo; 0.025 N; 0.2 + 4 (%C + %N) min - 0.8 max (Ti + Nb) 446 S44600 0.20 1.50 1.00 23.0- 27.0 . . . 0.04 0.03 0.25 N [...]... >0.2 3-0 .25 >0.00 9-0 .010 220 6-2 413 32 0-3 50 >0.2 5-0 .28 >0 .010 -0 . 011 219 2-2 399 31 8-3 48 >0.2 8-0 .30 >0 . 011 -0 .012 217 9-2 385 31 6-3 46 >0.3 0-0 .33 >0 .012 -0 .013 216 5-2 372 31 4-3 44 >0.3 3-0 .36 >0 .013 -0 .014 215 1-2 358 31 2-3 42 >0.3 6-0 .38 >0 .014 -0 .015 213 7-2 344 31 0-3 40 >0.3 8-0 .41 >0 .015 -0 .016 212 4-2 330 30 8-3 38 >0.4 1-0 .43 >0 .016 -0 .017 211 0-2 317 30 6-3 36 >0.4 3-0 .46 >0 .017 -0 .018 209 6-2 303 30 4-3 34 >0.4 6-0 .51 >0 .018 -0 .020... 120 7-1 413 17 5-2 05 >6.3 5-7 .06 >0.25 0-0 .278 115 8-1 365 16 8-1 98 >7.0 6-7 .77 >0.27 8-0 .306 111 0-1 324 16 1-1 92 >7.7 7-8 .41 >0.30 6-0 .331 106 9-1 282 15 5-1 86 >8.4 1-9 .20 >0.33 1-0 .362 102 0-1 241 14 8-1 80 >9.2 0-1 0 .01 >0.36 2-0 .394 97 9-1 193 14 2-1 73 >10 .0 1- 11. 12 >0.39 4-0 .438 93 1-1 138 13 5-1 65 >11. 1 2-1 2.70 >0.43 8-0 .500 86 2-1 069 12 5-1 55 Types 305 and 316 ≤ 0.25 ≤ 0 .010 168 9-1 896 24 5-2 75 >0.2 5-0 .38 >0 .010 -0 .015 165 5-1 862 24 0-2 70... >2.6 7-2 .92 >0.10 5-0 .115 156 5-1 772 22 7-2 57 >2.9 2-3 .18 >0 .11 5-0 .125 153 1-1 744 22 2-2 53 >3.1 8-3 .43 >0.12 5-0 .135 149 6-1 710 21 7-2 48 >3.4 3-3 .76 >0.13 5-0 .148 144 8-1 662 21 0-2 41 >3.7 6-4 .12 >0.14 8-0 .162 141 3-1 620 20 5-2 35 >4.1 2-4 .50 >0.16 2-0 .177 136 5-1 572 19 8-2 28 >4.5 0-4 .88 >0.17 7-0 .192 133 8-1 551 19 4-2 25 >4.8 8-5 .26 >0.19 2-0 .207 129 6-1 517 18 8-2 20 >5.2 6-5 .72 >0.20 7-0 .225 125 5-1 475 18 2-2 14 >5.7 2-6 .35 >0.22 5-0 .250... 206 8-2 275 30 0-3 30 >0.5 1-0 .56 >0.02 0-0 .022 204 1-2 248 29 6-3 26 >0.5 6-0 .61 >0.02 2-0 .024 2013 -2 220 29 2-3 22 >0.6 1-0 .66 >0.02 4-0 .026 200 6-2 206 29 1-3 20 >0.6 6-0 .71 >0.02 6-0 .028 199 3-2 192 28 9-3 18 >0.7 1-0 .79 >0.02 8-0 .031 196 5-2 172 28 5-3 15 >0.7 9-0 .86 >0.03 1-0 .034 194 4-2 137 28 2-3 10 >0.8 6-0 .94 >0.03 4-0 .037 193 0-2 124 28 0-3 08 >0.9 4-1 .04 >0.03 7-0 .041 189 6-2 096 27 5-3 04 >1.0 4-1 .14 >0.04 1-0 .045 187 5-2 068 27 2-3 00 >1.1 4-1 .27... >0.04 5-0 .050 184 1-2 034 26 7-2 95 >1.2 7-1 .37 >0.05 0-0 .054 182 7-2 020 26 5-2 93 >1.3 7-1 .47 >0.05 4-0 .058 180 0-1 993 26 1-2 89 >1.4 7-1 .60 >0.05 8-0 .063 177 9-1 965 25 8-2 85 >1.6 0-1 .78 >0.06 3-0 .070 173 7-1 937 25 2-2 81 >1.7 8-1 .90 >0.07 0-0 .075 172 4-1 917 25 0-2 78 >1.9 0-2 .03 >0.07 5-0 .080 169 6-1 896 24 6-2 75 >2.0 3-2 .21 >0.08 0-0 .087 166 8-1 868 24 2-2 71 >2.2 1-2 .41 >0.08 7-0 .095 164 1-1 848 23 8-2 68 >2.4 1-2 .67 >0.09 5-0 .105 160 0-1 806 23 2-2 62... >0.3 8-1 .04 >0 .015 -0 .041 162 0-1 827 23 5-2 65 >1.0 4-1 .19 >0.04 1-0 .047 158 6-1 723 23 0-2 60 >1.1 9-1 .37 >0.04 7-0 .054 155 1-1 758 22 5-2 55 >1.3 7-1 .58 >0.05 4-0 .062 151 7-1 724 22 0-2 50 >1.5 8-1 .85 >0.06 2-0 .072 148 2-1 689 21 5-2 45 >1.8 5-2 .03 >0.07 2-0 .080 144 8-1 655 21 0-2 40 >2.0 3-2 .34 >0.08 0-0 .092 141 3-1 620 20 5-2 35 >2.3 4-2 .67 >0.09 2-0 .105 137 9-1 586 20 0-2 30 >2.6 7-3 .05 >0.10 5-0 .120 134 4-1 551 19 5-2 25 >3.0 5-3 .76 >0.12 0-0 .148... >0.10 5-0 .120 134 4-1 551 19 5-2 25 >3.0 5-3 .76 >0.12 0-0 .148 127 6-1 482 18 5-2 15 >3.7 6-4 .22 >0.14 8-0 .166 124 1-1 448 18 0-2 10 >4.2 2-4 .50 >0.16 6-0 .177 117 2-1 379 17 0-2 00 >4.5 0-5 .26 >0.17 7-0 .207 110 3-1 310 16 0-1 90 >5.2 6-5 .72 >0.20 7-0 .225 106 9-1 276 15 5-1 85 >5.7 2-6 .35 >0.22 5-0 .250 103 4-1 241 15 0-1 80 >6.3 5-7 .92 >0.25 0-0 .312 93 1-1 138 13 5-1 65 >7.9 2-1 2.68 >0.31 2-0 .499 79 3-1 000 11 5-1 45 ... 0.00 3-0 .009 B; 0.7 5-1 .25 Nb; 0.1 5-0 .40 V Type 216 (XM-17) S21600 0.08 7. 5-9 .0 1.00 17.522.0 5. 0-7 .0 0.045 0.030 2. 0-3 .0 Mo; 0.2 5-0 .50 N Type 216 L (XM18) S21603 0.03 7. 5-9 .0 1.00 17.522.0 7. 5-9 .0 0.045 0.030 2. 0-3 .0 Mo; 0.2 5-0 .50 N Nitronic 60 S21800 0.10 7. 0-9 .0 3.54.5 16 .018 .0 8. 0-9 .0 0.040 0.030 0.0 8-0 .18 N Nitronic 40 (XM10) S21900 0.08 8. 0-1 0.0 1.00 19.021.5 5. 5-7 .5 0.060 0.030 0.1 5-0 .40 N 2 1-6 -9 ... 0.04 0.03 0.75 Mo 0.20 0.10 12.2 5- 7. 5-8 .5 0 .01 0.008 2. 0-2 .5 Mo; 0.9 0-1 .35 Al; 0 .01 N Precipitation-hardening types PH 1 3-8 S13800 0.05 Mo 13.25 1 5-5 PH S15500 0.07 1.00 1.00 14 .015 .5 3. 5-5 .5 0.04 0.03 2. 5-4 .5 Cu; 0.1 5-0 .45 Nb 1 7-4 PH S17400 0.07 1.00 1.00 15.517.5 3. 0-5 .0 0.04 0.03 3. 0-5 .0 Cu; 0.1 5-0 .45 Nb 1 7-7 PH S17700 0.09 1.00 1.00 16 .018 .0 6.57.75 0.04 0.04 0.7 5-1 .5 Al (a) Single values are maximum... 0.04 8. 0010 .00 1.00 19.0021.50 5.507.50 0.060 0.030 0.1 5-0 .40 N Nitronic 33 (1 8-3 Mn) S24000 0.08 11. 5014 .50 1.00 17. 0019 .00 2.503.75 0.060 0.030 0.2 0-0 .40 N Nitronic 32 (1 8-2 Mn) S24100 0.15 11. 0014 .00 1.00 16. 5019 .50 0.502.50 0.060 0.030 0.2 0-0 .45 N 1 8-1 8 Plus S28200 0.15 17 .019 .0 1.00 17.519.5 0.045 0.030 0. 5-1 .5 Mo; 0. 5-1 .5 Cu; 0.40.6 N 303 Plus X (XM5) S30310 0.15 2. 5-4 .5 1.00 17 .019 .0 7. 0-1 0.0 0.020 . Gall-Tough S 2016 1 0.15 4.0 0- 6.00 3.0 0- 4.00 15.0 0- 18.00 4.0 0- 6.00 0.040 0.040 0.0 8-0 .20 N 203 EZ (XM-1) S20300 0.08 5. 0-6 .5 1.00 16. 0- 18.0 5. 0-6 .5 0.040 0.1 8- 0.35 0.5 Mo; 1.7 5-2 .25. Nitronic 50 (XM- 19) S20910 0.06 4. 0-6 .0 1.00 20. 5- 23.5 11. 5- 13.5 0.040 0.030 1. 5-3 .0 M; 0. 2-0 .4 N; 0. 1-0 .3 Nb; 0. 1-0 .3 V Tenelon (XM-31) S21400 0.12 14. 5- 16.0 0. 3- 1.0 17. 0- 18.5 0.75. 0.030 0.1 5-0 .40 N 2 1-6 -9 LC S21904 0.04 8.0 0- 10.00 1.00 19.0 0- 21.50 5.5 0- 7.50 0.060 0.030 0.1 5-0 .40 N Nitronic 33 (1 8-3 - Mn) S24000 0.08 11. 5 0- 14.50 1.00 17.0 0- 19.00 2.5 0- 3.75