NO155351B - FERRITIC STAINLESS STEEL AND USE OF SAME. - Google Patents
FERRITIC STAINLESS STEEL AND USE OF SAME. Download PDFInfo
- Publication number
- NO155351B NO155351B NO800712A NO800712A NO155351B NO 155351 B NO155351 B NO 155351B NO 800712 A NO800712 A NO 800712A NO 800712 A NO800712 A NO 800712A NO 155351 B NO155351 B NO 155351B
- Authority
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- Norway
- Prior art keywords
- weight
- stainless steel
- titanium
- niobium
- carbon
- Prior art date
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 28
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 22
- 229910052757 nitrogen Inorganic materials 0.000 claims description 18
- 239000010936 titanium Substances 0.000 claims description 18
- 229910052719 titanium Inorganic materials 0.000 claims description 18
- 229910052799 carbon Inorganic materials 0.000 claims description 17
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 15
- 229910052758 niobium Inorganic materials 0.000 claims description 15
- 239000010955 niobium Substances 0.000 claims description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 14
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 13
- 229910052759 nickel Inorganic materials 0.000 claims description 11
- 229910052726 zirconium Inorganic materials 0.000 claims description 11
- 229910000831 Steel Inorganic materials 0.000 claims description 10
- 239000010959 steel Substances 0.000 claims description 10
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 9
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 239000011733 molybdenum Substances 0.000 claims description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 239000011651 chromium Substances 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 239000003795 chemical substances by application Substances 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 2
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 2
- 239000010935 stainless steel Substances 0.000 claims 6
- 238000010276 construction Methods 0.000 claims 1
- 239000000155 melt Substances 0.000 description 25
- 238000012360 testing method Methods 0.000 description 12
- 238000005260 corrosion Methods 0.000 description 11
- 230000007797 corrosion Effects 0.000 description 11
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 230000007704 transition Effects 0.000 description 8
- 239000000463 material Substances 0.000 description 5
- 239000003381 stabilizer Substances 0.000 description 3
- 238000003466 welding Methods 0.000 description 3
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- ARUVKPQLZAKDPS-UHFFFAOYSA-L copper(II) sulfate Chemical compound [Cu+2].[O-][S+2]([O-])([O-])[O-] ARUVKPQLZAKDPS-UHFFFAOYSA-L 0.000 description 1
- 229910000366 copper(II) sulfate Inorganic materials 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011572 manganese Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- -1 polytetrafluoroethylene Polymers 0.000 description 1
- 229920001343 polytetrafluoroethylene Polymers 0.000 description 1
- 239000004810 polytetrafluoroethylene Substances 0.000 description 1
- 229910052845 zircon Inorganic materials 0.000 description 1
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 1
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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- 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
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)
- Arc Welding In General (AREA)
- Catalysts (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Load-Engaging Elements For Cranes (AREA)
- Rolling Contact Bearings (AREA)
Description
Foreliggende oppfinnelse vedrører et ferrittisk rustfritt The present invention relates to a ferritic stainless steel
stål. I norsk utlegningsskrift nr. 154.585 er beskrevet ferrittisk rustfritt stål som er særpreget ved forbedret sprekkresistens og intergranulær korrosjonsresistens. Stål i henhold til norsk søknad nr. 80.0713 adskiller seg fra stålet vist i US patentene nr. 3.932.174 og 3.929.473 ved at det inneholder opptil 2 % av elementene fra gruppen bestående av titan, zirkonium og niob i henhold til fore- steel. In Norwegian design document no. 154,585, ferritic stainless steel is described, which is characterized by improved crack resistance and intergranular corrosion resistance. Steel according to Norwegian application no. 80.0713 differs from the steel shown in US patents no. 3,932,174 and 3,929,473 in that it contains up to 2% of the elements from the group consisting of titanium, zirconium and niobium according to pre-
liggende ligning horizontal equation
og et karbon pluss nitrogeninnhold som overstiger 275 ppm. and a carbon plus nitrogen content exceeding 275 ppm.
På grunn av dets høyere karbon og nitrogeninnhold kan det Because of its higher carbon and nitrogen content, it can
smeltes og raffineres ved mindre kostbare prosedyrer enn stålene i henhold til US patentene nr. 3.932.174 og 3.929.473. are melted and refined by less expensive procedures than the steels according to US patents no. 3,932,174 and 3,929,473.
Ved hjelp av foreliggende oppfinnelse er tilveiebragt et By means of the present invention, a
stål som er seigere enn det i henhold til norsk søknad nr. steel that is tougher than that according to Norwegian application no.
80.0713. I tillegg til stabilisatorer fra gruppen bestående av titan, zirkonium og niob og karbon pluss nitrogeninnhold overstigende 275 ppm har stål ifølge foreliggende oppfinnelse 2,00 - 5,00 vekt% nikkel og fortrinnsvis 3,00 - 80.0713. In addition to stabilizers from the group consisting of titanium, zirconium and niobium and carbon plus nitrogen content exceeding 275 ppm, steel according to the present invention has 2.00 - 5.00 wt% nickel and preferably 3.00 -
4,50 vekt%, men stål i henhold til norsk uti.skrift 154.585 inneholder opp til 2,00 vekt% og vanligvis mindre enn 1,00 4.50% by weight, but steel according to Norwegian publication 154.585 contains up to 2.00% by weight and usually less than 1.00
vekt/6. Nikkel er funnet å fremheve seigheten for legeringen i henhold til norsk uti.skrift nr. 154.585. Av de ovenfor gitte grunner er legeringen i henhold til foreliggende oppfinnelse klart forskjellig fra den i henhold til US weight/6. Nickel has been found to enhance the toughness of the alloy according to Norwegian publication no. 154.585. For the reasons given above, the alloy according to the present invention is clearly different from that according to US
patentene nr. 3.932.174 og 3.929.473. Den er også patents no. 3,932,174 and 3,929,473. It is too
forskjellig fra legeringen i henhold til US patent nr. different from the alloy according to US patent no.
4.119.765. Legeringen ifølge det sistnevnte patent angir et maksimalt molybdeninnhold under det i henhold til forelig- 4,119,765. The alloy according to the latter patent indicates a maximum molybdenum content below that according to the present
gende oppfinnelse. gent invention.
En annen referanse av interesse er en artikkel med tittelen Another reference of interest is an article titled
"Ferritic Stainless Steel Corrosion Resistance and Exonomy" "Ferritic Stainless Steel Corrosion Resistance and Exonomy"
av Remus A. Lula i juli utgaven 1976 av Metal Progress, by Remus A. Lula in the July 1976 issue of Metal Progress,
sidene 24-29. Denne artikkel angir ikke det ferrittiske rustfrie stål ifølge oppfinnelsen. pages 24-29. This article does not specify the ferritic stainless steel of the invention.
Det er hensikt med foreliggende oppfinnelse å tilveiebringe et ferrittisk rustfritt stål. It is the purpose of the present invention to provide a ferritic stainless steel.
Det ferrittiske rustfrie stål ifølge oppfinnelsen er særpreget ved en overlegen bedre seighet både før og etter sveising, med forbedret sprekkresistens og intergranulær korrosjonsresistens og med god sveisbarhet. Stålet består i det vesentlige av opp til 0,08 vekt-% karbon, opp til 0,06 vekt-% nitrogen, 28,5-30,5 vekt-% krom, 3,6 - 5,6 vekt-% molybden, 0-2 vekt-% mangan, 2,0 - 5,0 vekt-% nikkel og 0-2 vekt-% silisium, 0-0,5% aluminium som desoksyderingsmiddel og 0-2,0 vekt-% av elementene titan, zirkonium og niob og hvor resten i det vesentlige utgjøres av jern. Summen av karbon pluss nitrogen overstiger 0,0275 vekt-%. Titan, zirkonium og niob er tilstede i henhold til følgende ligning. The ferritic stainless steel according to the invention is characterized by superior toughness both before and after welding, with improved crack resistance and intergranular corrosion resistance and with good weldability. The steel essentially consists of up to 0.08 wt% carbon, up to 0.06 wt% nitrogen, 28.5-30.5 wt% chromium, 3.6 - 5.6 wt% molybdenum, 0-2 weight-% manganese, 2.0-5.0 weight-% nickel and 0-2 weight-% silicon, 0-0.5% aluminum as a deoxidizing agent and 0-2.0 weight-% of the elements titanium, zirconium and niobium and where the remainder essentially consists of iron. The sum of carbon plus nitrogen exceeds 0.0275% by weight. Titanium, zirconium and niobium are present according to the following equation.
Karbon og nitrogen er vanligvis til stede i de følgende respektive mengder på minst 0,005 vekt-% og 0,01 vekt-%, Carbon and nitrogen are typically present in the following respective amounts of at least 0.005% by weight and 0.01% by weight,
idet summen av disse elementer overstiger 0,003 vekt-%. Molybden er fortrinnsvis tilstede i 3,75 - 4,75 vekt-%. as the sum of these elements exceeds 0.003% by weight. The molybdenum is preferably present in 3.75 - 4.75% by weight.
Mangan og silisium er vanligvis til stede' i mengder på Manganese and silicon are usually present in amounts of
mindre enn 1,0 vekt-%. Aluminium som kan være til stede på grunn av dets virkning som desoksyderingsmiddel, er vanligvis tilstede i mengder på mindre enn 0,1 %. less than 1.0% by weight. Aluminum which may be present due to its action as a deoxidizing agent is usually present in amounts of less than 0.1%.
Titan, niob og/eller zirkonium tilsettes for å forbedre sprekkresistensen og intergranulær korrosjonsresistens for legeringen, som i en viss grad er en høykarbon plus nitrogen-variant av stålet ifølge US patent nr. 3.929.473. Det er funnet at stabilisatorer kan tilsettes til høykarbon og/eller ni-trogenvarianter av den nevnte patent uten å ødelegge dets seighet og/eller sveisbarhet. Selv om det er foretrukket å tilsette minst 0,15 vekt-% titan, idet kun tilstedeværelse av Titanium, niobium and/or zirconium are added to improve the crack resistance and intergranular corrosion resistance of the alloy, which is to some extent a high carbon plus nitrogen variant of the steel according to US Patent No. 3,929,473. It has been found that stabilizers can be added to high carbon and/or nitrogen variants of the said patent without destroying its toughness and/or weldability. Although it is preferred to add at least 0.15% by weight of titanium, only the presence of
niob kan uheldig påvirke legeringens sveisbarhet, så er det innen foreliggende oppfinnelses ramme å tilsette den nød-vendige mengde stabilisator enten i form av titan eller niob. niobium can adversely affect the weldability of the alloy, so it is within the framework of the present invention to add the necessary amount of stabilizer either in the form of titanium or niobium.
Niob har en gunstig effekt, sammenlignet med titan, på legeringens seighet. Ved en særlig utførelsesform av oppfinnelsen så inneholder denne minst 0,15 vekt-% niob og minst 0,15 vekt-% titan. Titan og zirkon er fortrinnsvis tilstede i mengder opp til 1,0 vekt-% i henhold til følg-ende ligning: Niobium has a beneficial effect, compared to titanium, on the toughness of the alloy. In a particular embodiment of the invention, this contains at least 0.15% by weight niobium and at least 0.15% by weight titanium. Titanium and zircon are preferably present in amounts up to 1.0% by weight according to the following equation:
Nikkel tilsettes til legeringen ifølge oppfinnelsen for å Nickel is added to the alloy according to the invention in order to
øke dens seighet. Den tilsettes i mengder på 2,0 - 5,0 increase its toughness. It is added in quantities of 2.0 - 5.0
vekt-%, fortrinnsvis i mengder på 3,0-4,5 vekt-%. % by weight, preferably in amounts of 3.0-4.5% by weight.
Det ferrittiske rustfrie stål i henhold til oppfinnelsen er særlig egnet for anvendelse i sveisede artikler. The ferritic stainless steel according to the invention is particularly suitable for use in welded articles.
De følgende eksempler illustrerer flere trekk ved oppfinnelsen. Barrer fra 25 smelter (smeltende A - X) ble oppvarmet til The following examples illustrate several features of the invention. Ingots from 25 melts (melts A - X) were heated to
1 120° og varmevalset til strimler med en tykkelse på 3,18 mm 1 120° and hot rolled into strips with a thickness of 3.18 mm
og vamebehandlet ved 1065°C eller 1120°C, kaldvalset til en tykkelse på 1,57 cm og varmebehandlet ved 1065°C eller 1120°C. Varmevalsede og koldvalsede prøver ble deretter evaluert med hensyn til seighet. Andre prøvestykker ble TIG sveiset og deretter undersøkt med hensyn til seighet. and heat treated at 1065°C or 1120°C, cold rolled to a thickness of 1.57 cm and heat treated at 1065°C or 1120°C. Hot-rolled and cold-rolled samples were then evaluated for toughness. Other test pieces were TIG welded and then examined for toughness.
Sammensetningen av smeltene fremgår av den etterfølgende tabell I.Bemerk at smeltene A-F faller utenfor oppfinnelsens ramme idet det ikke utviser et nikkelinnhold på 2,00 - 5,00 vekt-%. Foreliggende oppfinnelse er basert på et nikkelinnhold som overstiger 2,00 %. The composition of the melts appears in the following table I. Note that the melts A-F fall outside the scope of the invention as it does not exhibit a nickel content of 2.00 - 5.00% by weight. The present invention is based on a nickel content that exceeds 2.00%.
Ytterligere data vedrørende sammensetningen av smeltene fremgår av den etterfølgende tabell II Further data regarding the composition of the melts appears in the following table II
Seigheten ble bestemt ved å bestemme overgangstemperaturen under anvendelse av små transverse "Charpy" prøvestykker med V-utskjæringer for varmevalsede og varmebehandlede materialer (3,2 mm x 10,0 cm prøvestykker), for koldvalsede og varmebehandlede materialer (1,57 x 10,0 cm prøvestykke), som sveiset materiale (1,57 x 10,0 cm prøvestykker) og sveiste og varmebe-handlete materialer (1,57 mm x 10,0 mm prøvestykker). Overgangstemperaturen var basert på tilsynekomst av 50 % duktil - 50 % sprø brudd. Overgangstemperaturen for varmevalsede og koldvalsede prøver er vist i den etterfølgende tabell III. Smeltene A - L ble varmebehandlet ved 1065°C. De andre smelter ble varmebehandlet ved 1120°C. Toughness was determined by determining the transition temperature using small transverse "Charpy" specimens with V-cuts for hot-rolled and heat-treated materials (3.2 mm x 10.0 cm specimens), for cold-rolled and heat-treated materials (1.57 x 10, 0 cm test piece), such as welded material (1.57 x 10.0 cm test pieces) and welded and heat-treated materials (1.57 mm x 10.0 mm test pieces). The transition temperature was based on the appearance of 50% ductile - 50% brittle fracture. The transition temperature for hot-rolled and cold-rolled samples is shown in the subsequent table III. The melts A - L were heat treated at 1065°C. The other melts were heat treated at 1120°C.
Overgangstemperaturene for sveisede oa for sveisede samt varmebehandlede prøver fremgår av den etterfølgende tabell IV. Smeltene A-F ble varmebehandlet ved 1065°C før sveiseing. De andre smelter ble varmebehandlet ved 1120°C. Alle prøver ble vann-kjølt varmebehandling etter sveising var 1065°C for smeltene A-F og 1120°C for de gjenværende smelter. Alle smelter ble vannkjølt etter varmebehandlingen etter sveising. The transition temperatures for welded and other for welded and heat-treated samples appear in the following table IV. The melts A-F were heat treated at 1065°C before welding. The other melts were heat treated at 1120°C. All samples were water-cooled heat treatment after welding was 1065°C for melts A-F and 1120°C for the remaining melts. All melts were water-cooled after the post-weld heat treatment.
Den gunstige effekt av nikkel fremgår klart av tabellene III og IV. Smeltene G - X har betydelig lavere overgangstemperatur og er derfor vesentlig seigere enn smeltene A-F. Det må bemerkes at smeltene G - X faller innenfor foreliggende oppfinnelses ramme, mens smeltene A-F faller utenfor. Smeltene G - X inneholder mer enn 2,00 vekt-% nikkel. The beneficial effect of nickel is clear from Tables III and IV. The melts G - X have a significantly lower transition temperature and are therefore significantly tougher than the melts A-F. It must be noted that the melts G - X fall within the framework of the present invention, while the melts A-F fall outside. Melts G - X contain more than 2.00 wt% nickel.
De lavere overgangstemperaturer for smeltene G - X er eksem-plifisert i den etterfølgende tabell V som er basert på tabel-len III og IV. The lower transition temperatures for the melts G - X are exemplified in the following table V which is based on tables III and IV.
Bemerk at i hvert tilfelle er den maksimale overgangstemperatur for smeltene G - X lavere enn den minimale overgangstemperatur for smeltene A - F. Fra de angitte data fremgår det klart at smeltene G - X er seigere enn smeltene A-F. Note that in each case the maximum transition temperature for melts G - X is lower than the minimum transition temperature for melts A - F. It is clear from the data provided that melts G - X are tougher than melts A - F.
Ytterligere prøvestykker av smeltene G - X ble undersøkt med hensyn til sprekk- og intergranulær korrosjonsresistens. Prøvestykkene ble fremstilt på samme måte som de ovenfor omtal-te prøvestykker. Sprekkorrosjonsresistens ble bestemt ved å neddykke 2,5 x 5 cm overflatepolerte prøver i en 10 %-ig jern (III) kloridoppløsning i 72 timer. Prøvene ble utført ved 50°C. Sprekker ble dannet ved å anvende polytetrafluoetylen-blokker på for- og bakside som ble holdt i stilling ved hjelp av et par gummibånd og bøyet til 90°C i forhold til hverandre både i lengde og tverretningene. Denne prøve er betegnet: G 48 - 76 (American Society for Testing And Materials). Additional samples of the melts G - X were examined with respect to crevice and intergranular corrosion resistance. The test pieces were produced in the same way as the test pieces mentioned above. Crevice corrosion resistance was determined by immersing 2.5 x 5 cm surface polished samples in a 10% iron (III) chloride solution for 72 hours. The tests were carried out at 50°C. Cracks were formed by using polytetrafluoroethylene blocks on the front and back which were held in position by a pair of rubber bands and bent at 90°C relative to each other both lengthwise and transversely. This sample is designated: G 48 - 76 (American Society for Testing And Materials).
Resultatene av undersøkelsene fremgår i den etterfølgende tabell VI. Prøvestykkene var i koldvalset og varmebehandlet tilstand, samt i sveiset tilstand og i sveiset og varmebehandlet tilstand. The results of the investigations appear in the subsequent table VI. The test pieces were in the cold-rolled and heat-treated state, as well as in the welded state and in the welded and heat-treated state.
Fra tabell VI kan det sees at sprekk -korros jonsresistensen for smeltene G - X er utmerket. Legeringene ifølge foreliggende oppfinnelse er særpreget ved vesentlig forbedret sprekk-korrosjonsresistens. From Table VI it can be seen that the crevice corrosion resistance of the melts G - X is excellent. The alloys according to the present invention are characterized by substantially improved crevice corrosion resistance.
Intergranulær korrosjonsresistens ble bestemt ved å neddykke 2,54 cm x 5 cm overflatepolerte prøvestykker i kokende kobber (II) sulfat - 50 % svovelsyreoppløsning i 120 timer. De van-lige tilfredsstillende/ikke tilfredsstillende kriteria for denne prøve er en korrosjonshastighet på 0,6 mm/år (0,05 mm/ md) og en tilfredsstillende mikroskopisk bestemmelse. Denne prøven er anbefalt for stabiliserte ferritiske rustfrie stål med høyt krominnhold. Intergranular corrosion resistance was determined by immersing 2.54 cm x 5 cm surface polished specimens in boiling copper (II) sulfate - 50% sulfuric acid solution for 120 hours. The usual satisfactory/unsatisfactory criteria for this test are a corrosion rate of 0.6 mm/year (0.05 mm/md) and a satisfactory microscopic determination. This test is recommended for stabilized ferritic stainless steels with a high chromium content.
Resultatene av denne bestemmelse fremgår av den etterfølgende tabell VII. Prøvene var i sveiset tilstand og i sveiset og varmebehandlet tilstand. The results of this provision appear in the following table VII. The samples were in the welded state and in the welded and heat-treated state.
Fra tabell VII kan det sees at smeltene G - L og S - X utviser utmerket intergranulær korrosjonsresistens. Hvert prøvestykke tilfredsstilte denne prøve. From Table VII it can be seen that melts G-L and S-X exhibit excellent intergranular corrosion resistance. Each sample passed this test.
Claims (9)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US10936380A | 1980-01-03 | 1980-01-03 |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO800712L NO800712L (en) | 1981-07-06 |
| NO155351B true NO155351B (en) | 1986-12-08 |
| NO155351C NO155351C (en) | 1987-03-18 |
Family
ID=22327261
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO800712A NO155351C (en) | 1980-01-03 | 1980-03-12 | FERRITIC STAINLESS STEEL AND USE OF SAME. |
Country Status (19)
| Country | Link |
|---|---|
| JP (1) | JPS5698458A (en) |
| KR (1) | KR850000980B1 (en) |
| AT (1) | AT376707B (en) |
| AU (1) | AU535783B2 (en) |
| BE (1) | BE882793A (en) |
| BR (1) | BR8001877A (en) |
| CA (1) | CA1163470A (en) |
| CS (1) | CS216241B2 (en) |
| DE (1) | DE3011048A1 (en) |
| ES (1) | ES8104832A1 (en) |
| FR (1) | FR2473068A1 (en) |
| GB (1) | GB2066847B (en) |
| IT (1) | IT1188918B (en) |
| MX (1) | MX6596E (en) |
| NL (1) | NL8001740A (en) |
| NO (1) | NO155351C (en) |
| PL (1) | PL124420B1 (en) |
| RO (1) | RO79271A (en) |
| SE (1) | SE436576C (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE453838B (en) * | 1985-09-05 | 1988-03-07 | Santrade Ltd | HIGH-QUALITY FERRIT-AUSTENITIC STAINLESS STEEL |
| JPS6331535A (en) * | 1986-07-23 | 1988-02-10 | Jgc Corp | Apparatus for treating carbon-containing compound having carbon precipitation suppressing property |
| JPH0422870U (en) * | 1990-06-11 | 1992-02-25 |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA922543A (en) * | 1969-07-11 | 1973-03-13 | The International Nickel Company Of Canada | Corrosion resistant ferritic stainless steel |
| FR2091642A5 (en) * | 1970-05-16 | 1972-01-14 | Nippon Steel Corp | Stainless steel resistant to pitting corrosion -and suitable for comp - used in sewater |
| GB1359629A (en) * | 1971-10-26 | 1974-07-10 | Deutsche Edelstahlwerke Gmbh | Corrosion-resistant ferritic chrome steel |
| US3890143A (en) * | 1972-04-14 | 1975-06-17 | Nyby Bruk Ab | Welded constructions of stainless steels |
| AT338854B (en) * | 1972-09-04 | 1977-09-26 | Ver Edelstahlwerke Ag | FERRITIC OR FERRITIC-AUSTENITIC STEEL ALLOYS FOR OBJECTS THAT ARE CORROSION-RESISTANT TO ACID AND WATER MIXTURES UP TO 70 DEGREES C. |
| SE385383B (en) * | 1973-05-28 | 1976-06-28 | Asea Ab | PROCEDURE FOR THE PRODUCTION OF STAINLESS STEEL, FERRIT-AUSTENITIC STEEL |
| JPS5241113A (en) * | 1975-09-30 | 1977-03-30 | Nippon Steel Corp | Ferritic stainless steel having high toughness and high corrosion resi stance |
| DE2616599B2 (en) * | 1976-04-13 | 1981-03-26 | Mannesmann AG, 40213 Düsseldorf | Use of a high-alloy steel for the manufacture of high-strength objects that are resistant to acid gas corrosion |
| GB1565419A (en) * | 1976-04-27 | 1980-04-23 | Crucible Inc | Stainless steel welded articles |
| DE2701329C2 (en) * | 1977-01-14 | 1983-03-24 | Thyssen Edelstahlwerke AG, 4000 Düsseldorf | Corrosion-resistant ferritic chrome-molybdenum-nickel steel |
| DE2737116C2 (en) * | 1977-08-17 | 1985-05-09 | Gränges Nyby AB, Nybybruk | Process for the production of sheets and strips from ferritic, stabilized, rustproof chromium-molybdenum-nickel steels |
-
1980
- 1980-03-11 SE SE8001868A patent/SE436576C/en not_active IP Right Cessation
- 1980-03-12 NO NO800712A patent/NO155351C/en unknown
- 1980-03-13 AU AU56419/80A patent/AU535783B2/en not_active Ceased
- 1980-03-21 DE DE19803011048 patent/DE3011048A1/en not_active Ceased
- 1980-03-25 NL NL8001740A patent/NL8001740A/en not_active Application Discontinuation
- 1980-03-28 BR BR8001877A patent/BR8001877A/en not_active IP Right Cessation
- 1980-03-28 IT IT8048292A patent/IT1188918B/en active
- 1980-03-29 RO RO80100668A patent/RO79271A/en unknown
- 1980-04-01 CA CA000348953A patent/CA1163470A/en not_active Expired
- 1980-04-02 GB GB8011018A patent/GB2066847B/en not_active Expired
- 1980-04-15 BE BE0/200230A patent/BE882793A/en not_active IP Right Cessation
- 1980-04-18 FR FR8008816A patent/FR2473068A1/en active Granted
- 1980-04-18 KR KR1019800001595A patent/KR850000980B1/en active
- 1980-05-02 JP JP5935880A patent/JPS5698458A/en active Granted
- 1980-05-20 AT AT0268880A patent/AT376707B/en not_active IP Right Cessation
- 1980-05-26 MX MX808843U patent/MX6596E/en unknown
- 1980-06-12 ES ES492374A patent/ES8104832A1/en not_active Expired
- 1980-07-30 CS CS805326A patent/CS216241B2/en unknown
- 1980-09-11 PL PL1980226697A patent/PL124420B1/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| PL226697A1 (en) | 1981-08-07 |
| GB2066847B (en) | 1984-08-08 |
| JPS5698458A (en) | 1981-08-07 |
| DE3011048A1 (en) | 1981-07-23 |
| IT8048292A1 (en) | 1981-09-28 |
| NL8001740A (en) | 1981-08-03 |
| AU5641980A (en) | 1981-09-10 |
| BE882793A (en) | 1980-10-15 |
| KR850000980B1 (en) | 1985-07-05 |
| AU535783B2 (en) | 1984-04-05 |
| CA1163470A (en) | 1984-03-13 |
| ATA268880A (en) | 1984-05-15 |
| ES492374A0 (en) | 1981-04-16 |
| PL124420B1 (en) | 1983-01-31 |
| SE436576B (en) | 1985-01-07 |
| NO155351C (en) | 1987-03-18 |
| JPH0321624B2 (en) | 1991-03-25 |
| BR8001877A (en) | 1981-07-14 |
| CS216241B2 (en) | 1982-10-29 |
| SE436576C (en) | 1986-12-23 |
| ES8104832A1 (en) | 1981-04-16 |
| AT376707B (en) | 1984-12-27 |
| IT1188918B (en) | 1988-01-28 |
| RO79271A (en) | 1983-02-01 |
| GB2066847A (en) | 1981-07-15 |
| FR2473068A1 (en) | 1981-07-10 |
| FR2473068B1 (en) | 1985-03-08 |
| IT8048292A0 (en) | 1980-03-28 |
| MX6596E (en) | 1985-08-14 |
| KR830002902A (en) | 1983-05-31 |
| SE8001868L (en) | 1981-07-04 |
| NO800712L (en) | 1981-07-06 |
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