SE441455B - STALL OF AUSTENITIC TYPE - Google Patents
STALL OF AUSTENITIC TYPEInfo
- Publication number
- SE441455B SE441455B SE8305795A SE8305795A SE441455B SE 441455 B SE441455 B SE 441455B SE 8305795 A SE8305795 A SE 8305795A SE 8305795 A SE8305795 A SE 8305795A SE 441455 B SE441455 B SE 441455B
- Authority
- SE
- Sweden
- Prior art keywords
- steel
- steel according
- max
- corrosion
- steels
- Prior art date
Links
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 74
- 239000010959 steel Substances 0.000 claims abstract description 74
- 238000005260 corrosion Methods 0.000 claims abstract description 29
- 230000007797 corrosion Effects 0.000 claims abstract description 29
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 11
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 239000000126 substance Substances 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims description 9
- 239000000463 material Substances 0.000 abstract description 10
- 239000011651 chromium Substances 0.000 description 17
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 16
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 15
- 239000011572 manganese Substances 0.000 description 12
- 238000012360 testing method Methods 0.000 description 10
- 229910052804 chromium Inorganic materials 0.000 description 8
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 229910052759 nickel Inorganic materials 0.000 description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 239000010941 cobalt Substances 0.000 description 3
- 229910017052 cobalt Inorganic materials 0.000 description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 238000011835 investigation Methods 0.000 description 3
- 239000011733 molybdenum Substances 0.000 description 3
- 229910001220 stainless steel Inorganic materials 0.000 description 3
- 230000004580 weight loss Effects 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 241000196324 Embryophyta Species 0.000 description 2
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- OSVXSBDYLRYLIG-UHFFFAOYSA-N dioxidochlorine(.) Chemical compound O=Cl=O OSVXSBDYLRYLIG-UHFFFAOYSA-N 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000004076 pulp bleaching Methods 0.000 description 2
- 239000013535 sea water Substances 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 1
- 239000004155 Chlorine dioxide Substances 0.000 description 1
- 229910000531 Co alloy Inorganic materials 0.000 description 1
- 229910001341 Crude steel Inorganic materials 0.000 description 1
- 229910015400 FeC13 Inorganic materials 0.000 description 1
- 206010061217 Infestation Diseases 0.000 description 1
- 229910021578 Iron(III) chloride Inorganic materials 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 150000007513 acids Chemical class 0.000 description 1
- 238000007792 addition Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 239000011575 calcium Substances 0.000 description 1
- 239000000460 chlorine Substances 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- 235000019398 chlorine dioxide Nutrition 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 239000003344 environmental pollutant Substances 0.000 description 1
- 239000000706 filtrate Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- RBTARNINKXHZNM-UHFFFAOYSA-K iron trichloride Chemical compound Cl[Fe](Cl)Cl RBTARNINKXHZNM-UHFFFAOYSA-K 0.000 description 1
- 230000002427 irreversible effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 231100000719 pollutant Toxicity 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 230000002285 radioactive effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 125000006850 spacer group Chemical group 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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)
- Golf Clubs (AREA)
- Dowels (AREA)
- Powder Metallurgy (AREA)
Abstract
Description
15 20 25 30 35 8305795-0 ELI-stĂ„l, vilka ocksĂ„ har mycket god resistans mot spalt- och punktkorrosion i havsvatten och liknande miljöer, förutsatt att stĂ„len innehĂ„ller minst 25 Z Cr och minst 3.5 Z Mo. En allvarlig begrĂ€nsning med dessa material Ă€r att de inte tillverkas i tjockare dimensioner Ă€n cirka 3 mm. Ăr materialet tjockare blir det sprött och osvetsbart. 15 20 25 30 35 8305795-0 ELI steels, which also have very good resistance to crack and point corrosion in seawater and similar environments, provided that the steels contain at least 25 Z Cr and at least 3.5 Z Mo. A serious limitation with these materials is that they are not manufactured in dimensions thicker than about 3 mm. If the material is thicker, it becomes brittle and irreversible.
Det Àr Àven kÀnt att i austenitiska rostfria stÄl helt eller delvid ersÀtta nickel med mangan i syfte att nedbringa materialkostnaderna.It is also known to completely or partially replace nickel with manganese in austenitic stainless steels in order to reduce material costs.
'Det finns i litteraturen Àven uppgifter om att mangan kan öka kromets resistensbidrag jÀmfört med icke mangansubstituerade stÄl.'There is also information in the literature that manganese can increase the resistance contribution of chromium compared to non-manganese-substituted steels.
KÀnda mangansubstituerade stÄl har emellertid vÀsentligt lÀgre korrosionsresistens Àn ovan nÀmnda austenitiska och ferritiska stÄltyper och utgör inte nÄgot anvÀndbart substitut för dessa i de _miljöer för vilka föreliggande stÄl Àr avsett.However, known manganese-substituted steels have significantly lower corrosion resistance than the above-mentioned austenitic and ferritic steels and do not constitute a useful substitute for these in the environments for which the present steels are intended.
För att belysa teknikens nuvarande stÄndpunkt hÀnvisas till föl- jande litteraturreferenser. I de jÀmförande undersökningar som skall redovisas i det följande kommer att hÀnvisas till uppgifter hÀmtade ur dessa referenser.To illustrate the current state of the art, reference is made to the following literature references. In the comparative studies to be reported in the following, reference will be made to data taken from these references.
Litteraturreferenser: (1) Kohl H, Rabensteiner G, Hoehörtler G, VEW: Stainless Steels with High Strength and High Corrosion Resi- stance. Alloys for the eighties. (2) Glazkova S A, Shapiro M B: The Resistance of a CrNi- Steel Type 18-12-Mo to Localized Corrosion in Chloride Solutions. Zashch. Metallov lĂ„ (3), May-June 1979, p 320-324. (3) Bock H E: Korrosionsverhalten eines seewasserbestĂ€n- digen, nichtmagnetisierbaren CrNiMo-Stahles hoher Festigkeit. Arch. EisenhĂŒttenwes. §§_(1973)877. 10 15 20 25 30 8305795-0 (4) Brigham R J, Tozer E W: Localized Corrosion Resistance of Mn-SubstĂtuted Austenitic Stainless Steelsz Effect of Mo and Cr. Corr. §Ä(1976)274. (5) Letcher B F: An Austenitic Stainless Steel of Improved Strength and Corrosion Resistance (Firth Brown Rex 734). Report from Firth Brown Ltd.Literature references: (1) Kohl H, Rabensteiner G, Hoehörtler G, VEW: Stainless Steels with High Strength and High Corrosion Resistance. Alloys for the eighties. (2) Glazkova S A, Shapiro M B: The Resistance of a CrNi- Steel Type 18-12-Mo to Localized Corrosion in Chloride Solutions. Zashch. Metallov lĂ„ (3), May-June 1979, p 320-324. (3) Bock H E: Corrosion behavior of a seawater-resistant, non-magnetizable CrNiMo steel high strength. Arch. EisenhĂŒttenwes. §§_ (1973) 877. 10 15 20 25 30 8305795-0 (4) Brigham R J, Tozer E W: Localized Corrosion Resistance of Mn-Substituted Austenitic Stainless Steelsz Effect of Mo and Cr. Corr. §à (1976) 274. (5) Letcher B F: An Austenitic Stainless Steel of Improved Strength and Corrosion Resistance (Firth Brown Rex 734). Report from Firth Brown Ltd.
REDOGĂRELSE FĂR UPPFINNINGEN Ett primĂ€rt Ă€ndamĂ„l med uppfinningen Ă€r att erbjuda ett stĂ„l som, utan att det innehĂ„ller större utan fastmer lĂ€gre-halt av dyrbara legeringsĂ€mnen Ă€n jĂ€mförbara konventionella austenitiska stĂ„l, upp- visar en erforderlig kombination av egenskaper som krĂ€vs vid anvĂ€nd- ning för svetsade konstruktioner i starkt korrosiva miljöer. I syn- nerhet Ă€r ett syfte att erbjuda ett stĂ„l med extremt bra resistens mot punkt- och spaltkorrosion. FöretrĂ€desvĂs Ă€r ett syfte att erbjuda ett stĂ„] med mycket god resistens Ă€ven i andra nggresĂvn miljöer, sĂ„som HN03. Typiska anvĂ€ndningsomrĂ„den anges Ă€ven i in- gressen.DISCLOSURE OF THE INVENTION A primary object of the invention is to provide a steel which, without containing greater but more solid lower content of expensive alloying elements than comparable conventional austenitic steels, exhibits the required combination of properties required when used for welded constructions in highly corrosive environments. In particular, one aim is to offer a steel with extremely good resistance to point and crevice corrosion. Preferably, the aim is to offer a stand] with very good resistance even in other nggresĂvn environments, such as HN03. Typical areas of use are also stated in the preamble.
Vidare Àr ett syfte att Ästadkomma ett stÄl som Àr mycket bra svetsbart med lÄg energitillförsel utan att nÄgon av korrosions- egenskaperna i svetsen eller den vÀrmepÄverkade zonen pÄ nÄgot avgörande sÀtt försÀmras.Furthermore, an object is to provide a steel which is very well weldable with a low energy supply without any of the corrosion properties in the weld or the heat-affected zone being significantly degraded.
FöretrÀdesvis Àr Àven ett syfte att erbjuda ett stÄl med högre hÄllfasthetsvÀrden Àn konventionella austenitiska, molybdenlegerade stÄl.Preferably, it is also an object to offer a steel with higher strength values than conventional austenitic, molybdenum alloy steels.
Dessa och andra syften kan uppnĂ„s dĂ€rigenom att stĂ„let har följande kemiska sammansĂ€ttning i viktsprocent: 10 15 20 25 30 35 8505795-0 0.03 C 0.1-2 Si 8-15 Mn' 15-30 Cr 12-20 Ni 3.5-1go M0 .35~.55 N rest vĂ€sentligen endast jĂ€rn, föroreningar och acces- Max. soriska element i normala halter. ĂnskvĂ€rt Ă€r att kolhalten Ă€r sĂ„ lĂ„g som möjligt. Normalt Ă€r kol- halten dĂ€rför max. 0.02 Z och helst max 0.015 Z. Manganets och kvĂ€vets roller i stĂ„let Ă€r komplexa. Manganet verkar dels som austenitbildare, dels löser det kvĂ€ve i stĂ„let. Vissa indikationer pekar Ă€ven pĂ„ att manganet i denna legering direkt pĂ„verkar korro- sionsegenskaperna i gynnsam riktning. KvĂ€vet verkar ocksĂ„ som auste- nitbildare oĂh bidrar dessutom till korrosionsbestĂ€ndigheten. För att skapa helt austenitisk struktur tillsĂ€tts vid_sidan av mangan och kvĂ€ve ocksĂ„ en erforderlig mĂ€ngd nickel. I stĂ„let enligt upp- finningen uppnĂ„s Ă€ven en synergistĂsk effekt mellan molybden och kvĂ€ve med avseende pĂ„ motstĂ„ndet mot spaltkorrosion och punktfrĂ€t- lningl Detta kan ocksĂ„ uttryckas sĂ„, att kvĂ€ve förstĂ€rker molybdenets gynnsamma effekt. Krom utgör ett grundlĂ€ggande element för mot- stĂ„ndet mot allmĂ€nkorrosĂon och förstĂ€rker Ă€ven skyddet mot andra korrosionstyper.These and other objects can be achieved by the steel having the following chemical composition in weight percent: 10 15 20 25 30 35 8505795-0 0.03 C 0.1-2 Si 8-15 Mn '15-30 Cr 12-20 Ni 3.5-1go M0 .35 ~ .55 N traveled essentially only iron, impurities and acces- Max. Sorian elements at normal levels. It is desirable that the carbon content is as low as possible. Normally, the carbon content is therefore max. 0.02 Z and preferably max 0.015 Z. The roles of manganese and nitrogen in the steel are complex. The manganese acts partly as an austenite former, and partly it dissolves nitrogen in the steel. Some indications also indicate that the manganese in this alloy directly affects the corrosion properties in a favorable direction. Nitrogen also acts as an austenite former and also contributes to corrosion resistance. To create a completely austenitic structure, a required amount of nickel is also added to the manganese and nitrogen. In the steel according to the invention, a synergistic effect is also achieved between molybdenum and nitrogen with respect to the resistance to crevice corrosion and spot corrosion. This can also be expressed in such a way that nitrogen enhances the beneficial effect of molybdenum. Chromium is a fundamental element in resistance to general corrosion and also strengthens protection against other types of corrosion.
FöretrÀdesvis Àr ett kÀnnetecken pÄ stÄlet att det sÄ kallade PRE- vÀrdet (= Z Cr + 3.3 x Z Mb + 16 x Z N) Àr minst 41, och före- trÀdesvis frÄn 41-45.Preferably, a characteristic of the steel is that the so-called PRE value (= Z Cr + 3.3 x Z Mb + 16 x Z N) is at least 41, and preferably from 41-45.
LÀmpligen innehÄller stÄlet 14-17 Ni, 9-11 Mn, 18-23 Cr, 4-8 Mo, .38 - .48 N och max. .015 C.Suitably the steel contains 14-17 Ni, 9-11 Mn, 18-23 Cr, 4-8 Mo, .38 - .48 N and max. .015 C.
FöretrÀdesvis Àr ett kÀnnetecken pÄ stÄlet enligt uppfinningen ocksÄ att kromekvivalenten (enligt Schaeffler) Àr minst 24, och att nickelekvivalenten Àr minst 25, samtidigt som.förhÄllandet mellan 10 15 20 25 30 35 ssos79s-0 kromekvivalenten och nickelekvivalenten Àr högst 0.9, företrÀdesvis högst 0.8.Preferably, a characteristic of the steel according to the invention is also that the chromium equivalent (according to Schaeffler) is at least 24, and that the nickel equivalent is at least 25, while the ratio between the ssos79s-0 chromium equivalent and the nickel equivalent is at most 0.9, preferably at most 0.8 .
En föredragen samansÀttning pÄ stÄlet enligt uppfinningen Àr följande: Max. 0.015 C 0.2-1.5 Si 9-11 Mn max. 0.008 S, företrÀdesvis max. 0.005 S 19-22 Cr 14-17 Ni 4-5 Mo 0.38-0.48 N och rest vÀsentligen endast jÀrn och oundvikliga föroreningar.A preferred composition of the steel according to the invention is the following: Max. 0.015 C 0.2-1.5 Si 9-11 Mn max. 0.008 S, preferably max. 0.005 S 19-22 Cr 14-17 Ni 4-5 Mo 0.38-0.48 N and left essentially only iron and unavoidable impurities.
Förutom nÀmnda element kan koppar eventuellt förekomma upp till max. 3 Z. I vilken mÄn koppar inverkar pÄ det uppfinningsenliga stÄlets egenskaper har dock ej studerats. Eventuellt kan det för- bÀttra korrosionsresistensen i starka syror. Enligt den föredragna utföringsformen bör kopparhalten emellertid begrÀnsas till max. 0.5 Z.In addition to the mentioned elements, copper may possibly occur up to max. 3 Z. However, the extent to which copper affects the properties of the steel according to the invention has not been studied. It may improve the corrosion resistance of strong acids. According to the preferred embodiment, however, the copper content should be limited to max. 0.5 Z.
Koppar i halter lÀgre Àn 0.5 Z ingÄr i begreppet "accessoriska ele- ment", varmed förstÄs sÄdana element som kan förekomma i omsmÀlt- ningsskrot eller som finns kvar som rester av processmetallurgiska tillsatser. Bland den förra typen element kan nÀmnas kobolt. Detta element Àr dyrbart. Medvetna tillsatser av detta element bör dÀrför undvikas. Kobolt har Àven den negativa effekten att det blir radio- aktivt vid bestrÄlning, vilket gör koboltlegerat material oanvÀnd- bart för delar i kÀrnkraftverk som utsÀtts för bestrÄlning. Halten kobolt bör dÀrför begrÀnsas till max. 0.5 Z. Bland rester av ele- ment som tillsÀtts av processmetallurgiska skÀl kan nÀmnas alu- minium och kalcium. Niob, vanadin och titan bör inte förekomma i mer Àn föroreningshalter. 830579543 10 15 20 Ytterligare kÀnnetecken pÄ samt fördelar med stÄlet enligt upp- finningen komer att framgÄ av följande redogörelse av utförda försök och undersökningar.Copper in concentrations lower than 0.5 Z is included in the term "accessory elements", by which is meant those elements which may be present in remelting scrap or which remain as residues of process metallurgical additives. Among the former type of elements can be mentioned cobalt. This element is expensive. Deliberate additions of this element should therefore be avoided. Cobalt also has the negative effect of becoming radioactive during irradiation, which makes cobalt alloy material unusable for parts of nuclear power plants that are exposed to radiation. The cobalt content should therefore be limited to max. 0.5 Z. Aluminum and calcium can be mentioned among residues of elements that are added for process metallurgical reasons. Niobium, vanadium and titanium should not be present in more than pollutant levels. 830579543 10 15 20 Additional characteristics and advantages of the steel according to the invention will appear from the following account of experiments and investigations carried out.
BESKRIVNINĂ AV UTFĂRDA FĂRSĂK OCH UNDERSĂKNINGAR SamansĂ€ttningen av alla tillverkade och undersökta stĂ„lprover Ă„terfinns i Tabell 1, grupp 1. StĂ„l nr 1-15 tillverkades sĂ„som 2 kg:s smĂ€lter. Av dessa undersöktes de med helaustenitisk struktur (efter utvalsning och slĂ€ckglödgning) för vidare undersökning, frĂ€mst av korrosionsegenskaperna. För utvĂ€rdering av inledande undersökningar framstĂ€lldes dĂ€refter en 50 kgzs smĂ€lta, stĂ„l nr 16.DESCRIPTION OF EXAMINATIONS AND EXAMINATIONS The composition of all manufactured and examined steel samples is found in Table 1, group 1. Steel no. 1-15 was manufactured as 2 kg melts. Of these, they were examined with a fully austenitic structure (after rolling and extinguishing annealing) for further investigation, mainly by the corrosion properties. For the evaluation of preliminary investigations, a 50 kgz melt, steel no. 16, was then prepared.
I Tabell 1, grupp 2 och grupp 3 Äterfinns kommersiella stÄl som provats, respektive övriga studerade stÄl enligt litteratur, se litteraturförteckningen pÄ sid. 2-3.In Table 1, group 2 and group 3, there are commercial steels that have been tested, and other studied steels according to literature, see the bibliography on p. 2-3.
B-chargerna (stĂ„l nr 1-15) smiddes till 30 mmlĂŒ och valsades till band med 3 mm tjocklek, varefter banden slĂ€ekglödgades i 1100°C/1h/ H 0. Inga anmĂ€rkningsvĂ€rda bearbetningsproblem pĂ„ grund av dĂ„lig 2 varmduktilitet observerades. 8305795-0 D-chargerna (stĂ„l nr 1-15) smiddes till 30 nmlwb och valsades till band med 3 mm tjocklek, varefter banden slĂ€ekglödgades i 1100°C/1h/ H20. Inga anmĂ€rkningsvĂ€rda bearbetnĂngsproblem pĂ„ grund av dĂ„lig varmduktĂlĂtet Qhserverades.The B-charges (steel no. 1-15) were forged to 30 mmlĂŒ and rolled into strips with a thickness of 3 mm, after which the strips were annealed at 1100 ° C / 1h / H 0. No remarkable processing problems due to poor 2 hot ductility were observed. 8305795-0 The D-charges (steel no. 1-15) were forged to 30 nmlwb and rolled into strips with a thickness of 3 mm, after which the strips were annealed at 1100 ° C / 1h / H 2 O. No significant processing problems due to poor hot ductility were served.
TABELL '1 Kemisk sammansĂ€ttning (vikt- Z, rest Fe och accessorĂska element) hos tillverkade och/eller studerade StĂ„l.TABLE '1 Chemical composition (weight Z, residual Fe and accessory elements) of manufactured and / or studied steels.
Grupp 1: 2- och 50 kgzs prover StĂ„l Charge C Si Mn P S Cr Ni Mo N Cu Ăvr PREĂ) nr _ _ vĂ€rde 1 B 1142 .O11 .44 4.8 .006 .008 21.9 12.7 3.5 .22 37.0 2 B 1143 .012 .48 4.8 .006 .008 21.9 12.7 2.6 .22 34.0 3 P 1144 .010 .48 9.8 .006 .009 20.0 15.2 3.0 '.22 33.4 4 B 1145 .O11 .47 9.8 .006 .G09 20.0 15.2 4.6 .21 38.56 5 B 1146 .012 .43 7.7 .007 .G09 19.9 10.5 4.5 .44 41.75 6 B 1147 .014 .45 9.6 .009 .G07 19.8 15.1 4.5 .43 41.5 7 B 1401 .018 .SO 1.43 .005 .010 25.2 13.7 1.03 .39 .02 34.8 8 B 1402 .017 .43 1.59 .006 .010 25.9 15.1 2.49 .30 .97 38.9 9 B 1404 .017 .42 1.52 .004 .010 25.1 15.1 1.03 .34 .02 33.9 10 B 1411 .019 1.26 1.55 .006 .G10 25.1 13.4 1.04 .24 .02 32.4 11 B 1412 .020 1.27 1.58 .006 .010 24.9 15.1 2.45 .28 .89 37.5 12 B 1413 .020 1.24 1.60 .006 .010 25.0 16.1 3.2 .26 .97 39.7 13 B 1414 .018 1.27 1.58 .007 .G10 25.0 16.9 3.9 .23 .95 41.5 14 B 1419 .017 .35 4.66 .005 .010 21.1 15.7 5.5 .38 .95 45.3 .022 1.20 2.30 .006 .G10 24.2 5.6 2.96 .30 1.08 38.8 15 B 1420 .018 .36 1.43 .004 .006 24.1 6.6 2.97 .1S .47 36.4 16 Q 8072 .015 .68 10.3 .O11 .007 20.3 15.2 4.5 .4B 42.8 *)PRE-vĂ€rde: Z Cr + 3.3 x (Z Mo) + 16 x (Z N) 8305795-0 TABELL 1 (forts .) Grupp 2: ĂommersĂella stĂ„l StĂ„l Kvalitet C Si Mn P S Cr Ni _. [V10 . N Cu Ăvr PREĂŻ) m: vĂ€rde 17 A181 216 .047 .47 8.5 .025 .003 19.7 6.4 2.7 .38 .12 34.7 18 Nicronic 40 .018 .68 9.01 .024 .001 19.93 7.12 .18 .28 25.0 19 " 50 .045 .47 4.81 .025 .012 21.0813.702.28 .28 N6,v33.1 20 NU ss_904L .018 .65 1.67 .027 .004 19.4 24.6 4.4 1.43 33.9 21 nu ss 44LN .022 _39 1.71 .026 .010 25.1 6.3 1.56 .14 ' .17 ;32.5 22 ĂȘS§?2gfs .013 _42 .62 .031 .005 20.3 17.75.8 _21. .69 42.8 23 AIS: 316L .014 .43 1.58 .032 .004 18.0 .12.72.64 .23 26.7 24 Nu Momrw .012 .31 .43 .031 .006 325.3 4.13.8 1 .37 37.8 25 ĂȘS§?2gES .020 .52 .48 .024 .001 20.1 17.75 9 .19 06 42.6 ErĂP2.Ă«;_Ă«23Âżae.§E2ħwĂŠ83s„ƥ92F2li8s.lisĂ«sxaĂ«ar 1 max Ă„ 26 A 963,ref 1 .03 17.0 16.06,3 .15 1.6 40.2 27 A 905, " 1 .04 5.8 25.5 3.7z.3 .37 39.0 28 A 905* " 1 .04 '.70 4.5 26.0 , 7.52.0 .35 38.2 -weld 29 E81. ref. 2 .02 _36 4.18 .011 .016 18.90ïŹ2.105.0 ĆĄ.40 41.8 30 â " 3 .03 8.0 20 !14 73.1 ĆĄ.40 .14 kb §36.6 31 " " 4 .04 .5 8.8 .019 .016 20 h0.4 4.221.5 .01 Ă41.9 32 " " 4 .03 .63 5.88 .013 .011 22.1 §2.708.90:.41 .41.5 33 Yus 170 .031 .82 1.59 24.7 h3.45 .93§.36 . 33.5 ref. 5 i 34 REX 734, _05 .25 4.0 22.0 ĆĄ9.0 2.6 §.40 :M6 37.0 ref. 5 ĂŻ ' *)PRE-vĂ€rde; 2 cr + 3.3 X z M6 + 16 X z N 8305795-0 Eftersom syftet med uppfinningen Ă€r att utveckla ett.mangan- substituerat stĂ„l, gjĂžrdes strukturkontroll endast pĂ„ stĂ„len nr 1-6. Dessa undersökningar visade att endast stĂ„l nr 3 och nr 6 hade helaustenitisk struktur. StĂ„l nr 1, 4 och 5 innehöll U-fas, medan stĂ„l nr 2 innehöll 6-ferrit. De helaustenitiska stĂ„len 3 och 5 6 testades i en första omgĂ„ng med avseende pĂ„ lokal korrosions~ hĂ€rdighet och hĂ„llfasthet. Tabell 2 visar hĂ„llfasthetsvĂ€rden för de tvĂ„ provade stĂ„len 3 och 6 samt ett antal kommersiella och/eller i litteraturen redovisade kvĂ€velegerade stĂ„l. 10 TABELL 2 HĂ„llfasthetsvĂ€rden vid RT samt Cr- och Ni-ekvivalenter för ett antal representativa stĂ„l StĂ„l StrĂ€ckgrĂ€ns BrottgrĂ€ns FörlĂ€ngning HĂ„rdhet Cr-ekv1) Ni-ekvz) Cr/Ni-ekv nr Rp0_2 Nmm_2 Em Nmm_2 A,50 Z HV 30 enligt Schaeffler 17 488 837 48.2 f 261 23.1 23.5 .98 18 502 807 43.1 21.11 20.6 1.02 19 609 895 38.1 24.0 25.7 .93 3 309 671 49.4 239 23.7 27 .88 6 390 827 51.4 287 25.8 33.22 .78 20 240 600 45 155 24.8 26 .95 21 565 778 33.0 26.86 12 2.24 22 320 700 50 175 26.7 24.6 1.08 23 21.10 18.9 1.12 26 300 600 30 23.5 22 1.07 27 590 750 30 28.5 18.9 1.51 33 432 785 49.7 26.05 26 1.0 1)Cr-ekv: Z Cr + % Mo + 1.5 x 2 Si + 0.5 x 2 Nb 2) Ni-ekv: Z Ni + 0.5 x (Z Mn + Z Cu + Z Co) + 30 x (Z C + Z N) 1 10 15 20 25 30 35 8305795-O I det följande skall till en början redovisas resultaten frĂ„n jĂ€m- förande korrosionsprovning av dels stĂ„l nr 3 och 6; dels de kommer- siella stĂ„len 17-23.Group 1: 2- and 50 kgzs samples Steel Charge C Si Mn PS Cr Ni Mo N Cu Other PREĂ) no _ _ value 1 B 1142 .O11 .44 4.8 .006 .008 21.9 12.7 3.5 .22 37.0 2 B 1143 .012 .48 4.8 .006 .008 21.9 12.7 2.6 .22 34.0 3 P 1144 .010 .48 9.8 .006 .009 20.0 15.2 3.0 '.22 33.4 4 B 1145 .O11 .47 9.8 .006 .G09 20.0 15.2 4.6 .21 38.56 5 B 1146 .012 .43 7.7 .007 .G09 19.9 10.5 4.5 .44 41.75 6 B 1147 .014 .45 9.6 .009 .G07 19.8 15.1 4.5 .43 41.5 7 B 1401 .018 .SO 1.43 .005 .010 25.2 13.7 1.03 .39 .02 34.8 8 B 1402 .017 .43 1.59 .006 .010 25.9 15.1 2.49 .30 .97 38.9 9 B 1404 .017 .42 1.52 .004 .010 25.1 15.1 1.03 .34 .02 33.9 10 B 1411. 019 1.26 1.55 .006 .G10 25.1 13.4 1.04 .24 .02 32.4 11 B 1412 .020 1.27 1.58 .006 .010 24.9 15.1 2.45 .28 .89 37.5 12 B 1413 .020 1.24 1.60 .006 .010 25.0 16.1 3.2 .26 .97 39.7 13 B 1414 .018 1.27 1.58 .007 .G10 25.0 16.9 3.9 .23 .95 41.5 14 B 1419 .017 .35 4.66 .005 .010 21.1 15.7 5.5 .38 .95 45.3 .022 1.20 2.30 .006 .G10 24.2 5.6 2.96 .30 1.08 38.8 15 B 1420 .018 .36 1.43 .004 .006 24.1 6.6 2.97 .1S .47 36.4 16 Q 8072 .015 .68 10.3 .O11 .007 20.3 15.2 4.5 .4B 42.8 *) PRE-value: Z Cr + 3.3 x (Z Mo) + 16 x (ZN) 8305795 -0 TABLE 1 (continued) Group 2: Commercial Steel Steel Quality C Si Mn PS Cr Ni _. [V10. N Cu Other PREĂŻ) m: value 17 A181 216 .047 .47 8.5 .025 .003 19.7 6.4 2.7 .38 .12 34.7 18 Nicronic 40 .018 .68 9.01 .024 .001 19.93 7.12 .18 .28 25.0 19 "50 .045 .47 4.81 .025 .012 21.0813.702.28 .28 N6, v33.1 20 NU ss_904L .018 .65 1.67 .027 .004 19.4 24.6 4.4 1.43 33.9 21 nu ss 44LN .022 _39 1.71 .026 .010 25.1 6.3 1.56 .14 '.17; 32.5 22 ĂȘS§? 2gfs .013 _42 .62 .031 .005 20.3 17.75.8 _21. .69 42.8 23 AIS: 316L .014 .43 1.58 .032 .004 18.0 .12.72.64. 23 26.7 24 Nu Momrw .012 .31 .43 .031 .006 325.3 4.13.8 1 .37 37.8 25 ĂȘS§? 2gES .020 .52 .48 .024 .001 20.1 17.75 9 .19 06 42.6 ErĂP2.Ă«; _Ă«23 ÂżAe.§E2ħwĂŠ83s „ ĆĄ92F2li8s.lisĂ«sxaĂ«ar 1 max Ă„ 26 A 963, ref 1 .03 17.0 16.06,3 .15 1.6 40.2 27 A 905, "1 .04 5.8 25.5 3.7z.3 .37 39.0 28 A 905 * "1 .04 '.70 4.5 26.0, 7.52.0 .35 38.2 -weld 29 E81. Ref. 2 .02 _36 4.18 .011 .016 18.90ïŹ2.105.0 ĆĄ.40 41.8 30â "3 .03 8.0 20! 14 73.1 ĆĄ.40 .14 kb §36.6 31 "" 4 .04 .5 8.8 .019 .016 20 h0.4 4.221.5 .01 Ă41.9 32 "" 4 .03 .63 5.88 .013 .011 22.1 § 2.708.90: .41 .41. 5 33 Yus 170 .031 .82 1.59 24.7 h3.45 .93§.36. 33.5 ref. 5 i 34 REX 734, _05 .25 4.0 22.0 ĆĄ9.0 2.6 §.40: M6 37.0 ref. 5 ĂŻ '*) PRE value; 2 cr + 3.3 X z M6 + 16 X z N 8305795-0 Since the object of the invention is to develop a manganese-substituted steel, structural control was performed only on steels no. 1-6. These studies showed that only steels no. 3 and no. 6 had a fully austenitic structure. Steel Nos. 1, 4 and 5 contained U-phase, while Steel No. 2 contained 6-ferrite. The fully austenitic steels 3 and 56 were tested in a first round for local corrosion resistance and strength. Table 2 shows strength values for the two tested steels 3 and 6 as well as a number of commercial and / or nitrogen alloyed steels reported in the literature. TABLE 2 Strength values at RT and Cr and Ni equivalents for a number of representative steels Steel Tensile strength Fracture limit Elongation Hardness Cr-eq1) Ni-eqvz) Cr / Ni-eq no. Rp0_2 Nmm_2 Em Nmm_2 A, 50 Z HV 30 according to Schaeffler 17 488 837 48.2 f 261 23.1 23.5 .98 18 502 807 43.1 21.11 20.6 1.02 19 609 895 38.1 24.0 25.7 .93 3 309 671 49.4 239 23.7 27 .88 6 390 827 51.4 287 25.8 33.22 .78 20 240 600 45 155 24.8 26. 95 21 565 778 33.0 26.86 12 2.24 22 320 700 50 175 26.7 24.6 1.08 23 21.10 18.9 1.12 26 300 600 30 23.5 22 1.07 27 590 750 30 28.5 18.9 1.51 33 432 785 49.7 26.05 26 1.0 1) Cr-ekv: Z Cr + % Mo + 1.5 x 2 Si + 0.5 x 2 Nb 2) Ni-eq: Z Ni + 0.5 x (Z Mn + Z Cu + Z Co) + 30 x (ZC + ZN) 1 10 15 20 25 30 35 8305795- In the following, the results of comparative corrosion testing of steel nos. 3 and 6 shall be reported at the outset; partly the commercial steels 17-23.
TABELL 3 Resultat av jĂ€mförande korrosĂonsprovning StĂ„l Spaltkorr. Kritisk temperatur i FeC13, UC Angrepp i syntetisk potential skrubberlösning E58 , VikĆĄsförlust nr mV/ CE Punktfr. Spaltkorr. g/m h 3 + es 40 < 23 ' 10 6 > 785 65 45 17 + 25 V I 18 ' - 70 < 23 < 23 10 i 19 + 25 35 ~ < 23 7 22 75 40 _ 0 20 +105 45 < 23 '_ s 21 + 10 :_25 35 < 30 1 7 23 - 30 < 23 < 23 11 1)11.4 z Hzso + 1.17 z Hcl + 1 z cuc12 + 1 z Feel 4 3 SpalrkorrcsĂon §pg}5k2?:P§i2v§R2F2P5Ă€fÂżki Ess StĂ„l nr 6 visade sig genast helt överlĂ€gset de allra flesta rostfria stĂ„l som nĂ„gonsin provats hos sökanden. Medan det bĂ€sta resultatet för jĂ€mförelsematerialen var Esp = + 105 mV, hade stĂ„l nr 6 inte blivit angriper vid Esp = + 785 mV. Försökvt mĂ„ste dĂ„ avbrytas, eftersom klĂ€nmorna i provhĂ„lluren (tillverkade av stĂ„] av kvalitot NU SS 904L) dĂ„ hade korroderat sönder. Detta betyder att stĂ„let torde vara helt bestĂ€ndigt mot havsvatten vid rumstemperatur.TABLE 3 Results of comparative corrosion testing Steel Slotted corr. Critical temperature in FeC13, UC Attack in synthetic potential scrubber solution E58, Weight loss no. MV / CE Point no. Splitcorr. g / mh 3 + es 40 <23 '10 6> 785 65 45 17 + 25 VI 18' - 70 <23 <23 10 i 19 + 25 35 ~ <23 7 22 75 40 _ 0 20 +105 45 <23 ' _ s 21 + 10: _25 35 <30 1 7 23 - 30 <23 <23 11 1) 11.4 z Hzso + 1.17 z Hcl + 1 z cuc12 + 1 z Feel 4 3 SpalrkorrcsĂon §pg} 5k2?: P§i2v§ R2F2P5Ă€fÂżki Ess Steel No. 6 immediately proved to be completely superior to the vast majority of stainless steels ever tested by the applicant. While the best result for the comparison materials was Esp = + 105 mV, steel no. 6 had not been attacked at Esp = + 785 mV. Attempts must then be interrupted, as the clamps in the test retaining watch (made of stand] of the NU SS 904L quality) would then have corroded. This means that the steel should be completely resistant to seawater at room temperature.
StĂ„l nr 3 uppvisade lĂ„ngt ifrĂ„n lika goda r0su]taL som stĂ„l nr 6 och stannade nĂ„got under resultatet för stĂ„l nr 20, trots att krom- och nickelhalterna Ă€r lika höga och molybdenhalten endast 1.5 och kvĂ€vehalten .21 Z lĂ€gre Ă€n hos stĂ„l nr 6. 10 15 20 25 39 8305795-0 11 EfiïŹisĂ« :PeltkefrïŹeieïŹstsmaerasat»__°9T_ _ Vid den jĂ€mförande CCT-provning i FeCl3 angreps stĂ„l nr 6 först vid 45°C. NĂ€st bĂ€sta vĂ€rde noterades med stĂ„l nr 22, 40°C, medan övrigas CCT ligger under rumstempratur utom möjligen för stĂ„l nr 21, som gav bra resultat upp till 3000.Steel No. 3 showed far from as good crude steel as Steel No. 6 and remained somewhat below the result for Steel No. 20, despite the fact that the chromium and nickel contents are equally high and the molybdenum content only 1.5 and the nitrogen content .21 Z lower than in steel No. 6. 10 15 20 25 39 8305795-0 11 Efi ïŹ isĂ«: Peltkefr ïŹ egen ïŹ stsmaerasat »__ ° 9T_ _ In the comparative CCT test in FeCl3, steel no. 6 was first attacked at 45 ° C. The next best value was noted with steel no. 22, 40 ° C, while the others' CCT is below room temperature except possibly for steel no. 21, which gave good results up to 3000.
.Kritisk ruektfzĂ€tïŹiïŹssĂĂaveratari EPI Ăven denna provning utfördes i FeCl Tabell 3 visar i detta fall högsta CPT för stĂ„l nr 22, 75°C, följt av experimentstĂ„let nr 6, 6500. JĂ€mfört med spaltkorrosionsegenskaperna uppvisar experiment- stĂ„let nr 6 sĂ„lunda sĂ€mre punktfrĂ€tningsegenskaper. Detta kan bero pĂ„ den vanligen mindre gynnsamma inneslutningsbilden hos smĂ„ labo- ratorĂesmĂ€ltor jĂ€mfört med material som tillverkats under produk- tionsmĂ€ssiga förhĂ„llanden. Slaggbilden kan nĂ€mligen ha större betydelse för punktfrĂ€tning Ă€n för spaltkorrosion. Ä°zreĂi°e i evefsfisls ekzïŹĂ€berlöeïŹiïŹe Endast stĂ„l nr 6 och 22 var helt fria frĂ„n angrepp vid SOOC.Critical ruektfzĂ€t ïŹ i ïŹ ssĂĂaveratari EPI This test was also performed in FeCl Table 3 shows in this case the highest CPT for steel no. 22, 75 ° C, followed by experiment steel no. 6, 6500. Compared with the crevice corrosion properties, experiment steel no. This may be due to the generally less favorable containment picture of small laboratory melts compared to materials manufactured under production conditions. The slag image can be more important for point corrosion than for crevice corrosion. Ă„ ° zreĂi ° e i evefsfisls ekz ïŹ Ă€berlöe ïŹ i ïŹ e Only steels no. 6 and 22 were completely free from attack by SOOC.
TABELL 4 UtvÀrdering av korrosionsangrepp efter 6 mÄn exponering i pappersmassablekeri.TABLE 4 Evaluation of corrosion attack after 6 months exposure in pulp bleaching plant.
StĂ„l Viktsförlust Max angreppsdjup Korr hast Spaltangrepp under nr g mm g/mzh distansbricka, djup mm 16 -50 0.6 _ .004 < 0.1 24 1.16 1.1 .O11 < 0.1 25 1.50 1.0 .Ă13 .12 För att ytterligare utvĂ€rdera korrosionsogenskaperna hos det upp- fĂnnĂngsenliga stĂ„let framstĂ€lldes en 50 kg laboratoriesmĂ€lta, stĂ„l nr 16, med samma nominella sammansĂ€ttning som stĂ„l nr 6. Ăven detta material gick att smida och valsa utan anmĂ€rkning och gav likartade, myvkct goda korrosionsresultat. HĂ€r skall rapporteras dels resultat frĂ„n utförda fĂ€ltförsök, dels resultat frĂ„n labora- 10 15 20 25 30 35 8305795-0 12 toriemĂ€ssigt utförda korrosionsprovningar samt ett första svetsförsök.Steel Weight loss Maximum depth of attack Corrosive speed Slit infestation under no g mm g / mzh spacer, depth mm 16 -50 0.6 _ .004 <0.1 24 1.16 1.1 .O11 <0.1 25 1.50 1.0 .Ă13 .12 To further evaluate the corrosion properties of the In accordance with the invention, a 50 kg laboratory melt, steel No. 16, was produced with the same nominal composition as steel No. 6. This material could also be forged and rolled without remark and gave similar, very good corrosion results. Results from field tests performed and results from laboratory corrosion tests performed as well as a first welding test must be reported here.
FÀltprovet utfördes i klordioxidsteget i ett pappersmassablekeri.The field test was performed in the chlorine dioxide step in a pulp bleaching plant.
,Proverna, som hade formen av mindre plĂ„tstycken, placerades pĂ„ högkant i ena hörnet av filtrets ĂnloppslĂ„da. HĂ€lften av plĂ„tarna var nedsĂ€nkta i massasuspensionen, medan den övre hĂ€lften befann sig i gasfasen. Miljön i dessa filter Ă€r sĂ„ korrosiv att material- frĂ„gan hittills inte kunnat lösas pĂ„ tillfredsstĂ€llande sĂ€tt.The samples, which were in the form of smaller sheet metal pieces, were placed vertically in one corner of the filter headbox. Half of the plates were immersed in the pulp suspension, while the upper half was in the gas phase. The environment in these filters is so corrosive that the material issue has so far not been resolved satisfactorily.
Tidigare exponeringar har visat att endast titan klarar sig utan angrepp. Typiska miljöparametrar Àr: Redoxpotential 650 mV/SCE Aktivt klor i filtrat 7 mg/l_1 pa 3.8 ' Kiorid zzo Ing/l* Temperatur 7300 Proverna utgjordes av det uppfinningsenliga stÄlet nr 16 samt jÀm- förelsematerialen 24 och 25. Samtliga prover hade före exponeringen slipats samt betats i 10 Z HNO3 + 1 % HF, 6000/10 min.Previous exposures have shown that only titanium can survive without attack. Typical environmental parameters are: Redox potential 650 mV / SCE Active chlorine in filtrate 7 mg / l_1 pa 3.8 'Chloride zzo Ing / l * Temperature 7300 The samples consisted of the steel no. 16 according to the invention and the comparative materials 24 and 25. All samples had been ground before exposure and pickled in 10 Z HNO 3 + 1% HF, 6000/10 min.
Resultaten framgÄr av Tabell 4._ SÄvÀl viktsförlust i g/mzh som angreppsdjup för punkt- och spalt- angrepp var lÀgst för stÄl nr 16, högst för stÄl nr 25. Expone- ringen bekrÀftade ovan redovisade laboratoriedata för tvÄkilosprov, stÄl nr 6.The results are shown in Table 4._ Both weight loss in g / mzh and attack depth for point and gap attacks were lowest for steel no. 16, highest for steel no. 25. The exposure confirmed the above-reported laboratory data for two-kilo samples, steel no. 6.
De laboratoriemÀssigt utförda korrosionsundersökningarna av stÄl nr 16 har sammanfattats i Tabell 5. StÄlet hade svetsats med svets- elektrod av typ Avesta P12; MIG-svets. Speciellt vÀrt att notera Àr att nÄgra korrosionsangrepp inte uppstod i svetsgodset eller i den vÀrmepÄverkade zonen. SjÀlva svetsningen innebar inga problem.The laboratory corrosion tests of steel no. 16 have been summarized in Table 5. The steel had been welded with a welding electrode of type Avesta P12; MIG welding. It is especially worth noting that no corrosion attacks occurred in the weld metal or in the heat-affected zone. The welding itself did not cause any problems.
StÄlet kunde svetsas med mycket lÄg vÀrmetillförsel, 0.235 kJ/mm.The steel could be welded with a very low heat supply, 0.235 kJ / mm.
Svetsen var av god kvalitet, jĂ€mn, utan stĂ€nk eller porer. 8305795-O 13 TABELL 5 Sammanfattning av korrosionsresultat för stĂ„l nr 16, bĂ„de grundmaterĂal och Svets. . . o g 5 " m N m PunkLfrf- ' Krxtlsk tempvratur, (2 ,., p; Ă€; Ă€ Ă€) puh-nl Ănl >.,.-.. ..~~.-.---------~------'~--~ W" ~~"""""" _' '4 »1 f: 'r o i i . i syntoLĂsk u. E? Ă€; 4 5% NaCl l 6 Z FeclïŹĆĄ skrubberlösnĂng Ă„ pH 2.2 . .. 9o°c Punkc- spalc- VllfĆĄsffrmst mV/SCE frĂ€tn. korr. gm h 3? Ă€ 181 75 40 60(CPT) O 0.27 Ă„' ss o.34 F? s. 70 1 .4 5 andast l-Ă n Snltt* ytor 25 194 . ss - 0.39 0.38 o 3 âf U)The weld was of good quality, even, without splashes or pores. 8305795-O 13 TABLE 5 Summary of corrosion results for steel no. 16, both base material and Weld. . . og 5 "m N m PunkLfrf- 'Krxtlsk tempvratur, (2,., p; Ă€; Ă€ Ă€) puh-nl Ănl>., .- .. .. ~~.-.-------- - ~ ------ '~ - ~ W "~~" "" "" "_' '4» 1 f:' roii. i syntoLĂsk u. E? Ă€; 4 5% NaCl l 6 Z Fecl skru ĆĄ scrubber solution at pH 2.2. .. 9o ° c Punkc- spalc- VllfĆĄsffrmst mV / SCE frĂ€tn. corr. gm h 3? Ă€ 181 75 40 60 (CPT) O 0.27 Ă„ 'ss o.34 F? pp. 70 1 .4 5 andast l-Ă n Snltt * ytor 25 194. ss - 0.39 0.38 o 3 âf U)
Claims (10)
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE8305795A SE441455B (en) | 1983-10-21 | 1983-10-21 | STALL OF AUSTENITIC TYPE |
| AT84112048T ATE28087T1 (en) | 1983-10-21 | 1984-10-08 | AUSTENITIC STEEL. |
| EP84112048A EP0142015B1 (en) | 1983-10-21 | 1984-10-08 | Austenitic steel |
| DE8484112048T DE3464504D1 (en) | 1983-10-21 | 1984-10-08 | Austenitic steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| SE8305795A SE441455B (en) | 1983-10-21 | 1983-10-21 | STALL OF AUSTENITIC TYPE |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| SE8305795D0 SE8305795D0 (en) | 1983-10-21 |
| SE8305795L SE8305795L (en) | 1985-04-22 |
| SE441455B true SE441455B (en) | 1985-10-07 |
Family
ID=20352991
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| SE8305795A SE441455B (en) | 1983-10-21 | 1983-10-21 | STALL OF AUSTENITIC TYPE |
Country Status (4)
| Country | Link |
|---|---|
| EP (1) | EP0142015B1 (en) |
| AT (1) | ATE28087T1 (en) |
| DE (1) | DE3464504D1 (en) |
| SE (1) | SE441455B (en) |
Families Citing this family (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4560408A (en) * | 1983-06-10 | 1985-12-24 | Santrade Limited | Method of using chromium-nickel-manganese-iron alloy with austenitic structure in sulphurous environment at high temperature |
| NO891969L (en) * | 1988-05-17 | 1989-11-20 | Thyssen Edelstahlwerke Ag | Corrosion resistant AUSTENITIC STEEL. |
| JPH0699781B2 (en) * | 1989-08-11 | 1994-12-07 | æ ȘćŒäŒç€Ÿæ„ç«èŁœäœæ | Austenitic steel excellent in neutron irradiation embrittlement and its application |
| SE465373B (en) * | 1990-01-15 | 1991-09-02 | Avesta Ab | AUSTENITIC STAINLESS STEEL |
| FR2705689B1 (en) * | 1993-05-28 | 1995-08-25 | Creusot Loire | Austenitic stainless steel with high resistance to corrosion by chlorinated and sulfuric environments and uses. |
| JP2004043845A (en) * | 2002-07-09 | 2004-02-12 | Nippon Steel Corp | Fluid parts |
| JP2004043844A (en) * | 2002-07-09 | 2004-02-12 | Nippon Steel Corp | Fluid parts |
| JP2005281855A (en) * | 2004-03-04 | 2005-10-13 | Daido Steel Co Ltd | Heat resistant austenitic stainless steel and method for producing the same |
| KR20210100212A (en) | 2011-05-26 | 2021-08-13 | ì ëìŽí°ë íìŽíëŒìžì€ ììì íšìíœ íŒí°ìŽ 늏믞í°ë | Austenitic stainless steel |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE1205289B (en) * | 1964-05-27 | 1965-11-18 | Phoenix Rheinrohr Ag | Use of an austenitic steel alloy as a material for welded components that are exposed to attack by sea water and / or the sea atmosphere |
| FR1466926A (en) * | 1966-02-03 | 1967-01-20 | Suedwestfalen Ag Stahlwerke | austenitic steel construction elements |
| BE757048A (en) * | 1969-10-09 | 1971-03-16 | Boehler & Co Ag Geb | APPLICATIONS OF FULLY AUSTENIC STEEL UNDER CORRODING CONDITIONS |
| JPS5424364B2 (en) * | 1973-05-04 | 1979-08-21 | ||
| US3912503A (en) * | 1973-05-14 | 1975-10-14 | Armco Steel Corp | Galling resistant austenitic stainless steel |
-
1983
- 1983-10-21 SE SE8305795A patent/SE441455B/en not_active IP Right Cessation
-
1984
- 1984-10-08 AT AT84112048T patent/ATE28087T1/en active
- 1984-10-08 EP EP84112048A patent/EP0142015B1/en not_active Expired
- 1984-10-08 DE DE8484112048T patent/DE3464504D1/en not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| EP0142015B1 (en) | 1987-07-01 |
| DE3464504D1 (en) | 1987-08-06 |
| EP0142015A1 (en) | 1985-05-22 |
| SE8305795D0 (en) | 1983-10-21 |
| ATE28087T1 (en) | 1987-07-15 |
| SE8305795L (en) | 1985-04-22 |
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