NO151506B - APPLICATION OF A MANGANE-NICKEL BUILDING STEEL WITH A FINE CORN STRUCTURE FOR CRYOGENIC PURPOSES - Google Patents
APPLICATION OF A MANGANE-NICKEL BUILDING STEEL WITH A FINE CORN STRUCTURE FOR CRYOGENIC PURPOSES Download PDFInfo
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- NO151506B NO151506B NO793516A NO793516A NO151506B NO 151506 B NO151506 B NO 151506B NO 793516 A NO793516 A NO 793516A NO 793516 A NO793516 A NO 793516A NO 151506 B NO151506 B NO 151506B
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- Prior art keywords
- nickel
- steel
- application
- manganese
- mangane
- Prior art date
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- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 title claims abstract description 39
- 229910052759 nickel Inorganic materials 0.000 title claims abstract description 20
- 229910000831 Steel Inorganic materials 0.000 title claims description 36
- 239000010959 steel Substances 0.000 title claims description 36
- 239000000463 material Substances 0.000 claims abstract description 10
- 239000010949 copper Substances 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 239000010955 niobium Substances 0.000 claims abstract description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 4
- 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 abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 239000010703 silicon Substances 0.000 claims abstract description 4
- 229910000746 Structural steel Inorganic materials 0.000 claims abstract description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000004411 aluminium Substances 0.000 claims abstract description 3
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- ZAUUZASCMSWKGX-UHFFFAOYSA-N manganese nickel Chemical compound [Mn].[Ni] ZAUUZASCMSWKGX-UHFFFAOYSA-N 0.000 claims abstract description 3
- 238000004519 manufacturing process Methods 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims 1
- 239000011593 sulfur Substances 0.000 claims 1
- 239000005864 Sulphur Substances 0.000 abstract description 2
- 241001062472 Stokellia anisodon Species 0.000 abstract 1
- 230000001419 dependent effect Effects 0.000 abstract 1
- 229910052739 hydrogen Inorganic materials 0.000 description 8
- 239000001257 hydrogen Substances 0.000 description 8
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 7
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 6
- 238000010586 diagram Methods 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 239000007789 gas Substances 0.000 description 4
- 230000007704 transition Effects 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 238000005098 hot rolling Methods 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 238000003860 storage Methods 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000851 Alloy steel Inorganic materials 0.000 description 2
- VGGSQFUCUMXWEO-UHFFFAOYSA-N Ethene Chemical group C=C VGGSQFUCUMXWEO-UHFFFAOYSA-N 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000010410 layer Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 240000007594 Oryza sativa Species 0.000 description 1
- 235000007164 Oryza sativa Nutrition 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 150000001879 copper Chemical class 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- -1 hydrogen ions Chemical class 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 238000005342 ion exchange Methods 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- 235000009566 rice Nutrition 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 230000009044 synergistic interaction Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
Classifications
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- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
Abstract
Description
Foreliggende oppfinnelse angår anvendelse av et mangan-nikkel-bygningsstål med finkornet struktur, med 0,04 - 0,09% karbon, 1,2 - 1,8% mangan, 0,1 - 0,4% silisium, 0,03 The present invention relates to the use of a manganese-nickel structural steel with a fine-grained structure, with 0.04 - 0.09% carbon, 1.2 - 1.8% manganese, 0.1 - 0.4% silicon, 0.03
- 0,08% niob, opptil 0,025% aluminium, opptil 0,015% svovel, 0,5 -1,5% nikkel og fakultativt 0,2 - 0,4% kobber, idet resten er jern inkludert fremstillingsbetingede forurensninger. Et legert stål av den ovenfor angitte art er kjent fra DE-OS 24 07 338; dette inneholder 0,01 - 0,1% karbon, 0,5 - 2% mangan, 0,1 - 0,9% silisium, 0,001 - 0,10% niob, 0,01 - 0,3% aluminium og 1,4 - 3,5% nikkel. Dette stål har en viss koldfasthet når det i avhengighet av nikkelinnholdet er kontrollert varmevalset. En i avhengighet av det for-håndenværende nikkelinnhold styrt varmevalsing viser seg dog i praksis å være vanskelig og spesielt kostbar. I tillegg til dette kommer det at koldseigheten til dette stål ikke er tilstrekkelig til å kunne anvende stålet ved temperaturer som flytende metan og spesielt flytende etylen fører med seg. - 0.08% niobium, up to 0.025% aluminium, up to 0.015% sulphur, 0.5 -1.5% nickel and optionally 0.2 - 0.4% copper, the rest being iron including manufacturing-related impurities. An alloy steel of the type indicated above is known from DE-OS 24 07 338; this contains 0.01 - 0.1% carbon, 0.5 - 2% manganese, 0.1 - 0.9% silicon, 0.001 - 0.10% niobium, 0.01 - 0.3% aluminum and 1, 4 - 3.5% nickel. This steel has a certain cold resistance when, depending on the nickel content, the hot rolling has been controlled. In practice, however, controlled hot rolling depending on the existing nickel content proves to be difficult and particularly expensive. In addition to this, the cold toughness of this steel is not sufficient to be able to use the steel at temperatures that liquid methane and especially liquid ethylene bring with it.
For transport og lagring av flytendegjorte gasser er det nødvendig med materialer som har en tilstrekkelig fasthet og seighet ved temperaturer ned til -120°C. I tillegg må disse materialer være sveisbare for å kunne muliggjøre en økonomisk fremstilling av rør og beholdere. For the transport and storage of liquefied gases, it is necessary to use materials that have sufficient strength and toughness at temperatures down to -120°C. In addition, these materials must be weldable in order to enable an economic production of pipes and containers.
Det er kjent at rustfrie stål kan tåle - driftstemperaturer til under -270°C. Ansvarlig for koldseigheten er her spesielt nikkel. Den høye andel av dyre legeringsbestand-deler setter imidlertid grenser for anvendelse av de rustfrie stål og gjør at man søker etter rimeligere legerte stål. Dette har ført til utvikling av en rekke stål med ca. 9% nikkel, 0,1% karbon, 0,8% mangan og 0,02% fosfor, stål som sammenlignet med det rustfrie stål utmerker seg ved en høyere strekkfasthet og en ned til ca. It is known that stainless steels can withstand operating temperatures below -270°C. Nickel in particular is responsible for the cold toughness here. The high proportion of expensive alloy stock parts, however, limits the use of the stainless steels and causes people to search for less expensive alloy steels. This has led to the development of a range of steels with approx. 9% nickel, 0.1% carbon, 0.8% manganese and 0.02% phosphorus, steel which, compared to stainless steel, is distinguished by a higher tensile strength and a down to approx.
-200°C tilstrekkelig koldseighet. Forutsetning for den høye koldseighet er dog en 2-trinns normalglødning og anløpning, noe som tar sikte på å oppnå en tilstrekkelig austenittandel i det ferrittiske grunnskjelett. Dette fordi man vet at seigheten øker med økende austenittandel. Forsøk har i denne sammeheng vist at koldseigheten økes med avtagende innhold av karbon, fosfor og mangan. Videre har det vist seg at en trinnvis reduksjon av nikkelinholdet til 2,1% fører til en økende innvirkning på koldseigheten. Således ble f.eks. skårslagseigheten på 42,5 J/cm<2> ved -196°C for normalisert og anløpet stål inneholdende 8,5 - 9,5% nikkel, for stål inneholdende 3,25 - 3,75% nikkel redusert til 25 J/cm<2> ved -100°C og for stål innehold-ende 2,1 - 2,5% nikkel redusert til 22,5 J/cm<2> ved -68°C. Stål med nikkelinnhold under 9% er således ansett som ikke egnet for de laveste temperaturer. -200°C sufficient cold resistance. However, a prerequisite for the high cold toughness is a 2-stage normal annealing and tempering, which aims to achieve a sufficient proportion of austenite in the ferritic basic skeleton. This is because it is known that toughness increases with increasing austenite content. Experiments have shown in this connection that cold toughness increases with decreasing content of carbon, phosphorus and manganese. Furthermore, it has been shown that a gradual reduction of the nickel content to 2.1% leads to an increasing impact on the cold toughness. Thus, e.g. the shear strength of 42.5 J/cm<2> at -196°C for normalized and annealed steel containing 8.5 - 9.5% nickel, for steel containing 3.25 - 3.75% nickel reduced to 25 J/cm <2> at -100°C and for steel containing 2.1 - 2.5% nickel reduced to 22.5 J/cm<2> at -68°C. Steel with a nickel content below 9% is thus considered unsuitable for the lowest temperatures.
Oppfinnelsen har nu til oppgave å foreslå et legert stål som kan sveises, som oppviser en høy strekkgrense ved romtemperatur og koldseighet samt bestandighet mot hydrogenriss og som derfor er spesielt egnet som materiale for sveisede deler så som rør og beholdere, og som tjener til transport og lagring av flytendegjorte gasser,også ved nærvær av hydrogensulfid og vann. Spesielt skal stålet være bestandig overfor flytende etylen og tåle temperaturer til -120°C. The invention now has the task of proposing an alloy steel that can be welded, which exhibits a high tensile strength at room temperature and cold toughness as well as resistance to hydrogen cracking and which is therefore particularly suitable as a material for welded parts such as pipes and containers, and which serves for transport and storage of liquefied gases, also in the presence of hydrogen sulphide and water. In particular, the steel must be resistant to liquid ethylene and withstand temperatures down to -120°C.
Løsningen av denne oppgave består i å benytte et stål av den innledingsvis nevnte sammenseting til det nettopp nevnte formål. The solution to this task consists in using a steel of the initially mentioned composition for the purpose just mentioned.
Stålet har allerede i valseherdet og anløpt tilstand, på tross av sitt meget lave nikkelinnhold, en meget høy skårslagseighet og en overgangstemperatur som tillater anvendelse ved temperaturer til -70°C. De fullstendige materialegenskaper utvikler seg dog imidlertid først når det foreslåtte stål er normalglødet og eventuelt også anløpt. Etter en slik varmebehandling har stålet en romtemperaturstrekkgrense på minst 420 N/mm og en overgangstemperatur på tvers av valseretningen på minst -120°C for en skårslagseighet på 51 J/cm<2>, samt en skårslagseighet på minst 280 J/cm<2> ved romtemperatur. Despite its very low nickel content, the steel already in the roll-hardened and annealed state has a very high chip resistance and a transition temperature that allows use at temperatures down to -70°C. However, the full material properties only develop when the proposed steel is normally annealed and possibly also annealed. After such a heat treatment, the steel has a room temperature tensile strength of at least 420 N/mm and a transition temperature across the rolling direction of at least -120°C for a notch impact toughness of 51 J/cm<2>, as well as a notch impact toughness of at least 280 J/cm<2 > at room temperature.
Inneholder stålet 0,2 - 0,4% kobber, er rissbestan-digheten i nærvær av hydrogensulfidspor speielt høy. Dette har så langt en betydelig betydning da flytendegjorte gasser hyppig inneholder spor av hydrogensulfid som ved samtidig nærvær av vann virker korroderende og som spesielt fører til hydrogeninduserte sprekker. If the steel contains 0.2 - 0.4% copper, the corrosion resistance in the presence of traces of hydrogen sulphide is very high. This has so far been of considerable importance as liquefied gases frequently contain traces of hydrogen sulphide which, in the simultaneous presence of water, has a corrosive effect and which in particular leads to hydrogen-induced cracks.
Det lave karboninnhold i stålet betinger på den ene side en god sveisbarhet og fremmer på den annen side skårslagseigheten. Tilsammen finner de utmerkede egen-skaper for det foreslåtte stål sin forklaring i den synergistiske sammenvirkning av nikkel, niob og mangan. The low carbon content in the steel conditions, on the one hand, good weldability and, on the other hand, promotes chipping resistance. Together, the excellent properties of the proposed steel can be explained in the synergistic interaction of nickel, niobium and manganese.
Stålet blir fortrinnsvis normalglødet inntil kjerne-temperaturen ligger 30-50°C over AC3~punktet og deretter anløpes 2-4 minutter pr. 2 mm materialtykkelse ved 550 - 650°C, spesielt ved 630°C, for å innstille koldseigheten. The steel is preferably normally annealed until the core temperature is 30-50°C above the AC3~ point and then tempered for 2-4 minutes per 2 mm material thickness at 550 - 650°C, especially at 630°C, to set the cold toughness.
Oppfinnelsen skal nedenfor forklares nærmere under hen-visning til de i tegningene viste diagrammer og på grunnlag av utførelseseksempler. The invention will be explained in more detail below with reference to the diagrams shown in the drawings and on the basis of exemplary embodiments.
I tegningene viser: The drawings show:
Fig. 1 avhengigheten for romtemperatur-skårslagseigheten med hensyn til nikkelinnholdet og typen varmebehandling aK<H>(+20°C) . Fig. 2 avhengigheten for overgangstemperturen med hensyn til nikkelinnholdet og varmebehandling aK=51 J/cm<2 >Fig. 3 avhengigheten for skårslagseigheten og formendringsbrudd av prøvetemperaturen for et innenfor oppfinnelsen liggende stål samt for kjente stål. Fig.4 innholdet av oppløst hydrogen i avhengighet av kobberinnholdet etter en 96-timers neddypping i et med hydrogensulfid mettet sjøvann, og Fig. 5 lengden av de hydrogeninduserte riss i avhengighet av hydrogeninnholdet. Fig. 1 the dependence of the room temperature shear strength with respect to the nickel content and the type of heat treatment aK<H>(+20°C) . Fig. 2 the dependence of the transition temperature with respect to the nickel content and heat treatment aK=51 J/cm<2 >Fig. 3 the dependence of the shear strength and deformation fracture on the test temperature for a steel within the scope of the invention as well as for known steels. Fig.4 the content of dissolved hydrogen as a function of the copper content after a 96-hour immersion in seawater saturated with hydrogen sulphide, and Fig. 5 the length of the hydrogen-induced cracks as a function of the hydrogen content.
Forsøkene som ligger til grunn for diagrammene i fig.l og 2 ble gjennomført på stålene 1 - 5 i den følgende tabell. Av de angitte stål ligger stålene 2 og 3 innenfor oppfinnelsen. Prøver av forsøksstål ble underkastet de varmebetingelser som fremgår av diagrammene og undersøkt på skårslagseighet og koldseighet. Resultatene ser man fra diagrammene i fig. 1 og 2 og disse viser at både skårslagseigheten ved romtemperatur og også overgangs-temperaturen i området fra 0,5 - 1,5% nikkel gjennomløper et optimum uavhengig av den gjennomførte varmebehandling uten at det er nødvendig med spesielle forholdsregler. Dette er så langt overraskende fordi man etter vanlig oppfatning må regne med en forringelse av kold- og skårslagseigheten ved avtagende nikkelinnhold hvis man ikke tar spesielle forholdsregler slik som en kontrollert varmvalsing for å innstille koldseigheten. The experiments that form the basis of the diagrams in fig.1 and 2 were carried out on steels 1 - 5 in the following table. Of the specified steels, steels 2 and 3 are within the scope of the invention. Samples of test steel were subjected to the heating conditions shown in the diagrams and examined for impact toughness and cold toughness. The results can be seen from the diagrams in fig. 1 and 2 and these show that both the shear strength at room temperature and also the transition temperature in the range from 0.5 - 1.5% nickel run through an optimum regardless of the heat treatment carried out without the need for special precautions. This is so far surprising because, according to common opinion, one must expect a deterioration of the cold and chipping toughness with decreasing nickel content if one does not take special precautions such as a controlled hot rolling to set the cold toughness.
Fra diagrammene i fig. 3 ser man overlegenheten for stålet som anvendes ifølge oppfinnelsen sammenlignet med vanlige normstål hvorved man må passe på at det ved stål ifølge oppfinnelsen dreier seg om tverrprøver og i de andre tilfeller med ett unntak om langsprøver. From the diagrams in fig. 3 shows the superiority of the steel used according to the invention compared to ordinary standard steel, whereby care must be taken that with steel according to the invention it concerns transverse tests and in the other cases, with one exception, longitudinal tests.
De undersøkte stål hadde i tillegg hver gang ved romtemperatur en strekkgrense på minst 420 N/mm og en skårslagseighet på minst 280 J/cm<2>. In addition, the examined steels each time at room temperature had a tensile strength of at least 420 N/mm and a shear strength of at least 280 J/cm<2>.
Videre viser diagrammene i fig.4 og 5 at rissøm-fintligheten i nærvær av hydrogensulfid ved kobberinnhold over ca. 0,02% er spesielt liten slik at det foreslåtte stål spesielt egner seg til transport og lagring også av forurenset flytende gass. Den høye rissbestandighet forklares ved at det i drift under innflytelse av hydrogensulfid og vann dannes en svak syre. De derved oppståtte hydrogenioner vandrer inn i materialet og skilles ut molekylært ved korngrensene. Dette resulterer ved vanlige stål i trykk som fører til rissdannelse. Ved de stål som skal anvendes ifølge oppfinnelsen oppløses imidlertid en del av kobberet i syren og de derved oppstående ioner vandrer ved ionebytting til materialoverflaten og danner der et molekylært beskyttelsesjikt av kobber. Dette kobbersjikt virker som sperresjikt mot en ytterligere inntrengning av hydrogen og forklarer den høye hydrogenbestandighet for stålet som skal anvendes ifølge oppfinnelsen og som fremgår av fig.4. Furthermore, the diagrams in fig.4 and 5 show that the rice seam sensitivity in the presence of hydrogen sulphide at a copper content above approx. 0.02% is particularly small so that the proposed steel is particularly suitable for the transport and storage also of contaminated liquefied gas. The high crack resistance is explained by the fact that a weak acid is formed during operation under the influence of hydrogen sulphide and water. The resulting hydrogen ions migrate into the material and are separated molecularly at the grain boundaries. With ordinary steel, this results in pressure that leads to the formation of cracks. However, with the steels to be used according to the invention, part of the copper dissolves in the acid and the resulting ions migrate by ion exchange to the material surface and form a molecular protective layer of copper there. This copper layer acts as a barrier layer against a further penetration of hydrogen and explains the high hydrogen resistance of the steel to be used according to the invention and which appears in fig.4.
Claims (3)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE2847506A DE2847506C2 (en) | 1978-11-02 | 1978-11-02 | Use of a low-temperature manganese-nickel fine-grain structural steel |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO793516L NO793516L (en) | 1980-05-05 |
| NO151506B true NO151506B (en) | 1985-01-07 |
| NO151506C NO151506C (en) | 1985-04-24 |
Family
ID=6053669
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO793516A NO151506C (en) | 1978-11-02 | 1979-11-01 | APPLICATION OF A MANGANE-NICKEL BUILDING STEEL WITH A FINE CORN STRUCTURE FOR CRYOGENIC PURPOSES |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP0010755B2 (en) |
| AT (1) | ATE4228T1 (en) |
| CA (1) | CA1149647A (en) |
| DE (1) | DE2847506C2 (en) |
| NO (1) | NO151506C (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE3663263D1 (en) * | 1986-09-25 | 1989-06-15 | Mannesmann Ag | Process for the production of tubes for use at temperatures up to minus 40 degrees celsius |
| HU205393B (en) * | 1988-06-22 | 1992-04-28 | Gyoergy Vizi | Process for producing corner element of steel container from hot rolled steel plate |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB974028A (en) * | 1963-02-13 | 1964-11-04 | South Durham Steel & Iron Comp | Improvements in and relating to low alloy steels |
| DE1758507B1 (en) * | 1968-06-15 | 1970-12-10 | Thyssen Roehrenwerke Ag | Use of high-strength manganese-alloyed fine-grain structural steel as a material for welded objects with good low-temperature properties |
| US3619302A (en) * | 1968-11-18 | 1971-11-09 | Yawata Iron & Steel Co | Method of heat-treating low temperature tough steel |
| DE2039910B2 (en) * | 1970-08-11 | 1973-08-02 | Nippon Steel Corp , Tokio | HEAT TREATMENT PROCESS FOR A STEEL |
| JPS5215523B1 (en) * | 1970-11-18 | 1977-04-30 | ||
| CA966702A (en) * | 1972-05-12 | 1975-04-29 | Reginald N. Shaughnessy | Method for the production of high strength notch tough steel |
| US3834949A (en) * | 1973-02-14 | 1974-09-10 | Inland Steel Co | Hot rolled flat steel article for cryogenic service and method for producing same |
| JPS5411774B2 (en) * | 1973-02-15 | 1979-05-17 | ||
| GB1436846A (en) * | 1973-03-16 | 1976-05-26 | Int Nickel Ltd | Steels |
| DE2461087A1 (en) * | 1973-12-28 | 1975-07-03 | Sumitomo Metal Ind | HYDROGEN RESISTANT STEEL FOR PIPING PIPES |
| US4138278A (en) * | 1976-08-27 | 1979-02-06 | Nippon Steel Corporation | Method for producing a steel sheet having remarkably excellent toughness at low temperatures |
-
1978
- 1978-11-02 DE DE2847506A patent/DE2847506C2/en not_active Expired
-
1979
- 1979-10-31 EP EP79104222A patent/EP0010755B2/en not_active Expired
- 1979-10-31 AT AT79104222T patent/ATE4228T1/en not_active IP Right Cessation
- 1979-11-01 NO NO793516A patent/NO151506C/en unknown
- 1979-11-02 CA CA000339072A patent/CA1149647A/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| EP0010755B2 (en) | 1986-08-06 |
| EP0010755A1 (en) | 1980-05-14 |
| EP0010755B1 (en) | 1983-07-20 |
| CA1149647A (en) | 1983-07-12 |
| DE2847506A1 (en) | 1980-05-14 |
| DE2847506C2 (en) | 1986-04-17 |
| NO151506C (en) | 1985-04-24 |
| NO793516L (en) | 1980-05-05 |
| ATE4228T1 (en) | 1983-08-15 |
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