EP2855724A1 - Nickel-chrom-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit - Google Patents
Nickel-chrom-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeitInfo
- Publication number
- EP2855724A1 EP2855724A1 EP13731274.0A EP13731274A EP2855724A1 EP 2855724 A1 EP2855724 A1 EP 2855724A1 EP 13731274 A EP13731274 A EP 13731274A EP 2855724 A1 EP2855724 A1 EP 2855724A1
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- EP
- European Patent Office
- Prior art keywords
- alloy
- alloy according
- content
- max
- chromium
- 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.)
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Classifications
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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%
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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
- C22C19/053—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
- C22C19/058—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
- 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
- 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
- Nickel-chromium alloy with good processability, creep resistance and
- the invention relates to a nickel-chromium alloy with good high-temperature corrosion resistance, good creep resistance and improved processability.
- Nickel 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, A Oß layer. Small additions of strongly oxygen-affinitive elements such. B. 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. Further enhancement of high temperature corrosion resistance could be achieved by additions of aluminum and silicon, if required. 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.
- An increase in 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), but 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% and Alloy 690 (N06690) with a chromium content of 30% are significantly more resistant (Hermse, CGM and van Wortel, JC: Metal dusting: Correlation Engineering, Science and Technology 44 (2009), pp. 182-185). Resistance to metal dusting increases with the sum Cr + AI.
- the heat resistance or creep resistance at the specified temperatures is u. a. improved by a high carbon content. But even high contents of solid solution strengthening elements such as chromium, aluminum, silicon, molybdenum and tungsten improve the heat resistance. In the range of 500 ° C to 900 ° C, additions of aluminum, titanium and / or niobium can improve the strength by precipitating the y 'and / or y "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) due to the high carbon and aluminum content excellent heat resistance and creep resistance in the temperature range in which metal dusting occurs.
- 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, the higher the aluminum content (Alloy 693 - N06693). The same applies to an increased degree for silicon, which forms low-melting intermetallic phases with nickel.
- Alloy 602 CA (N06025) or Alloy 603 (N06603) in particular the cold workability is limited by a high proportion of primary carbides.
- US 6623869 B1 discloses a metallic material consisting of ⁇ 0.2% C, 0.01 - 4% Si, 0.05 - 2.0% Mn, ⁇ 0.04% P, ⁇ 0.015% S, 10 - 35% Cr, 30-78% Ni, 0.005-4.5% Al, 0.005-0.2% N, and at least one element 0.015-3% Cu or 0.015-3% Co, with the remainder being 100% iron consists.
- 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.
- EP 0 549 286 discloses a high temperature resistant Ni-Cr alloy including 55-65% Ni, 19-25%, Cr 1-4.5% 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% in total of at least one of the elements of the group containing Mg, Ca, Ce, ⁇ 0.5% in Sum 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.
- the object underlying the invention is to design a nickel-chromium alloy, which exceeds the metal dusting resistance of Alloy 690, so that an excellent metal dusting resistance is ensured, but at the same time
- This object is achieved by a nickel-chromium alloy, with (in wt .-%) 29 to 37% chromium, 0.001 to 1, 8% aluminum, 0, 10 to 7.0% iron, 0.001 to 0.50% Silicon, 0.005 to 2.0% manganese, 0.00 to 1, 00% titanium and / or 0.00 to 1, 10% niobium, each 0.0002 to 0.05% magnesium and / or calcium, 0.005 to 0 , 12% carbon, 0.001-0.050% nitrogen, 0.001-0.030% phosphorus, 0.0001-0.020% oxygen, max. 0.010% sulfur, max. 2.0% molybdenum, max. 2.0% tungsten, balance nickel and the usual process-related impurities, the following relationships must be fulfilled:
- the aluminum content is between 0.001 and 1.8%, whereby here too, depending on the area of use of the alloy, preferred aluminum contents can be set as follows:
- the iron content is between 0.1 and 7.0%, whereby, depending on the field of application, defined contents can be set within the following spreading ranges:
- the silicon content is between 0.001 and 0.50%.
- Si within the spreading range can be set in the alloy as follows:
- the titanium content is between 0.00 and 1.0%.
- Ti within the spreading range can be adjusted in the alloy as follows:
- Nb content is between 0.00 to 1.1%.
- Nb within the spreading range can be adjusted in the alloy as follows:
- magnesium and / or calcium is contained in contents of 0.0002 to 0.05%. It is preferably possible to adjust these elements in the alloy as follows:
- the alloy contains 0.005 to 0.12% carbon. Preferably, this can be adjusted within the spreading range in the alloy as follows:
- the alloy further contains phosphorus at levels between 0.001 and 0.030%.
- Preferred contents can be given as follows:
- the alloy further contains oxygen in amounts between 0.0001 and 0.020%, in particular 0.0001 to 0.010%.
- the element sulfur is given in the alloy as follows:
- Molybdenum and tungsten are contained singly or in combination in the alloy each containing not more than 2.0%. Preferred contents can be given as follows:
- Preferred areas can be set with
- Preferred ranges can be set with:
- the element yttrium may be adjusted in amounts of 0.01 to 0.20%.
- Y within the spreading range can be set in the alloy as follows:
- the element lanthanum may be adjusted in amounts of 0.001 to 0.20%.
- La can be set in the alloy as follows:
- the element Ce may be adjusted in amounts of 0.001 to 0.20%.
- Ce within the spreading range can be adjusted in the alloy as follows:
- cerium mischmetal may also be used in amounts of from 0.001 to 0.20%.
- cerium misch metal within the spreading range can be adjusted in the alloy as follows:
- the alloy may also be added to Zr.
- the zirconium content is between 0.01 and 0.20%.
- Zr can be adjusted within the spreading range in the alloy as follows:
- zirconium can also be replaced in whole or in part by
- the alloy may also contain from 0.001 to 0.60% tantalum
- the element boron may be included in the alloy as follows:
- the alloy may contain, as needed, between 0.00 to 5.0% cobalt, which may be further limited as follows:
- the content of copper may be further limited as follows:
- Fp Cr + 0.272 * Fe + 2.36 * Al + 2.22 * Si + 2.48 * Ti + 1, 26 * Nb + 0.477 * Cu + 0.374 * Mo + 0.538 * W - 1 1, 8 * C (4b) where Cr, Fe, Al, Si, Ti, Nb, Cu, Mo, W and C are the concentration of the element in mass%.
- impurities may still contain the elements lead, zinc and tin in amounts as follows:
- Preferred ranges can be set with:
- Fk> 40 with (7a) Fk Cr + 19 * Ti + 34.3 * Nb + 10.2 * Al + 12.5 * Si + 98 * C (8a) where Cr, Ti, Nb, Al, Si and C is the concentration of the elements in mass%.
- Preferred ranges can be set with:
- Fk Cr + 19 * Ti + 34.3 * Nb + 10.2 * Al + 12.5 * Si + 98 * C + 2245 * B (8b) where Cr, Ti, Nb, Al, Si, C and B the concentration of the elements in question are in mass%.
- 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 annealed at temperatures between 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.
- cold forming with degrees of deformation of up to 98% into the desired semifinished product form optionally with intermediate annealing between 700 ° C. and 1250 ° C. for 0.1 min to 70 h, if necessary under inert gas, such as.
- 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 manufactured with a mean particle size of 5 ⁇ to 600 ⁇ .
- the preferred particle size range is between 20 ⁇ and 200 ⁇ .
- 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 elongation at break is provided with indices:
- the experiments were carried out on round samples with a diameter of 6 mm in the measuring range and a measuring length l_o of 30 mm.
- the sampling took place transversely to the forming direction of the semifinished product.
- the forming speed was at R p0 , 2 0 MPa / s and at R m 6,7 10 "3 1 / s (40% / min).
- 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 p o, 2, the tensile strength R m and the elongation A to 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 of 30 mm. The sampling took place transversely to the forming direction of the semifinished product.
- the forming speed was R p o, 2 8,33 10 "5 1 / s (0,5% / min) and R m 8,33 10- 1 / s (5% / min).
- the 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 subjected to no load for one hour (600 ° C) or two hours (700 ° C to 1 100 ° C) held for a 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 were 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 is the gross mass change of the respective sample.
- the specific mass change is the mass change related to the surface of the samples. These are referred to hereinafter m N etto for the specific net change in mass, m Br utto for the specific gross change in mass, m spa ii for the specific mass change of the spalled 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.
- the alloy according to the invention in addition to excellent metal dusting resistance, should also have the following properties:
- N06690, the batch 1 1 1389, show computationally the formation of a-chromium (BCC phase in Figure 2) below 720 ° C (T s B cc) in large proportions.
- This phase is formed by the fact that it is analytically very different from the basic material is difficult. However, if the formation temperature T s BCC of this phase is very high, then it may well occur, as z.
- T s BCC of this phase is very high, then it may well occur, as z.
- E. Slevolden, JZ Albertsen. U. Fink "Tjeldbergodden Methanol Plant: Metal Dusting Investigations," Corrosion / 201 1, paper no. 1 1 144 (Houston, TX: NACE 201 1), p. 15 "for a variant of Alloy 693 (US 06693)
- This phase is brittle and leads to undesirable embrittlement of the material.
- Figure 3 and Figure 4 show the phase diagrams of the Alloy 693 variants (from US 4,882,125 Table 1) Alloy 3 or Alloy 10 from Table 2.
- Alloy 3 has a formation temperature T s BCC of 1079 ° C, Alloy 10 of 939 ° C ,
- T s BCC formation temperature
- Alloy 10 of 939 ° C
- the formation temperature T s BC c ⁇ 939 ° C - the lowest formation temperature T s B cc should be among the examples of Alloy 693 in Table 2 (from US 4,882,125 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, resulting in additions of AI and other elements such.
- B Ti, to form a nickel alloy or by carbides, which is characterized by adding carbon to a chromium-containing nickel alloy forms (see, for example, Ralf Bürgel, Handbuch der Hochtemperaturtechnik, 3rd edition, Vieweg Verlag, Wiesbaden, 2006, pages 358-369).
- strains A5 are aimed at in the tensile test at room temperature of> 50%, but at least> 45%.
- the chromium content has been set in the case of the alloy according to the invention> 29%, preferably> 30% or> 31%.
- the aluminum content of ⁇ 1. 8%, preferably ⁇ 1.4%, has been chosen in the lower range.
- the aluminum content contributes significantly to the tensile strength or creep resistance (both by solid solution hardening, as well as by ⁇ '-hardening) has the consequence that the target for the hot strength, or the creep strength, not that of Alloy 602 CA but which were taken from Alloy 601, although much higher values for heat resistance and creep resistance would of course be desirable.
- Fk> 40 with (7a) Fk Cr + 19 * Ti + 34.3 * Nb + 10.2 * Al + 12.5 * Si + 98 * C + 2245 * B (8b) where Cr, Ti, Nb, Al, Si, C and B are the concentration of the respective elements in mass%.
- the oxidation resistance of a good Chromoxidsentners is sufficient.
- the alloy according to the invention is therefore said to have a corrosion resistance in air similar to that of Alloy 690 or Alloy 601.
- Tables 3a and 3b show the laboratory scale analyzes of batches smelted together with some of the prior art large scale molten batches used for comparison of Alloy 602CA (N06025), 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 annealed Hot rolling and further intermediate annealing between 900 ° C and 1270 ° C for 0, 1 to 1 h hot rolled to a final thickness of 13 mm or 6 mm.
- 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 taken.
- All alloy variants typically had a particle size between 65 and 310 ⁇ m.
- batches 2294 to 2314 and 250053 to 250150 were melted.
- the inventions marked E correspond to the formula (2a) with Cr + Al> 30 and are thus more resistant to metal dusting than Alloy 690.
- the batches 2298, 2299, 2303, 2304, 2305, 2308, 2314, 250063, 260065, 250066, 250067, 250068, 250079, 250139, 250140 and 250141 satisfy the formula (2b) Al + Cr> 31. They are therefore particularly good metal dusting resistant.
- 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 alloys of the invention 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 range that the yield strength and tensile strength should reach at 600 ° C and 800 ° C, respectively. This is described by the relations 7a to 7d.
- the value for Fk is> 40.
- the alloys 2298, 2299, 2303, 2304, 2305, 2308, 2314, 250060, 250063, 260065, 250066, 250067, 250068, 250079, 250139, 250140, 250141, 250143, 250150 satisfy the requirement in that at least 3 of the 4 relations 7a to 7d are fulfilled.
- Fk is also greater than 40.
- Laboratory lots 2295, 2303, 250053, 250054 and 250057 are examples of less than 3 of the 4 relations 7a to 7d being met. Then Fk ⁇ 45 is also.
- Table 5 shows the specific mass changes after an oxidation test at 1100 ° C in air after 1 1 cycles of 96 h, so a total of 1056 h. Given in Table 5 are the gross mass change, the net mass change and the specific mass change of the chipped oxides after 1056 h.
- the prior art alloys Alloy 601 and Alloy 690 showed a significantly higher gross mass change than Alloy 602 CA.
- Alloy 601 and Alloy 690 form a chromium oxide layer which grows faster than an aluminum oxide layer but has Alloy 602 CA underneath the chromium oxide layer at least partially closed alumina layer. This noticeably reduces the growth of the oxide layer and thus also the specific mass increase.
- the alloy according to the invention should have a corrosion resistance in air similar to that of Alloy 690 or Alloy 601. Ie. the gross mass change should be below 60 g / m 2 . This is the case for all laboratory batches in Table 5, thus also for the invention.
- Too low Cr contents mean that when the alloy is used in a corrosive atmosphere, the Cr concentration drops very quickly below the critical limit, so that no closed chromium oxide layer can form any more. That is why 29% Cr is the lower limit for chromium. Too high Cr contents deteriorate the phase stability of the alloy. Therefore, 37% Cr is considered the upper limit.
- a certain minimum aluminum content of 0.001% is required for the manufacturability of the alloy. Excessive Al contents, especially at very high chromium contents, affect the processability and phase stability of the alloy. Therefore, an AI content of 1, 8% forms the upper limit.
- 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 chromium levels. 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 1, 0%, the oxidation behavior can be greatly degraded, which is why 1, 0% is the maximum value.
- Niobium like titanium, enhances high-temperature strength. Higher levels increase costs very much.
- the upper limit is therefore set at 1, 1%.
- 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% each 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 the formation of 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 ⁇ 0.030% because this surfactant affects the oxidation resistance. Too low a P content increases 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.
- a minimum content of 0.001% cerium mischmetal is necessary to obtain the oxidation resistance enhancing effect of the cerium misch metal.
- the upper limit is set at 0.20% for cost reasons.
- 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.
- 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.
- 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 reduces the oxidation resistance.
- Pb is set to max. 0.002% limited because this element reduces the oxidation resistance. The same applies to Zn and Sn.
- carbide-forming elements Cr, Ti and C can be satisfied, which describes a particularly good processability:
- Fa Cr + 6.15 * Nb + 20.4 * Ti + 201 * C (6a) where Cr, Nb, Ti and C are the concentration of the respective elements in mass%.
- the boundaries for Fa were substantiated in detail in the foregoing description.
- the following relationship between the strength-enhancing elements can be satisfied, which describes a particularly good hot strength / creep resistance:
- Fk> 40 with (7a) Fk Cr + 19 * Ti + 34.3 * Nb + 10.2 * Al + 12.5 * Si + 98 * C (8a) where Cr, Ti, Nb, Al, Si and C is the concentration of the elements in mass%.
- the limits for Fa and the possible inclusion of further elements have been extensively substantiated in the foregoing description.
- Table 2 Typical compositions of some alloys according to ASTM B 168-11 (prior art). All figures in% by mass * ) Alloy composition from patent US 4,882,125 Table 1
- Table 3a Composition of laboratory batches, part 1. All data in mass% (T: alloy according to the prior art, E: alloy according to the invention, L: melted on a laboratory scale, G: melted on an industrial scale)
- Table 3b Composition of laboratory batches, part 2. All data in mass% (For all alloys applies: Pb: max 0.002%, Zn: max 0.002%, Sn: max 0.002%) (meaning of T, E, G, L, see Table 3a)
- Table 4 Results of tensile tests at room temperature (RT), 600 ° C and 800 ° C.
- the forming speed at Rpo, 2 was 8.33 10 "5 1 / s (0.5% / min) and at R m 8.33 was 10 " 1 / s (5% / min);
- KG grain size, *) sample defective.
- Table 5 Results of the oxidation tests at 1000 ° C in air after 1056 h.
- Hermse, CGM and van Wortel, JC Metal dusting: relationship between alloy composition and degradation rate: Corrosion Engineering, Science and Technology 44 (2009), pp. 182-185).
- FIG. 4 proportions of the phases in the thermodynamic equilibrium in FIG.
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DE102012011162.2A DE102012011162B4 (de) | 2012-06-05 | 2012-06-05 | Nickel-Chrom-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit |
PCT/DE2013/000269 WO2013182178A1 (de) | 2012-06-05 | 2013-05-15 | Nickel-chrom-legierung mit guter verarbeitbarkeit, kriechfestigkeit und korrosionsbeständigkeit |
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EP (1) | EP2855724B1 (de) |
JP (1) | JP6177317B2 (de) |
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CN (1) | CN104245977B (de) |
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DE (1) | DE102012011162B4 (de) |
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MX (1) | MX369312B (de) |
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EP2671669B1 (de) * | 2011-02-01 | 2021-06-23 | MITSUBISHI HEAVY INDUSTRIES, Ltd. | Ni-basierter legierungsdraht mit einem hohen cr-anteil, stange für schutzschweissgasverfahren und metall für schutzschweissgasverfahren |
DE102014001329B4 (de) | 2014-02-04 | 2016-04-28 | VDM Metals GmbH | Verwendung einer aushärtenden Nickel-Chrom-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit |
DE102014001330B4 (de) | 2014-02-04 | 2016-05-12 | VDM Metals GmbH | Aushärtende Nickel-Chrom-Kobalt-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit |
DE102014001328B4 (de) * | 2014-02-04 | 2016-04-21 | VDM Metals GmbH | Aushärtende Nickel-Chrom-Eisen-Titan-Aluminium-Legierung mit guter Verschleißbeständigkeit, Kriechfestigkeit, Korrosionsbeständigkeit und Verarbeitbarkeit |
US11130201B2 (en) * | 2014-09-05 | 2021-09-28 | Ametek, Inc. | Nickel-chromium alloy and method of making the same |
DE102015008322A1 (de) * | 2015-06-30 | 2017-01-05 | Vdm Metals International Gmbh | Verfahren zur Herstellung einer Nickel-Eisen-Chrom-Aluminium-Knetlegierung mit einer erhöhten Dehnung im Zugversuch |
US10487377B2 (en) * | 2015-12-18 | 2019-11-26 | Heraeus Deutschland GmbH & Co. KG | Cr, Ni, Mo and Co alloy for use in medical devices |
CN105714152B (zh) * | 2016-02-29 | 2017-06-23 | 钢铁研究总院 | 一种镍基耐蚀合金及制备方法 |
ITUA20161551A1 (it) | 2016-03-10 | 2017-09-10 | Nuovo Pignone Tecnologie Srl | Lega avente elevata resistenza all’ossidazione ed applicazioni di turbine a gas che la impiegano |
CN107042370B (zh) * | 2017-03-16 | 2019-04-02 | 南京航空航天大学 | 一种高Cr含量Ni基耐高温合金焊丝及制备工艺 |
CN110079702B (zh) * | 2019-05-31 | 2020-09-04 | 东北大学 | 一种Ni-Cr基合金及其制备方法 |
DE102020132219A1 (de) | 2019-12-06 | 2021-06-10 | Vdm Metals International Gmbh | Verwendung einer Nickel-Chrom-Aluminium-Legierung mit guter Verarbeitbarkeit, Kriechfestigkeit und Korrosionsbeständigkeit |
US11697869B2 (en) | 2020-01-22 | 2023-07-11 | Heraeus Deutschland GmbH & Co. KG | Method for manufacturing a biocompatible wire |
JP7437240B2 (ja) | 2020-06-04 | 2024-02-22 | レンゴー株式会社 | 包装箱 |
CN114318059B (zh) * | 2020-09-29 | 2022-07-15 | 宝武特种冶金有限公司 | 镍铬钨钼钴铁中间合金及其制备方法和应用 |
CN113106298B (zh) * | 2021-04-16 | 2022-02-25 | 江苏兄弟合金有限公司 | 一种高精度直径0.03mm电热丝圆丝及其制备方法 |
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 |
CN114635062A (zh) * | 2022-03-18 | 2022-06-17 | 西安聚能高温合金材料科技有限公司 | 一种镍铬中间合金 |
CN115161502A (zh) * | 2022-07-14 | 2022-10-11 | 江苏以豪合金有限公司 | 一种电热元件用镍基高电阻电热合金丝的制备工艺 |
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DE4111821C1 (de) | 1991-04-11 | 1991-11-28 | Vdm Nickel-Technologie Ag, 5980 Werdohl, De | |
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RU2125110C1 (ru) | 1996-12-17 | 1999-01-20 | Байдуганов Александр Меркурьевич | Жаропрочный сплав |
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KR100372482B1 (ko) | 1999-06-30 | 2003-02-17 | 스미토모 긴조쿠 고교 가부시키가이샤 | 니켈 베이스 내열합금 |
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JP2003138334A (ja) | 2001-11-01 | 2003-05-14 | Hitachi Metals Ltd | 高温耐酸化性及び高温延性に優れたNi基合金 |
EP1325965B1 (de) * | 2001-12-21 | 2005-10-05 | Hitachi Metals, Ltd. | Ni-Legierung mit verbesserter Oxidations- Resistenz, Warmfestigkeit and Warmbearbeitbarkeit |
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JP2006274443A (ja) * | 2005-03-03 | 2006-10-12 | Daido Steel Co Ltd | 非磁性高硬度合金 |
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JP4978790B2 (ja) | 2007-08-27 | 2012-07-18 | 三菱マテリアル株式会社 | 樹脂成形用金型部材 |
DE102008051014A1 (de) | 2008-10-13 | 2010-04-22 | Schmidt + Clemens Gmbh + Co. Kg | Nickel-Chrom-Legierung |
JP4780189B2 (ja) * | 2008-12-25 | 2011-09-28 | 住友金属工業株式会社 | オーステナイト系耐熱合金 |
JP5284252B2 (ja) | 2009-12-10 | 2013-09-11 | 株式会社神戸製鋼所 | 耐割れ性に優れたNi−Cr−Fe合金系溶接金属 |
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CN104245977B (zh) | 2016-07-06 |
US9650698B2 (en) | 2017-05-16 |
MX369312B (es) | 2019-11-05 |
WO2013182178A1 (de) | 2013-12-12 |
RU2014153533A (ru) | 2016-08-10 |
KR101698075B1 (ko) | 2017-01-19 |
ES2605949T3 (es) | 2017-03-17 |
KR20150006871A (ko) | 2015-01-19 |
DE102012011162B4 (de) | 2014-05-22 |
EP2855724B1 (de) | 2016-09-14 |
CN104245977A (zh) | 2014-12-24 |
MX2014014555A (es) | 2015-07-06 |
US20150093288A1 (en) | 2015-04-02 |
RU2605022C1 (ru) | 2016-12-20 |
BR112014023691B1 (pt) | 2019-06-25 |
JP6177317B2 (ja) | 2017-08-09 |
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DE102012011162A1 (de) | 2013-12-05 |
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