NO154585B - FERRITIC STAINLESS STEEL AND USE THEREOF. - Google Patents
FERRITIC STAINLESS STEEL AND USE THEREOF. Download PDFInfo
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- NO154585B NO154585B NO800713A NO800713A NO154585B NO 154585 B NO154585 B NO 154585B NO 800713 A NO800713 A NO 800713A NO 800713 A NO800713 A NO 800713A NO 154585 B NO154585 B NO 154585B
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- Prior art keywords
- weight
- titanium
- niobium
- zirconium
- steel according
- Prior art date
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 28
- 239000010936 titanium Substances 0.000 claims description 23
- 229910052719 titanium Inorganic materials 0.000 claims description 23
- 229910052758 niobium Inorganic materials 0.000 claims description 22
- 239000010955 niobium Substances 0.000 claims description 22
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 20
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 19
- 229910052799 carbon Inorganic materials 0.000 claims description 17
- 229910052757 nitrogen Inorganic materials 0.000 claims description 17
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 14
- 229910052726 zirconium Inorganic materials 0.000 claims description 14
- 229910000831 Steel Inorganic materials 0.000 claims description 13
- 239000010959 steel Substances 0.000 claims description 13
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 11
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 239000011733 molybdenum Substances 0.000 claims description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 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
- 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 3
- 229910052759 nickel Inorganic materials 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
- 238000010276 construction Methods 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 description 14
- 239000000956 alloy Substances 0.000 description 14
- 238000005260 corrosion Methods 0.000 description 13
- 230000007797 corrosion Effects 0.000 description 13
- 239000000155 melt Substances 0.000 description 11
- 238000012360 testing method Methods 0.000 description 9
- 239000000463 material Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 238000000034 method Methods 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
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000003381 stabilizer Substances 0.000 description 2
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 1
- VVTSZOCINPYFDP-UHFFFAOYSA-N [O].[Ar] Chemical compound [O].[Ar] VVTSZOCINPYFDP-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 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
- 230000007423 decrease Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000000203 mixture Substances 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
- 230000007704 transition Effects 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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 Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
- Catalysts (AREA)
- Load-Engaging Elements For Cranes (AREA)
- Treatment Of Steel In Its Molten State (AREA)
- Compounds Of Iron (AREA)
Description
Foreliggende oppfinnelse vedrører ferrittisk rustfritt The present invention relates to ferritic stainless steel
stål. steel.
I US-patentene nr. 3.932.174 og 3.929.473 er beskrevet ferrittiske, rustfrie stål med utmerket sprekkdannelse-resistens og intergranulær korrosjonsresistens. De beskrevne stål inneholder 29 % krom og 4 % molybden, de har også et maksimalt karbon + nitrogeninnhold på 250 ppm. Karbon og nitrogeninnholdet er begrenset da korrosjonsresistensen for slike stål avtar ved stigende innhold av de nevnte elementer. US patents no. 3,932,174 and 3,929,473 describe ferritic stainless steels with excellent crack resistance and intergranular corrosion resistance. The described steels contain 29% chromium and 4% molybdenum, they also have a maximum carbon + nitrogen content of 250 ppm. The carbon and nitrogen content is limited as the corrosion resistance of such steels decreases with increasing content of the aforementioned elements.
Det lave karbon- og nitrogenkrav for legeringene i henhold The low carbon and nitrogen requirements for the alloys accordingly
til US-patentene nr. 3.932.174 og 3.929.473 er ufordelaktig ved at det nødvendiggjør kostbare smelteprosedyrer, så som vakuuminduksjonssmelting. to US Patents Nos. 3,932,174 and 3,929,473 is disadvantageous in that it necessitates expensive melting procedures, such as vacuum induction melting.
Ved hjelp av foreliggende oppfinnelse er det tilveiebrakt By means of the present invention it is provided
en legering med egenskaper som er sammenlignbare med leger- an alloy with properties comparable to alloys
ingene i henhold til US-patentene nr. 3.932.174 og 3.929.473, likevel er det ikke nødvendig med de omtalte kostbare smelteprosedyrer omtalt ovenfor. Legeringen i henhold til oppfinnelsen kan eksempelvis smeltes og raffineres under anven- in accordance with US Patent Nos. 3,932,174 and 3,929,473, however, the costly melting procedures discussed above are not necessary. The alloy according to the invention can, for example, be melted and refined during use
delse av argon-oksygen dekarbonisering (AOD) prosedyrer. sharing argon-oxygen decarbonisation (AOD) procedures.
Legeringen ifølge oppfinnelsen inneholder opptil 2 % av elementene bestående av titan, zirkon og niob i henhold til følgende ligning: The alloy according to the invention contains up to 2% of the elements consisting of titanium, zirconium and niobium according to the following equation:
og karbon + nitrogeninnholdet overstiger 275 ppm. Fore- and the carbon + nitrogen content exceeds 275 ppm. Pre-
liggende stål utmerker seg med utmerket sprekkresistens og intergranulær korrosjonsresistens, god sveisbarhet og til-fredsstillende seighet både før og etter sveising. På grunn av det som ovenfor er angitt er legeringen i henhold til foreliggende oppfinnelse klart forskjellig fra de i henhold til US-patentene nr. 3.932.174 og 3.929.473. Den er også forskjellig fra to andre legeringer, nemlig de i henhold til lying steel is characterized by excellent crack resistance and intergranular corrosion resistance, good weldability and satisfactory toughness both before and after welding. Because of the above, the alloy according to the present invention is clearly different from those according to US Patent Nos. 3,932,174 and 3,929,473. It also differs from two other alloys, namely those according to
US-patent nr. 3.957.544 og 4.119.765. Begge de sistnevnte legeringer har et maksimalt molybdeninnhold under det som er angitt for foreliggende oppfinnelse. US Patent Nos. 3,957,544 and 4,119,765. Both of the latter alloys have a maximum molybdenum content below that specified for the present invention.
En annen referanse av interesse er en artikkel med tittelen "Ferritic Stainless Steel Corrosion Resistance and Economy", skrevet av Remus A. Lula i juli 1976 utgaven av Metal Progress, sidene 24 - 29. Heller ikke denne artikkel angir det ferrittiske stål ifølge foreliggende oppfinnelse. Another reference of interest is an article entitled "Ferritic Stainless Steel Corrosion Resistance and Economy", written by Remus A. Lula in the July 1976 issue of Metal Progress, pages 24 - 29. This article also does not state the ferritic steel of the present invention .
Det er således en hensikt med foreliggende oppfinnelse å tilveiebringe et ferrittisk rustfritt stål. It is thus an aim of the present invention to provide a ferritic stainless steel.
Det ferrittiske rustfrie stål ifølge foreliggende oppfinnelse er særpreget ved utmerket sprekkresistens og intergranulær korrosjonsresistens, god sveisbarhet og tilfred-stillende seighet både før og etter sveising. Legeringen består i det vesentlige av 0,005 til 0,08 vekt-% karbon, The ferritic stainless steel according to the present invention is characterized by excellent crack resistance and intergranular corrosion resistance, good weldability and satisfactory toughness both before and after welding. The alloy consists essentially of 0.005 to 0.08 wt% carbon,
0,010 til 0,06 vekt-% nitrogen, 28,50 til 30,50 vekt-% 0.010 to 0.06 wt% nitrogen, 28.50 to 30.50 wt%
krom, 3,60 til 5,6 vekt-% molybden, 0 til 2,00 vekt-% chromium, 3.60 to 5.6% by weight molybdenum, 0 to 2.00% by weight
mangan, 0 til 2,0 vekt-% nikkel, 0 til 2,0 vekt-% silisium, manganese, 0 to 2.0 wt% nickel, 0 to 2.0 wt% silicon,
0 til 0,5 vekt-% aluminium, 0 til 2,00 vekt-% av elementene fra gruppen bestående av titan, zirkon og niob og hvor resten i det vesentlige utgjøres av jern. Summen av karbon + nitrogen overstiger 0,0275 vekt-%. Titan, zirkonium og niob er tilstede i henhold til følgende ligning. 0 to 0.5% by weight aluminium, 0 to 2.00% by weight of the elements from the group consisting of titanium, zirconium and niobium and where the rest is essentially made up of iron. The sum of carbon + nitrogen exceeds 0.0275% by weight. Titanium, zirconium and niobium are present according to the following equation.
Karbon og nitrogen er vanligvis tilstede i mengder på henholdsvis minst 0,005 vekt-% og 0,010 vekt-%, og hvor summen overstiger 0,0300 vekt-%. Molybden er fortrinnsvis tilstede i en mengde på 3,75 til 4,75 vekt-%. Mangan, nikkel og silisium er hver vanligvis tilstede i mengder på mindre enn 1,00 vekt-%. Aluminium som kan være tilstede på grunn av dens effekt som desoksyderinasmiddel er vanligvis tilstede i mengder på mindre enn 0,1 vekt-%. Carbon and nitrogen are usually present in amounts of at least 0.005% by weight and 0.010% by weight, respectively, and where the sum exceeds 0.0300% by weight. The molybdenum is preferably present in an amount of 3.75 to 4.75% by weight. Manganese, nickel, and silicon are each typically present in amounts of less than 1.00% by weight. Aluminum which may be present due to its effect as a deoxiderin agent is usually present in amounts of less than 0.1% by weight.
Titan, niob og/eller zirkonium tilsettes for å forbedre sprekkresistensen og intergranulær korrosjonsresistens for legeringen, som kan sies å være en høy karbon + nitrogen-variant av legeringen beskrevet i US-patentene nr. 3.932.174 og 3.929.473. Det er funnet at stabilisatorer kan tilsettes til høy karbon-og/eller nitrogen-variantene ifølge US-patentene nr. 3.932.174 og 3.929.473 uten å ødelegge seigheten og/eller sveisbarheten av legeringen. Selv om det er foretrukket å tilsette minst 0,15 % titan fordi tilstedeværelse av niob alene kan i uheldig grad påvirke legeringens sveisbarhet, det er innen foreliggende oppfinnelses ramme å tilsette den nødvendige mengde av stabilisator, enten i form av titan eller niob. Niob har en gunstig effekt sammen-lignet med titan på legeringens seighet. En særlig utførel-sesform av oppfinnelsen krever minst 0,15 vekt-% niob og minst 0,15 vekt-% titan. Titan, niob og zirkonium er fortrinnsvis tilstede i mengder på opptil 1,00 vekt-% Titanium, niobium and/or zirconium are added to improve the crack resistance and intergranular corrosion resistance of the alloy, which can be said to be a high carbon + nitrogen variant of the alloy described in US Patent Nos. 3,932,174 and 3,929,473. It has been found that stabilizers can be added to the high carbon and/or nitrogen variants of US Patent Nos. 3,932,174 and 3,929,473 without destroying the toughness and/or weldability of the alloy. Although it is preferred to add at least 0.15% titanium because the presence of niobium alone can adversely affect the weldability of the alloy, it is within the scope of the present invention to add the necessary amount of stabilizer, either in the form of titanium or niobium. Compared to titanium, niobium has a favorable effect on the toughness of the alloy. A particular embodiment of the invention requires at least 0.15% by weight of niobium and at least 0.15% by weight of titanium. Titanium, niobium and zirconium are preferably present in amounts of up to 1.00% by weight
i henhold til den følgende ligning: according to the following equation:
Det ferrittiske rustfrie stål ifølge oppfinnelsen er særlig egnet for anvendelse i sveisede artikler med en tykkelse som ikke er større enn 1,8 mm (vanligvis ikke tykkere enn 1,2 mm), og særlig som sveisede kondensatorrør som typisk har en tykkelse i området 0,66 - 0,94 mm. De følgende eksem-pler viser forskjellige trekk ved oppfinnelsen. The ferritic stainless steel according to the invention is particularly suitable for use in welded articles with a thickness not greater than 1.8 mm (usually not thicker than 1.2 mm), and in particular as welded condenser tubes which typically have a thickness in the range 0 .66 - 0.94 mm. The following examples show various features of the invention.
Barrer fra 15 smelter (smelte A - O) ble oppvarmet Ingots from 15 melts (melts A - O) were heated
til 1 120°C og varmevalset til en strimmel med en tykkelse på 3,2 mm og varmebehandlet ved 1 065°C eller 1 121°C, kald-valset til strimler med tykkelse i området 1,57 - 1,65 mm og varmebehandlet igjen ved 1 065°C eller 1 121°C. Prøve- to 1,120°C and hot-rolled to a strip with a thickness of 3.2 mm and heat-treated at 1,065°C or 1,121°C, cold-rolled to strips with a thickness in the range of 1.57 - 1.65 mm and heat-treated again at 1,065°C or 1,121°C. Try-
stykkene ble deretter evaluert med hensyn til sprekk-korrosjonsresistens. Andre prøvestykker ble TIG-sveiset og evaluert med hensyn til sprekkresistens og intergranulær korrosjonsresistens. the pieces were then evaluated for crevice corrosion resistance. Other specimens were TIG welded and evaluated for crack resistance and intergranular corrosion resistance.
Sammensetningen av smeltene er vist i den etterfølgende tabell I. The composition of the melts is shown in the following table I.
Ytterligere data vedrørende smeltene fremgår av den etter-følgende tabell II. Further data regarding the melts appears in the following table II.
Bemerk at smelte A og B faller utenfor oppfinnelsens ramme idet de ikke tilfredsstiller ligningen: Note that melts A and B fall outside the scope of the invention as they do not satisfy the equation:
Sprekk-korrosjonsresistens ble bestemt ved å neddykke 2,5 x Crevice corrosion resistance was determined by immersion 2.5x
5 cm overflateslepne prøvestykker i en 10 %<1>ig jern (III) kloridoppløsning i 72 h. Prøvene ble utført ved temperaturer på 35°C og 50°C. Sprekker ble dannet ved kantene og over-flaten ved å anvende polytetrafluoretylenblokker på for- og baksiden holdt i stilling ved hjelp av gummibånd strukket til 90° til hverandre, både i lengde- og tverr-retningene. Denne prøve er beskrevet som "G48-76" (American Society For Testing And Materials). 5 cm surface-ground test pieces in a 10% iron (III) chloride solution for 72 h. The tests were carried out at temperatures of 35°C and 50°C. Cracks were formed at the edges and surface by using polytetrafluoroethylene blocks on the front and back held in position by means of rubber bands stretched at 90° to each other, both in the longitudinal and transverse directions. This sample is described as "G48-76" (American Society For Testing And Materials).
Resultatene av forsøkene er vist i den etterfølgende tabell The results of the experiments are shown in the following table
III. III.
Fra tabell III kan det bemerkes at sprekk-korrosjonsresistenser for smeltene C - G og I - 0 er overlegent bedre enn de for smeltene A og B. Basismetallet fra smelte B tapte så meget som 0,8519 g. Støpte metaller fra smeltene A og B tapte henholdsvis 0,4195 og 0,5783 g. From Table III, it can be noted that crevice corrosion resistances of melts C - G and I - 0 are superiorly better than those of melts A and B. The base metal from melt B lost as much as 0.8519 g. Cast metals from melts A and B lost 0.4195 and 0.5783 g respectively.
Det er viktig å bemerke at smeltene A og B ligger utenfor oppfinnelsens ramme, mens smeltene C - G og I - 0 faller innenfor oppfinnelsens ramme. It is important to note that melts A and B lie outside the scope of the invention, while melts C - G and I - 0 fall within the scope of the invention.
Intergranulær korrosjonsresistens ble bestemt ved å neddykke 2,5 x 5 cm overflateslepne prøvestykker i kokende kobber (II) sulfat - 50 % svovelsyreoppløsning i 120 h. Det vanlige godtagbare - ikke godtagbare kriterium for denne prøve er en korrosjonshastighet på 0,6 mm/år (0,05 mm/måned) og til-fredsstillende mikroskopiundersøkelse. Denne prøve er an-befalt for stabiliserte, høykromferrittiske rustfrie stål. Resultatene av prøven er vist i den etterfølgende tabell IV. Intergranular corrosion resistance was determined by immersing 2.5 x 5 cm surface-ground test pieces in boiling copper (II) sulfate - 50% sulfuric acid solution for 120 h. The usual acceptable - not acceptable criterion for this sample is a corrosion rate of 0.6 mm/year (0.05 mm/month) and satisfactory microscopic examination. This test is recommended for stabilized, high chromium ferritic stainless steels. The results of the test are shown in the following table IV.
Fra tabell IV kan det bemerkes at kun smelte B falt utenfor From Table IV, it can be noted that only melt B fell out
i denne prøve. Smelte B hadde en korrosjonshastighet på in this sample. Melt B had a corrosion rate of
3,58 mm/år. Som tidligere angitt er dette en av de to smelter som faller utenfor foreliggende oppfinnelses ramme. Den andre smelte som faller utenfor foreliggende oppfinnelses ramme er A. Imidlertid faller smelte B mere utenfor oppfinnelsens ramme enn smelte A ved at den har et lavere titan til karbon + nitrogenforhold. 3.58 mm/year. As previously indicated, this is one of the two melts that fall outside the scope of the present invention. The other melt that falls outside the scope of the present invention is A. However, melt B falls more outside the scope of the invention than melt A in that it has a lower titanium to carbon + nitrogen ratio.
Seighet ble evaluert ved å bestemme omslagstemper^turen Toughness was evaluated by determining the wrap temperature
under anvendelse av "Charpy" prøvestykker med V-innhakk for varmevalsede og varmebehandlede materialer (3,2 x 10,0 mm prøvestykker), samt for sveiset materiale (1,57 - 0,165 x 10 mm prøvestykker). Omslagstemperaturen var basert på fremkomst av et 50 % duktilt - 50 % sprøtt brudd. De erholdte omslagstemperaturen er vist i den etterfølgende tabell V. using "Charpy" test pieces with V-notch for hot-rolled and heat-treated materials (3.2 x 10.0 mm test pieces), as well as for welded material (1.57 - 0.165 x 10 mm test pieces). The wrap temperature was based on the occurrence of a 50% ductile - 50% brittle fracture. The obtained cover temperatures are shown in the subsequent table V.
(2) Strimmel varmebehandlet ved 1 06 5°C før sveising, vann-avkjølet (3) Varmebehandlet ved 1 121°C - vannkjølt, prøve i tverr-retning (4) Varmebehandlet ved 1 065°C - vannkjølt, prøve i tverr-retning (2) Strip heat-treated at 1,065°C before welding, water-cooled (3) Heat-treated at 1,121°C - water-cooled, sample in transverse direction (4) Heat-treated at 1,065°C - water-cooled, sample in transverse direction direction
Omslagstemperaturen indikerer at stålet ifølge foreliggende oppfinnelse kan kaldvalses, formes og sveises,selv om forvarming til tider kan være ønskelig. De niobinne-holdende prøver hadde lavere overgangstemperaturer enn de titaninneholdende prøver. Prøver inneholdende både titan og niob utviste op:- ;. ag s temper a turer mellom de for niob-inneholdende og titaninneholdende prøver. The envelope temperature indicates that the steel according to the present invention can be cold rolled, formed and welded, although preheating may sometimes be desirable. The niobium-containing samples had lower transition temperatures than the titanium-containing samples. Samples containing both titanium and niobium exhibited op:- ;. ag s temper a tures between the for niobium-containing and titanium-containing samples.
Claims (8)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US10937380A | 1980-01-03 | 1980-01-03 |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO800713L NO800713L (en) | 1981-07-06 |
| NO154585B true NO154585B (en) | 1986-07-28 |
| NO154585C NO154585C (en) | 1986-11-05 |
Family
ID=22327323
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO800713A NO154585C (en) | 1980-01-03 | 1980-03-12 | FERRITIC STAINLESS STEEL AND USE THEREOF. |
Country Status (19)
| Country | Link |
|---|---|
| JP (1) | JPS5698459A (en) |
| KR (1) | KR850000995B1 (en) |
| AT (1) | AT376706B (en) |
| AU (1) | AU535724B2 (en) |
| BE (1) | BE882792A (en) |
| BR (1) | BR8001876A (en) |
| CA (1) | CA1163471A (en) |
| CS (1) | CS216220B2 (en) |
| DE (1) | DE3012957A1 (en) |
| ES (1) | ES8105040A1 (en) |
| FR (1) | FR2473069A1 (en) |
| GB (1) | GB2066848B (en) |
| IT (1) | IT1188919B (en) |
| MX (1) | MX6668E (en) |
| NL (1) | NL8001739A (en) |
| NO (1) | NO154585C (en) |
| PL (1) | PL124421B1 (en) |
| SE (1) | SE436577B (en) |
| SU (1) | SU1258328A3 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6331535A (en) * | 1986-07-23 | 1988-02-10 | Jgc Corp | Apparatus for treating carbon-containing compound having carbon precipitation suppressing property |
| US10883160B2 (en) | 2018-02-23 | 2021-01-05 | Ut-Battelle, Llc | Corrosion and creep resistant high Cr FeCrAl alloys |
| CN114867879B (en) * | 2020-04-15 | 2023-07-07 | 日铁不锈钢株式会社 | Ferritic stainless steel material and method for producing same |
Family Cites Families (7)
| 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 |
| 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. |
| JPS5241113A (en) * | 1975-09-30 | 1977-03-30 | Nippon Steel Corp | Ferritic stainless steel having high toughness and high corrosion resi stance |
| 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 |
-
1980
- 1980-03-11 SE SE8001869A patent/SE436577B/en not_active IP Right Cessation
- 1980-03-12 NO NO800713A patent/NO154585C/en unknown
- 1980-03-13 AU AU56418/80A patent/AU535724B2/en not_active Ceased
- 1980-03-25 NL NL8001739A patent/NL8001739A/en not_active Application Discontinuation
- 1980-03-28 BR BR8001876A patent/BR8001876A/en not_active IP Right Cessation
- 1980-03-31 IT IT48299/80A patent/IT1188919B/en active
- 1980-04-01 CA CA000348952A patent/CA1163471A/en not_active Expired
- 1980-04-02 DE DE19803012957 patent/DE3012957A1/en not_active Ceased
- 1980-04-02 GB GB8011020A patent/GB2066848B/en not_active Expired
- 1980-04-07 KR KR1019800001438A patent/KR850000995B1/en active
- 1980-04-15 BE BE0/200229A patent/BE882792A/en not_active IP Right Cessation
- 1980-04-18 FR FR8008817A patent/FR2473069A1/en active Granted
- 1980-05-02 JP JP5935980A patent/JPS5698459A/en active Granted
- 1980-05-06 SU SU2917251A patent/SU1258328A3/en active
- 1980-05-13 AT AT0255980A patent/AT376706B/en not_active IP Right Cessation
- 1980-05-26 MX MX808842U patent/MX6668E/en unknown
- 1980-06-12 ES ES492375A patent/ES8105040A1/en not_active Expired
- 1980-07-30 CS CS805325A patent/CS216220B2/en unknown
- 1980-09-11 PL PL1980226698A patent/PL124421B1/en unknown
Also Published As
| Publication number | Publication date |
|---|---|
| SE8001869L (en) | 1981-07-04 |
| BR8001876A (en) | 1981-07-14 |
| AT376706B (en) | 1984-12-27 |
| JPS5698459A (en) | 1981-08-07 |
| AU535724B2 (en) | 1984-04-05 |
| CA1163471A (en) | 1984-03-13 |
| FR2473069A1 (en) | 1981-07-10 |
| IT8048299A1 (en) | 1981-10-01 |
| FR2473069B1 (en) | 1984-12-07 |
| NO154585C (en) | 1986-11-05 |
| JPH0321625B2 (en) | 1991-03-25 |
| GB2066848A (en) | 1981-07-15 |
| BE882792A (en) | 1980-10-15 |
| NO800713L (en) | 1981-07-06 |
| NL8001739A (en) | 1981-08-03 |
| IT8048299A0 (en) | 1980-03-31 |
| GB2066848B (en) | 1983-06-02 |
| IT1188919B (en) | 1988-01-28 |
| KR830002901A (en) | 1983-05-31 |
| ES492375A0 (en) | 1981-05-16 |
| PL124421B1 (en) | 1983-01-31 |
| DE3012957A1 (en) | 1981-09-03 |
| SE436577B (en) | 1985-01-07 |
| CS216220B2 (en) | 1982-10-29 |
| ATA255980A (en) | 1984-05-15 |
| MX6668E (en) | 1985-10-07 |
| PL226698A1 (en) | 1981-08-07 |
| KR850000995B1 (en) | 1985-07-15 |
| ES8105040A1 (en) | 1981-05-16 |
| SU1258328A3 (en) | 1986-09-15 |
| AU5641880A (en) | 1981-07-09 |
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