EP3330390B1 - Nickel-chromium alloy - Google Patents
Nickel-chromium alloy Download PDFInfo
- Publication number
- EP3330390B1 EP3330390B1 EP17207317.3A EP17207317A EP3330390B1 EP 3330390 B1 EP3330390 B1 EP 3330390B1 EP 17207317 A EP17207317 A EP 17207317A EP 3330390 B1 EP3330390 B1 EP 3330390B1
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- EP
- European Patent Office
- Prior art keywords
- alloy
- nickel
- chromium
- heating
- iron
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- 229910000623 nickel–chromium alloy Inorganic materials 0.000 title claims description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 38
- 239000000956 alloy Substances 0.000 claims description 38
- 239000000463 material Substances 0.000 claims description 29
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 28
- 229910052782 aluminium Inorganic materials 0.000 claims description 28
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 26
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 22
- 238000010438 heat treatment Methods 0.000 claims description 20
- 230000015572 biosynthetic process Effects 0.000 claims description 18
- 230000003647 oxidation Effects 0.000 claims description 18
- 238000007254 oxidation reaction Methods 0.000 claims description 18
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 17
- 238000000034 method Methods 0.000 claims description 16
- 239000011651 chromium Substances 0.000 claims description 15
- 229910052804 chromium Inorganic materials 0.000 claims description 14
- 238000005336 cracking Methods 0.000 claims description 14
- 229910052742 iron Inorganic materials 0.000 claims description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 14
- 229910052799 carbon Inorganic materials 0.000 claims description 13
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 11
- 229910052759 nickel Inorganic materials 0.000 claims description 11
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 239000010936 titanium Substances 0.000 claims description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 10
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 10
- 229910052721 tungsten Inorganic materials 0.000 claims description 10
- 239000010937 tungsten Substances 0.000 claims description 10
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 9
- 239000010955 niobium Substances 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 9
- 239000010703 silicon Substances 0.000 claims description 9
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 8
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 8
- 238000000137 annealing Methods 0.000 claims description 8
- 229930195733 hydrocarbon Natural products 0.000 claims description 8
- 150000002430 hydrocarbons Chemical class 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 239000011733 molybdenum Substances 0.000 claims description 8
- 229910052758 niobium Inorganic materials 0.000 claims description 8
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 8
- 229910052727 yttrium Inorganic materials 0.000 claims description 8
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 8
- 229910052726 zirconium Inorganic materials 0.000 claims description 8
- 229910052715 tantalum Inorganic materials 0.000 claims description 7
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 7
- 229910052684 Cerium Inorganic materials 0.000 claims description 6
- 238000005266 casting Methods 0.000 claims description 6
- GWXLDORMOJMVQZ-UHFFFAOYSA-N cerium Chemical compound [Ce] GWXLDORMOJMVQZ-UHFFFAOYSA-N 0.000 claims description 6
- 230000003750 conditioning effect Effects 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 5
- 229910052739 hydrogen Inorganic materials 0.000 claims description 5
- 239000001257 hydrogen Substances 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 229910052760 oxygen Inorganic materials 0.000 claims description 5
- 239000001301 oxygen Substances 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 4
- 238000009434 installation Methods 0.000 claims description 4
- 239000011572 manganese Substances 0.000 claims description 4
- 229910052756 noble gas Inorganic materials 0.000 claims description 4
- 150000002835 noble gases Chemical class 0.000 claims description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000003054 catalyst Substances 0.000 claims description 2
- 150000002431 hydrogen Chemical class 0.000 claims description 2
- 239000011261 inert gas Substances 0.000 claims description 2
- 230000008018 melting Effects 0.000 claims description 2
- 238000002844 melting Methods 0.000 claims description 2
- 239000004411 aluminium Substances 0.000 claims 2
- 238000001125 extrusion Methods 0.000 claims 1
- 239000010410 layer Substances 0.000 description 26
- 239000000571 coke Substances 0.000 description 18
- 230000003197 catalytic effect Effects 0.000 description 8
- 150000001247 metal acetylides Chemical class 0.000 description 7
- 238000010586 diagram Methods 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 6
- 239000007789 gas Substances 0.000 description 6
- 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 description 6
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 6
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 5
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 5
- 238000005255 carburizing Methods 0.000 description 5
- 125000004122 cyclic group Chemical group 0.000 description 5
- 230000001590 oxidative effect Effects 0.000 description 5
- 229910052717 sulfur Inorganic materials 0.000 description 5
- 239000011593 sulfur Substances 0.000 description 5
- 229910000990 Ni alloy Inorganic materials 0.000 description 4
- 239000002041 carbon nanotube Substances 0.000 description 4
- 229910021393 carbon nanotube Inorganic materials 0.000 description 4
- 239000010941 cobalt Substances 0.000 description 4
- 229910017052 cobalt Inorganic materials 0.000 description 4
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 4
- 238000001000 micrograph Methods 0.000 description 4
- -1 C 6 carbides Chemical class 0.000 description 3
- 239000004215 Carbon black (E152) Substances 0.000 description 3
- 229910000640 Fe alloy Inorganic materials 0.000 description 3
- 239000000567 combustion gas Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000011065 in-situ storage Methods 0.000 description 3
- 238000002407 reforming Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- OTMSDBZUPAUEDD-UHFFFAOYSA-N Ethane Chemical compound CC OTMSDBZUPAUEDD-UHFFFAOYSA-N 0.000 description 2
- 229910018487 Ni—Cr Inorganic materials 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- BIJOYKCOMBZXAE-UHFFFAOYSA-N chromium iron nickel Chemical compound [Cr].[Fe].[Ni] BIJOYKCOMBZXAE-UHFFFAOYSA-N 0.000 description 2
- VNNRSPGTAMTISX-UHFFFAOYSA-N chromium nickel Chemical compound [Cr].[Ni] VNNRSPGTAMTISX-UHFFFAOYSA-N 0.000 description 2
- 238000004939 coking Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 239000004848 polyfunctional curative Substances 0.000 description 2
- 230000008092 positive effect Effects 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 239000011241 protective layer Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000004584 weight gain Effects 0.000 description 2
- 235000019786 weight gain Nutrition 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910000713 I alloy Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 230000001464 adherent effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 229910052785 arsenic Inorganic materials 0.000 description 1
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 description 1
- 229910052797 bismuth Inorganic materials 0.000 description 1
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000011575 calcium Substances 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 1
- 230000001143 conditioned effect Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 229910052735 hafnium Inorganic materials 0.000 description 1
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 1
- 230000008642 heat stress Effects 0.000 description 1
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 239000011133 lead Substances 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000005121 nitriding Methods 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 239000003348 petrochemical agent Substances 0.000 description 1
- 239000002243 precursor Substances 0.000 description 1
- 238000002203 pretreatment Methods 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910052714 tellurium Inorganic materials 0.000 description 1
- PORWMNRCUJJQNO-UHFFFAOYSA-N tellurium atom Chemical compound [Te] PORWMNRCUJJQNO-UHFFFAOYSA-N 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/053—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 30% but less than 40%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
Definitions
- petrochemicals require materials that are resistant to both temperature and corrosion and, in particular, have grown on the one hand from the hot product and, on the other hand, from the hot combustion gases of, for example, steam crackers.
- Their coils are subject to external oxidizing aufstickenden combustion gases with temperatures up to 1100 ° C and more and in the interior at temperatures up to about 900 ° C and optionally also high pressure of a carburizing and oxidizing atmosphere.
- the carburizing hydrocarbon atmosphere inside the pipes is associated with the danger that diffuses from there the carbon in the pipe material, the carbides in the material and increase from the existing carbide M 23 C 9 with increasing carburizing the carbon-rich carbide M 7 C 6 forms.
- the consequence of this is internal stresses due to the increase in carbide volume associated with carbide formation or conversion as well as a reduction in the strength and toughness of the tubing material.
- German patent specification describes 103 02 989 a nickel-chromium casting alloy also suitable as a material for coils of cracking and reforming furnaces with up to 0.8% carbon, 15 to 40% chromium, 0.5 to 13% iron, 1.5 to 7% aluminum, to 0, 2% silicon, to 0.2% manganese, 0.1 to 2.5% niobium, to 11% tungsten and molybdenum, to 1.5% titanium, 0.1 to 0.4% zirconium and 0.01 to 0 , 1% yttrium, balance nickel.
- This alloy has proven itself in particular when used as a pipe material, although the practice continues to call for pipe materials with extended life.
- Out JP 2004 052036A is an alloy with 0.1 to 0.6% carbon, 20 to 40% chromium, 1.5 to 4% aluminum, up to 3.0% silicon, up to 3.0% manganese, 20 to 65% nickel with the remainder iron which may also have 0.5 to 5% tungsten, 0.5 to 2% niobium, 0.5 to 5% molybdenum, 0.01 to 0.5% titanium and 0.01 to 0.5% zirconium.
- the invention is therefore directed to a nickel-chromium alloy having improved durability under conditions such as cracking and reforming of hydrocarbons.
- the solution to this problem consists in a nickel-chromium alloy with 0.4 to 0.6% carbon, 28 to 33% chromium, 15 to 25% iron, 2 to 6% aluminum, each up to 2% silicon and manganese, respectively up to 1.5% niobium and tantalum, each up to 1.0% tungsten, titanium and zirconium, each up to 0.5% yttrium and cerium, up to 0.5% molybdenum and up to 0.1% nitrogen remainder including nickel impurities caused by melting.
- this alloy contains, individually or side by side, 17 to 22% iron, 3 to 4.5% aluminum, in each case 0.01 to 1% silicon, to 0.5% manganese, 0.5 to 1.0% niobium, bis 0.5 tantalum, to 0.6% tungsten, 0.001 to 0.5% titanium each, to 0.3% zirconium, to 0.3% yttrium, to 0.3% cerium, 0.01 to 0.5% Molybdenum and 0.001 to 0.1% nitrogen.
- the alloy according to the invention is characterized in particular by its comparatively high contents of chromium and nickel and by a compelling carbon content within a comparatively narrow range.
- the silicon improves the oxidation and carburization resistance.
- the manganese also has a positive effect on the oxidation resistance and additionally on the weldability, deoxidizes the melt and stably binds off the sulfur:
- Niobium improves creep strength, forms stable carbides and carbonitrides; It also serves as a mixed crystal hardener. Titanium and Tantalum improve creep strength. Even at very low levels, very finely divided carbides and carbonitrides form. At higher levels, titanium and tantalum act as mixed crystal hardeners.
- Tungsten improves the creep rupture strength. Particularly at high temperatures, tungsten improves the strength by means of solid solution hardening, since the carbides partly dissolve at higher temperatures.
- Cobalt also improves creep strength by means of solid solution hardening, zirconium through the formation of carbides, especially in conjunction with titanium and tantalum.
- Yttrium and cerium obviously not only improve the oxidation resistance and especially the adhesion and growth of the Al 2 O 3 cover layer.
- yttrium and cerium improve the creep resistance even at very low levels, since they stably bind the remaining free sulfur.
- Low levels of boron also improve creep strength, prevent sulfur segregation, and retard aging by coarsening the M 23 C 6 carbides.
- Molybdenum also improves the creep rupture strength, especially at high temperatures, by means of solid solution hardening. Especially because at high temperatures, the carbides partially go into solution.
- the nitrogen improves the creep rupture strength by means of carbonitride formation, while hafnium, even at low levels, improves the oxidation resistance by means of better adhesion of the cover layer and has a positive effect on the creep rupture strength.
- Phosphorous, sulfur, zinc, lead, arsenic, bismuth, tin and tellurium are among the impurities, their contents should therefore be as low as possible.
- the alloy is particularly suitable as a casting material for components of petrochemical plants, for example for the production of coils for cracking and reforming furnaces, reformer tubes, but also as a material for iron ore direct reduction plants and for similarly stressed components.
- these include furnace parts, radiant tubes for heating ovens, rolls for annealing furnaces, parts of Strip and strip casting plants, hoods and sleeves for annealing furnaces, parts of large diesel engines and shaped bodies for catalyst fillings.
- the alloy is characterized by a high oxidation and carburization resistance as well as good creep strength and creep resistance.
- the inner surface of cracking or reformer tubes is characterized by a catalytically inert, aluminum-containing oxide layer, thus preventing the formation of catalytic coke strands, known as carbon nanotubes.
- the properties that characterize the material also remain with multiple burn-out of the coke which inevitably deposits on the inner wall of the pipes during cracking.
- the alloy for producing centrifugally cast tubes if they are drilled with a contact pressure of 10 to 40 MPa, for example 10 to 25 MPa. In such a boring occurs due to the contact pressure to a cold deformation or work hardening of the pipe material in a near-surface zone with depths of, for example, 0.1 to 0.5 mm.
- the cold-worked zone recrystallizes, resulting in a very fine-grained microstructure.
- the recrystallization structure enhances the diffusion of the oxide-forming elements aluminum and chromium, which promotes the formation of a closed layer of high density and stability consisting primarily of alumina.
- the resulting adherent aluminum-containing oxide forms a closed protective layer of the tube inner wall, which is largely free of catalytically active centers such as nickel or iron and even after a prolonged cyclic heat stress is still stable.
- This aluminum-containing oxide layer prevents, in contrast to other pipe materials without such a cover layer, the penetration of oxygen into the base material and thus an internal oxidation of the pipe material.
- the cover layer suppresses not only the carburizing of the pipe material, but also corrosion by impurities in the process gas.
- the top layer consists mainly of Al 2 O 3 and the mixed oxide (Al, Cr) 2 O 3 and is largely inert to a catalytic coke formation. It is poor in elements that catalyze coke formation, such as iron and nickel.
- a durable oxide protective layer serves to condition, for example, the inner surface of steam cracker pipes after their installation when the relevant furnace is heated to its operating temperature.
- This conditioning can be carried out as heating with interposed isothermal heat treatments in a furnace atmosphere, which is set during the heating according to the invention, for example in a very weakly oxidizing water vapor-containing atmosphere with an oxygen partial pressure of at most 10 -20 , preferably at most 10 -30 bar.
- Particularly suitable is a protective gas atmosphere of 0.1 to 10 mol% of water vapor, 7 to 99.9 mol% of hydrogen and hydrocarbon individually or side by side and 0 to 88 mol% noble gases.
- the atmosphere during the conditioning preferably consists of an extremely weakly oxidizing mixture of water vapor, hydrogen, hydrocarbons and noble gases in an amount such that the oxygen partial pressure of the mixture at a temperature of 600 ° C is less than 10 -20 bar, preferably less than 10 -30 bar is.
- the initial heating of the tube interior after a previous mechanical removal of a surface layer, d. H. the separate heating of the resulting cold-formed surface zone is preferably carried out under very weak oxidizing inert gas in several phases each at a rate of 10 to 100 ° C / h initially to 400 to 750 ° C, preferably about 550 ° C at the inner surface of the tube.
- This heating phase is followed by holding for one to fifty hours within the temperature range mentioned.
- the heating takes place in the presence of a steam atmosphere as soon as the temperature has reached a value which precludes the formation of condensed water. Following this holding the tube is then brought to the operating temperature, for example to 800 to 900 ° C and is ready for operation.
- the tube temperature gradually increases in the cracking operation as a result of the deposition of pyrolytic coke and finally reaches about 1000 ° C or even 1050 ° C on the inner surface.
- the inner layer consisting essentially of Al 2 O 3 and to a small extent of (Al, Cr) 2 O 3 converts from a transition oxide such as ⁇ , ⁇ or ⁇ -Al 2 O 3 into stable ⁇ -aluminum oxide.
- the tube has reached its operating state with its mechanically removed inner layer in a multi-stage, but preferably eintoxicityen method.
- This precursor includes initial heating after abrading the inner surface to holding at 400 to 750 ° C.
- the pipe thus pretreated can then be further processed in situ, for example in another manufacturing facility, starting from its cold state in the manner described above, that is to say in another factory. H. be brought to the operating temperature in the installed state.
- the mentioned separate pre-treatment is not limited to tubes, but is also suitable for a partial or complete conditioning of surface zones of other workpieces, which are then treated according to their nature and use as in the invention or by other methods, but with a defined initial state.
- alloy 9 experiences no internal oxidation even after more than 200 cycles of annealing at 1150 ° C for 45 minutes, whereas the two comparative alloys 12 and 13 show increasing weight loss after only a few cycles as a result of catastrophic oxidation.
- the alloy 9 is also characterized by a high carburization resistance; because, according to the diagram of FIG. 2, it has the lowest weight gain after all three carburizing treatments, compared with the conventional alloys 12 and 13, due to the low weight gain.
- FIGS. 3a and 3b show that the creep strength of the nickel alloy 11 is even better in a substantial range than in the case of the two comparative alloys 12 and 13.
- the exception here is the alloy 15, which is not covered by the invention because of its low iron content. however, with their much lower oxidation, carburization and coking resistance.
- FIGS. 5 and 6 Examples of the surface condition of the tube interior of furnace tubes with the composition of the alloy 8 are shown in FIGS. 5 and 6.
- the FIGS Figure 6 (Experiment 7 according to Table II) shows the superiority of a surface after a conditioning according to the invention in comparison to the Figure 5 , which relates to a not according to the invention conditioned surface (Table II, Experiment 2).
- FIG. 7 Shown in Figures 7 (Alloy 14) and 8 are shallow areas in cross section.
- the samples were heated to 950 ° C and then subjected to 10 crack cycles of 10 hours each in an atmosphere of water vapor, hydrogen and hydrocarbons. After each cycle, the sample tubes were burned out for one hour to remove the coke deposits.
- the micrograph of the image 7 in the form of the dark areas shows the large-area and thus bulky result of internal oxidation on the inside of a tube in a conventional nickel-chromium casting alloy compared to the micrograph of the image 8 of the alloy 9, which is virtually none Internal oxidation, although both samples were similarly subjected to multiple cyclic treatment from cracking on the one hand and removal of the carbon deposits on the other.
- Figure 11 relates to an SEM top view of the conventional sample shown in Figure 7 in section; Due to the missing cover layer, it shows a catastrophic oxidation and a corresponding catastrophic formation of catalytic coke in the form of carbon nanotubes.
- the stability of the oxide layer on an alloy according to the invention is particularly clear from the course of the aluminum concentration over the depth of the edge zone after ten cracking phases with respective removal of the coke deposits by burnout in an intermediate phase when the diagrams according to FIGS. 9 and 10 are compared of the image 9 in the near-surface region due to the local failure of the protective overcoat and then onset of strong internal aluminum oxidation of the material is depleted of aluminum, the aluminum concentration in the diagram of the image 10 moves approximately at the initial level of the casting material. This clearly shows the importance of a continuous, dense and in particular firmly adhering inner aluminum-containing oxide layer in the tubes according to the invention.
- the stability of the aluminum-containing oxide layer was also investigated by long-term tests in a laboratory plant under process-related conditions.
- the samples of alloys 9 and 11 were heated to 950 ° C. under steam and then subjected to cracking at this temperature three times each for 72 hours; they were then subjected to burnout at 900 ° C for four hours each.
- Image 12 shows the closed aluminum-containing oxide layer after the three crack cycles and beyond how the aluminum-containing oxide layer covers the material itself over chromium carbides in the surface. It can be seen that chromium carbides present on the surface are completely covered by the aluminum-containing oxide layer.
- the inventive nickel-chromium-iron alloy is characterized, for example, as a pipe material after removal of the inner surface under mechanical pressure and a subsequent multi-stage in situ heat treatment for conditioning the inner surface by a high oxidation, corrosion and especially high Creep rupture and creep resistance.
Description
Die Erdölchemie verlangt für Hochtemperatur-Verfahren Werkstoffe, die sowohl temperatur- als auch korrosionsbeständig sind und insbesondere einerseits den heißen Produkt- und andererseits den ebenfalls heißen Verbrennungsgasen beispielsweise von Steam-Crackern gewachsen sind. Deren Rohrschlangen unterliegen von außen den oxidierenden aufstickenden Verbrennungsgasen mit Temperaturen bis 1.100 °C und mehr sowie im Innern bei Temperaturen bis etwa 900 °C und gegebenenfalls auch hohem Druck einer aufkohlenden und oxidierenden Atmosphäre.For high-temperature processes, petrochemicals require materials that are resistant to both temperature and corrosion and, in particular, have grown on the one hand from the hot product and, on the other hand, from the hot combustion gases of, for example, steam crackers. Their coils are subject to external oxidizing aufstickenden combustion gases with temperatures up to 1100 ° C and more and in the interior at temperatures up to about 900 ° C and optionally also high pressure of a carburizing and oxidizing atmosphere.
Im Kontakt mit den heißen Verbrennungsgasen kommt es deshalb, ausgehend von der äußeren Rohroberfläche zu einer Aufstickung des Rohrwerkstoffs und zum Entstehen einer ZunderschichtIn contact with the hot combustion gases, it is therefore, starting from the outer pipe surface to a nitriding of the pipe material and the formation of a scale layer
Die aufkohlende Kohlenwasserstoff-Atmosphäre im Innern der Rohre ist mit der Gefahr verbunden, dass von dort der Kohlenstoff in den Rohrwerkstoff diffundiert, die Karbide im Werkstoff zunehmen und aus dem dort vorhandenen Karbid M23C9 mit zunehmender Aufkohlung das kohlenstoffreichere Karbid M7C6 bildet. Die Folge davon sind innere Spannungen aufgrund der mit der Karbidbildung bzw. -umwandlung verbundenen Volumenzunahme der Karbide sowie eine Verringerung der Festigkeit und Zähigkeit des Rohrwerkstoffs. Des weiteren kommt es an der Innenoberfläche zum Entstehen einer festhaftenden, bis zu mehreren Millimeter dicken Koksschicht. Zyklische Temperaturbelastungen, wie sie als Folge eines Herunterfahrens der Anlage auftreten, führen des weiteren dazu, dass die Rohre infolge der unterschiedlichen Wärmeausdehnungskoeffizienten des metallischen Rohrs und der Koksschicht auf die Koksschicht aufschrumpfen. Das führt zu hohen Spannungen im Rohr, die zum Entstehen von Rissen in der inneren Rohroberfläche führen. Durch solche Risse kann dann vermehrt Kohlenstoffwasserstoff in den Rohrwerkstoff gelangen.The carburizing hydrocarbon atmosphere inside the pipes is associated with the danger that diffuses from there the carbon in the pipe material, the carbides in the material and increase from the existing carbide M 23 C 9 with increasing carburizing the carbon-rich carbide M 7 C 6 forms. The consequence of this is internal stresses due to the increase in carbide volume associated with carbide formation or conversion as well as a reduction in the strength and toughness of the tubing material. Furthermore, it comes on the inner surface to the emergence of a firmly adhering, up to several millimeters thick coke layer. Cyclic temperature loads, as they occur as a result of shutdown of the system, lead the further that the tubes shrink to the coke layer due to the different coefficients of thermal expansion of the metallic tube and the coke layer. This leads to high stresses in the pipe, which lead to the formation of cracks in the inner pipe surface. Through such cracks, hydrocarbon gas can then increasingly enter the pipe material.
Aus der
Des weiteren beschreibt die deutsche Patentschrift
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Die Erfindung ist daher auf eine Nickel-Chrom-Legierung mit verbesserter Beständigkeit unter Bedingungen gerichtet, wie sie beispielsweise beim Cracken und Reformieren von Kohlenwasserstoffen gegeben sind.The invention is therefore directed to a nickel-chromium alloy having improved durability under conditions such as cracking and reforming of hydrocarbons.
Die Lösung dieser Aufgabe besteht in einer Nickel-Chrom-Legierung mit 0,4 bis 0,6% Kohlenstoff, 28 bis 33% Chrom, 15 bis 25% Eisen, 2 bis 6% Aluminium, jeweils bis 2% Silizium und Mangan, jeweils bis 1,5% Niob und Tantal, jeweils bis 1,0% Wolfram, Titan und Zirkonium, jeweils bis 0,5% Yttrium und Cer, bis 0,5% Molybdän und bis 0,1% Stickstoff Rest einschließlich erschmelzungsbedingter Verunreinigungen Nickel.The solution to this problem consists in a nickel-chromium alloy with 0.4 to 0.6% carbon, 28 to 33% chromium, 15 to 25% iron, 2 to 6% aluminum, each up to 2% silicon and manganese, respectively up to 1.5% niobium and tantalum, each up to 1.0% tungsten, titanium and zirconium, each up to 0.5% yttrium and cerium, up to 0.5% molybdenum and up to 0.1% nitrogen remainder including nickel impurities caused by melting.
Vorzugsweise enthält diese Legierung jeweils einzeln oder nebeneinander, 17 bis 22% Eisen, 3 bis 4,5% Aluminium, jeweils 0,01 bis 1% Silizium, bis 0,5% Mangan, 0,5 bis 1,0% Niob, bis 0,5 Tantal, bis 0,6% Wolfram, jeweils 0,001 bis 0,5% Titan, bis 0,3% Zirkonium, bis 0,3% Yttrium, bis 0,3% Cer, 0,01 bis 0,5% Molybdän und 0,001 bis 0,1% Stickstoff.Preferably, this alloy contains, individually or side by side, 17 to 22% iron, 3 to 4.5% aluminum, in each case 0.01 to 1% silicon, to 0.5% manganese, 0.5 to 1.0% niobium, bis 0.5 tantalum, to 0.6% tungsten, 0.001 to 0.5% titanium each, to 0.3% zirconium, to 0.3% yttrium, to 0.3% cerium, 0.01 to 0.5% Molybdenum and 0.001 to 0.1% nitrogen.
Die erfindungsgemäße Legierung ist insbesondere geprägt durch ihre vergleichsweise hohen Gehalte an Chrom und Nickel sowie einen zwingenden Kohlenstoffgehalt innerhalb eines vergleichsweise engen Bereichs.The alloy according to the invention is characterized in particular by its comparatively high contents of chromium and nickel and by a compelling carbon content within a comparatively narrow range.
Von den fakultativen Legierungsbestandteilen verbessert das Silizium die Oxidations- und die Aufkohlungsbeständigkeit. Das Mangan wirkt sich ebenfalls positiv auf die Oxidationsbeständigkeit sowie zusätzlich günstig auf die Schweißbarkeit aus, desoxidiert die Schmelze und bindet den Schwefel stabil ab:Of the optional alloying ingredients, the silicon improves the oxidation and carburization resistance. The manganese also has a positive effect on the oxidation resistance and additionally on the weldability, deoxidizes the melt and stably binds off the sulfur:
Niob verbessert die Zeitstandfestigkeit, bildet stabile Karbide und Karbonitride; es dient zudem als Mischkristallhärter. Titan und Tantal verbessern die Zeitstandfestigkeit. Schon bei sehr geringen Gehalten bilden sich sehr fein verteilte Karbide und Karbonitride. Bei höheren Gehalten wirken Titan und Tantal als Mischkristallhärter.Niobium improves creep strength, forms stable carbides and carbonitrides; It also serves as a mixed crystal hardener. Titanium and Tantalum improve creep strength. Even at very low levels, very finely divided carbides and carbonitrides form. At higher levels, titanium and tantalum act as mixed crystal hardeners.
Wolfram verbessert die Zeitstandfestigkeit. Insbesondere bei hohen Temperaturen verbessert Wolfram im Wege einer Mischkristallhärtung die Festigkeit, da die Karbide bei höheren Temperaturen zum Teil in Lösung gehen.Tungsten improves the creep rupture strength. Particularly at high temperatures, tungsten improves the strength by means of solid solution hardening, since the carbides partly dissolve at higher temperatures.
Kobalt verbessert ebenfalls die Zeitstandfestigkeit im Wege einer Mischkristallhärtung, Zirkonium durch die Bildung von Karbiden, insbesondere im Zusammenwirken mit Titan und Tantal.Cobalt also improves creep strength by means of solid solution hardening, zirconium through the formation of carbides, especially in conjunction with titanium and tantalum.
Yttrium und Cer verbessern offensichtlich nicht nur die Oxidationsbeständigkeit und insbesondere die Haftung sowie das Wachstum der Al2O3-Deckschicht. Zudem verbessern Yttrium und Cer schon bei sehr geringen Gehalten die Kriechbeständigkeit, da sie den etwa noch vorhandenen freien Schwefel stabil abbinden. Geringe Gehalte an Bor verbessern ebenfalls die Zeitstandfestigkeit, verhindern eine Schwefelseigerung und verzögern die Alterung durch Vergröberung der M23C6-Carbide.Yttrium and cerium obviously not only improve the oxidation resistance and especially the adhesion and growth of the Al 2 O 3 cover layer. In addition, yttrium and cerium improve the creep resistance even at very low levels, since they stably bind the remaining free sulfur. Low levels of boron also improve creep strength, prevent sulfur segregation, and retard aging by coarsening the M 23 C 6 carbides.
Auch Molybdän verbessert die Zeitstandfestigkeit insbesondere bei hohen Temperaturen im Wege einer Mischkristallhärtung. Insbesondere weil bei hohen Temperaturen die Karbide teilweise in Lösung gehen. Der Stickstoff verbessert die Zeitstandfestigkeit im Wege einer Karbonitridbildung, während Hafnium schon bei geringen Gehalten die Oxidationsbeständigkeit im Wege einer besseren Haftung der Deckschicht verbessert und sich positiv auf die Zeitstandfestigkeit auswirkt.Molybdenum also improves the creep rupture strength, especially at high temperatures, by means of solid solution hardening. Especially because at high temperatures, the carbides partially go into solution. The nitrogen improves the creep rupture strength by means of carbonitride formation, while hafnium, even at low levels, improves the oxidation resistance by means of better adhesion of the cover layer and has a positive effect on the creep rupture strength.
Phosphor, Schwefel, Zink, Blei, Arsen, Wismut, Zinn und Tellur zählen zu den Verunreinigungen, ihre Gehalte sollten daher geringstmöglich sein.Phosphorous, sulfur, zinc, lead, arsenic, bismuth, tin and tellurium are among the impurities, their contents should therefore be as low as possible.
Unter diesen Bedingungen eignet sich die Legierung insbesondere als Gusswerkstoff für Komponenten von petrochemischen Anlagen, beispielsweise zum Herstellen von Rohrschlangen für Crack- und Reformeröfen, Reformerrohre, aber auch als Werkstoff für Eisenerz-Direktreduktionsanlagen sowie für ähnlich beanspruchte Bauteile. Hierzu gehören Ofenteile, Strahlrohre zum Beheizen von Öfen, Rollen für Glühöfen, Teile von Strang- und Bandgussanlagen, Hauben und Muffen für Glühöfen, Teile von Großdieselmotoren und Formkörper für Katalysatorfüllungen.Under these conditions, the alloy is particularly suitable as a casting material for components of petrochemical plants, for example for the production of coils for cracking and reforming furnaces, reformer tubes, but also as a material for iron ore direct reduction plants and for similarly stressed components. These include furnace parts, radiant tubes for heating ovens, rolls for annealing furnaces, parts of Strip and strip casting plants, hoods and sleeves for annealing furnaces, parts of large diesel engines and shaped bodies for catalyst fillings.
Insgesamt zeichnet sich die Legierung durch eine hohe Oxidations- und Aufkohlungsbeständigkeit sowie eine gute Zeitstandsfestigkeit und Kriechfestigkeit aus. Die Innenoberfläche von Crack- oder Reformerrohren zeichnet sich zudem durch eine katalytisch inerte aluminiumhaltige Oxidschicht aus und unterbindet damit das Entstehen katalytischer Koksfäden, sogenannten Carbon-Nanotubes. Die den Werkstoff auszeichnenden Eigenschaften bleiben auch bei einem vielfachen Herausbrennen des sich beim Cracken zwangsläufig an der Innenwand der Rohre abscheidenden Kokses erhalten.Overall, the alloy is characterized by a high oxidation and carburization resistance as well as good creep strength and creep resistance. In addition, the inner surface of cracking or reformer tubes is characterized by a catalytically inert, aluminum-containing oxide layer, thus preventing the formation of catalytic coke strands, known as carbon nanotubes. The properties that characterize the material also remain with multiple burn-out of the coke which inevitably deposits on the inner wall of the pipes during cracking.
Besonders vorteilhaft ist eine Verwendung der Legierung zum Herstellen von Schleudergussrohren, wenn diese mit einem Anpressdruck von 10 bis 40 MPa, beispielsweise 10 bis 25 MPa, aufgebohrt werden. Bei einem derartigen Aufbohren kommt es aufgrund des Anpressdrucks zu einer Kaltverformung bzw. Kaltverfestigung des Rohrwerkstoffs in einer oberflächennahen Zone mit Tiefen von beispielsweise 0,1 bis 0,5 mm. Beim Aufheizen des Rohrs rekristallisiert die kaltverformte Zone, wobei es zu einem sehr feinkörnigen Gefüge kommt. Das Rekristallisationsgefüge verbessert die Diffusion der oxidbildenden Elemente Aluminium und Chrom, die das Entstehen einer vornehmlich aus Aluminiumoxid bestehenden geschlossenen Schicht mit hoher Dichte und Stabilität fördert.Particularly advantageous is a use of the alloy for producing centrifugally cast tubes, if they are drilled with a contact pressure of 10 to 40 MPa, for example 10 to 25 MPa. In such a boring occurs due to the contact pressure to a cold deformation or work hardening of the pipe material in a near-surface zone with depths of, for example, 0.1 to 0.5 mm. When the tube is heated, the cold-worked zone recrystallizes, resulting in a very fine-grained microstructure. The recrystallization structure enhances the diffusion of the oxide-forming elements aluminum and chromium, which promotes the formation of a closed layer of high density and stability consisting primarily of alumina.
Das dabei entstehende fest haftende aluminiumhaltige Oxid bildet eine geschlossene Schutzschicht der Rohrinnenwand, die weitestgehend frei von katalytisch aktiven Zentren beispielsweise aus Nickel oder Eisen und selbst nach einer längeren zyklischen Wärmebeanspruchung noch stabil ist. Diese aluminiumhaltige Oxidschicht verhindert im Gegensatz zu anderen Rohrwerkstoffen ohne eine solche Deckschicht das Eindringen von Sauerstoff in den Grundwerkstoff und damit eine innere Oxidation des Rohrwerkstoffs. Des Weiteren unterdrückt die Deckschicht nicht nur die Aufkohlung des Rohrwerkstoffs, sondern auch eine Korrosion durch Verunreinigungen im Prozessgas. Die Deckschicht besteht vornehmlich aus Al2O3 und dem Mischoxid (Al, Cr)2O3 und ist weitgehend inert gegen eine katalytische Koksbildung. Sie ist arm an Elementen, die wie Eisen und Nickel die Koksbildung katalysieren.The resulting adherent aluminum-containing oxide forms a closed protective layer of the tube inner wall, which is largely free of catalytically active centers such as nickel or iron and even after a prolonged cyclic heat stress is still stable. This aluminum-containing oxide layer prevents, in contrast to other pipe materials without such a cover layer, the penetration of oxygen into the base material and thus an internal oxidation of the pipe material. Furthermore, the cover layer suppresses not only the carburizing of the pipe material, but also corrosion by impurities in the process gas. The top layer consists mainly of Al 2 O 3 and the mixed oxide (Al, Cr) 2 O 3 and is largely inert to a catalytic coke formation. It is poor in elements that catalyze coke formation, such as iron and nickel.
Von besonderem Vorteil für die Bildung einer haltbaren oxidischen Schutzschicht ist die Wärmebehandlung, die in sehr wirtschaftlicher Weise auch in situ stattfinden kann; sie dient einer Konditionierung beispielsweise der Innenoberfläche von Steam-Cracker-Rohren nach deren Einbau, wenn der betreffende Ofen auf seine Betriebstemperatur aufgeheizt wird.Of particular advantage for the formation of a durable oxide protective layer is the heat treatment, which can take place in a very economical manner in situ; it serves to condition, for example, the inner surface of steam cracker pipes after their installation when the relevant furnace is heated to its operating temperature.
Dieses Konditionieren lässt sich als Aufheizen mit zwischengeschalteten isothermen Wärmebehandlungen in einer Ofenatmosphäre durchführen, die während des erfindungsgemäßen Aufheizens eingestellt wird, beispielsweise in einer sehr schwach oxidierenden wasserdampfhaltigen Atmosphäre mit einem Sauerstoffpartialdruck von höchstens 10-20, vorzugsweise höchstens 10-30 bar.This conditioning can be carried out as heating with interposed isothermal heat treatments in a furnace atmosphere, which is set during the heating according to the invention, for example in a very weakly oxidizing water vapor-containing atmosphere with an oxygen partial pressure of at most 10 -20 , preferably at most 10 -30 bar.
Besonders geeignet ist eine Schutzgasatmosphäre aus 0,1 bis 10 Mol-% Wasserdampf, 7 bis 99,9 Mol-% Wasserstoff und Kohlenwasserstoff einzeln oder nebeneinander sowie 0 bis 88 Mol-% Edelgase.Particularly suitable is a protective gas atmosphere of 0.1 to 10 mol% of water vapor, 7 to 99.9 mol% of hydrogen and hydrocarbon individually or side by side and 0 to 88 mol% noble gases.
Die Atmosphäre beim Konditionieren besteht vorzugsweise aus einem äußerst schwach oxidierenden Gemisch aus Wasserdampf, Wasserstoff, Kohlenwasserstoffen und Edelgasen in einem Mengenverhältnis, dass der Sauerstoffpartialdruck des Gemischs bei einer Temperatur von 600 °C geringer als 10-20 bar, vorzugsweise geringer als 10-30 bar ist.The atmosphere during the conditioning preferably consists of an extremely weakly oxidizing mixture of water vapor, hydrogen, hydrocarbons and noble gases in an amount such that the oxygen partial pressure of the mixture at a temperature of 600 ° C is less than 10 -20 bar, preferably less than 10 -30 bar is.
Das anfängliche Aufheizen des Rohrsinnern nach einem vorherigen mechanischen Abtragen einer Oberflächenschicht, d. h. das separate Aufheizen der dabei entstandenen kaltverformten Oberflächenzone geschieht vorzugsweise unter sehr schwach oxidierendem Schutzgas in mehreren Phasen jeweils mit einer Geschwindigkeit von 10 bis 100 °C/h zunächst auf 400 bis 750 °C, vorzugsweise etwa 550 °C an der die Innenoberfläche des Rohrs. Diese Aufheizphase schließt sich ein ein- bis fünfzigstündiges Halten innerhalb des erwähnten Temperaturbereich an. Das Aufheizen geschieht in Anwesenheit einer Wasserdampf-Atmosphäre, sobald die Temperatur einen Wert erreicht hat, der das Entstehen von kondensiertem Wasser ausschließt. Im Anschluss an dieses Halten wird das Rohr sodann bis auf die Betriebstemperatur, beispielsweise auf 800 bis 900 °C gebracht und ist damit betriebsbereit.The initial heating of the tube interior after a previous mechanical removal of a surface layer, d. H. the separate heating of the resulting cold-formed surface zone is preferably carried out under very weak oxidizing inert gas in several phases each at a rate of 10 to 100 ° C / h initially to 400 to 750 ° C, preferably about 550 ° C at the inner surface of the tube. This heating phase is followed by holding for one to fifty hours within the temperature range mentioned. The heating takes place in the presence of a steam atmosphere as soon as the temperature has reached a value which precludes the formation of condensed water. Following this holding the tube is then brought to the operating temperature, for example to 800 to 900 ° C and is ready for operation.
Die Rohrtemperatur erhöht sich jedoch im Crack-Betrieb allmählich als Folge des Abscheidens von pyrolytischem Koks weiter und erreicht schließlich an der Innenoberfläche etwa 1.000 °C oder auch 1.050 °C. Bei dieser Temperatur wandelt sich die im wesentlichen aus Al2O3 und in geringem Maße aus (AI, Cr)2O3 bestehende Innenschicht aus einem Übergangsoxid wie γ, δ- oder θ - Al2O3 in stabiles α-Aluminiumoxid um.However, the tube temperature gradually increases in the cracking operation as a result of the deposition of pyrolytic coke and finally reaches about 1000 ° C or even 1050 ° C on the inner surface. At this temperature, the inner layer consisting essentially of Al 2 O 3 and to a small extent of (Al, Cr) 2 O 3 converts from a transition oxide such as γ, δ or θ-Al 2 O 3 into stable α-aluminum oxide.
Damit hat das Rohr mit seiner mechanisch abgetragenen Innenschicht in einem mehrstufigen, jedoch vorzugsweise einzügigen Verfahren seinen Betriebszustand erreicht.Thus, the tube has reached its operating state with its mechanically removed inner layer in a multi-stage, but preferably einzügigen method.
Das Verfahren braucht jedoch nicht zwingend einstufig abzulaufen, sondern kann auch mit einer separaten Vorstufe beginnen. Diese Vorstufe umfasst das anfängliche Aufheizen nach dem Abtragen der Innenoberfläche bis zu dem Halten bei 400 bis 750 °C.However, the process does not necessarily have to run in one stage, but can also start with a separate preliminary stage. This precursor includes initial heating after abrading the inner surface to holding at 400 to 750 ° C.
Das so vorbehandelte Rohr kann dann beispielsweise in einer anderen Fabrikationsstätte ausgehend von seinem kalten Zustand in der oben beschriebenen Weise in situ weiterbehandelt, d. h. im eingebauten Zustand auf die Betriebstemperatur gebracht werden.The pipe thus pretreated can then be further processed in situ, for example in another manufacturing facility, starting from its cold state in the manner described above, that is to say in another factory. H. be brought to the operating temperature in the installed state.
Die erwähnte separate Vorbehandlung ist allerdings nicht auf Rohre beschränkt, sondern eignet sich auch für eine partielle oder auch vollständige Konditionierung von Oberflächenzonen anderer Werkstücke, die sodann entsprechend ihrer Beschaffenheit und Verwendung weiterbehandelt werden wie nach der Erfindung oder auch nach anderen Verfahren, jedoch mit einem definierten Ausgangszustand.The mentioned separate pre-treatment is not limited to tubes, but is also suitable for a partial or complete conditioning of surface zones of other workpieces, which are then treated according to their nature and use as in the invention or by other methods, but with a defined initial state.
Die Erfindung wird nachfolgend beispielhaft anhand von fünf Nickellegierungen, die im Unterschied zu der im Anspruch 1 beanspruchten Legierung noch geringe Rest an Kobalt enthalten, im Vergleich mit zehn herkömmlichen Nickellegierungen erläutert, deren Zusammensetzung sich aus Tabelle I ergibt und die sich insbesondere hinsichtlich ihrer Gehalte an Kohlenstoff (Legierungen 5 und 6), Chrom (Legierungen 4, 13 und 14), Aluminium (Legierungen 12, 13), Kobalt (Legierungen 1, 2) und Eisen (Legierungen 3, 12, 14, 15), von der erfindungsgemäßen Nickel-Chrom-Eisen-Legierung unterscheiden.The invention will be explained below by way of example with reference to five nickel alloys, which, unlike the claimed in
Wie sich aus dem Diagramm gemäß Bild 1 ergibt, kommt es bei der Legierung 9 nach einem fünfundvierzigminütigen Glühen bei 1.150 °C an Luft auch bei mehr als 200 Zyklen zu keinerlei Innenoxidation, während die beiden Vergleichslegierungen 12 und 13 schon nach wenigen Zyklen einer zunehmenden Gewichtsabnahme als Folge einer katastrophalen Oxidation unterliegen.As can be seen from the diagram in Fig. 1,
Des Weiteren zeichnet sich die Legierung 9 auch durch eine hohe Aufkohlungsbeständigkeit aus; denn sie besitzt nach dem Diagramm des Bildes 2 aufgrund der geringen Gewichtszunahme nach allen drei Aufkohlungsbehandlungen die geringste Gewichtszunahme im Vergleich zu den herkömmlichen Legierungen 12 und 13.Furthermore, the
Weiterhin zeigen die Diagramme der Bilder 3a und 3b, dass die Zeitstandfestigkeit der Nickellegierung 11 in einem wesentlichen Bereich noch besser ist als bei den beiden Vergleichslegierungen 12 und 13. Eine Ausnahme bildet hier die wegen ihres zu geringen Eisengehalts nicht unter die Erfindung fallende Legierung 15, mit ihrer jedoch wesentlich schlechteren Oxidations-, Aufkohlungs- und Verkokungsbeständigkeit.Furthermore, the diagrams of FIGS. 3a and 3b show that the creep strength of the
Schließlich ergibt sich aufgrund des Diagramms nach Bild 4, dass die Kriechfestigkeit der Legierung 11 weitaus besser ist, als diejenige der Vergleichslegierung 12.Finally, based on the diagram according to FIG. 4, the creep strength of the
Des weiteren wurden bei der Simulationsreihe eines Crack-Betriebes mehrere Rohrabschnitte aus einer erfindungsgemäßen Nickellegierung in einer Laboranlage eingesetzt, um Aufheizversuche mit unterschiedlichen Gasatmosphären und Aufheizbedingungen durchzuführen, denen sich eine dreißigminütige Crackphase bei einer Temperatur von 900 °C anschloss, um die Anfangsphase der katalytischen Koksbildung, bzw. die Neigung zur katalytischen Koksbildung zu untersuchen und zu bewerten.Furthermore, in the simulation series of a cracking operation, several pipe sections of a nickel alloy according to the invention were used in a laboratory plant to carry out heating experiments with different gas atmospheres and heating conditions, followed by a thirty minute cracking phase at a temperature of 900 ° C to the initial phase of the catalytic coke formation , and to investigate and assess the tendency for catalytic coke formation.
Die Daten und die Ergebnisse dieser Versuche mit Proben der Legierung 11 aus Tabelle I sind in der Tabelle II zusammengestellt. Sie zeigen, dass die jeweilige Gasatmosphäre in Verbindung mit einer erfindungsgemäßen Temperatursteuerung mit einer erheblichen Reduzierung der ohnehin geringen katalytischen Koksbildung verbunden ist.The data and the results of these experiments with samples of
Beispiele für die Oberflächenbeschaffenheit des Rohrinneren von Ofenrohren mit der Zusammensetzung der Legierung 8 ergeben sich aus den Abbildungen 5 und 6. Die
In den Bildern 7 (Legierung 14) und 8 sind oberflächennahe Bereiche im Querschliff dargestellt. Die Proben wurden auf 950 °C aufgeheizt und unterlagen sodann 10 Crack-Zyklen von jeweils 10 Stunden in einer Atmosphäre aus Wasserdampf, Wasserstoff und Kohlenwasserstoffen. Nach jedem Zyklus wurden die Proberohre zum Entfernen der Koksablagerungen eine Stunde ausgebrannt. Dazu zeigt die Gefügeaufnahme des Bildes 7 in Gestalt der dunklen Bereiche das großflächige und damit auch großvolumige Ergebnis einer inneren Oxidation an der Innenseite eines Rohrs bei einer herkömmlichen Nickel-Chrom-Gusslegierung im Vergleich zu der Gefügeaufnahme des Bildes 8 der Legierung 9, die praktisch keiner Innenoxidation unterlag, obgleich beide Proben in gleicher Weise einer mehrfachen zyklischen Behandlung aus Cracken einerseits und Entfernen der Kohlenstoffablagerungen andererseits unterworfen wurden.Shown in Figures 7 (Alloy 14) and 8 are shallow areas in cross section. The samples were heated to 950 ° C and then subjected to 10 crack cycles of 10 hours each in an atmosphere of water vapor, hydrogen and hydrocarbons. After each cycle, the sample tubes were burned out for one hour to remove the coke deposits. For this purpose, the micrograph of the
Die Versuche zeigen, dass es bei den Proben aus den herkömmlichen Legierungen ausgehend von Oberflächendefekten zu einer starken inneren Oxidation auf der Rohrinnenseite kommt. Dadurch bedingt entstehen auf der inneren Rohroberfläche kleine metallische Zentren mit einem hohen Anteil an Nickel, an denen sich in erheblichem Maße Kohlenstoff in Form von Carbon-Nanotubes bildet (Bild 11).The experiments show that in the samples from the conventional alloys, starting from surface defects, there is a strong internal oxidation on the inside of the tube. As a result, small metallic centers with a high proportion of nickel are formed on the inner surface of the tube, which forms a considerable amount of carbon in the form of carbon nanotubes (Figure 11).
Die Probe 9 weist hingegen nach demselben zehnfachen zyklischen Cracken und einem anschließenden Auslagern in einer Verkokungsatmosphäre keine Carbon-Nanotubes auf, was auf eine im wesentlichen durchgehend dichte, katalytisch inerte aluminiumhaltige Oxidschicht zurückzuführen ist. Dagegen betrifft Bild 11 eine REM-Draufsicht der in Bild 7 im Schliff dargestellten herkömmlichen Probe; sie zeigt aufgrund der fehlenden Deckschicht eine katastrophale Oxidation und ein dementsprechend katastrophales Entstehen von katalytischem Koks in Gestalt von Carbon-Nanotubes.The
Besonders anschaulich zeigt sich die Stabilität der Oxidschicht auf einer erfindungsgemäßen Legierung anhand des Verlaufs der Aluminiumkonzentration über die Tiefe der Randzone nach zehn Crackphasen mit jeweiligem Entfernen der Koksablagerungen durch Ausbrennen in einer Zwischenphase bei einem Vergleich der Diagramme nach Bild 9 und 10. Während nach dem Diagramm des Bildes 9 im oberflächennahen Bereich infolge des lokalen Versagens der schützenden Deckschicht und danach einsetzender starker innerer Aluminiumoxidation der Werkstoff an Aluminium verarmt ist, bewegt sich die Aluminiumkonzentration bei dem Diagramm des Bildes 10 in etwa auf dem Ausgangsniveau des Gusswerkstoffs. Hier zeigt sich deutlich die Bedeutung einer durchgehenden, dichten und insbesondere fest haftenden inneren aluminiumhaltigen Oxidschicht bei den Rohren nach der Erfindung.The stability of the oxide layer on an alloy according to the invention is particularly clear from the course of the aluminum concentration over the depth of the edge zone after ten cracking phases with respective removal of the coke deposits by burnout in an intermediate phase when the diagrams according to FIGS. 9 and 10 are compared of the
Die Stabilität der aluminiumhaltigen Oxidschicht wurde ebenfalls durch Langzeitversuche in einer Laboranlage unter prozessnahen Bedingungen untersucht. Die Proben der Legierungen 9 und 11 wurden unter Wasserdampf auf 950 °C aufgeheizt und unterlagen sodann jeweils dreimal einem 72-stündigen Cracken bei dieser Temperatur; sie wurden sodann jeweils vier Stunden einem Ausbrennen bei 900 °C unterworfen. Die Aufnahme des Bildes 12 zeigt die geschlossene aluminiumhaltige Oxidschicht nach den drei Crackzyklen und darüber hinaus, wie die aluminiumhaltige Oxidschicht den Werkstoff selbst über Chromkarbide in der Oberfläche hinweg abdeckt. Es ist erkennbar, dass an der Oberfläche vorhandene Chromkarbide von der aluminiumhaltigen Oxidschicht vollständig überdeckt sind.The stability of the aluminum-containing oxide layer was also investigated by long-term tests in a laboratory plant under process-related conditions. The samples of
Selbst in gestörten Oberflächenbereichen, in denen primäre Karbide des Grundwerkstoffs gehäuft vorliegen und die deshalb besonders anfällig für eine innere Oxidation sind, wird der Werkstoff durch eine gleichmäßige aluminiumhaltige Oxidschicht geschützt, wie dies die Gefügeaufnahme des Bildes 13 deutlich macht. Es ist erkennbar, wie oxidiertes ehemaliges MC-Karbid von aluminiumhaltigem Oxid überwachsen und somit gekapselt ist.Even in disturbed surface areas, in which primary carbides of the base material are heaped up and therefore particularly susceptible to internal oxidation, the material is protected by a uniform aluminum-containing oxide layer, as the micrograph of the
Die Gefügeaufnahmen der oberflächennahen Zone nach den Bildern 14 und 15 zeigen, dass selbst nach den zyklischen Langzeitversuchen keine innere Oxidation aufgetreten ist, was durch die stabile und durchgehende aluminiumhaltige Oxidschicht bedingt ist. Bei diesen Versuchen wurden Proben der Legierungen 8 bis 11 eingesetzt.The micrographs of the near-surface zone according to Figures 14 and 15 show that even after the long-term cyclic tests, no internal oxidation has occurred, which is due to the stable and continuous aluminum-containing oxide layer. In these experiments, samples of
Insgesamt zeichnet sich die erfindungsgemäße Nickel-Chrom-Eisen-Legierung beispielsweise als Rohrwerkstoff nach einem Abtragen der Innenoberfläche unter mechanischem Druck und einer sich anschließenden mehrstufigen In-situ-Wärmebehandlung zum Konditionieren der Innenoberfläche durch eine hohe Oxidations-, Korrosions- und insbesondere durch eine hohe Zeitstandfestigkeit und Kriechbeständigkeit aus.Overall, the inventive nickel-chromium-iron alloy is characterized, for example, as a pipe material after removal of the inner surface under mechanical pressure and a subsequent multi-stage in situ heat treatment for conditioning the inner surface by a high oxidation, corrosion and especially high Creep rupture and creep resistance.
Besonders hervorzuheben ist jedoch vor allem die außerordentliche Aufkohlungsbeständigkeit des Werkstoffs, die durch einen raschen Aufbau einer im wesentlichen geschlossenen und stabilen Oxid- bzw. Al2O3-Schicht bedingt ist. Vor allem auch unterdrückt diese Schicht bei Steam-Cracker- und Reformerrohren weitestgehend das Entstehen von katalytisch aktiven Zentren mit der Gefahr einer katalytischen Koksbildung. Diese Werkstoffeigenschaften gehen auch nicht nach einer Vielzahl von jeweils deutlich verlängerten Crack-Zyklen, verbunden jeweils mit einem Ausbrennen des abgelagerten Kokses, verloren.
**: Nach Erreichen der Betriebstemperatur 1 h Behandlung mit 250 ppm Schwefel (H2S) in Wasserdampf.
**: After reaching operating temperature for 1 h treatment with 250 ppm sulfur (H 2 S) in water vapor.
Claims (15)
- A nickel-chromium alloy with high resistance to oxidation and carburisation and high creep rupture strength and creep resistance, formed of0.4 to 0.6% carbon28 to 33% chromium15 to 25% iron2 to 6% aluminiumup to 2% siliconup to 2% manganeseup to 1.5% niobiumup to 1.5% tantalumup to 1.0% tungstenup to 1.0% titaniumup to 1.0% zirconiumup to 0.5% yttriumup to 0.5% ceriumup to 0.5% molybdenumup to 0.1% nitrogenthe rest being formed by nickel inclusive of melting-related impurities.
- The alloy according to claim 1, but containing, individually or in combination,0.4 to 0.6% carbon28 to 33% chromium17 to 22% iron3 to 4.5% aluminium0.01 to 1% silicon0.01 to 0.5% manganese0.01 to 1.0% niobium0.01 to 0.5% tantalum0.01 to 0.6% tungsten0.001 to 0.5% titanium0.001 to 0.3% zirconium0.001 to 0.3% yttrium0.001 to 0.3% cerium0.01 to 0.5% molybdenum0.001 to 0.1% nitrogen.
- A method for at least partial conditioning of objects made of an alloy according to claim 1 or 2 in a surface zone by mechanical removal with a contact pressure of from 10 to 40 MPa and subsequent heating with a heating rate of from 10 to 100°C/h to a temperature at the surface of from 400 to 740°C under weakly oxidising conditions with avoidance of condensate formation.
- The method according to claim 3, characterised in that the contact pressure is 15 to 30 Mpa.
- The method according to claim 3 or 4, characterised in that the heating takes place under inert gas.
- The method according to claim 3 to 5, characterised in that, during the removal, a surface zone of from 0.1 to 0.5 mm depth is cold-formed.
- The method according to any one of claims 3 to 6, characterised by a subsequent annealing, holding for one to fifty hours at 400 to 750°C, and a subsequent heating at a rate of from 10 to 100°C/h to the operating temperature.
- The method according to claim 7, characterised in that the holding temperature is 550 to 650°C.
- The method according to any one of claims 7 to 8, characterised in that the annealing atmosphere consists of a weakly oxidising mixture of water vapour, hydrogen, hydrocarbons, and noble gases with an oxygen partial pressure at 600°C below 10-20.
- The method according to claim 9, characterised by an oxygen partial pressure below 10-30 bar.
- The method according to any one of claims 3 to 10, characterised in that the annealing atmosphere consists of 0.1 to 10 mol % water vapour, 7 to 99.9 mol % hydrogen and hydrocarbons individually or in combination, and 0 to 88 mol % noble gases individually or in combination.
- Use of an alloy according to one or more of claims 1 to 11 as material for producing cast parts.
- Use of an alloy according to one or more of claims 1 to 11 as material for petrochemical installations.
- Use of an alloy according to one or more of claims 1 to 11 as material for pipe coils of cracking and reformer furnaces, preheaters, reformer tubes and iron direct-reduction installations.
- Use of an alloy according to one or more of claims 1 to 11 as material for producing furnace parts, radiant tubes for heating furnaces, rollers for annealing furnaces, parts of extrusion and strip casting installations, hoods and sleeves for annealing furnaces, parts of large diesel engines and moulded articles for catalyst charges.
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EP19172613.2A EP3550045A1 (en) | 2008-10-13 | 2009-10-13 | Nickel-chromium alloy |
PL17207317T PL3330390T3 (en) | 2008-10-13 | 2009-10-13 | Nickel-chromium alloy |
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DE102008051014A DE102008051014A1 (en) | 2008-10-13 | 2008-10-13 | Nickel-chromium alloy |
PCT/EP2009/007345 WO2010043375A1 (en) | 2008-10-13 | 2009-10-13 | Nickel-chromium alloy |
EP09744619.9A EP2350329B1 (en) | 2008-10-13 | 2009-10-13 | Nickel-chromium alloy |
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PCT/EP2009/007345 Previously-Filed-Application WO2010043375A1 (en) | 2008-10-13 | 2009-10-13 | Nickel-chromium alloy |
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