EP2855723B1 - Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit - Google Patents

Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit Download PDF

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EP2855723B1
EP2855723B1 EP13731273.2A EP13731273A EP2855723B1 EP 2855723 B1 EP2855723 B1 EP 2855723B1 EP 13731273 A EP13731273 A EP 13731273A EP 2855723 B1 EP2855723 B1 EP 2855723B1
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EP2855723A1 (de
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Heike Hattendorf
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VDM Metals International GmbH
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    • 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
    • C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major 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
    • 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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon

Definitions

  • the invention relates to a nickel-chromium-aluminum alloy having excellent high temperature corrosion resistance, creep resistance and improved processability.
  • Austenitic nickel-chromium-aluminum alloys with different nickel, chromium and aluminum contents have long been used in furnace construction and in the chemical and petrochemical industries. For this application, a good high-temperature corrosion resistance is required even in carburizing atmospheres and a good heat resistance / creep resistance.
  • the high temperature corrosion resistance of the alloys listed in Table 1 increases with increasing chromium content. All these alloys form a chromium oxide layer (Cr 2 O 3 ) with an underlying, more or less closed, Al 2 O 3 layer. Small additions of strongly oxygen-affinitive elements such as Y or Ce improve the oxidation resistance. The content of chromium is slowly consumed in the course of use in the application area for the formation of the protective layer. Therefore, a higher chromium content increases the life of the material, since a higher content of the protective layer-forming element chromium retards the time at which the Cr content is below the critical limit and forms oxides other than Cr 2 O 3 , eg ferrous and nickel containing oxides are. A further increase in high temperature corrosion resistance can be achieved by adding aluminum and silicon. From a certain minimum content, these elements form a closed layer below the chromium oxide layer and thus reduce the consumption of chromium.
  • High resistance to carburization is achieved by materials with low solubility for carbon and low diffusion rate of carbon.
  • Nickel alloys are therefore generally more resistant to carburization than iron-base alloys because both carbon diffusion and carbon solubility in nickel are lower than in iron.
  • Increasing the chromium content results in a higher carburization resistance by forming a protective chromium oxide layer, unless the oxygen partial pressure in the gas is insufficient to form this protective chromium oxide layer.
  • materials can be used which form a layer of silicon oxide or the even more stable alumina, both of which can form protective oxide layers even at significantly lower oxygen contents.
  • Typical conditions for the occurrence of metal dusting are strongly carburizing CO, H 2 or CH 4 gas mixtures, as they occur in ammonia synthesis, in methanol plants, in metallurgical processes, but also in hardening furnaces.
  • the resistance to metal dusting tends to increase with increasing nickel content of the alloy ( Grabke, HJ, Krajak, R., Müller-Lorenz, EM, Strauss, S .: Materials and Corrosion 47 (1996), p. 495 ), however, nickel alloys are not generally resistant to metal dusting.
  • the chromium and aluminum content has a significant influence on the corrosion resistance under metal dusting conditions (see Figure 1).
  • Low chromium nickel alloys (such as alloy Alloy 600, see Table 1) show comparatively high corrosion rates under metal dusting conditions.
  • the nickel alloy Alloy 602 CA (N06025) with a chromium content of 25% and an aluminum content of 2.3% as well as Alloy 690 (N06690) with a chromium content of 30% is significantly more resistant ( Hermse, CGM and van Wortel, JC: Metal Dusting: relationship between alloy composition and degradation rate. Corrosion Engineering, Science and Technology 44 (2009), p. 182 - 185 ). Resistance to metal dusting increases with the sum Cr + AL.
  • the heat resistance or creep resistance at the specified temperatures is u. a. improved by a high carbon content.
  • high contents of solid solution hardening elements such as chromium, aluminum, silicon, molybdenum and tungsten also improve the heat resistance.
  • additions of aluminum, titanium and / or niobium can improve the strength by excretion of the y'- and / or ⁇ "-phase.
  • Alloys such as Alloy 602 CA (N06025), Alloy 693 (N06693) or Alloy 603 (N06603) are superior in their corrosion resistance compared to Alloy 600 (N06600) or Alloy 601 (N06601) due to the high aluminum content of more than 1.8 % known.
  • Alloy 602 CA (N06025), Alloy 693 (N06693), Alloy 603 (N06603) and Alloy 690 (N06690) show excellent carburization resistance or metal dusting resistance due to their high chromium and / or aluminum content.
  • alloys such as Alloy 602 CA (N06025), Alloy 693 (N06693) or Alloy 603 are shown (N06603), because of the high carbon and aluminum contents, excellent hot strength or creep resistance occurs in the temperature range in the metal dusting.
  • Alloy 602 CA (N06025) and Alloy 603 (N06603) have excellent heat resistance and creep resistance even at temperatures above 1000 ° C.
  • z For example, the high aluminum content impairs processability, and the higher the aluminum content, the stronger the deterioration (for example, for Alloy 693 - N06693).
  • Alloy 602 CA (N06025) or Alloy 603 (N06603) in particular the cold workability is limited by a high proportion of primary carbides.
  • the US 6,623,869B1 discloses a metallic material consisting of not more than 0.2% C, 0.01-4% Si, 0.05-2.0% Mn, not more than 0.04% P, not more than 0.015% S, 10 - 35% Cr, 30 - 78% Ni, 0.005 - ⁇ 4.5% Al, 0.005 - 0.2% N, and at least one of the elements 0.015 - 3% Cu and 0.015 - 3% Co, with the balance consists of 100% iron.
  • the value of 40Si + Ni + 5Al + 40N + 10 (Cu + Co) is not less than 50, the symbols of the elements meaning the content of the corresponding elements.
  • the material has excellent corrosion resistance in an environment where metal dusting can take place and therefore can be used for stovepipes, piping systems, heat exchanger tubes and the like. ⁇ . Used in petroleum refineries or petrochemical plants and can significantly improve the life and safety of the plant.
  • the EP 0 508 058 A1 discloses an austenitic nickel-chromium-iron alloy consisting of (in weight%) C 0.12-0.3%, Cr 23-30%, Fe 8-11%, Al 1.8 2.4% , Y 0.01 - 0.15%, Ti 0.01 - 1.0%, Nb 0.01 - 1.0%, Zr 0.01 - 0.2%, Mg 0.001 - 0.015%, Ca 0.001 - 0.01%, N max. 0.03%, Si max. 0.5%, Mn max. 0.25%, P max. 0.02%, S max. 0.01%, Ni remainder, including unavoidable melt contaminants.
  • the US 4,882,125 B1 discloses a chromium-containing nickel alloy which, with excellent resistance to desulfurization and oxidation at temperatures greater than 1093 ° C, has excellent creep resistance of more than 200 hours at temperatures above 983 ° C and a tension of 2000 PSI, good tensile strength and good Elongation, both at room temperature and elevated temperatures, consisting of (in% by weight) 27-35% Cr, 2.5-5% Al, 2.5-6% Fe, 0.5-2.5% Nb, up to 0.1% C, up to 1% each of Ti and Zr, up to 0.05% Ce, up to 0.05% Y, up to 1% Si, up to 1% Mn and Ni remainder.
  • the EP 0 549 286 B1 discloses a high temperature resistant Ni-Cr alloy including 55-65% Ni, 19-25% Cr1-4.5% Al, 0.045-0.3% Y, 0.15-1% Ti, 0.005-0.5 % C, 0.1-1.5% Si, 0-1% Mn and at least 0.005%, at least one of the elements of the group containing Mg, Ca, Ce, ⁇ 0.5% in total Mg + Ca, ⁇ 1 % Ce, 0.0001 - 0.1% B, 0 - 0.5% Zr, 0.0001 - 0.2% N, 0 - 10% Co, 0 - 0.5% Cu, 0 - 0.5 % Mo, 0-0.3% Nb, 0-0.1% V, 0-0.1% W, balance iron and impurities.
  • a heat-resistant nickel-based alloy comprising ⁇ 0.1% C, 0.01-2% Si, ⁇ 2% Mn, ⁇ 0.005% S, 10-25% Cr, 2.1- ⁇ 4.5% Al, ⁇ 0.055% N, in total 0.001-1% of at least one of the elements B, Zr, Hf, wherein said elements may be present in the following contents: B ⁇ 0.03%, Zr ⁇ 0.2%, Hf ⁇ 0.8 %.
  • Mo and W the following formula must be fulfilled: 2 . 5 ⁇ Not a word + W ⁇ 15
  • Nickel-chromium-aluminum alloy with (in% by weight) 24 to 33% chromium, 1.8 to ⁇ 3.0% aluminum, 0.10 to ⁇ 2.5% iron, 0.001 to 0.50% Silicon, 0.005 to 2.0% manganese, 0.00 to 0.60% titanium, each 0.0002 to 0.05% magnesium and / or calcium, 0.005 to 0.12% carbon, 0.001 to 0.050% nitrogen, 0 , 0001 - 0.020% oxygen, 0.001 to 0.030% phosphorus, max. 0.010% sulfur, max. 2.0% molybdenum, max.
  • the alloy further contains oxygen in amounts between 0.0001 and 0.020%, in particular 0.0001 to 0.010%.
  • Preferred ranges can be set with: fp ⁇ 38 . 4 fp ⁇ 36 . 6
  • Nb is present in the alloy
  • the alloy may also contain from 0.001 to 0.60% tantalum.
  • a maximum of 0.5% Cu may be contained in the alloy.
  • a maximum of 0.5% vanadium may be present in the alloy.
  • impurities may still contain the elements lead, zinc and tin in amounts as follows: pb Max. 0.002% Zn Max. 0.002% sn Max. 0.002%.
  • Preferred ranges can be set with: fa ⁇ 54
  • Preferred ranges can be set with: Fk ⁇ 49 Fk ⁇ 53
  • the alloy of the invention is preferably melted open, followed by treatment in a VOD or VLF plant. But also a melting and pouring in a vacuum is possible. Thereafter, the alloy is poured in blocks or as a continuous casting. If necessary, the block is then at temperatures between Annealed 900 ° C and 1270 ° C for 0.1 h to 70 h. Furthermore, it is possible to remelt the alloy additionally with ESU and / or VAR. Thereafter, the alloy is brought into the desired semifinished product.
  • the surface of the material may optionally (also several times) be removed chemically and / or mechanically in between and / or at the end for cleaning.
  • After the end of the hot forming can optionally be a cold forming with degrees of deformation up to 98% in the desired semi-finished mold, possibly with intermediate anneals between 700 ° C and 1250 ° C for 0.1 min to 70 h, possibly under inert gas such.
  • the alloy according to the invention can be produced and used well in the product forms strip, sheet metal, rod wire, longitudinally welded tube and seamless tube.
  • These product forms are produced with an average particle size of 5 ⁇ m to 600 ⁇ m.
  • the preferred range is between 20 ⁇ m and 200 ⁇ m.
  • the alloy according to the invention should preferably be used in areas in which carburizing conditions prevail, such as. As in components, especially pipes in the petrochemical industry. In addition, it is also suitable for furnace construction.
  • the occurring phases in equilibrium were calculated for the different alloy variants with the program JMatPro from Thermotech.
  • the database used for the calculations was the TTNI7 nickel base alloy database from Thermotech.
  • the formability is determined in a tensile test according to DIN EN ISO 6892-1 at room temperature.
  • the yield strength R p0.2 , the tensile strength R m and the elongation A are determined until the fracture.
  • the experiments were carried out on round samples with a diameter of 6 mm in the measuring range and a measuring length L 0 of 30 mm.
  • the sampling took place transversely to the forming direction of the semifinished product.
  • the forming speed was 10 MPa / s at R p0.2 and 40% / min at R m 6.7 10 -3 .
  • the amount of elongation A in the tensile test at room temperature can be taken as a measure of the deformability.
  • a good workable material should have an elongation of at least 50%.
  • the hot strength is determined in a hot tensile test according to DIN EN ISO 6892-2.
  • the yield strength R p0.2 , the tensile strength R m and the Elongation A until break determined analogously to the tensile test at room temperature (DIN EN ISO 6892-1).
  • the experiments were carried out on round samples with a diameter of 6 mm in the measuring range and an initial measuring length L 0 of 30 mm. The sampling took place transversely to the forming direction of the semifinished product.
  • the forming speed at R p0.2 was 8.33 10 -5 1 / s (0.5% / min) and at R m was 8.33 10 -4 1 / s (5% / min).
  • the respective sample is installed at room temperature in a tensile testing machine and heated to a desired temperature without load with a tensile force. After reaching the test temperature, the sample is held without load for one hour (600 ° C) or two hours (700 ° C to 1100 ° C) for temperature compensation. Thereafter, the sample is loaded with a tensile force to maintain the desired strain rates, and the test begins.
  • the creep resistance of a material improves with increasing heat resistance. Therefore, the hot strength is also used to evaluate the creep resistance of the various materials.
  • the corrosion resistance at higher temperatures was determined in an oxidation test at 1000 ° C in air, the test was interrupted every 96 hours and the mass changes of the samples was determined by the oxidation.
  • the samples were placed in the ceramic crucible in the experiment, so that possibly spalling oxide was collected and by weighing the crucible containing the oxides, the mass of the chipped oxide can be determined.
  • the sum of the mass of the chipped oxide and the mass change of the samples corresponds to the gross mass change of the sample.
  • the specific mass change is the mass change related to the surface of the samples. These are m net for the specific net mass change, m gross for the specific gross mass change, m spall for the following designates specific mass change of the chipped oxides.
  • the experiments were carried out on samples with about 5 mm thickness. 3 samples were removed from each batch, the values given are the mean values of these 3 samples.
  • batch 111389 for N06690 shows computationally the formation of ⁇ -chromium with a low content of Ni and / or Fe (BCC phase in Figure 2) below 720 ° C (T s BCC ) large proportions.
  • this phase is difficult to form because it is very different analytically from the basic material.
  • T s BCC of this phase is very high, then it may well occur, as z.
  • the formation temperature T s BCC should be less than or equal to 939 ° C. - the lowest formation temperature T s BCC under the examples of Alloy 693 in Table 2 (out US 4,88,125 Table 1).
  • An alloy can be hardened by several mechanisms so that it has a high heat resistance or creep resistance.
  • the alloying of another element causes a greater or lesser increase in strength (solid solution hardening).
  • Far more effective is an increase in strength through fine particles or precipitates (particle hardening).
  • This can be z. B. by the ⁇ '-phase, which form with additions of Al and other elements, such as Ti, to a nickel alloy or by carbides which form by the addition of carbon to a chromium-containing nickel alloy ( see eg Ralf Bürgel, Handbuch der Hochtemperaturtechnik, 3rd edition, Vieweg Verlag, Wiesbaden, 2006, pages 358 - 369 ).
  • strains A5 in the tensile test at room temperature of ⁇ 50%, but at least ⁇ 45%, are aimed for.
  • the yield strength, or the tensile strength, at higher temperatures should at least reach the values of Alloy 601 (see Table 4).
  • 600 ° C Yield point R p 0 . 2 > 150 MPA ;
  • Tensile strength R m > 500 MPA 800 ° C Yield point R p 0 . 2 > 130 MPA ;
  • the yield strength or tensile strength prefferably in the range of Alloy602 CA (see Table 4). At least 3 of the 4 following relations should be fulfilled: 600 ° C : Yield point R p 0 . 2 > 230 MPA ; Tensile strength R m > 550 MPA 800 ° C : Yield point R p 0 . 2 > 180 MPA ; Tensile strength R m > 190 MPA
  • Tables 3a and 3b show the analyzes of laboratory-scale molten batches along with some prior art large scale molten batches of Alloy 602CA (N06025) used for comparison. Alloy 690 (N06690), Alloy 601 (N06601). The prior art batches are marked with a T, those of the invention with an E. The batches marked on the laboratory scale are marked with an L, the large-scale blown batches with a G.
  • the blocks of laboratory-scale molten alloys in Tables 3a and b were annealed between 900 ° C and 1270 ° C for 8 hours and hot rolled and further intermediate anneals between 900 ° C and 1270 ° C for 0.1 to 1 hour Final thickness of 13 mm or 6 mm hot rolled.
  • the sheets produced in this way were solution-annealed between 900 ° C. and 1270 ° C. for 1 h. From these sheets, the samples required for the measurements were produced.
  • All alloy variants typically had a particle size of 70 to 300 ⁇ m.
  • Table 4 shows the yield strength R p0.2 , the tensile strength R m and the elongation A 5 for room temperature (RT) and for 600 ° C, furthermore the tensile strength R m for 800 ° C.
  • the values for Fa and Fk are entered.
  • Example batches 156817 and 160483 of the prior art alloy Alloy 602 CA have in Table 4 a relatively low elongation A5 at room temperature of 36 and 42%, respectively, which are below the requirements for good formability.
  • Fa is> 60, which is above the range that indicates good formability.
  • All inventive alloys (E) show an elongation> 50%. They thus fulfill the requirements.
  • Fa is ⁇ 60 for all alloys according to the invention. They are therefore in the range of good formability. The elongation is particularly high when Fa is comparatively small.
  • Example Example 156658 of the prior art Alloy 601 in Table 4 is an example of the minimum requirements for yield strength and tensile strength at 600 ° C and 800 ° C, respectively.
  • Example lots 156817 and 160483 of the prior art Alloy 602 CA alloy on the other hand are examples of very good values of yield strength and tensile strength at 600 ° C and 800 ° C, respectively.
  • Alloy 601 represents a material that meets the minimum requirements Creep resistance described in Relation 9a to 9d shows Alloy 602 CA a material exhibiting excellent creep strength described in Relation 10a to 10d.
  • the value for Fk is significantly greater for both alloys than 45 and for Alloy 602 CA additionally significantly higher than the value of Alloy 601, reflecting the increased strength values of Alloy 602 CA.
  • the alloys (E) according to the invention all exhibit a yield strength and tensile strength at 600 ° C. or 800 ° C. in the region or significantly above that of Alloy 601, ie they have fulfilled the relations 9a to 9d. They are in the range of the values of Alloy 602 CA and also meet the desirable requirements, ie 3 of the 4 relations 10a to 10d. Also for all alloys according to the invention in the examples in Table 4, Fk is greater than 45, and even most greater than 54, and thus in the range characterized by good heat resistance or creep resistance.
  • the batches 2297 and 2300 are an example that the relations 9a to 9d are not fulfilled and also a Fk ⁇ 45 is given.
  • Table 5 shows the specific mass changes after an oxidation test at 1100 ° C in air after 11 cycles of 96 h, for a total of 1056 h. Given in Table 5 are the specific gross mass change, the net specific mass change and the specific mass change of the chipped oxides after 1056 h.
  • the example batches of the prior art alloys Alloy 601 and Alloy 690 showed a significantly higher gross mass change than Alloy 602 CA, with that of Alloy 601 again being significantly larger than that of Alloy 690. Both form a chromium oxide layer that grows faster than an aluminum oxide layer. Alloy 601 still contains about 1.3% Al.
  • Alloy 602 CA has approx. 2.3% aluminum. This can be below the Chromoxid für form an at least partially closed aluminum oxide layer. This noticeably reduces the growth of the oxide layer and thus also the specific mass increase.
  • All alloys (E) according to the invention contain at least 2% aluminum and thus have a similarly low or lower gross mass increase than Alloy 602 CA. Also, all of the alloys of the invention, similar to the example batches of Alloy 602 CA, exhibit flaking in the area of measurement accuracy, while Alloy 601 and Alloy 690 show large flaking.
  • Si is needed in the production of the alloy. It is therefore necessary a minimum content of 0.001%. Too high levels, in turn, affect processability and phase stability, especially at high levels of aluminum and chromium. The Si content is therefore limited to 0.50%.
  • a minimum content of 0.005% Mn is required to improve processability.
  • Manganese is limited to 2.0% because this element reduces oxidation resistance.
  • Titanium increases the high-temperature strength. From 0.60%, the oxidation behavior can be degraded, which is why 0.60% is the maximum value.
  • Mg and / or Ca contents improve the processing by the setting of sulfur, whereby the occurrence of low-melting NiS Eutektika is avoided.
  • Mg and or Ca therefore, a minimum content of 0.0002% is required. If the contents are too high, intermetallic Ni-Mg phases or Ni-Ca phases may occur, which again significantly impair processability.
  • the Mg and / or Ca content is therefore limited to a maximum of 0.05%.
  • a minimum content of 0.005% C is required for good creep resistance.
  • C is limited to a maximum of 0.12%, since this element reduces the processability by the excessive formation of primary carbides from this content.
  • N A minimum content of 0.001% N is required, which improves the processability of the material. N is limited to a maximum of 0.05%, since this element reduces the processability by forming coarse carbonitrides.
  • the oxygen content must be ⁇ 0.020% to ensure the manufacturability of the alloy. Too low an oxygen content increases the costs. The oxygen content is therefore ⁇ 0.0001%.
  • the content of phosphorus should be less than or equal to 0.030%, since this surfactant affects the oxidation resistance. A too low P content increases the costs. The P content is therefore ⁇ 0.001%.
  • the levels of sulfur should be adjusted as low as possible, since this surfactant affects the oxidation resistance. It will therefore max. 0.010% S set,
  • Molybdenum is reduced to max. 2.0% limited as this element reduces oxidation resistance.
  • Tungsten is limited to max. 2.0% limited as this element also reduces oxidation resistance.
  • the oxidation resistance can be further improved. They do this by incorporating them into the oxide layer and blocking the diffusion paths of the oxygen there on the grain boundaries.
  • a minimum content of 0.01% Y is necessary to obtain the oxidation resistance-enhancing effect of Y.
  • the upper limit is set at 0.20% for cost reasons.
  • a minimum content of 0.001% La is necessary to obtain the oxidation resistance enhancing effect of La.
  • the upper limit is set at 0.20% for cost reasons.
  • a minimum content of 0.001% Ce is necessary to obtain the oxidation resistance-enhancing effect of Ce.
  • the upper limit is set at 0.20% for cost reasons.
  • cerium mischmetal A minimum content of 0.001% cerium mischmetal is necessary to obtain the oxidation resistance enhancing effect of cerium mischmetal.
  • the upper limit is set at 0.20% for cost reasons.
  • niobium can be added, as niobium also increases the high-temperature strength. Higher levels increase costs very much. The upper limit is therefore set at 1.10%.
  • the alloy may also contain tantalum, since tantalum also increases high-temperature strength. Higher levels increase costs very much.
  • the upper limit is therefore set at 0.60%.
  • a minimum level of 0.001% is required to have an effect.
  • the alloy can also be given Zr.
  • a minimum content of 0.01% Zr is necessary to obtain the high-temperature strength and oxidation resistance-enhancing effect of Zr.
  • the upper limit is set at 0.20% Zr for cost reasons.
  • Zr can be wholly or partially replaced by Hf, since this element, such as Zr, also increases high-temperature strength and oxidation resistance. Replacement is possible from 0.001%.
  • the upper limit is set at 0.20% Hf for cost reasons.
  • boron may be added to the alloy because boron improves creep resistance. Therefore, a content of at least 0.0001% should be present. At the same time, this surfactant deteriorates the oxidation resistance. It will therefore max. 0.008% Boron set.
  • Cobalt can be contained in this alloy up to 5.0%. Higher contents considerably reduce the oxidation resistance.
  • Copper is heated to max. 0.5% limited as this element reduces the oxidation resistance.
  • Vanadium is reduced to max. 0.5% limited as this element also reduces oxidation resistance.
  • Pb is set to max. 0.002% limited because this element reduces the oxidation resistance.
  • Zn and Sn are set to max. 0.002% limited because this element reduces the oxidation resistance.
  • Zn and Sn are set to max. 0.002% limited because this element reduces the oxidation resistance.

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EP13731273.2A 2012-06-05 2013-05-15 Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit Active EP2855723B1 (de)

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DE102012011161.4A DE102012011161B4 (de) 2012-06-05 2012-06-05 Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
PCT/DE2013/000268 WO2013182177A1 (de) 2012-06-05 2013-05-15 Nickel-chrom-aluminium-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit

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DE102020132193A1 (de) 2019-12-06 2021-06-10 Vdm Metals International Gmbh Verwendung einer Nickel-Chrom-Eisen-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
DE102020132219A1 (de) * 2019-12-06 2021-06-10 Vdm Metals International Gmbh Verwendung einer Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit
RU2748445C1 (ru) * 2020-06-09 2021-05-25 Акционерное общество "Объединенная двигателестроительная корпорация" (АО "ОДК") Жаропрочный сплав на никелевой основе и изделие, выполненное из него
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JP6076472B2 (ja) 2017-02-08
CN104245978B (zh) 2016-10-26
KR101668383B1 (ko) 2016-10-21
BR112014024761B1 (pt) 2019-03-26
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US9657373B2 (en) 2017-05-23
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