US3284250A - Austenitic stainless steel and process therefor - Google Patents

Austenitic stainless steel and process therefor Download PDF

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Publication number
US3284250A
US3284250A US336808A US33680864A US3284250A US 3284250 A US3284250 A US 3284250A US 336808 A US336808 A US 336808A US 33680864 A US33680864 A US 33680864A US 3284250 A US3284250 A US 3284250A
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steels
austenitic stainless
columbium
steel
carbon
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US336808A
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Ralph B G Yeo
Tom E Scott
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Huntington Alloys Corp
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International Nickel Co Inc
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Priority to US336808A priority Critical patent/US3284250A/en
Priority to GB289/65A priority patent/GB1061511A/en
Priority to SE95/65A priority patent/SE307371B/xx
Priority to FR1343A priority patent/FR1420834A/fr
Priority to BE658149A priority patent/BE658149A/fr
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum

Definitions

  • the present invention relates to austenitic stainless steels and, more particularly, to austenitic stainless steels of special composition and of the A151 300 series type which in the annealed condition are characterized by a combination of properties markedly superior to those characteristic of known austenitic stainless steels.
  • the austenitic grades have by far found the greatest commercial use as is evident from the fact that present commercial produc tion of the austenitic grades is more than double the combined production of the martensitic and ferritic grades. This is not, in retrospect, surprising in view of the combinations of properties characteristic of the austenitic stainless steels, including their high degree of resistance to corrosive environments, their excellent tensile strength levels at both normal and high temperatures, their established ability to be fabricated with relative case on a commercial scale, etc. These factors, among others, have led to their wide acceptance and diversified utility and application.
  • the 1936 edition indicates at page 379 that the yield strength of the 18-8 type of stainless steel (18% chromium, 8% nickel) was about 35,000 pounds per square inch (p.s.i.) in the annealed condition and exhibited an elongation value of about 55% to 60% (2 inch gage length).
  • the 1961 edit-ion, page 414 reflects that a comparable 18-8 type, i.e., A181 302 or 304, has approximately the same yield strength and ductility (elongation) levels in the annealed condition. This is not to say that very high yield strengths cannot be obtained with austenitic stainless. In the cold-worked condition, yield strengths above 200,000 psi. have been obtained, but, as is well known, cold-worked austenitic stainless is rather the antithesis of austenitic stainless in the annealed condition.
  • austenitic stainless steels of the A181 300 series type but containing special amounts of columbium in conjunction with correlated amounts of other essential constituents are capable of exhibiting yield strengths of 50,000 psi. to 60,000 psi. in the annealed condition provided the common process annealing treatment is eliminated. Such yield strength levels obtain without a concomitant deleterious impairment of other properties.
  • a certain ratio of columbium to carbon had to be observed and the ratio that has been generally adopted is that the amount of columbium must be at least ten times the carbon content as is reflected by the standard columbium stabilized grade of stainless steel, i.e., A181 347.
  • the other carbide stabilizers act in a similar manner.
  • intergranular corrosion is also greatly minimized by maintaining the carbon level below 0.03%, thus rendering the use of columbium or other stabilizers unnecessary.
  • Another object of the invention is to provide a process for achieving a combined high level of yield strength and ductility in austcnitic stainless steels in the annealed condition.
  • FIGURES 1 to 5 are reproductions of photomicrographs showing the structure of various austenitic stainless steels after being subjected to different heat treatments.
  • an optimum combination of properties including yield strengths of atv least about 50,000 psi. (0.2% offset) together with ductilities of at least 50% (using standard ASTM specimens) are obtained in the annealed condition with austenitic stainless steels having com-positions (based on weight percentage) within the following most advantageous ranges: at least 0.05%, 'e.g., 0.06%, and up to about 0.08% carbon, about 17.5% to about 19.5% chromium, about 8% to about 12% nickel, about 0.18% to about 0.28% columbium, up to about 2% manganese, up to about 1% silicon, up to about 0.1% aluminum, up to 0.5% nitrogen and the balance essentially iron.
  • the steels contemplated herein have a unique fine-grained structure, i.e., an ASTM grain size of 11 to 14 or finer, and are substantially free of coarse carbide precipitates. This characteristic of an extremely fine grain structure is discussed more fully hereinafter.
  • the aforediscussed process annealing treatment i.e., the anneal between the hot working and cold working operations at temperatures above about 1900 F.
  • the constituents of the alloy composition must be balanced and correlated such that at the working temperature employed in processing, i.e., 2300 F. down to above 1900 F., the presence of detrimental delta ferrite is avoided.
  • delta ferrite will be retained in the final product and while it increases yield strength, it substantially adversely affects ductility and formability properties particularly when such properties are measured in the transverse direction.
  • the presence of delta ferrite should be avoided although Improved yield strength levels in the annealed condition can also be attained with austenitic stainless steels within the following compositional ranges -and without detrimentally affecting other properties: carbon in an amount more than 0.03%, e.g., more than 0.04%, and up to 0.12%, at least 16% and up to 20% chromium, about 6% to about 12% nickel, 0.15% to not more than 0.5 columbium, up to 2% manganese, up to 2% silicon, up to 0.5 aluminum, up to 0.5% nitrogen and the balance essentially iron.
  • the alloying constituents must be properly cor- (related to provide for an austenitic structure.
  • the steel In carrying the invention into practice, it is preferred to soak the steel at a high temperature, such as 2250 F. to 2350" F., e.g., 2300 F., before hot rolling and to then apply and continue the hot-rolling treatment within the temperature range of 2300 F. down to above 1900 F. Temperatures as low as 1650 F. are commonly employed but it is most advantageous to hot work from a temperature of about 2300 F. down to 2000 F. After this treatment, the steel has a hardness as low as annealed material and is suitable for subsequent cold rolling. If the finishing temperature of the hot-working operation falls significantly below about 2000 F., e.g., below about 1950 F., a high temperature process annealing treatment may otherwise be required at, say, 2300" F. But since it is desirable to eliminate the process anneal, it is beneficial to maintain a minimum hotworking temperature of about 2000 F.
  • a high temperature such as 2250 F. to 2350" F.
  • the steels are subjected to a cold reduction operation for control of gage and surface finish and to assure the occurrence of recrystallization during the final anneal treatment (the only annealing treatment required in accordance with the invention).
  • the steel should be advantageously cold reduced at least 15% and up to about 70%. Cold reductions of less than about 15%, e.g., 5%, tend to cause excessive grain growth while reductions of over 70% result in a steel which is too hard to further work without difficulty on a commercial basis. Cold reductions of 40% to 60% are most advantageous with 50% being highly satisfactory.
  • intermediate annealing may be employed provided that the temperature range of 1900 F. to 2200 F. is avoided. If the cold-working operation or equivalent is omitted, it makes little difference at what temperature the final anneal is conducted since yield strengths of at least 50,000 p.s.i. will not be obtained.
  • the heat treatment employed (after cold working) to achieve the annealed condition is important.
  • the most advantageous temperature range is 1750 F. to 1850 F. and the steel should be held within this range for about 3 hours to 0.4 hour, e.g., 1 hour at 1800 F.
  • the annealing temperature can be as high as 2000 F.
  • the holding time should be not greater than 5 minutes and preferably not greater than 3 minutes, otherwise, adverse results can occur.
  • the unusually high yields strengths result, inter alia, partially from the very fine grain size, i.e., ASTM 11 to 14 or finer, and partially from dislocation tangles.
  • High annealing temperatures i.e., 2000 F.
  • the minimum annealing temperature must be above 1600 F., e.g., 1700 F. and above, to assure the occurrence of recrystallization.
  • the steels should be annealed for about 3 hours.
  • the annealing treatment should be in accordance with the following formula:
  • compositions for AISI Alloys Nos. 3 through 7 of Table II illustrate that yield 304 and 347 as set forth at page 409 of the Metals strengths of Well over 50,000 p.s.i., e.g., 55,000 p.s.i.,
  • the steels 1 through 11 and A through B were prepared and over 70% reduction in area) can be obtained in in an air induction furnace, the ingredients being melted austenitic stainless steels in the annealed condition. Such in magnesia crucibles. Silicon-manganese was used for strength levels represent an increase of about 50% or deoxidation purposes with aluminum additions of less more as can be seen from a comparison of Alloys AISI than about 0.1% being made. Final deoxidizing addi- 304 and 347 with Alloys Nos. 3 through 7. It will be tions were made following slag removal and normal further noted that Alloys A through E (which were temperature adjustment.
  • the steels were produced in given a process anneal) manifested significantly lower ingot form and hot rolled at temperatures of 2000 F. r yield strengths than Alloys Nos. 3 through 7. Further, or 2300 F. after a liberal soak.
  • the hot-rolled product the steels containing less than 0.03% carbon (Alloys Nos. was in the form of A-inch round bars. Alloys Nos. 1 8, 10 and 11) all manifested yield strengths much below through 11 were subjected to a treatment whi h com- 50,000 p.s.i. and such data illustrate that the steels should ri ed old redu in the b about 45 d annealing contain carbon contents in excess of 0.03%.
  • Alloys Nos. 1 and A indicate that in the absence of No initial or process anneal was employed. Alloys A columbium it is immaterial whether the steels are or are through E were treated in the same manner except a not given a Process anneal treatmentprocess neal of 1 ho t 2000 F, was employed prior A striking feature is the effect of columbium in acto cold working. It should be noted that Alloys Nos.
  • FIG. 1 250 magnification
  • FIG. 2 100 magnification
  • FIG. 2 100 magnification
  • FIG. 2 depicts the grain size of each of the steels after a process anneal at 2300 F. for 2 hours following the hot-rolling operation. It will be noted that the process anneal completely eliminated all observable difierence among the three steels.
  • FIGURES 3 and 4 represent the microstructure obtained after a final anneal, i.e., the alloys were hot rolled, process annealed at 2300 F. for 2 hours, cold rolled (a reduction in area of about 45%) and given a final anneal at 1800 F. (FIG. 3) and 2000 F. (FIG. 4) for 1 hour.
  • FIGURE 5 (250 magnification) depicts the extremely fine grain structure (finer than ASTM size 14) obtained for Alloys Nos. 4 and 6 (alloys within the invention) in the absence of the process annealing treatment.
  • the steels (FIG- URE 5) were hot rolled, cold rolled (45% reduction in area) and annealed at 1800 F.
  • austenitic stainless steels within the invention are uniquely characterized by a very fine grain structure, i.e., an ASTM grain size of 11 or finer, e.g., ASTM grain size 14 or finer, in the absence of a process anneal.
  • ASTM grain size 11 or finer
  • ASTM grain size 14 or finer e.g., ASTM grain size 14 or finer
  • the austenitic stainless steels in accordance with the invention are characterized by extremely fine grain sizes, i.e., ASTM grain sizes of at least 11, e.g., 12 to 14. This fine grain size affords many other advantages, such as improved deepdrawing characteristics and machinability. It should be mentioned that grain size as referred to herein, was determined with the Standard ASTM Grain Size Chart at a magnification of 500x. This is higher than the 100 magnification normally used because of the extreme fineness of the grains of the steels within the invention. Correction for higher magnification was made by using the ASTM correction formula,
  • the austenitic stainless steels of the invention can, of course, be used in all applications for which such steels are presently used. However, by virtue of the increased yield strength coupled with good ductility, etc., characteristic of the steels, an expanded field of use is opened particularly where higher strength-to-weight ratios are necessary or advantageous, e.g., transportation tanks carrying various media, including corrosives.
  • balance or balance essentially as used herein in referring to the iron content of the steels does not exclude the presence of other elements commonly present as incidental elements, eg., deoxidizing and cleansing elements, and impurities ordinarily associated therewith in amounts which do not adversely affect the basic characteristics of the steels.
  • incidental elements eg., deoxidizing and cleansing elements
  • impurities ordinarily associated therewith in amounts which do not adversely affect the basic characteristics of the steels.
  • up to 3% molybdenum can be present in the steels.
  • austenitic as used herein means that the structure of the alloys at room temperature is substantially or completely of an austenite matrix although up to not more than 10%, and most advantageously not more than 5%, of other phases, e.g., ferrite, can be present.
  • the present invention is applicable to the austenitic stainless steels of the AISI 201 and 202 types, i.e., the nickel content can be as low as 3% and the manganese content can be as high as 10%, the remainder of the composition being within the limits set forth before herein.
  • the nickel and manganese contents in combination with the other elements would have to be correlated to insure an austenitic structure. In such instances the yield strength of the AISI 201 and 202 types is increased to above 70,000 p.s.i., e.g., 75,000
  • a process for improving the yield strengths of and achieving finer grain sizes in austenitic stainless steels consisting of about 0.06% to about 0.08% carbon, about 8% to about 12% nickel, about 17.5% to about 19.5% chromium, about 0.18% to about 0.28% columbium, up to 1% silicon, up to 2% manganese, up to 0.1% aluminum, up to 0.3% nitrogen and the balance essentially iron which comprises hot working the steels within the temperature range of about 2300 F. to about 2000 F., cold working the steel without a prior process annealing treatment -to obtain a reduction in area of 40% to 60% and thereafter recrystallizing the steel by subjecting it to an annealing treatment within the temperature range of about 1750" F. to about 1850 F. in accordance with the following formula:
  • T represents temperature in degrees Fahrenheit and t is time in hours.
  • a process for improving the yield strengths of and achieving finer grain sizes in austenitic stainless steels consisting of carbon in an amount above 0.03% and up to about 0.12%, about 6% to about 12% nickel, about 16% to about 20% chromium, about 0.15% to less than about 0.3% columbium, up to 2% silicon, up to 2% maganese, up to 0.5% aluminum, up to 0.5 nitrogen and the balance essentially iron which comprises hot working the steels within the temperature range of about 2000 F. and up to 2300 F., cold working the steel without a prior P SS annealing treatment to obtain a reduction in area of at least 15% and thereafter substantially recrystallizing the steel by subjecting it to an annealing treatment within the temperature range of about 1725 F. to 1950 F. for a period of about 4 hours to about 0.4 hour, the period of the shortest holding time being employed at the highest temperature.
  • a process for improving the yield strengths of and achieving finer grain sizes in austentic stainless steels consisting of about 0.05 to about 0.12% carbon, about 6% to about 12% nickel, about 16% to about 20% chromium, 0.15% to not more than 0.5% columbium, up to 2% silicon, up to 2% manganese, up to 0.5 aluminum, up to 0.5% nitrogen and the balance essentially iron which comprises hot working the steel within the temperature range of above 1900 F. and up to 2300 F., cold Working the steel without a prior process annealing treatment to obtain a reduction in area of at least 15 and thereafter substantially recrystallizing the steel by subjecting it to an annealing treatment within the temperature range of above about 1700 F. and up to not more than about 2000" F.
  • An austenitic stainless steel in the annealed condition consisting of at least 0.05% and up to 0.12% carbon, about 3% to about 12% nickel, about 16% to about 20% chromium, about 0.16% to not more than 0.3% columbium, up to 1% silicon, up to manganese, up to 0.1% aluminum, up to 0.3% nitrogen, up to 3% molybdenum and the balance essentially iron, said steel being characterized by a yield strength of at least 50,000 p.s.i., an elongation of at least and a grain size of at least about ASTM No. 12 when hot worked at a temperature of about 2000 F. to about 2300 F. followed by cold working to obtain a reduction in area of at least 15% and then substantially recrystallized by subjecting it to an annealing treatment within the temperature range of over about 1700 F. to not more than 2000" F.
  • An austenitic stainless steel consisting essentially of carbon in an amount above 0.03% and up to 0.12%, about 3% to about 12% nickel, about 16% to about 20% chromium, about 0.15% to about 0.3% columbium, up to 2% silicon, up to 10% manganese, up to 0.5% aluminum, up to 0.5% nitrogen, up to 3% molybdenum, and the balance essentially iron, said steel having a yield strength of at least 50,000 p.s.i., an elongation of at least 50% and a grain size fineness of at least about ASTM No. 12.

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US336808A 1964-01-09 1964-01-09 Austenitic stainless steel and process therefor Expired - Lifetime US3284250A (en)

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US336808A US3284250A (en) 1964-01-09 1964-01-09 Austenitic stainless steel and process therefor
GB289/65A GB1061511A (en) 1964-01-09 1965-01-04 Improved austenitic stainless steel and process therefor
SE95/65A SE307371B (enrdf_load_stackoverflow) 1964-01-09 1965-01-07
FR1343A FR1420834A (fr) 1964-01-09 1965-01-08 Acier austénitique inoxydable perfectionné et son procédé de préparation
BE658149A BE658149A (enrdf_load_stackoverflow) 1964-01-09 1965-01-11

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Cited By (23)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3384476A (en) * 1963-11-22 1968-05-21 Sandvikens Jernverks Ab Alloy steel and method of making same
US3645725A (en) * 1969-05-02 1972-02-29 Armco Steel Corp Austenitic steel combining strength and resistance to intergranular corrosion
US3770426A (en) * 1971-09-17 1973-11-06 Republic Steel Corp Cold formable valve steel
USRE28772E (en) * 1968-04-30 1976-04-13 Armco Steel Corporation High strength corrosion-resistant stainless steel
US3957545A (en) * 1970-07-28 1976-05-18 Nippon Kokan Kabushiki Kaisha Austenitic heat resisting steel containing chromium and nickel
US3969161A (en) * 1973-11-07 1976-07-13 Nippon Kokan Kabushiki Kaisha Cr-Ni system austenitic heat-resisting steel
US4008078A (en) * 1974-04-03 1977-02-15 Fried. Krupp Huttenwerke Low-carbon rail steel
US4450008A (en) * 1982-12-14 1984-05-22 Earle M. Jorgensen Co. Stainless steel
US4550487A (en) * 1981-10-21 1985-11-05 Nisshin Steel Company, Ltd. Process for preparing strips or sheets of high strength austenitic steel having improved fatigue strength
US4559090A (en) * 1984-02-24 1985-12-17 Mannesmann Aktiengesellschaft Using a corrosion proof austenitic iron chromium nickel nitrogen alloy for high load components
US4584031A (en) * 1984-02-24 1986-04-22 Mannesmann Aktiengesellschaft Using a corrosion proof austenitic alloy for high load weldable components
US4718908A (en) * 1984-06-04 1988-01-12 Richards Medical Company High-strength, cold-forged type 316L stainless steel for orthopedic implant
US4775426A (en) * 1986-04-03 1988-10-04 Richards Medical Company Method of manufacturing surgical implants from cast stainless steel and product
EP0332460A1 (en) * 1988-03-11 1989-09-13 General Electric Company Austenitic stainless steel alloy
WO1994014993A1 (en) * 1992-12-18 1994-07-07 Electric Power Institute, Inc. Manufacture of materials and workpieces for components in nuclear plant applications
WO1994014992A1 (en) * 1992-12-18 1994-07-07 Electric Power Research Institute, Inc. Manufacture of materials and workpieces having fine grain for components in nuclear plant applications
US20040213665A1 (en) * 2001-05-10 2004-10-28 Shinjiro Ohishi Exhaust gas assembly with improved heat resistance for vgs turbocharger, method for manufacturing heat resisting member applicable thereto, and method for manufacturing shaped material for adjustable blade applicable thereto
FR2864108A1 (fr) * 2003-12-22 2005-06-24 Ugine Et Alz France Tole en acier inoxydable presentant une grande resistance et un bon allongement, et procede de fabrication
US20110061776A1 (en) * 2008-03-21 2011-03-17 Arcelormittal-Stainless France Process for manufacturing sheet of austenitic stainless steel having high mechanical properties and sheet thus obtained
US20150337421A1 (en) * 2007-12-20 2015-11-26 Ati Properties, Inc. Lean austenitic stainless steel
US9624564B2 (en) 2007-12-20 2017-04-18 Ati Properties Llc Corrosion resistant lean austenitic stainless steel
US9873932B2 (en) * 2007-12-20 2018-01-23 Ati Properties Llc Lean austenitic stainless steel containing stabilizing elements
US10370748B2 (en) 2007-11-29 2019-08-06 Ati Properties Llc Lean austenitic stainless steel

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS49113716A (enrdf_load_stackoverflow) * 1973-03-02 1974-10-30
JP2602015B2 (ja) * 1986-08-30 1997-04-23 愛知製鋼株式会社 耐腐食疲労性、耐海水性に優れたステンレス鋼およびその製造方法
US20020110476A1 (en) 2000-12-14 2002-08-15 Maziasz Philip J. Heat and corrosion resistant cast stainless steels with improved high temperature strength and ductility
US11193190B2 (en) 2018-01-25 2021-12-07 Ut-Battelle, Llc Low-cost cast creep-resistant austenitic stainless steels that form alumina for high temperature oxidation resistance

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
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Cited By (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3384476A (en) * 1963-11-22 1968-05-21 Sandvikens Jernverks Ab Alloy steel and method of making same
USRE28772E (en) * 1968-04-30 1976-04-13 Armco Steel Corporation High strength corrosion-resistant stainless steel
US3645725A (en) * 1969-05-02 1972-02-29 Armco Steel Corp Austenitic steel combining strength and resistance to intergranular corrosion
US3957545A (en) * 1970-07-28 1976-05-18 Nippon Kokan Kabushiki Kaisha Austenitic heat resisting steel containing chromium and nickel
US3770426A (en) * 1971-09-17 1973-11-06 Republic Steel Corp Cold formable valve steel
US3969161A (en) * 1973-11-07 1976-07-13 Nippon Kokan Kabushiki Kaisha Cr-Ni system austenitic heat-resisting steel
US4008078A (en) * 1974-04-03 1977-02-15 Fried. Krupp Huttenwerke Low-carbon rail steel
US4550487A (en) * 1981-10-21 1985-11-05 Nisshin Steel Company, Ltd. Process for preparing strips or sheets of high strength austenitic steel having improved fatigue strength
US4450008A (en) * 1982-12-14 1984-05-22 Earle M. Jorgensen Co. Stainless steel
US4559090A (en) * 1984-02-24 1985-12-17 Mannesmann Aktiengesellschaft Using a corrosion proof austenitic iron chromium nickel nitrogen alloy for high load components
US4584031A (en) * 1984-02-24 1986-04-22 Mannesmann Aktiengesellschaft Using a corrosion proof austenitic alloy for high load weldable components
US4718908A (en) * 1984-06-04 1988-01-12 Richards Medical Company High-strength, cold-forged type 316L stainless steel for orthopedic implant
US4775426A (en) * 1986-04-03 1988-10-04 Richards Medical Company Method of manufacturing surgical implants from cast stainless steel and product
EP0332460A1 (en) * 1988-03-11 1989-09-13 General Electric Company Austenitic stainless steel alloy
WO1994014993A1 (en) * 1992-12-18 1994-07-07 Electric Power Institute, Inc. Manufacture of materials and workpieces for components in nuclear plant applications
WO1994014992A1 (en) * 1992-12-18 1994-07-07 Electric Power Research Institute, Inc. Manufacture of materials and workpieces having fine grain for components in nuclear plant applications
US20040213665A1 (en) * 2001-05-10 2004-10-28 Shinjiro Ohishi Exhaust gas assembly with improved heat resistance for vgs turbocharger, method for manufacturing heat resisting member applicable thereto, and method for manufacturing shaped material for adjustable blade applicable thereto
US20090145523A1 (en) * 2001-05-10 2009-06-11 Shinjiro Ohishi Method for manufacturing heat resisting member applicable to an exhaust gas guide assembly with improved heat resistance for VGS turbocharger
FR2864108A1 (fr) * 2003-12-22 2005-06-24 Ugine Et Alz France Tole en acier inoxydable presentant une grande resistance et un bon allongement, et procede de fabrication
US10370748B2 (en) 2007-11-29 2019-08-06 Ati Properties Llc Lean austenitic stainless steel
US9822435B2 (en) * 2007-12-20 2017-11-21 Ati Properties Llc Lean austenitic stainless steel
US9624564B2 (en) 2007-12-20 2017-04-18 Ati Properties Llc Corrosion resistant lean austenitic stainless steel
US20150337421A1 (en) * 2007-12-20 2015-11-26 Ati Properties, Inc. Lean austenitic stainless steel
US9873932B2 (en) * 2007-12-20 2018-01-23 Ati Properties Llc Lean austenitic stainless steel containing stabilizing elements
US10323308B2 (en) 2007-12-20 2019-06-18 Ati Properties Llc Corrosion resistant lean austenitic stainless steel
US20110061776A1 (en) * 2008-03-21 2011-03-17 Arcelormittal-Stainless France Process for manufacturing sheet of austenitic stainless steel having high mechanical properties and sheet thus obtained

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FR1420834A (fr) 1965-12-10
GB1061511A (en) 1967-03-15
SE307371B (enrdf_load_stackoverflow) 1969-01-07
BE658149A (enrdf_load_stackoverflow) 1965-07-12

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