US20050129567A1 - Thermostable and corrosion-resistant cast nickel-chromium alloy - Google Patents

Thermostable and corrosion-resistant cast nickel-chromium alloy Download PDF

Info

Publication number
US20050129567A1
US20050129567A1 US10/945,859 US94585904A US2005129567A1 US 20050129567 A1 US20050129567 A1 US 20050129567A1 US 94585904 A US94585904 A US 94585904A US 2005129567 A1 US2005129567 A1 US 2005129567A1
Authority
US
United States
Prior art keywords
chromium
nickel
aluminum
alloy
alloys
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.)
Abandoned
Application number
US10/945,859
Other languages
English (en)
Inventor
Rolf Kirchheiner
Dietlinde Jakobi
Petra Becker
Ricky Durham
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Schmidt and Clemens GmbH and Co KG
Original Assignee
Schmidt and Clemens GmbH and Co KG
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Schmidt and Clemens GmbH and Co KG filed Critical Schmidt and Clemens GmbH and Co KG
Priority to US10/945,859 priority Critical patent/US20050129567A1/en
Assigned to SCHMIDT + CLEMENS GMBH + CO. KG reassignment SCHMIDT + CLEMENS GMBH + CO. KG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: BECKER, PETRA, DURHAM, RICKY, JAKOBI, DIETLINDE, KIRCHHEINER, ROLF
Publication of US20050129567A1 publication Critical patent/US20050129567A1/en
Priority to US12/169,229 priority patent/US10041152B2/en
Priority to US16/055,645 priority patent/US10724121B2/en
Abandoned legal-status Critical Current

Links

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
    • 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
    • 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%
    • 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
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • 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

Definitions

  • the present invention relates to a thermostable and corrosion-resistant cast nickel-chromium alloy.
  • High-temperature processes for example those used in the petrochemical industry, require materials which are not only heat-resistant but also sufficiently corrosion-resistant and in particular are able to withstand the loads imposed by hot product and combustion gases.
  • the tube coils used in cracking and reformer furnaces are externally exposed to strongly oxidizing combustion gases with a temperature of up to 1100° C. and above, whereas a strongly carburizing atmosphere at temperatures of up to 1100° C. prevails in the interior of cracking tubes, and a weakly carburizing, differently oxidizing atmosphere prevails in the interior of reformer tubes at temperatures of up to 900° C. and a high pressure.
  • contact with the hot combustion gases leads to nitriding of the tube material and to the formation of a layer of scale, which is associated with an increase in the external diameter of the tube by a few percent and a reduction in the wall thickness by up to 10%.
  • the carburizing atmosphere inside the tube causes carbon to diffuse into the tube material, where, at temperatures of over 900° C., it leads to the formation of carbides, such as M 23 C 6 , and, with increasing carburization, to the formation of the carbon-rich carbide M 7 C 3 .
  • carbides such as M 23 C 6
  • carburization to the formation of the carbon-rich carbide M 7 C 3 .
  • the consequence of this is internal stresses resulting from the increase in volume associated with the carbide formation or transformation and a decrease in the strength and ductility of the tube material.
  • graphite or dissociation carbon may form in the interior of the tube material, which can, in combination with internal stresses, lead to the formation of cracks, which in turn cause more carbon to diffuse into the tube material.
  • high-temperature processes require materials with a high creep strength or limiting rupture stress, microstructural stability and resistance to carburization and oxidation.
  • This requirement is—within limits—satisfied by alloys which, in addition to iron, contain 20 to 35% of nickel, 20 to 25% of chromium and, to improve the resistance to carburization, up to 1.5% of silicon, such as for example the nickel-chromium steel alloy 35Ni25Cr-1.5Si, which is suitable for centrifugally cast tubes and is still resistant to oxidation and carburization even at temperatures of 1100° C.
  • the high nickel content reduces the diffusion rate and the solubility of the carbon and therefore increases the resistance to carburization.
  • the alloys form a covering layer of Cr 2 O 3 , which acts as a barrier layer preventing the penetration of oxygen and carbon into the tube material beneath it.
  • the Cr 2 O 3 becomes volatile, and consequently the protective action of the covering layer is rapidly lost.
  • the resistance to carburization and oxidation is further put at risk by the limited creep rupture strength and ductility of the conventional nickel-chromium alloys, which lead to the formation of creep cracks in the chromium oxide covering layer and to the penetration of carbon and oxygen into the tube material via the cracks.
  • covering layer cracks may form and also the covering layer may become partially detached.
  • microstructural phase reactions in particular at higher silicon contents, for example of over 2.5%, evidently lead to a loss of ductility and to a reduction in the short-time strength.
  • a nickel-chromium casting alloy having defined aluminum and yttrium contents and comprising up to 0.8% of carbon up to 1% of silicon up to 0.2% of manganese 15 to 40% of chromium 0.5 to 13% of iron 1.5 to 7% of aluminum up to 2.5% of niobium up to 1.5% of titanium 0.01 to 0.4% of zirconium up to 0.06% of nitrogen up to 12% of cobalt up to 5% of molybdenum up to 6% of tungsten 0.01 to 0.1% of yttrium remainder nickel.
  • the total content of nickel, chromium and aluminum combined in the alloy should be from 80 to 90%.
  • the alloy individually or in combination with one another, to contain at most 0.7% of carbon, up to 30% of chromium, up to 12% of iron, 2.2 to 6% of aluminum, 0.1 to 2.0% of niobium, 0.01 to 1.0% of titanium, up to 0.15% of zirconium and—to achieve a high creep rupture strength—up to 10% of cobalt, at least 3% of molybdenum and up to 5% of tungsten, for example 4 to 8% of cobalt, up to 4% of molybdenum and 2 to 4% of tungsten, if the high resistance to oxidation is not the primary factor. Therefore, depending on the loads encountered in the specific circumstances, the cobalt, molybdenum and tungsten contents have to be selected within the content limits specified by the invention.
  • An alloy comprising at most 0.7% of carbon, at most 0.2, more preferably at most 0.1% of silicon, up to 0.2% of manganese, 18 to 30% of chromium, 0.5 to 12% of iron, 2.2 to 5% of aluminum, 0.4 to 1.6% of niobium, 0.01 to 0.6% of titanium, 0.01 to 0.15% of zirconium, at most 0.6% of nitrogen, at most 10% of cobalt, and at most 5% of tungsten, is particularly suitable.
  • the chromium content is at most 26.5%
  • the iron content is at most 11%
  • the aluminum content is from 3 to 6%
  • the titanium content is over 0.15%
  • the zirconium content is over 0.05%
  • the cobalt content is at least 0.2%
  • the tungsten content is over 0.05%
  • the yttrium content is 0.019 to 0.089%.
  • the high creep rupture strength of the alloy according to the invention for example a service life of 2000 hours under a load of from 4 to 6 MPa and a temperature of 1200° C., guarantees that a continuous, securely bonded oxidic barrier layer is retained in the form of an Al 2 O 3 layer which has the effect of preventing carburization and oxidation, results from the high aluminum content of the alloy and continues to top itself up or grow.
  • this layer comprises ⁇ -Al 2 O 3 and contains at most isolated spots of mixed oxides, which do not alter the essential nature of the ⁇ -Al 2 O 3 layer; at higher temperatures, in particular over 1050° C., in view of the rapidly decreasing stability of the Cr 2 O 3 layer of conventional materials at these temperatures, is increasingly responsible for protecting the alloy according to the invention from carburization and oxidation.
  • On the Al 2 O 3 barrier layer there may also—at least in part—be a covering layer of nickel oxide (NiO) and mixed oxides (Ni(Cr,Al) 2 O 4 ), the condition and extent of which, however, is not of great significance, since the Al 2 O 3 barrier layer below is responsible for protecting the alloy from oxidation and carburization. Cracks in the covering layer and the (partial) flaking of the covering layer which occurs at higher temperatures are therefore harmless.
  • the microstructure of the alloy according to the invention On account of its high aluminum content, the microstructure of the alloy according to the invention, at over 4% of aluminum, inevitably contains ⁇ ′ phase, which has a strengthening action at low and medium temperatures but also reduces the ductility or elongation at break. In individual cases, therefore, it may be necessary to reach a compromise between ductility and resistance to oxidation/carburization which is oriented according to the intended use.
  • the barrier layer according to the invention comprising ⁇ -Al 2 O 3 , which is the most stable Al 2 O 3 modification, is able to withstand all oxygen concentrations.
  • FIG. 1 shows a graphical illustration of various alloys, illustrating the elongation limit as a function of the temperature
  • FIG. 2 shows a graphical illustration of the alloys, illustrating the tensile strength as a function of the temperature
  • FIG. 3 shows a graphical illustration of the alloys, illustrating the elongation at break as a function of the temperature
  • FIG. 4 shows a graphical illustration of alloys, illustrating the load as a function of the Larson-Miller parameter/100
  • FIG. 5 shows a graphical illustration of other alloys, illustrating the load as a function of the Larson-Miller parameter/100;
  • FIG. 6 shows a graphical illustration of still other alloys, illustrating the load as a function of the Larson-Miller parameter/100
  • FIG. 7 shows a graphical illustration of comparative tests between alloys according to the invention and standard alloys at a temperature of 1100° C.
  • FIG. 8 shows a graphical illustration of alloys, illustrating the increase in weight as a function of time
  • FIGS. 9 and 10 show graphical illustrations of alloys, illustrating the increase in weight as a function of cycles
  • FIG. 11 shows a graphical illustration of test results of alloys with regard to influence of preliminary oxidation on the carburization behavior
  • FIG. 12 shows a graphical illustration of alloys, illustrating the increase in weight as a function of time between an alloy according to the invention and standard alloys;
  • FIG. 13 shows a graphical illustration of contents of the alloy according to the invention
  • FIG. 14 show a graphical illustration of a comparison between steel alloys according to the invention and alloys.
  • FIGS. 15 and 16 show graphical illustrations of an alloy according to the invention with respect to influence of the aluminum.
  • the table includes, as an example for two wrought alloys which are not covered by the invention and have a comparatively low carbon content and a very fine-grained microstructure with a grain size of ⁇ 10 ⁇ m, comparative alloys 5 and 7, whereas all the other test alloys are casting alloys.
  • Yttrium has a strong oxide-forming action which, in the alloy according to the invention, considerably improves the formation conditions and bonding of the ⁇ -Al 2 O 3 layer.
  • the aluminum content of the alloy according to the invention has an important role in that aluminum leads to the formation of a ⁇ ′ precipitation phase, which significantly increases the tensile strength.
  • the yield strength and the tensile strength of the three alloys according to the invention 13, 19, 20 to 900° C. are well above the corresponding strengths of the four comparative alloys.
  • the elongation at break of the alloys according to the invention substantially correspond to that of the comparative alloys; it increases considerably above approximately 900° C., as can be seen from the diagram presented in FIG. 3 , while the strength reaches the level of the comparative alloys ( FIGS. 1, 2 ). This can be explained by the fact that above approximately 900° C. the ⁇ ′ phase starts to form a solution, and is completely dissolved at above approximately 1000° C.
  • the deterioration in the resistance to carburization at lower aluminum contents can be explained by the fact that the inheritantly protective oxide layer cracks open or (partially) flakes off during cooling after the annealing treatment, so that carburization occurs in the region of the cracks and flaked-off areas.
  • the abovementioned Al 2 O 3 barrier layer is formed beneath the oxide layer (covering layer).
  • the straight line in the diagram shown in FIG. 13 divides the range of alloys with a sufficiently protective ⁇ -aluminum oxide layer above the straight line from the range of alloys with a resistance to carburization or catalytic coking which is adversely affected by mixed oxides.
  • the diagram illustrated in FIG. 14 reveals the superiority of the steel alloy according to the invention using six exemplary embodiments 21 to 26 by comparison with the conventional comparative alloys 1, 3, 4, 6 and 7.
  • the compositions of the comparative alloys 21 to 26 are given in the table.
  • FIGS. 15 and 16 compare the service life of the alloy according to the invention 13, comprising 2.4% of aluminum, as reference variable, with service life 1, in each case at 1100° C. ( FIG. 15 ) and 1200° C. ( FIG. 16 ) for three loading situations (15.9 MPa; 13.5 MPa; 10.5 MPa) with the service lives of the alloys according to the invention 19 (3.3% of aluminum) and 20 (4.8% of aluminum) referenced on the basis of the above reference variable.
  • the diagram shown in FIG. 15 reveals that in the case of alloy 19, with a medium aluminum content of 3.3%, the decrease in the service life becomes more intensive with increasing load, whereas in the case of alloy 20, with its high aluminum content of 4.8%, there is a strong but approximately equal decrease in the relative service life for all the loading situations.
  • the diagram for 1200° C. reveals a reduction in the service life when the aluminum content is increased from 2.4% (alloy 13) to 3.3% (alloy 19) for all three loading situations, with the relative service life dropping by approximately one third.
  • a further increase in the aluminum content to 4.8% (alloy 20) in turn reveals a load-dependent reduction in the relative service life.
  • the two diagrams reveal that as the aluminum content increases, the service life until fracture in the limiting rupture stress test is reduced. Furthermore, as the temperature increases and the duration of loading increases and/or the loading level decreases, the negative influence of the aluminum on the limiting rupture stress life decreases.
  • the alloys with a high aluminum content are particularly suitable for long-term use at temperatures for which it has hitherto been impossible to use cast or centrifugally cast materials.
  • the casting alloy according to the invention is particularly suitable for use as a material for furnace parts, radiant tubes for heating furnaces, rollers for annealing furnaces, parts of continuous-casting and strip-casting installations, hoods and muffles for annealing furnaces, parts of large diesel engines, containers for catalysts and for cracking and reformer tubes.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
  • Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
  • Mold Materials And Core Materials (AREA)
  • Catalysts (AREA)
  • Laminated Bodies (AREA)
  • Powder Metallurgy (AREA)
  • Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)
  • Production Of Liquid Hydrocarbon Mixture For Refining Petroleum (AREA)
  • Ceramic Products (AREA)
  • Soft Magnetic Materials (AREA)
  • Coating By Spraying Or Casting (AREA)
  • Exhaust Silencers (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
  • Furnace Housings, Linings, Walls, And Ceilings (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Supercharger (AREA)
US10/945,859 2003-01-25 2004-09-21 Thermostable and corrosion-resistant cast nickel-chromium alloy Abandoned US20050129567A1 (en)

Priority Applications (3)

Application Number Priority Date Filing Date Title
US10/945,859 US20050129567A1 (en) 2003-01-25 2004-09-21 Thermostable and corrosion-resistant cast nickel-chromium alloy
US12/169,229 US10041152B2 (en) 2003-01-25 2008-07-08 Thermostable and corrosion-resistant cast nickel-chromium alloy
US16/055,645 US10724121B2 (en) 2003-01-25 2018-08-06 Thermostable and corrosion-resistant cast nickel-chromium alloy

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
DE10302989A DE10302989B4 (de) 2003-01-25 2003-01-25 Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung
DE10302989.3 2003-01-25
PCT/EP2004/000504 WO2004067788A1 (fr) 2003-01-25 2004-01-22 Alliage nickel-chrome-fonte resistant a la chaleur et a la corrosion
US10/945,859 US20050129567A1 (en) 2003-01-25 2004-09-21 Thermostable and corrosion-resistant cast nickel-chromium alloy

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
PCT/EP2004/000504 Continuation WO2004067788A1 (fr) 2003-01-25 2004-01-22 Alliage nickel-chrome-fonte resistant a la chaleur et a la corrosion

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US12/169,229 Continuation US10041152B2 (en) 2003-01-25 2008-07-08 Thermostable and corrosion-resistant cast nickel-chromium alloy

Publications (1)

Publication Number Publication Date
US20050129567A1 true US20050129567A1 (en) 2005-06-16

Family

ID=32667854

Family Applications (3)

Application Number Title Priority Date Filing Date
US10/945,859 Abandoned US20050129567A1 (en) 2003-01-25 2004-09-21 Thermostable and corrosion-resistant cast nickel-chromium alloy
US12/169,229 Expired - Lifetime US10041152B2 (en) 2003-01-25 2008-07-08 Thermostable and corrosion-resistant cast nickel-chromium alloy
US16/055,645 Expired - Lifetime US10724121B2 (en) 2003-01-25 2018-08-06 Thermostable and corrosion-resistant cast nickel-chromium alloy

Family Applications After (2)

Application Number Title Priority Date Filing Date
US12/169,229 Expired - Lifetime US10041152B2 (en) 2003-01-25 2008-07-08 Thermostable and corrosion-resistant cast nickel-chromium alloy
US16/055,645 Expired - Lifetime US10724121B2 (en) 2003-01-25 2018-08-06 Thermostable and corrosion-resistant cast nickel-chromium alloy

Country Status (26)

Country Link
US (3) US20050129567A1 (fr)
EP (1) EP1501953B8 (fr)
JP (1) JP4607092B2 (fr)
KR (1) KR20050092452A (fr)
CN (1) CN100351412C (fr)
AT (1) ATE362997T1 (fr)
AU (1) AU2004207921A1 (fr)
BR (1) BRPI0406570B1 (fr)
CA (1) CA2513830C (fr)
DE (2) DE10302989B4 (fr)
EA (1) EA008522B1 (fr)
EG (1) EG23864A (fr)
ES (1) ES2287692T3 (fr)
HR (1) HRP20050728A2 (fr)
IL (1) IL169579A0 (fr)
MA (1) MA27650A1 (fr)
MX (1) MXPA05007806A (fr)
NO (1) NO20053617L (fr)
NZ (1) NZ541874A (fr)
PL (1) PL377496A1 (fr)
PT (1) PT1501953E (fr)
RS (1) RS20050552A (fr)
TR (1) TR200502892T1 (fr)
UA (1) UA80319C2 (fr)
WO (1) WO2004067788A1 (fr)
ZA (1) ZA200505714B (fr)

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20090280024A1 (en) * 2005-08-25 2009-11-12 Solvolthermal Crystal Growth Technology Research Alliance Ni-based corrosion resistant alloy and corrosion resistant member for supercritical ammonia reactor made of the alloy
US20100136368A1 (en) * 2006-08-08 2010-06-03 Huntington Alloys Corporation Welding alloy and articles for use in welding, weldments and method for producing weldments
US20100266865A1 (en) * 2005-06-01 2010-10-21 U Chicago Argonne Llc Nickel based alloys to prevent metal dusting degradation
US20100272597A1 (en) * 2009-04-24 2010-10-28 L. E. Jones Company Nickel based alloy useful for valve seat inserts
CN105463288A (zh) * 2016-01-27 2016-04-06 大连理工大学 高强高塑耐氯离子腐蚀的铸造合金及其制备方法
US9650698B2 (en) 2012-06-05 2017-05-16 Vdm Metals International Gmbh Nickel-chromium alloy having good processability, creep resistance and corrosion resistance
US9657373B2 (en) 2012-06-05 2017-05-23 Vdm Metals International Gmbh Nickel-chromium-aluminum alloy having good processability, creep resistance and corrosion resistance
WO2019055060A1 (fr) 2017-09-12 2019-03-21 Exxonmobil Chemical Patents Inc. Tube de transfert de chaleur pour craquage thermique formant un oxyde d'aluminium
CN110300811A (zh) * 2017-02-17 2019-10-01 株式会社日本制钢所 Ni基合金、燃气轮机材料和制造Ni基合金的方法
US10870908B2 (en) 2014-02-04 2020-12-22 Vdm Metals International Gmbh Hardening nickel-chromium-iron-titanium-aluminium alloy with good wear resistance, creep strength, corrosion resistance and processability
US11098389B2 (en) 2014-02-04 2021-08-24 Vdm Metals International Gmbh Hardened nickel-chromium-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and workability
US11479836B2 (en) 2021-01-29 2022-10-25 Ut-Battelle, Llc Low-cost, high-strength, cast creep-resistant alumina-forming alloys for heat-exchangers, supercritical CO2 systems and industrial applications
CN115449670A (zh) * 2022-09-14 2022-12-09 浙江大学 一种无中温脆性的高强镍基变形高温合金
US11732331B2 (en) 2020-05-26 2023-08-22 Daido Steel Co., Ltd. Ni-based alloy, and Ni-based alloy product and methods for producing the same
US11866809B2 (en) 2021-01-29 2024-01-09 Ut-Battelle, Llc Creep and corrosion-resistant cast alumina-forming alloys for high temperature service in industrial and petrochemical applications
US12024685B2 (en) 2018-12-20 2024-07-02 Exxonmobil Chemical Patents Inc. High pressure ethane cracking with small diameter furnace tubes

Families Citing this family (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE10302989B4 (de) * 2003-01-25 2005-03-03 Schmidt + Clemens Gmbh & Co. Kg Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung
WO2009045136A1 (fr) 2007-10-05 2009-04-09 Sandvik Intellectual Property Ab Utilisation et procédé de fabrication d'un acier renforcé par dispersion comme matériau d'un rouleau de four à rouleaux
CN101260487B (zh) * 2008-04-17 2010-06-02 攀钢集团攀枝花钢铁研究院有限公司 由含钛高铬镍合金制得的喷涂材料及其制备方法和用途
DE102008051014A1 (de) * 2008-10-13 2010-04-22 Schmidt + Clemens Gmbh + Co. Kg Nickel-Chrom-Legierung
RU2395606C1 (ru) * 2009-04-06 2010-07-27 Байдуганов Александр Меркурьевич Жаропрочный сплав
RU2395607C1 (ru) * 2009-04-13 2010-07-27 Байдуганов Александр Меркурьевич Жаропрочный сплав
KR20120053645A (ko) * 2010-11-18 2012-05-29 한국기계연구원 고온에서의 기계적 특성이 우수한 다결정 니켈기 초내열합금
CN102828070B (zh) * 2012-08-24 2014-05-07 宁波市阳光汽车配件有限公司 一种锅炉管道防护涂层材料
CN104745884A (zh) * 2013-12-27 2015-07-01 新奥科技发展有限公司 一种镍基合金及其应用
JP6358503B2 (ja) * 2014-05-28 2018-07-18 大同特殊鋼株式会社 消耗電極の製造方法
JP6434306B2 (ja) * 2014-12-26 2018-12-05 株式会社クボタ アルミナバリア層を有する耐熱管
CN104862535A (zh) * 2015-05-15 2015-08-26 新奥科技发展有限公司 一种镍基合金及其制备方法和应用
WO2018003823A1 (fr) 2016-06-29 2018-01-04 新日鐵住金株式会社 Acier inoxydable austénitique
RU2672647C1 (ru) * 2017-08-01 2018-11-16 Акционерное общество "Чепецкий механический завод" Коррозионностойкий сплав
GB201713066D0 (en) 2017-08-15 2017-09-27 Paralloy Ltd Oxidation resistant alloy
KR101998979B1 (ko) * 2017-12-07 2019-07-10 주식회사 포스코 고온변형 저항성 및 균열 저항성이 우수한 복사관용 Ｃｒ-Ｎｉ계 합금 및 그 제조방법
CN108285998A (zh) * 2018-03-29 2018-07-17 冯满 一种耐高温合金钢
JP7131318B2 (ja) * 2018-11-14 2022-09-06 日本製鉄株式会社 オーステナイト系ステンレス鋼
CN113227328B (zh) 2018-12-20 2025-01-21 埃克森美孚化学专利公司 用于热裂化反应器的耐侵蚀合金
CN110527911B (zh) * 2019-09-16 2020-12-18 北京航空航天大学 一种低密度高强高耐蚀齿轮轴承钢及其制备方法
CN112733321B (zh) * 2020-12-08 2024-05-10 中国科学院金属研究所 一种管材高速成形性能的评测方法
CN113481419A (zh) * 2021-06-30 2021-10-08 南京欣灿奇冶金设备有限公司 一种永不脱落的步进式加热炉装出料悬臂辊及其加工工艺
CN121219254A (zh) 2023-04-26 2025-12-26 埃克森美孚技术与工程公司 具有升高的盘管出口压力的蒸汽裂化方法
CN117089741A (zh) * 2023-07-07 2023-11-21 江苏三鑫特殊金属材料股份有限公司 一种耐磨镍基合金及其制备方法
CN117535559B (zh) * 2024-01-10 2024-05-07 北京北冶功能材料有限公司 一种低密度镍基高温合金箔材及其制备方法与应用
CN120843893B (zh) * 2025-07-16 2026-03-31 青岛新力通工业有限责任公司 一种综合性能优异的含铝耐热合金及其制备方法

Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4039330A (en) * 1971-04-07 1977-08-02 The International Nickel Company, Inc. Nickel-chromium-cobalt alloys
US4444589A (en) * 1981-04-27 1984-04-24 Kubota, Ltd. Heat resistant alloy excellent in bending property and ductility after aging and its products
US4671931A (en) * 1984-05-11 1987-06-09 Herchenroeder Robert B Nickel-chromium-iron-aluminum alloy
US4832912A (en) * 1981-08-27 1989-05-23 Mitsubishi Kinzoku Kabushiki Kaisha Thermal and wear resistant tough alloy
US5306358A (en) * 1991-08-20 1994-04-26 Haynes International, Inc. Shielding gas to reduce weld hot cracking
US5403547A (en) * 1989-12-15 1995-04-04 Inco Alloys International, Inc. Oxidation resistant low expansion superalloys
US5980821A (en) * 1991-04-11 1999-11-09 Krupp-Vdm Gmbh Austenitic nickel-chromium-iron alloy
US5997809A (en) * 1998-12-08 1999-12-07 Inco Alloys International, Inc. Alloys for high temperature service in aggressive environments
US20020004017A1 (en) * 2000-05-06 2002-01-10 Quayle Brian Edwin Melting crucible

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5631345B2 (fr) * 1972-01-27 1981-07-21
JPS5974266A (ja) 1982-10-19 1984-04-26 Mitsubishi Metal Corp エンジンバルブおよび同バルブシ−ト用高硬度Ｆｅ−Ｎｉ−Ｃｒ系合金
JPS5974256A (ja) 1982-10-20 1984-04-26 Kawasaki Steel Corp 鉄損の少ない無方向性珪素鋼板
US4787945A (en) 1987-12-21 1988-11-29 Inco Alloys International, Inc. High nickel chromium alloy
JPH01252750A (ja) * 1988-03-31 1989-10-09 Nkk Corp 耐溶融炭酸塩腐食性に優れたＮｉ基合金
ES2073873T3 (es) * 1991-12-20 1995-08-16 Inco Alloys Ltd Aleacion de ni-cr con alta resistencia a la temperatura.
KR940014865A (ko) * 1992-12-11 1994-07-19 에드워드 에이. 스틴 고온 저항성 니켈-크롬 합금
DE4404185A1 (de) * 1993-02-10 1994-08-11 Thomas Robert Metall Elektro Brenngutträger für keramische Formlinge
KR100372482B1 (ko) * 1999-06-30 2003-02-17 스미토모 긴조쿠 고교 가부시키가이샤 니켈 베이스 내열합금
JP3965869B2 (ja) * 2000-06-14 2007-08-29 住友金属工業株式会社 Ｎｉ基耐熱合金
JP4154885B2 (ja) * 2000-11-16 2008-09-24 住友金属工業株式会社 Ｎｉ基耐熱合金からなる溶接継手
JP3952861B2 (ja) * 2001-06-19 2007-08-01 住友金属工業株式会社 耐メタルダスティング性を有する金属材料
DE10302989B4 (de) * 2003-01-25 2005-03-03 Schmidt + Clemens Gmbh & Co. Kg Verwendung einer Hitze- und korrosionsbeständigen Nickel-Chrom-Stahllegierung

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4039330A (en) * 1971-04-07 1977-08-02 The International Nickel Company, Inc. Nickel-chromium-cobalt alloys
US4444589A (en) * 1981-04-27 1984-04-24 Kubota, Ltd. Heat resistant alloy excellent in bending property and ductility after aging and its products
US4832912A (en) * 1981-08-27 1989-05-23 Mitsubishi Kinzoku Kabushiki Kaisha Thermal and wear resistant tough alloy
US4671931A (en) * 1984-05-11 1987-06-09 Herchenroeder Robert B Nickel-chromium-iron-aluminum alloy
US5403547A (en) * 1989-12-15 1995-04-04 Inco Alloys International, Inc. Oxidation resistant low expansion superalloys
US5980821A (en) * 1991-04-11 1999-11-09 Krupp-Vdm Gmbh Austenitic nickel-chromium-iron alloy
US5306358A (en) * 1991-08-20 1994-04-26 Haynes International, Inc. Shielding gas to reduce weld hot cracking
US5997809A (en) * 1998-12-08 1999-12-07 Inco Alloys International, Inc. Alloys for high temperature service in aggressive environments
US20020004017A1 (en) * 2000-05-06 2002-01-10 Quayle Brian Edwin Melting crucible

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100266865A1 (en) * 2005-06-01 2010-10-21 U Chicago Argonne Llc Nickel based alloys to prevent metal dusting degradation
US8414828B2 (en) 2005-08-25 2013-04-09 Furuya Metal Co., Ltd. Ni-based corrosion resistant alloy and corrosion resistant member for supercritical ammonia reactor made of the alloy
US20090280024A1 (en) * 2005-08-25 2009-11-12 Solvolthermal Crystal Growth Technology Research Alliance Ni-based corrosion resistant alloy and corrosion resistant member for supercritical ammonia reactor made of the alloy
US20100136368A1 (en) * 2006-08-08 2010-06-03 Huntington Alloys Corporation Welding alloy and articles for use in welding, weldments and method for producing weldments
US8187725B2 (en) 2006-08-08 2012-05-29 Huntington Alloys Corporation Welding alloy and articles for use in welding, weldments and method for producing weldments
US20100272597A1 (en) * 2009-04-24 2010-10-28 L. E. Jones Company Nickel based alloy useful for valve seat inserts
WO2010123552A3 (fr) * 2009-04-24 2011-01-27 L. E. Jones Company Alliage à base de nickel utile pour inserts de siège de soupape
US9650698B2 (en) 2012-06-05 2017-05-16 Vdm Metals International Gmbh Nickel-chromium alloy having good processability, creep resistance and corrosion resistance
US9657373B2 (en) 2012-06-05 2017-05-23 Vdm Metals International Gmbh Nickel-chromium-aluminum alloy having good processability, creep resistance and corrosion resistance
US10870908B2 (en) 2014-02-04 2020-12-22 Vdm Metals International Gmbh Hardening nickel-chromium-iron-titanium-aluminium alloy with good wear resistance, creep strength, corrosion resistance and processability
US11098389B2 (en) 2014-02-04 2021-08-24 Vdm Metals International Gmbh Hardened nickel-chromium-titanium-aluminum alloy with good wear resistance, creep resistance, corrosion resistance and workability
CN105463288A (zh) * 2016-01-27 2016-04-06 大连理工大学 高强高塑耐氯离子腐蚀的铸造合金及其制备方法
US11131013B2 (en) * 2017-02-17 2021-09-28 Japan Steel Works M&E, Inc. Ni-based alloy, gas turbine material, and method for manufacturing Ni-based alloy
CN110300811A (zh) * 2017-02-17 2019-10-01 株式会社日本制钢所 Ni基合金、燃气轮机材料和制造Ni基合金的方法
US10456768B2 (en) 2017-09-12 2019-10-29 Exxonmobil Chemical Patents Inc. Aluminum oxide forming heat transfer tube for thermal cracking
WO2019055060A1 (fr) 2017-09-12 2019-03-21 Exxonmobil Chemical Patents Inc. Tube de transfert de chaleur pour craquage thermique formant un oxyde d'aluminium
US12024685B2 (en) 2018-12-20 2024-07-02 Exxonmobil Chemical Patents Inc. High pressure ethane cracking with small diameter furnace tubes
US11732331B2 (en) 2020-05-26 2023-08-22 Daido Steel Co., Ltd. Ni-based alloy, and Ni-based alloy product and methods for producing the same
US11479836B2 (en) 2021-01-29 2022-10-25 Ut-Battelle, Llc Low-cost, high-strength, cast creep-resistant alumina-forming alloys for heat-exchangers, supercritical CO2 systems and industrial applications
US11866809B2 (en) 2021-01-29 2024-01-09 Ut-Battelle, Llc Creep and corrosion-resistant cast alumina-forming alloys for high temperature service in industrial and petrochemical applications
CN115449670A (zh) * 2022-09-14 2022-12-09 浙江大学 一种无中温脆性的高强镍基变形高温合金

Also Published As

Publication number Publication date
AU2004207921A1 (en) 2004-08-12
EP1501953B8 (fr) 2008-01-23
EG23864A (en) 2007-11-19
DE10302989B4 (de) 2005-03-03
NZ541874A (en) 2008-03-28
US20090016926A1 (en) 2009-01-15
ATE362997T1 (de) 2007-06-15
UA80319C2 (en) 2007-09-10
MXPA05007806A (es) 2006-04-27
HRP20050728A2 (en) 2005-12-31
IL169579A0 (en) 2007-07-04
ES2287692T3 (es) 2007-12-16
CA2513830C (fr) 2010-12-14
ZA200505714B (en) 2006-04-26
BRPI0406570A (pt) 2005-12-20
TR200502892T2 (tr) 2005-09-21
CA2513830A1 (fr) 2004-08-12
CN1742106A (zh) 2006-03-01
JP4607092B2 (ja) 2011-01-05
HK1075679A1 (zh) 2005-12-23
RS20050552A (sr) 2007-09-21
TR200502892T1 (tr) 2008-02-21
US10041152B2 (en) 2018-08-07
BRPI0406570B1 (pt) 2016-05-17
EP1501953B1 (fr) 2007-05-23
NO20053617L (no) 2005-10-06
MA27650A1 (fr) 2005-12-01
NO20053617D0 (no) 2005-07-26
CN100351412C (zh) 2007-11-28
WO2004067788A1 (fr) 2004-08-12
PT1501953E (pt) 2007-08-17
EA200501178A1 (ru) 2005-12-29
JP2006516680A (ja) 2006-07-06
EA008522B1 (ru) 2007-06-29
DE502004003863D1 (de) 2007-07-05
KR20050092452A (ko) 2005-09-21
PL377496A1 (pl) 2006-02-06
US20190106770A1 (en) 2019-04-11
EP1501953A1 (fr) 2005-02-02
DE10302989A1 (de) 2004-08-05
US10724121B2 (en) 2020-07-28

Similar Documents

Publication Publication Date Title
US10724121B2 (en) Thermostable and corrosion-resistant cast nickel-chromium alloy
ES2661333T3 (es) Aleación de níquel-cromo
US5980821A (en) Austenitic nickel-chromium-iron alloy
KR101236222B1 (ko) 오스테나이트계 내열성 니켈계 합금
EP4276209A1 (fr) Alliage austénitique à haute teneur en aluminium présentant d'excellentes capacités anticorrosion à haute température et une excellente résistance au fluage
JP3106157B2 (ja) 鍛造可能なニッケル合金
CA1215254A (fr) Alliage de nickel-chrome-aluminium-yttrium renfermant du fer
JPH04358037A (ja) ニッケル基耐熱合金
CN111394663A (zh) 耐热铁基合金及其制备方法
US5997809A (en) Alloys for high temperature service in aggressive environments
CN120624894B (zh) 一种耐高温的奥氏体耐热铸造合金材料及其应用方法
HK1075679B (en) Thermostable and corrosion-resistant cast nickel-chromium alloy
US2983603A (en) High strength alloy for use at elevated temperatures
KR0172521B1 (ko) 고온 가단성 합금
EA046964B1 (ru) Аустенитный сплав с высоким содержанием алюминия, имеющий превосходные высокотемпературные и антикоррозионные способности и сопротивление ползучести
JPS62207846A (ja) 高温強度と延性に優れた耐熱鋳鋼
JPS626623B2 (fr)
JPS5935984B2 (ja) 耐熱鋳鋼
JPS6151623B2 (fr)
JPS62207836A (ja) クリ−プ破断強度と延性に優れた耐熱鋳鋼

Legal Events

Date Code Title Description
AS Assignment

Owner name: SCHMIDT + CLEMENS GMBH + CO. KG, GERMANY

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:KIRCHHEINER, ROLF;JAKOBI, DIETLINDE;BECKER, PETRA;AND OTHERS;REEL/FRAME:016286/0395

Effective date: 20041203

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION