EP2227572A1 - Austenitic heat-resistant nickel-base alloy - Google Patents
Austenitic heat-resistant nickel-base alloyInfo
- Publication number
- EP2227572A1 EP2227572A1 EP08865541A EP08865541A EP2227572A1 EP 2227572 A1 EP2227572 A1 EP 2227572A1 EP 08865541 A EP08865541 A EP 08865541A EP 08865541 A EP08865541 A EP 08865541A EP 2227572 A1 EP2227572 A1 EP 2227572A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- max
- alloy according
- mass
- sum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 51
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 51
- 238000004519 manufacturing process Methods 0.000 claims abstract description 9
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 20
- 239000000463 material Substances 0.000 claims description 20
- 229910052719 titanium Inorganic materials 0.000 claims description 13
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 9
- 229910052796 boron Inorganic materials 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 6
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 229910052735 hafnium Inorganic materials 0.000 claims description 5
- 229910052717 sulfur Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 229910052797 bismuth Inorganic materials 0.000 claims description 2
- 229910052709 silver Inorganic materials 0.000 claims description 2
- 238000005260 corrosion Methods 0.000 description 29
- 230000007797 corrosion Effects 0.000 description 29
- 239000010936 titanium Substances 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 229910052782 aluminium Inorganic materials 0.000 description 8
- 239000011572 manganese Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 238000007792 addition Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 230000008092 positive effect Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical group [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 230000003628 erosive effect Effects 0.000 description 2
- 230000002349 favourable effect Effects 0.000 description 2
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 description 2
- 238000011835 investigation Methods 0.000 description 2
- 230000007774 longterm Effects 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 238000005486 sulfidation Methods 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 241000080590 Niso Species 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000009533 lab test Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000010248 power generation Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000003856 thermoforming Methods 0.000 description 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
-
- 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
- the invention relates to an austenitic heat-resistant nickel-based alloy.
- Alloy 81 with (in% by mass) 0.05% C, 30% Cr, 66% Ni, 0.9% Al and 1.8% Ti was used.
- these alloys are used as valve base materials, wherein the valve seat section is additionally coated with an abrasion-resistant material, as described for example in EP-B 0521821.
- This document gives the chemical composition (in mass%) of the base material as follows: 0.04 - 0.10% C 1 ⁇ 1, 0% Si, ⁇ 0.2% Cu, ⁇ 1, 0% Fe, ⁇ 1, 9% Mn, 18-21% Cr, 1, 8-2.7% Ti, 1, 0-1, 8% Al, ⁇ 2.0% Co, ⁇ 0.3% Mo, B, Zr, Rest of nickel.
- a variant of this alloy is also mentioned among other things with 29 - 31% Cr.
- 6,039,919 which describe an alloy of the following composition (in% by mass) for intake and exhaust valves of diesel engines, relate to this: ⁇ 0.1% C, ⁇ 1.0% Si , ⁇ 0.1% Mn, ⁇ 25 - ⁇ 32.2% Cr, ⁇ 3% Ti,> 1 - ⁇ 2% Al, balance Ni. But even this alloy does not provide sufficient hot corrosion resistance. In addition, in the future, more powerful engines, such as marine diesel engines, are operated at temperatures up to about 850 ° C, which also makes higher demands on the valve material, especially since the service life is to be maintained and no additional maintenance is desired.
- DE-C 101 23 566 discloses an austenitic heat-resistant nickel-based alloy which has the following composition (in% by mass): 0.03-0.1% C, max. 0.005% S, max. 0.05% N, 25-35% Cr, max. 0.2% Mn, max. 0.1% Si, max. 0.2% Mo, 2 - 3% Ti, 0.02 - 1, 1% Nb, max. 0.1% Cu, max. 1% Fe, max. 0.08% P, 0.9-1.3% AI, max. 0.01% Mg, 0.02 - 0.1% Zr, max. 0.2% Co, the sum of Al + Ti + Nb being> 3.5%, the remainder being Ni and production-related conditions.
- the alloy is characterized by additions of (in% by mass) 0.001-0.005% B, 0.01-0.04% Hf, and 0.01-0.04% Y.
- the invention has for its object, up to a temperature of 850 ° C hot corrosion resistant material with mechanical properties which are not inferior to those of Alloy 80 A.
- Remaining Ni and production-related admixtures where the sum of Ti + Al is between 3.3 and 4.3%, the sum of C + (10 x B) is between 0.05 and 0.2%, the sum of Hf + Zr is between 0.05 and 0.15% and the ratio Ti / Al> 3.
- the material of the invention as a valve material is generally applicable and can be used in particular for future generations of marine diesel engines in the temperature range up to 850 ° C.
- Table 1 shows an example of the chemical composition of two inventive examples E1 and E2.
- two typical analyzes of the commercial alloys Alloy 80 A and Alloy 81 are listed.
- the analyzes of the alloys E1 and E2 were obtained from a series of laboratory melts, which were melted in 10 kg blocks in the vacuum induction furnace, then hot rolled and solution heat treated at 1180 ° C for two hours in air with subsequent water quenching. The hardening of the alloys took place by two further annealing:
- the alloys differed in the content of the elements discussed below, so that the evaluation of their mechanical properties and their behavior in the corrosive medium led to the analysis according to the invention.
- the atmosphere was air with an SO 2 content of 0.5%.
- the samples were swapped out at both 750 ° C and 850 ° C for 20 hours, 100 hours and 400 hours, respectively.
- the ash was renewed after 100 hours, 200 hours and 300 hours to maintain the corrosiveness.
- the depth of the internal corrosion could be reliably measured.
- the Cr content must be as high as possible from the corrosion point of view. Metallurgically, however, 32% is a sensible upper limit. This shows the clear difference between the alloy variants with about 30% Cr and those with 20% Cr. The corrosion attack in the first mentioned alloys is at best only half as large.
- the samples tested in the valve with a Cr content of 30% show a cobblestone-like appearance on macro photographs, which is reflected in the micrographs as a wavy sample surface, which is indicative of only moderate corrosion erosion. In contrast, the poorer samples already show strong even flaking.
- Ti, Al A TkAI ratio of> 3 results in better corrosion resistance than lower Ti: Al ratios. This is attributed to the formation of a Ti-rich seam between the outer oxide layer and the region of internal sulfidation at high Ti contents.
- Aluminum and titanium have a positive effect on the heat resistance due to the formation of ⁇ '-phase.
- the sum of the elements Al + Ti should advantageously be between 3.5 and 4.3%. Too high a total content of these elements makes the thermoforming of the material difficult.
- Si Silicon has been found to have no positive effect on corrosion properties and should be no more than 0.5%, better less than 0.1%.
- Nb The niobium-alloyed samples basically have the thinnest corrosion layer, but this has no effect on the material loss itself Protective corrosion layer acts against the progression of the corrosion attack, the Nb content should be limited to a maximum of 0.5%. Furthermore, the Nb influences the material strength due to its high solubility in the ⁇ '-phase. At lower Nb levels below 0.5%, the Ti and Al content need not be adjusted.
- B, C The addition of boron at levels of 0.002 - 0.01% improves corrosion resistance by reducing the internal sulfidation, which preferably proceeds along the grain boundaries, and thus reducing overall corrosion attack.
- Carbon preferably forms Cr carbides at the grain boundaries.
- Boron forms borides, which contribute to the stabilization of the grain boundaries and thus to long-term stability.
- the forming Cr carbides lead to a Cr depletion in the vicinity of the grain boundaries, which is why at a high C content, the corrosion accelerated progresses.
- carbides and borides must not overburden the grain boundaries, as they then hard precipitates greatly reduce the ductility of the material.
- the sum of C + (10 x B) should not exceed 0.1%.
- said sum is about 0.08%.
- Hf Hafnium is often added to improve the high temperature oxidation resistance and obviously also influences the durability of the samples in vanadium ash and SO 2 atmosphere positively. Furthermore, Hf also changes the grain boundary properties under carbide or carbosulfide formation. Too high an HF content should be avoided, as otherwise the hot forming is no longer guaranteed. This results in a favorable concentration range between 0.02 and 0.08%, preferably 0.05%. The effect of Hf on the grain boundaries is comparable to the effect of Zr, which is why the empirical formula Hf + Zr ⁇ 0.10% advantageously results.
- Zr Zirconium forms carbosulfides, which have a positive effect on the long-term strength and also contribute to the hot corrosion resistance by the binding of sulfur. It turned out that a Zr content between 0.01 and 0.05%. The aim is to have a Zr content in the range of 0.02%.
- Co is an element that in principle increases the resistance to sulfur-containing media. On the other hand, it is also very expensive, which is why the co-alloying of Co is dispensed with. Due to admixtures in the feedstocks, however, the Co content can reach up to 2% without incurring increased costs.
- the element iron occurs i.a. as an accompaniment element. Reducing the iron content to well below 1% increases the costs, since higher-quality starting materials would have to be selected. With a Fe content limited to 3%, you do not have to expect a significant deterioration of the corrosion resistance and not too high costs of the starting materials. However, an Fe content below 1% should be sought.
- Mn The conditions mentioned for Fe also apply to Mn, whereby the Mn content can be reduced to less than 1% without much effort.
- the alloy can be prepared by the usual methods of a melt operation, advantageously a melting in a vacuum with subsequent remelting in the electroslag process is useful.
- a melting in a vacuum with subsequent remelting in the electroslag process is useful.
- the formability for the production of rods for further processing to valves, such as marine diesel valves, is given.
- the alloy according to the invention is also particularly suitable for the production of valves for large diesel engines in general, that is, for example, for such large diesel engines that are used in stationary facilities for power generation.
Abstract
Description
Claims
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE102007062417A DE102007062417B4 (en) | 2007-12-20 | 2007-12-20 | Austenitic heat-resistant nickel-based alloy |
PCT/DE2008/001964 WO2009079972A1 (en) | 2007-12-20 | 2008-11-25 | Austenitic heat-resistant nickel-base alloy |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2227572A1 true EP2227572A1 (en) | 2010-09-15 |
EP2227572B1 EP2227572B1 (en) | 2016-01-27 |
Family
ID=40445808
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP08865541.0A Active EP2227572B1 (en) | 2007-12-20 | 2008-11-25 | Austenitic heat-resistant nickel-base alloy |
Country Status (7)
Country | Link |
---|---|
US (1) | US20100310412A1 (en) |
EP (1) | EP2227572B1 (en) |
JP (1) | JP2011506771A (en) |
KR (1) | KR101236222B1 (en) |
CN (1) | CN101896630A (en) |
DE (1) | DE102007062417B4 (en) |
WO (1) | WO2009079972A1 (en) |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US9050682B2 (en) | 2010-11-16 | 2015-06-09 | Daniel R. Danks | Electroslag welding with alternating electrode weld parameters |
CN102876953A (en) * | 2012-09-27 | 2013-01-16 | 无锡宏昌五金制造有限公司 | High-temperature nickel-chromium alloy |
CN103882263A (en) * | 2012-12-19 | 2014-06-25 | 江苏龙鑫特殊钢实业总公司 | Nickel-based alloy for nuclear power steam generator vibration-resisting strips and application thereof |
CN104451655B (en) * | 2013-09-13 | 2018-02-16 | 中国科学院金属研究所 | High temperature resistance material surface alloy coating composite material, coating and preparation method thereof |
DE102014001330B4 (en) | 2014-02-04 | 2016-05-12 | VDM Metals GmbH | Curing nickel-chromium-cobalt-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and processability |
DE102014001329B4 (en) * | 2014-02-04 | 2016-04-28 | VDM Metals GmbH | Use of a thermosetting nickel-chromium-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and processability |
DE102014001328B4 (en) * | 2014-02-04 | 2016-04-21 | VDM Metals GmbH | Curing nickel-chromium-iron-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and processability |
CN105838925B (en) * | 2015-01-12 | 2017-11-28 | 宝钢特钢有限公司 | High temperature oxidation resisting nickel-base alloy |
CN104862532B (en) * | 2015-04-22 | 2017-01-11 | 苏州劲元油压机械有限公司 | Nickel alloy wire for oil filter screen and manufacturing process thereof |
CN104818430A (en) * | 2015-05-15 | 2015-08-05 | 钢铁研究总院 | Nickel-saving high-temperature-resistant gas valve alloy |
JP6739187B2 (en) * | 2016-02-22 | 2020-08-12 | 株式会社神戸製鋼所 | Ni-based alloy solid wire for welding and method for producing Ni-based alloy weld metal |
CN106498236B (en) * | 2016-10-26 | 2017-11-10 | 济宁市北辰金属材料有限公司 | A kind of glass fibre production alloy crucible and preparation method thereof |
JP6842316B2 (en) * | 2017-02-17 | 2021-03-17 | 日本製鋼所M&E株式会社 | Manufacturing method of Ni-based alloy, gas turbine material and Ni-based alloy with excellent creep characteristics |
EP3620628A1 (en) | 2018-09-04 | 2020-03-11 | Winterthur Gas & Diesel Ltd. | Pre-chamber |
CN109022922A (en) * | 2018-09-22 | 2018-12-18 | 广州宇智科技有限公司 | A kind of corrosion-resistant liquid spinodal decomposition type nickel alloy of ship power system condenser |
CN109112363A (en) * | 2018-09-22 | 2019-01-01 | 广州宇智科技有限公司 | A kind of corrosion-resistant liquid spinodal decomposition type nickel alloy of lithium bromide refrigerator |
Family Cites Families (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE3043457A1 (en) * | 1980-11-18 | 1982-07-08 | Klöckner-Humboldt-Deutz AG, 5000 Köln | HEATING SYSTEM |
DE3778731D1 (en) * | 1986-01-20 | 1992-06-11 | Sumitomo Metal Ind | NICKEL-BASED ALLOY AND METHOD FOR THEIR PRODUCTION. |
GB8922161D0 (en) * | 1989-10-02 | 1989-11-15 | Inco Alloys Ltd | Exhaust valve alloy |
DE59206839D1 (en) * | 1991-07-04 | 1996-09-05 | New Sulzer Diesel Ag | Exhaust valve of a diesel engine and method of manufacturing the valve |
JPH10219377A (en) * | 1997-02-07 | 1998-08-18 | Daido Steel Co Ltd | Manufacture of high corrosion resistant valve for intake and exhaust valve for diesel engine and intake and exhaust valve |
JPH1122427A (en) * | 1997-07-03 | 1999-01-26 | Daido Steel Co Ltd | Manufacture of diesel engine valve |
DE10123566C1 (en) * | 2001-05-15 | 2002-10-10 | Krupp Vdm Gmbh | Nickel-based austenitic alloy used as a valve material for diesel engines of ships contains alloying additions of carbon, chromium, aluminum and zirconium |
EP1586669B1 (en) * | 2004-04-07 | 2014-05-21 | United Technologies Corporation | Oxidation resistant superalloy and article |
-
2007
- 2007-12-20 DE DE102007062417A patent/DE102007062417B4/en not_active Expired - Fee Related
-
2008
- 2008-11-25 US US12/808,612 patent/US20100310412A1/en not_active Abandoned
- 2008-11-25 JP JP2010538321A patent/JP2011506771A/en active Pending
- 2008-11-25 CN CN2008801199142A patent/CN101896630A/en active Pending
- 2008-11-25 KR KR1020107013401A patent/KR101236222B1/en active IP Right Grant
- 2008-11-25 WO PCT/DE2008/001964 patent/WO2009079972A1/en active Application Filing
- 2008-11-25 EP EP08865541.0A patent/EP2227572B1/en active Active
Non-Patent Citations (1)
Title |
---|
See references of WO2009079972A1 * |
Also Published As
Publication number | Publication date |
---|---|
US20100310412A1 (en) | 2010-12-09 |
JP2011506771A (en) | 2011-03-03 |
DE102007062417A1 (en) | 2009-06-25 |
KR101236222B1 (en) | 2013-02-22 |
DE102007062417B4 (en) | 2011-07-14 |
KR20100083847A (en) | 2010-07-22 |
WO2009079972A1 (en) | 2009-07-02 |
CN101896630A (en) | 2010-11-24 |
EP2227572B1 (en) | 2016-01-27 |
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