US20030086808A1 - Duplex stainless steel alloy - Google Patents

Duplex stainless steel alloy Download PDF

Info

Publication number
US20030086808A1
US20030086808A1 US10/232,726 US23272602A US2003086808A1 US 20030086808 A1 US20030086808 A1 US 20030086808A1 US 23272602 A US23272602 A US 23272602A US 2003086808 A1 US2003086808 A1 US 2003086808A1
Authority
US
United States
Prior art keywords
weight
content
ferrite
alloy according
alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Abandoned
Application number
US10/232,726
Other languages
English (en)
Inventor
Ann Sundstrom
Pasi Kangas
Anna-Lena Nystrom
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Sandvik Intellectual Property AB
Original Assignee
Individual
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Individual filed Critical Individual
Assigned to SANDVIK AB reassignment SANDVIK AB ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KANGAS, PASI, NYSTROM, ANNA-LENA, SUNDSTROM, ANN
Publication of US20030086808A1 publication Critical patent/US20030086808A1/en
Assigned to SANDVIK INTELLECTUAL PROPERTY HB reassignment SANDVIK INTELLECTUAL PROPERTY HB ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SANDVIK AB
Assigned to SANDVIK INTELLECTUAL PROPERTY AKTIEBOLAG reassignment SANDVIK INTELLECTUAL PROPERTY AKTIEBOLAG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: SANDVIK INTELLECTUAL PROPERTY HB
Abandoned legal-status Critical Current

Links

Images

Classifications

    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to stainless steel alloys, and more particularly a duplex stainless steel alloy with ferritic-austenitic matrix with high resistance to corrosion in combination with good structural stability and hot workability.
  • a duplex stainless steel with a ferrite content of 40-65 volume % and a well balanced composition which imparts corrosion resistant properties which make it more suitable for use in chloride-containing environments than previously considered possible.
  • PRE Pitting Resistance Equivalent
  • the elements Cu and W have shown to be efficient alloying additions for further optimization of the steel's corrosion properties in chloride environments.
  • the element W has by then been used as substitute for a portion of Mo, as for example in the commercial alloy DP3W (UNS S39274) or Zeron100, which contain 2.0% and 0.7% W, respectively.
  • the later contains 0.7% Cu with the purpose to increase the corrosion resistance of the alloy in acid environments.
  • U.S. Pat. No. 4,985,091 describes an alloy intended for use in hydrochloric and sulfuric acid environments, where mainly intergranular corrosion arises. It is primarily intended as alternative to recently used austenitic steels.
  • U.S. Pat. No. 6,048,413 describes a duplex stainless alloy as alternative to austenitic stainless steels, intended for use in chloride-containing environments.
  • CPT Critical Pitting Corrosion Temperature
  • CCT Critical Crevice Corrosion Temperature
  • the material according to the present invention shows remarkably good workability, in particular hot workability, and shall thereby be very suitable to be used for example the production of bars, tubes, such as welded and seamless tubes, plate, strip, wire, welding wire, constructive parts, such as pumps, valves, flanges and couplings.
  • duplex stainless steel alloys which contain (in weight %) up to 0.03% C, up to 0.5% Si, 24.0-30.0% Cr, 4.9-10.0% Ni, 3.0-5.0% Mo, 0.28-0.5% N, 0-3.0% Mn, 0-0.0030% B, up to 0.010% S, 0-0.03% Al, 0-0.010% Ca, 0-3.0% W, 0-2.0% Cu, 0-3.5% Co, 0-0.3% Ru, balance Fe and inevitable impurities.
  • FIG. 1 shows CPT values from tests of the test heats in the modified ASTM G48C test in “Green Death” solution compared with the duplex steels SAF2507, SAF 2906 as well as the high alloyed austenitic steel 654SMO.
  • FIG. 2 shows CPT values attained with the help of the modified ASTM G48C test in “Green Death” solution for the test heats compared with the duplex steel SAF2507 as well as the austenitic steel 654SMO.
  • FIG. 3 shows the average amount of erosion in mm/year in 2% HCl at a temperature of 75° C.
  • FIG. 4 shows the results from hot ductility testing for most of the heats.
  • the alloy according to the invention contains (in weight %): C Max 0.03% Si Max 0.5% Mn 0-3.0% Cr 24.0-30.0% Ni 4.9-10.0% Mo 3.0-5.0% N 0.28-0.5% B 0-0.0030% S max 0.010% Co 0-3.5% W 0-3.0% Cu 0-2.0% Ru 0-0.3% Al 0-0.03% Ca 0-0.010%
  • Carbon (C) has limited solubility in both ferrite and austenite.
  • the limited solubility implies a risk of precipitation of chromium carbides and the content should therefore not exceed 0.03 weight %, preferably not exceed 0.02 weight %.
  • Si is utilized as desoxidation agent in the steel production as well as it increases the flowability during production and welding.
  • too high of a content of Si leads to precipitation of unwanted intermetallic phases, thus the content is limited to max 0.5 weight %, preferably max 0.3 weight %.
  • Mn Manganese
  • Mn is added in order to increase the N solubility in the material.
  • Mn only has a limited influence on the N solubility in the type of alloy in question. Instead there are other elements found to have higher influence on the solubility.
  • Mn in combination with high contents of sulfur can give rise to formation of manganese sulfides, which act as initiation points for pitting corrosion.
  • the content of Mn should therefore be limited to between 0-3.0 weight %, preferably 0.5-1.2 weight %.
  • Chromium (Cr) is an active element in order to improve the resistance to a majority of corrosion types. Furthermore, a high content of chromium implies that one gets a very good N solubility in the material. Thus, it is desirable to keep the Cr content as high as possible in order to improve the corrosion resistance. For very good amounts of corrosion resistance the content of chromium should be at least 24.0 weight %, preferably 27.0-29.0 weight %. However, high contents of Cr increase the risk for intermetallic precipitations, for what reason the content of chromium must be limited up to max 30.0 weight %.
  • Nickel (Ni) is used as austenite stabilizing element and is added in suitable amounts in order to obtain the desired content of ferrite.
  • Molybdenum is an active element which improves the resistance to corrosion in chloride environments as well as preferably in reducing acids. Too high of a Mo content in combination with high Cr contents, implies that the risk for intermetallic precipitations increases.
  • the Mo content in the present invention should lie in the range of 3.0-5.0 weight %, preferably 3.6-4.7 weight %, in particular 4.0-4.3 weight %.
  • Nitrogen (N) is a very active element, which increases the corrosion resistance, the structural stability as well as the strength of the material. Further, a high N content improves recovery of the austenite phase after welding, which gives good properties within the welded joint. In order to obtain a good effect of N, at least 0.28 weight % N should be added. At high contents of N, the risk for precipitation of chromium nitrides increases, especially when the chromium content is also high. Further, a high N content implies that the risk for porosity increases because of the exceeded solubility of N in the smelt. For these reasons the N content should be limited to max 0.5 weight %, preferably >0.35-0.45 weight % N is added.
  • Boron (B) is added in order to increase the hot workability of the material. At an excessive content of boron the weldability as well as the corrosion resistance could deteriorate. Therefore, the content of boron should be limited to 0.0030 weight %.
  • S Sulfur influences the corrosion resistance negatively by forming soluble sulfides. Further, the hot workability deteriorates, for what reason the content of sulfur is limited to max 0.010 weight %.
  • Co Co is added primarily in order to improve the structural stability as well as the corrosion resistance.
  • Co is an austenite-stabilizing element. In order to obtain effect should at least 0.5 weight %, preferably at least 1.5 weight % be added. Because cobalt is a relatively expensive element, the addition of cobalt is therefor limited to max 3.5 weight %.
  • Tungsten increases the resistance to pitting and crevice corrosion. But the addition of too much tungsten in combination with high Cr contents as well as high Mo contents means that the risk for intermetallic precipitations increases.
  • the W content in the present invention should be of 0-3.0 weight %, preferably 0.5 and 1.8 weight %.
  • Copper is added in order to improve the general corrosion resistance in acid environments such as sulfuric acid. At the same time Cu influences the structural stability. However, high contents of Cu imply that the solid solubility will be exceeded. Therefor the Cu content should be limited to max 2.0 weight %, preferably 0.5 to 1.5 weight %.
  • Ruthenium is added in order to increase the corrosion resistance. Because ruthenium is a very expensive element, the content should be limited to max 0.3 weight %, preferably more than 0 and up to 0.1 weight %.
  • Aluminum (Al) and Calcium (Ca) are used as desoxidation agents at the steel production.
  • the content of Al should be limited to max 0.03 weight % in order to limit the forming of nitrides.
  • Ca has a favorable effect on the hot ductility.
  • the Ca content should be limited to 0.010 weight % in order to avoid an unwanted amount of slag.
  • the content of ferrite is important in order to obtain good mechanical properties and corrosion properties as well as good weldability. From a corrosion resistance point of view and a point of view of weldability, a content of ferrite of 40-65% is desirable in order to obtain good properties. Further, high contents of ferrite imply that the impact strength at low temperatures as well as the resistance to hydrogen-induced brittleness suffers.
  • the content of ferrite is therefore 40-65 volume %, preferably 42-60 volume %, more preferably 45-55 volume %.
  • test heats according to this example were produced by casting of 170 kg ingots in the laboratory, which were hot forged to round bars. Those were hot extruded to bars (round bars as well as flat bars), where test material was taken out from the round bars. Further, the flat bars were annealed before cold rolling took place, whereafter further test material was taken out. From a materials engineering point of view, the process can be considered to be representative for production on a bigger scale, for example for the production of seamless tubes by the extrusion method, followed by cold rolling. Table 1 shows the composition of the first batch of test heats. TABLE 1 Composition for test heats, weight %.
  • T max sigma was calculated with Thermo-Calc (TC version N thermodynamic database for steel TCFE99) based on characteristic amounts for all specified elements in the different variations.
  • T max sigma is the dissolving temperature for the sigma phase, where high dissolving temperatures indicate lower structural stability.
  • CPT Critical Pitting Temperature
  • the test heat 605183, alloyed with cobalt shows good structural stability at a controlled cooling rate of ( ⁇ 140° C./min) in spite of the fact that it contains high contents of chromium as well as of molybdenum, shows better results than SAF2507 and SAF2906. It appears from this investigation that a high PRE does not solely explain the CPT values.
  • the relationship or ratio of PRE austenite/PRE ferrite is of extreme importance for the properties of the higher alloyed duplex steels, and a very narrow and exact balance between the alloying elements is required in order to obtain this optimum ratio, which lies between 0.9-1.15; preferably 0.9-1.05 and simultaneously obtain PRE values of above 46.
  • the relationship PRE austenite/PRE ferrite against CPT in the modified ASTM G48C test for the test heats is given in Table 3.
  • Tensile test specimen (DR-5C50) were manufactured from extruded bars, ⁇ 20 mm, which were heat treated at temperatures according to Table 2 for 20 minutes followed by cooling down in air, or water (605195, 605197, 605184). The results of the tests are presented in Table 4 and 5. The results of the tensile test show that the contents of chromium, nitrogen and tungsten strongly influence the impact strength of the material. Besides 605153, all heats fulfill the requirement of a 25% elongation at tensile testing at room temperature (RT).
  • Table 6 shows the results from the Tungsten-Inert-Gas remelting test (henceforth-abbreviated TIG), where the heats 605193, 605183, 605184 as well as 605253 show a good structure in the heat affected zone (Heat Affected Zone, henceforth-abbreviated HAZ).
  • the Ti-containing heats show TiN in HAZ.
  • An excessive chromium and nitrogen content results in precipitation of Cr 2 N, which shall be avoided because it deteriorates the properties of the material.
  • test heats were produced by casting of 270 kg ingots, which where hot forged to round bars. Those were extruded to bars, fro which test samples were taken. Afterwards the bar was annealed before cold rolling to flat bars was executed, after that further test material was taken out. Table 7 shows the composition for these test heats.
  • Thermo-Calc values according to Table 8 are based on characteristic amounts for all specified elements in the different variations.
  • the PRE number for the ferrite and austenite is based on their equilibrium composition at 1100° C.
  • T max sigma is the dissolving temperature for the sigma phase, where high dissolving temperatures indicate lower structural stability.
  • heats lie within the identified range of 0.9-1.15; preferably 0.9-1.05 applicable for the ratio PRE austenite/PRE ferrite at the same time as PRE in both austenite and ferrite is in excess of 44 and for most of the heats even considerably in excess of 44. Some of the heats attain a total PRE of 50. It is very interesting to note that heat 605251, alloyed with 1.5 weight % cobalt, performs almost equivalent with heat 605250, alloyed with 0.6 weight % cobalt in “Green Death” solution in spite of the lower chromium content in heat 605251. It is particularly surprising and interesting because heat 605251 has a PRE number of ca. 48, which is in excess of some of today's commercial superduplex alloys. Further, the T max sigma-value below 1010° C. indicates a good structural stability based on the values in Table 2 in Example 1.
  • heat 605249 alloyed with 1.5 weight % cobalt
  • heat 605250 alloyed with 0.6 weight % cobalt
  • Both heats are alloyed with high contents of chromium, approximately 29.0 weight % and the molybdenum content of approximately 4.25 weight %. If one compares the compositions of the heats 605249, 605250, 605251 and 605252 with respect to the content of sigma phase, it is very evident that the range of composition for that optimum material is very narrow, in this case with regard to structural stability.
  • heat 605268 contains only minor amounts of sigma phase compared to heat 605263, which contains much sigma phase. What mainly distinguishes these heats from each other is the addition of copper to heat 605268. Heat 605266 and also 605267 are free from sigma phase, despite of a high content of chromium the later heat is alloyed with copper. Further, the heats 605262 and 605263 with addition of 1.0 weight % tungsten show a structure with much sigma phase, while it is interesting to note that heat 605269, also with 1.0 weight % tungsten but with higher content of nitrogen than 605262 and 605263 shows a considerable smaller amount of sigma phase. Consequently, a very good balance between different alloying elements at these high alloying contents is required. For example, chromium and molybdenum contents must be balanced in order to obtain good structural properties.
  • Table 11 shows the results from the light optical examination after annealing at 1080° C., 20 min followed by water quenching.
  • the amount of sigma phase is specified with values from 1 to 5, where 1 represents that no sigma phase was detected in the examination, while 5 represents that a very high content of sigma phase was detected in the examination.
  • Table 12 the results from the impact strength testing of some of the heats are shown. The results are very good, which indicates a good structure after annealing at 1100° C. followed by water quenching. The requirement of at least 100J is exceeded by a large margin in all tested heats.
  • FIG. 4 shows the results from the hot ductility testing of the most of the heats.
  • a good workability is of course of vital importance in order to be able to produce the material to product in forms such as bars, tubes (such as welded and seamless tubes), plate, strip, wire, welding wire, constructive elements (such as pumps, valves, flanges and couplings).
  • the material should have one or more, if not all, of the following:
  • PRE number in ferrite should exceed 45, but preferably be at least 47;
  • PRE number in austenite should exceed 45, but preferably be at least 47;
  • PRE number for the entire alloy should preferably be at least 46;
  • Relationship PRE austenite/PRE ferrite should be 0.9-1.15, preferably 0.9-1.05;
  • the content of ferrite should be preferably 45-55 volume %
  • T max sigma should not exceed 1010° C.
  • the content of nitrogen should be 0.28-0.5 weight % preferably 0.35-0.48 weight %, more preferably 0.38-0.40 weight %;
  • the content of cobalt should be 0-3.5 weight %, preferably 1.0-2.0 weight %, more preferably 1.3-1.7 weight %;
  • the alloy In order to ensure the high nitrogen solubility, i.e. if the content of nitrogen is in the range 0.38-0.40 weight %, the alloy should be at least 29 weight % Cr, as well as at least 3.0 weight % Mo, thus the total content of the elements Cr, Mo and N fulfills the requirements of the PRE number.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
  • Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
  • Load-Engaging Elements For Cranes (AREA)
  • Crystals, And After-Treatments Of Crystals (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Contacts (AREA)
  • Glass Compositions (AREA)
US10/232,726 2001-09-02 2002-09-03 Duplex stainless steel alloy Abandoned US20030086808A1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0102931-3 2001-09-02
SE0102931A SE524952C2 (sv) 2001-09-02 2001-09-02 Duplex rostfri stållegering

Publications (1)

Publication Number Publication Date
US20030086808A1 true US20030086808A1 (en) 2003-05-08

Family

ID=20285220

Family Applications (1)

Application Number Title Priority Date Filing Date
US10/232,726 Abandoned US20030086808A1 (en) 2001-09-02 2002-09-03 Duplex stainless steel alloy

Country Status (18)

Country Link
US (1) US20030086808A1 (da)
EP (2) EP1423548B1 (da)
JP (1) JP4234592B2 (da)
KR (2) KR20090128568A (da)
CN (1) CN100465325C (da)
AT (2) ATE391192T1 (da)
AU (1) AU2002328002B9 (da)
BR (1) BR0212270B1 (da)
CA (1) CA2459253A1 (da)
DE (2) DE60213828T2 (da)
DK (2) DK1423548T3 (da)
ES (2) ES2300088T3 (da)
MX (1) MXPA04002017A (da)
NO (1) NO338090B1 (da)
OA (1) OA12657A (da)
PL (1) PL199387B1 (da)
SE (1) SE524952C2 (da)
WO (1) WO2003020994A1 (da)

Cited By (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030133823A1 (en) * 2001-09-02 2003-07-17 Ann Sundstrom Use of a duplex stainless steel alloy
US20050028893A1 (en) * 2001-09-25 2005-02-10 Hakan Silfverlin Use of an austenitic stainless steel
US20070089810A1 (en) * 2003-03-02 2007-04-26 Sandvik Intellectual Property Ab Duplex stainless steel alloy for use in seawater applications
WO2009054799A1 (en) * 2007-10-26 2009-04-30 Sandvik Intellectual Property Ab Use of a duplex stainless steel in a phosphoric acid production system
US20090142218A1 (en) * 2007-11-29 2009-06-04 Ati Properties, Inc. Lean austenitic stainless steel
US20090162237A1 (en) * 2007-12-20 2009-06-25 Ati Properties, Inc. Lean austenitic stainless steel containing stabilizing elements
US20090162238A1 (en) * 2007-12-20 2009-06-25 Ati Properties, Inc. Corrosion resistant lean austenitic stainless steel
US8337749B2 (en) 2007-12-20 2012-12-25 Ati Properties, Inc. Lean austenitic stainless steel
US9803267B2 (en) 2011-05-26 2017-10-31 Upl, L.L.C. Austenitic stainless steel

Families Citing this family (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
SE527175C2 (sv) * 2003-03-02 2006-01-17 Sandvik Intellectual Property Duplex rostfri ställegering och dess användning
SE528782C2 (sv) * 2004-11-04 2007-02-13 Sandvik Intellectual Property Duplext rostfritt stål med hög sträckgräns, artiklar och användning av stålet
SE531305C2 (sv) * 2005-11-16 2009-02-17 Sandvik Intellectual Property Strängar för musikinstrument
SE530711C2 (sv) * 2006-10-30 2008-08-19 Sandvik Intellectual Property Duplex rostfri stållegering samt användning av denna legering
CN101353769B (zh) * 2007-07-26 2011-10-05 傅丰仁 铬23镍6铁素体-奥氏体不锈钢管及其制造工艺
CN101215673B (zh) * 2008-01-08 2010-12-01 上海大学 高性能双相不锈钢合金材料及其制备方法
FI121340B (fi) * 2008-12-19 2010-10-15 Outokumpu Oy Dupleksinen ruostumaton teräs
ES2632008T3 (es) 2011-03-10 2017-09-07 Nippon Steel & Sumitomo Metal Corporation Acero inoxidable dúplex
FI125854B (fi) * 2011-11-04 2016-03-15 Outokumpu Oy Dupleksi ruostumaton teräs
EP2865776B1 (en) * 2012-06-22 2018-08-08 Nippon Steel & Sumitomo Metal Corporation Duplex stainless steel
DE102013110743B4 (de) * 2013-09-27 2016-02-11 Böhler Edelstahl GmbH & Co. KG Verfahren zur Herstellung eines Duplexstahles
CA2991658C (en) 2015-07-20 2023-12-19 Sandvik Intellectual Property Ab Duplex stainless steel and formed object thereof
CN107937825A (zh) * 2017-11-15 2018-04-20 江阴方圆环锻法兰有限公司 油气用双相钢阀门锻件及其锻造方法
LT3502293T (lt) * 2017-12-22 2020-07-10 Saipem S.P.A. Dupleksinio nerūdijančio plieno panaudojimas
JP7277484B2 (ja) * 2018-06-15 2023-05-19 エービー サンドビック マテリアルズ テクノロジー 二相ステンレス鋼ストリップおよびそれを製造するための方法
CN111230406A (zh) * 2018-11-28 2020-06-05 无锡市新峰管业有限公司 一种海洋环境下双相不锈钢管及其加工方法
CN112342473A (zh) * 2020-09-17 2021-02-09 江苏华久辐条制造有限公司 一种冷轧带钢表面耐蚀处理方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3861908A (en) * 1973-08-20 1975-01-21 Crucible Inc Duplex stainless steel
US4678523A (en) * 1986-07-03 1987-07-07 Cabot Corporation Corrosion- and wear-resistant duplex steel
US4765953A (en) * 1985-09-05 1988-08-23 Santrade Limited High nitrogen containing duplex stainless steel having high corrosion resistance and good structure stability
US4985091A (en) * 1990-01-12 1991-01-15 Carondelet Foundry Company Corrosion resistant duplex alloys
US5238508A (en) * 1984-02-07 1993-08-24 Kubota, Ltd. Ferritic-austenitic duplex stainless steel
US5284530A (en) * 1991-09-30 1994-02-08 Sumitomo Metal Industries, Ltd. Duplex stainless steel having improved corrosion resistance
US5906791A (en) * 1997-07-28 1999-05-25 General Electric Company Steel alloys
US6048413A (en) * 1994-05-21 2000-04-11 Park; Yong Soo Duplex stainless steel with high corrosion resistance
US20010003121A1 (en) * 1997-12-05 2001-06-07 Astrazeneca Uk Limited Novel compounds
US20030133823A1 (en) * 2001-09-02 2003-07-17 Ann Sundstrom Use of a duplex stainless steel alloy

Family Cites Families (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS60165362A (ja) * 1984-02-07 1985-08-28 Kubota Ltd 高耐食性高耐力二相ステンレス鋼
AT397515B (de) * 1990-05-03 1994-04-25 Boehler Edelstahl Hochfeste korrosionsbeständige duplex-legierung
JP2500162B2 (ja) * 1991-11-11 1996-05-29 住友金属工業株式会社 耐食性に優れた高強度二相ステンレス鋼
JP3166798B2 (ja) * 1992-10-06 2001-05-14 住友金属工業株式会社 耐食性、相安定性に優れた二相ステンレス鋼
SE501321C2 (sv) * 1993-06-21 1995-01-16 Sandvik Ab Ferrit-austenitiskt rostfritt stål samt användning av stålet
AT405297B (de) * 1997-08-13 1999-06-25 Boehler Edelstahl Duplexlegierung für komplex beanspruchte bauteile
US6033497A (en) * 1997-09-05 2000-03-07 Sandusky International, Inc. Pitting resistant duplex stainless steel alloy with improved machinability and method of making thereof
SE514044C2 (sv) * 1998-10-23 2000-12-18 Sandvik Ab Stål för havsvattentillämpningar
SE0000678L (sv) * 2000-03-02 2001-04-30 Sandvik Ab Duplext rostfritt stål

Patent Citations (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3861908A (en) * 1973-08-20 1975-01-21 Crucible Inc Duplex stainless steel
US5238508A (en) * 1984-02-07 1993-08-24 Kubota, Ltd. Ferritic-austenitic duplex stainless steel
US4765953A (en) * 1985-09-05 1988-08-23 Santrade Limited High nitrogen containing duplex stainless steel having high corrosion resistance and good structure stability
US4678523A (en) * 1986-07-03 1987-07-07 Cabot Corporation Corrosion- and wear-resistant duplex steel
US4985091A (en) * 1990-01-12 1991-01-15 Carondelet Foundry Company Corrosion resistant duplex alloys
US5284530A (en) * 1991-09-30 1994-02-08 Sumitomo Metal Industries, Ltd. Duplex stainless steel having improved corrosion resistance
US6048413A (en) * 1994-05-21 2000-04-11 Park; Yong Soo Duplex stainless steel with high corrosion resistance
US5906791A (en) * 1997-07-28 1999-05-25 General Electric Company Steel alloys
US20010003121A1 (en) * 1997-12-05 2001-06-07 Astrazeneca Uk Limited Novel compounds
US6303659B2 (en) * 1997-12-05 2001-10-16 Astrazeneca Ab Compounds
US20030133823A1 (en) * 2001-09-02 2003-07-17 Ann Sundstrom Use of a duplex stainless steel alloy

Cited By (24)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030133823A1 (en) * 2001-09-02 2003-07-17 Ann Sundstrom Use of a duplex stainless steel alloy
US20050028893A1 (en) * 2001-09-25 2005-02-10 Hakan Silfverlin Use of an austenitic stainless steel
US20070089810A1 (en) * 2003-03-02 2007-04-26 Sandvik Intellectual Property Ab Duplex stainless steel alloy for use in seawater applications
WO2009054799A1 (en) * 2007-10-26 2009-04-30 Sandvik Intellectual Property Ab Use of a duplex stainless steel in a phosphoric acid production system
EP2215421A1 (en) * 2007-10-26 2010-08-11 Sandvik Intellectual Property Ab Use of a duplex stainless steel in a phosphoric acid production system
EP2215421A4 (en) * 2007-10-26 2010-10-06 Sandvik Intellectual Property USE OF A STAINLESS DUPLEX STEEL IN A SYSTEM FOR THE PREPARATION OF PHOSPHORIC ACID
US20100294472A1 (en) * 2007-10-26 2010-11-25 Sandvik Intellectual Property Ab Use of a duplex stainless steel in a phosphoric acid production system
US20090142218A1 (en) * 2007-11-29 2009-06-04 Ati Properties, Inc. Lean austenitic stainless steel
US10370748B2 (en) 2007-11-29 2019-08-06 Ati Properties Llc Lean austenitic stainless steel
US9617628B2 (en) 2007-11-29 2017-04-11 Ati Properties Llc Lean austenitic stainless steel
US8313691B2 (en) 2007-11-29 2012-11-20 Ati Properties, Inc. Lean austenitic stainless steel
US8858872B2 (en) 2007-11-29 2014-10-14 Ati Properties, Inc. Lean austenitic stainless steel
US8337749B2 (en) 2007-12-20 2012-12-25 Ati Properties, Inc. Lean austenitic stainless steel
US8337748B2 (en) 2007-12-20 2012-12-25 Ati Properties, Inc. Lean austenitic stainless steel containing stabilizing elements
US8877121B2 (en) 2007-12-20 2014-11-04 Ati Properties, Inc. Corrosion resistant lean austenitic stainless steel
US9121089B2 (en) 2007-12-20 2015-09-01 Ati Properties, Inc. Lean austenitic stainless steel
US9133538B2 (en) 2007-12-20 2015-09-15 Ati Properties, Inc. Lean austenitic stainless steel containing stabilizing elements
US20090162238A1 (en) * 2007-12-20 2009-06-25 Ati Properties, Inc. Corrosion resistant lean austenitic stainless steel
US9624564B2 (en) 2007-12-20 2017-04-18 Ati Properties Llc Corrosion resistant lean austenitic stainless steel
US9822435B2 (en) 2007-12-20 2017-11-21 Ati Properties Llc 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
US20090162237A1 (en) * 2007-12-20 2009-06-25 Ati Properties, Inc. Lean austenitic stainless steel containing stabilizing elements
US9803267B2 (en) 2011-05-26 2017-10-31 Upl, L.L.C. Austenitic stainless steel

Also Published As

Publication number Publication date
SE0102931D0 (sv) 2001-09-02
ATE335867T1 (de) 2006-09-15
AU2002328002B2 (en) 2007-07-05
EP1722002A1 (en) 2006-11-15
WO2003020994A1 (en) 2003-03-13
JP4234592B2 (ja) 2009-03-04
ATE391192T1 (de) 2008-04-15
AU2002328002B9 (en) 2008-03-13
EP1423548A1 (en) 2004-06-02
DK1423548T3 (da) 2006-12-04
OA12657A (en) 2006-06-19
NO338090B1 (no) 2016-07-25
DE60213828D1 (de) 2006-09-21
CN100465325C (zh) 2009-03-04
KR20090128568A (ko) 2009-12-15
KR100989022B1 (ko) 2010-10-20
PL368230A1 (en) 2005-03-21
BR0212270B1 (pt) 2011-05-31
DE60213828T2 (de) 2007-03-01
EP1423548B1 (en) 2006-08-09
JP2005501969A (ja) 2005-01-20
EP1722002B1 (en) 2008-04-02
NO20040900L (no) 2004-04-30
ES2300088T3 (es) 2008-06-01
DE60225951D1 (de) 2008-05-15
DE60225951T2 (de) 2009-04-09
ES2266557T3 (es) 2007-03-01
SE524952C2 (sv) 2004-10-26
BR0212270A (pt) 2004-10-13
CN1571862A (zh) 2005-01-26
PL199387B1 (pl) 2008-09-30
CA2459253A1 (en) 2003-03-13
SE0102931L (sv) 2003-03-03
MXPA04002017A (es) 2004-07-08
DK1722002T3 (da) 2008-07-28
KR20040029142A (ko) 2004-04-03

Similar Documents

Publication Publication Date Title
US20030086808A1 (en) Duplex stainless steel alloy
AU2002328002A1 (en) Duplex steel alloy
US7081173B2 (en) Super-austenitic stainless steel
US20100316522A1 (en) Duplex stainless steel alloy and use of this alloy
US6749697B2 (en) Duplex stainless steel
US20030133823A1 (en) Use of a duplex stainless steel alloy
SE527178C2 (sv) Användning av en duplex rostfri stållegering
US6623569B2 (en) Duplex stainless steels
AU2002329144A1 (en) Use of a duplex stainless steel alloy
US11702714B2 (en) High fracture toughness, high strength, precipitation hardenable stainless steel
EP0333422A1 (en) Austenitic stainless steel

Legal Events

Date Code Title Description
AS Assignment

Owner name: SANDVIK AB, SWEDEN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:SUNDSTROM, ANN;KANGAS, PASI;NYSTROM, ANNA-LENA;REEL/FRAME:013549/0717

Effective date: 20021023

AS Assignment

Owner name: SANDVIK INTELLECTUAL PROPERTY HB, SWEDEN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:SANDVIK AB;REEL/FRAME:016290/0628

Effective date: 20050516

Owner name: SANDVIK INTELLECTUAL PROPERTY HB,SWEDEN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:SANDVIK AB;REEL/FRAME:016290/0628

Effective date: 20050516

AS Assignment

Owner name: SANDVIK INTELLECTUAL PROPERTY AKTIEBOLAG, SWEDEN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:SANDVIK INTELLECTUAL PROPERTY HB;REEL/FRAME:016621/0366

Effective date: 20050630

Owner name: SANDVIK INTELLECTUAL PROPERTY AKTIEBOLAG,SWEDEN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:SANDVIK INTELLECTUAL PROPERTY HB;REEL/FRAME:016621/0366

Effective date: 20050630

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION