EP3102710A1 - Alliage thermodurcissable de nickel-chrome-cobalt-titane-aluminium présentant une résistance à l'usure, une résistance au fluage, une résistance à la corrosion et une aptitude au façonnage satisfaisantes - Google Patents

Alliage thermodurcissable de nickel-chrome-cobalt-titane-aluminium présentant une résistance à l'usure, une résistance au fluage, une résistance à la corrosion et une aptitude au façonnage satisfaisantes

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Publication number
EP3102710A1
EP3102710A1 EP15704947.9A EP15704947A EP3102710A1 EP 3102710 A1 EP3102710 A1 EP 3102710A1 EP 15704947 A EP15704947 A EP 15704947A EP 3102710 A1 EP3102710 A1 EP 3102710A1
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EP
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Prior art keywords
max
alloy
alloy according
content
nickel
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German (de)
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EP3102710B1 (fr
Inventor
Heike Hattendorf
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VDM Metals International GmbH
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VDM Metals International GmbH
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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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/053—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 30% but less than 40%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01L—CYCLICALLY OPERATING VALVES FOR MACHINES OR ENGINES
    • F01L3/00—Lift-valve, i.e. cut-off apparatus with closure members having at least a component of their opening and closing motion perpendicular to the closing faces; Parts or accessories thereof
    • F01L3/02—Selecting particular materials for valve-members or valve-seats; Valve-members or valve-seats composed of two or more materials

Definitions

  • the invention relates to a nickel-chromium-cobalt-titanium-aluminum wrought alloy with very good wear resistance, at the same time very good creep resistance, good high temperature corrosion resistance and good processability.
  • Austenitic, thermosetting nickel-chromium-titanium-aluminum alloys with different nickel, chromium, titanium and aluminum contents have long been used for exhaust valves of engines.
  • a good wear resistance, a good heat resistance / creep resistance, a good fatigue strength and a good high-temperature corrosion resistance (especially in exhaust gases) is required.
  • DIN EN 10090 specifies austenitic alloys of which nickel alloys 2.4955 and 2.4952 (NiCr20TiAI) have the highest hot and creep strengths of all alloys specified in this standard.
  • Table 1 shows the composition of the nickel alloys mentioned in DIN EN 10090
  • Tables 2 to 4 show the tensile strengths, the 0.2% proof stress and creep resistance values after 1000 h.
  • NiFe25Cr20NbTi with 0.05-0.10% C, max. 1, 0% Si, max. 1, 0% Mn, max.
  • NiCr20TiAI has significantly higher tensile strengths, 0.2% yield strengths and higher creep rupture strength than NiFe25Cr20NbTi.
  • EP 0 639 654 A2 discloses an iron nickel-chromium alloy consisting of (in weight%) up to 0.15% C, up to 1.0% Si, up to 3.0% Mn, 30 to 49% Ni, 10 to 18% Cr, 1, 6 to 3.0% Al, one or more elements from the group IVa to Va with a total content of 1.5 to 8.0%, balance Fe and inevitable impurities, wherein AI is an indispensable additional element and one or more elements from the already mentioned group IVa to Va must satisfy the following formula in atom%:
  • WO 2008/007190 A2 discloses a wear-resistant alloy consisting of (in% by weight) 0.15 to 0.35% C, up to 1.0% Si, up to 1.0% Mn,> 25 to ⁇ 40 % Ni, 15 to 25% Cr, up to 0.5% Mo, up to 0.5% W,> 1, 6 to 3.5% Al,> 1, 1% to 3% in the sum Nb plus Ta, to to 0.015% B, Fe and unavoidable impurities, where Mo + 0.5W ⁇ 0.75%; Ti + Nb> 4.5% and 13 ⁇ (Ti + Nb) / C ⁇ 50.
  • the alloy is particularly useful for the manufacture of exhaust valves for internal combustion engines.
  • the good wear resistance of this alloy is based on the high proportion of primary carbides that form due to the high carbon content. However, a high proportion of primary carbides causes processing problems in the production of this alloy as a wrought alloy.
  • the hot strength or creep strength is in the range of 500 ° C to 900 ° C on the additions of aluminum, titanium and / or niobium (or other elements such as Ta, ..) for excretion of ⁇ 'and / or ⁇ "phase
  • the hot strength or creep resistance also improved by high levels of solid solution strengthening elements such as chromium, aluminum, silicon, molybdenum and tungsten, as well as by a high carbon content.
  • alloys with a chromium content around 20% form a chromium oxide layer (Cr20 3 ) protecting the material.
  • 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 improves the life of the material because 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, cobalt and nickel containing oxides.
  • the object underlying the invention is to design a nickel-chromium Knet alloy
  • This object is achieved by a hardening nickel-chromium-cobalt-titanium-aluminum wrought alloy with very good wear resistance, at the same time very good creep resistance, good high-temperature corrosion resistance and good processibility with (in% by mass)> 18 to 31% chromium, 1, 0 to 3.0% titanium, 0.6 to 2.0% aluminum,> 3.0 to 40% Cobalt, 0.005 to 0.10% carbon, 0.0005 to 0.050% nitrogen, 0.0005 to 0.030% phosphorus, max. 0.010% sulfur, max. 0.020% oxygen, max. 0.70% silicon, max. 2.0% manganese, max. 0.05% magnesium, max. 0.05% calcium, max. 2.0% molybdenum, max. 2.0% tungsten, max.
  • the spread range for the chrome element is between> 18 and 31%, whereby preferred ranges can be set as follows:
  • Ti within the spreading range can be adjusted in the alloy as follows:
  • the aluminum content is between 0.6 and 2.0%, although here too, depending on the area of use of the alloy, preferred aluminum contents can be set as follows:
  • the cobalt range is between> 3.0 and 40%, whereby, depending on the field of application, preferred contents can be set within the following spreading ranges:
  • the alloy contains 0.005 to 0.10% carbon. Preferably, this can be set within the spreading range in the alloy as follows:
  • the alloy further contains phosphorus in amounts between 0.0005 and 0.030%.
  • Preferred contents can be given as follows:
  • the element sulfur is given in the alloy as follows:
  • the element oxygen is present in the alloy in a content of max. 0.020% included.
  • Preferred further contents can be given as follows:
  • the element Si is present in the alloy in levels of max. 0.70% included. Preferred further contents can be given as follows:
  • the element Mn in the alloy is in contents of max. 2.0% included. Preferred further contents can be given as follows:
  • the element Mg is present in the alloy in a content of max. 0.05% included. Preferred further contents can be given as follows:
  • the element Ca is present in the alloy in a content of max. 0.05% included. Preferred further contents can be given as follows:
  • the element niobium is in the alloy in contents of max. 0.5% included. Preferred further contents can be given 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:
  • a maximum of 0.5% Cu may be contained in the alloy.
  • the content of copper may be further limited as follows:
  • a maximum of 0.5% vanadium may be present in the alloy.
  • the alloy may, if necessary, contain between 0 and 20.0% iron, which may be further limited as follows:
  • the alloy may contain between 0.0 and 0.20% zirconium as required, which may be further limited as follows:
  • the nickel content should be above 35%. Preferred contents can be given as follows: > 40%.
  • Preferred areas can be set with
  • Preferred areas can be set with
  • the following relationship between Cr, Mo, W, Fe, Co, Ti, Al and Nb may be satisfied to provide a sufficiently good processability:
  • the element yttrium may be adjusted in levels of 0.0 to 0.20%.
  • Y within the spreading range can be set in the alloy as follows:
  • the element lanthanum may be adjusted in levels of 0.0 to 0.20%.
  • La within the spreading range can be adjusted in the alloy as follows:
  • the element Ce may be adjusted in contents of 0.0 to 0.20%.
  • Ce can be adjusted within the spreading range in the alloy as follows:
  • cerium mischmetal may also be used in amounts of from 0.0 to 0.20%.
  • cerium misch metal within the spreading range can be adjusted in the alloy as follows:
  • 0.0 to 0.20% hafnium may also be included in the alloy.
  • Preferred ranges can be given as follows.
  • tantalum may also be included in the alloy
  • impurities may still contain the elements lead, zinc and tin in amounts as follows:
  • the alloy of the present invention is preferably melted in the vacuum induction furnace (VIM), but may be melted open, followed by treatment in a VOD or VLF plant. After casting in blocks or possibly as a continuous casting, the alloy is optionally annealed at temperatures between 600 ° C and 1100 ° C for 0.1 hours (h) to 100 hours, if necessary under inert gas, such. As argon or hydrogen, followed by a cooling in air or in the moving annealing atmosphere. Thereafter, a remelting by means of VAR or ESU, possibly followed by a second remelting process by means of VAR or ESU.
  • VIM vacuum induction furnace
  • the blocks are optionally annealed at temperatures between 900 ° C and 1270 ° C for 0.1 to 70 hours, then hot formed, optionally with one or more intermediate anneals between 900 ° C and 1270 ° C for 0.05 to 70 hours.
  • Hot working can be done, for example, by forging or hot rolling.
  • the surface of the material may be in the whole process if necessary (also several times) in between and / or at the end for cleaning by chemical (eg by pickling) and / or mechanically (eg by machining, by blasting or by grinding) are removed.
  • the leadership of the thermoforming process can be such that the semifinished after then recrystallized with particle sizes between 5 and 100 ⁇ , preferably between 5 and 40 ⁇ , is present. Possibly.
  • inert gas such as. As argon or hydrogen
  • a cold forming for example, rolling, drawing, hammering, embossing, pressing
  • degrees of deformation up to 98% in the desired semi-finished mold possibly with intermediate annealing between 700 ° C and 1270 ° C for 0, 1 min to 70 hours, if necessary under inert gas, such.
  • the final properties of the alloys according to the invention and the parts produced therefrom are achieved by annealing between 600 ° C. and 900 ° C. for 0.1 to 300 hours, followed by air and / or oven cooling.
  • the alloy according to the invention is cured by precipitation of a finely divided ⁇ 'phase.
  • two-stage annealing may be performed by first annealing in the range of 800 ° C to 900X for 0.1 to 300 hours, followed by air cooling and / or furnace cooling and a second anneal between 600 ° C and 800 ° C for 0.1 hours to 300 hours followed by air cooling.
  • 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 3 ⁇ m to 600 ⁇ m. The preferred range is between 5 pm and 70 pm, in particular between 5 and 40 ⁇ m.
  • the alloy of the invention can be well by means of forging, upsetting hot extrusion, hot rolling u. ⁇ . process processes. By means of these methods u. a. Manufacture components such as valves, hollow valves or bolts.
  • the alloy according to the invention should preferably be used in areas for valves, in particular exhaust valves of internal combustion engines. But also a use in components of gas turbines, as fastening bolts, in springs and in turbochargers is possible.
  • the parts produced from the alloy according to the invention in particular z.
  • As the valves or the valve seat surfaces can be subjected to further surface treatments such. As a nitration, to further increase the wear resistance.
  • the hot strength was determined in a hot tensile test according to DIN EN ISO 6892-2.
  • the yield strength R p0 , 2 and the tensile strength R m were determined.
  • 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 10-1 / s (5% / min).
  • the sample was placed in a tensile testing machine at room temperature and heated to the desired temperature with no tensile force. After reaching the test temperature, the sample was held without load for one hour (600 ° C) or two hours (700 ° C to 100 ° C) for temperature compensation. Thereafter, the tensile load was applied to the sample to maintain the desired strain rates and testing was begun.
  • 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 800 ° C in air, the test being interrupted every 96 hours and the mass changes of the samples 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 sample is the gross mass change of the sample.
  • the specific mass change is the mass change related to the surface of the samples.
  • nriNetto for the specific net change in mass m B rutto referred to for the specific gross change in mass m S p a 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.
  • thermoforming should not take place because it forms phases that strongly solidify the material and thus lead to cracking during thermoforming. For a good processability, especially in the hot forming, such. As hot rolling, forging, upsetting, hot extrusion u. A process, a sufficiently large temperature range, in which such phases do not form, must be available.
  • the alloy should have the following properties: • better wear resistance compared to NiCr20TiAI
  • the new material is said to have better wear resistance than the reference alloy NiCr20TiAI.
  • Stellite 6 was also tested for comparison.
  • Stellite 6 is a highly wear-resistant cobalt-based casting alloy with a network of tungsten carbides consisting of approx. 28% Cr, 1% Si, 2% Fe, 6% W, 1, 2% C, but the remainder is directly due to its high carbide content must be poured into the desired shape. Due to its network of tungsten carbides, Stellite 6 achieves a very high hardness of 438 HV30, which is very advantageous for wear.
  • the alloy "E” according to the invention is intended to come as close as possible to the volume loss of Stellite 6. The aim is, in particular, to reduce high-temperature wear between 600 and 800 ° C., which is the relevant temperature range, for example for use as an outlet valve the following criteria apply to the alloys "E” according to the invention:
  • volume loss average (alloy "E") ⁇ 1.3 x volume loss average (reference NiCr20TiAI) at 25 ° C and 300 ° C. (4b) If there is a volume loss of NiCr20TiAI in a measurement series for a large-scale batch and a reference laboratory batch, then the mean value of these two lots is in inequalities (4a) and (4b).
  • Table 3 shows the lower end of the 0.2% yield strength spreading band for NiCr20TiAI when cured at temperatures between 500 and 800 ° C
  • Table 2 shows the lower end of the tensile strength spreading band.
  • the 0.2% yield strength of the alloy according to the invention should be at least in this range for 600 ° C or below 800 ° C this range by not more than 50 MPa to obtain sufficient strength. Ie. In particular, the following values should be achieved:
  • the alloys of the invention do not fall below this value range at 800 ° C, i.
  • the inequalities (5a) and (5b) are achieved when the following relationship between Ti, Al, Fe, Co, Cr and C is satisfied.
  • the alloy of the invention is said to have a corrosion resistance to air similar to that of NiCr20TiAI.
  • the heat resistance or creep strength in the range of 500 ° C. to 900 ° C. is based on the addition of aluminum, titanium and / or niobium, which precipitate the ⁇ 'and / or ⁇ . " If the hot forming of these alloys is carried out in the precipitation area of these phases, there is a risk of crack formation, ie the hot forming should preferably take place above the solvus temperature ⁇ 5 ⁇ ⁇ (or T sy ) of these phases is available, the solvus temperature ⁇ 8 ⁇ ⁇ (or T sy ) should be less than 1020 ° C.
  • Tables 5a and 5b show the analyzes of laboratory scale molten batches together with some prior art large scale molten batches used for comparison (NiCr20TiAl).
  • the batches of the prior art are marked with a T, the inventive with an E.
  • the melted laboratory scale batches are marked with an L, the large-scale molten batches with a G.
  • Lot 250212 is NiCr20TiAI, but melted as a laboratory batch, and serves for reference.
  • the blocks of the laboratory-scale molten alloys in Table 5a and b were annealed between 1100 ° C and 1250 ° C for 0.1 to 70 hours, and by hot rolling and further intermediate annealing between 1100 ° C and 1250 ° C for 0.1 to Hot rolled for 1 hour to a final thickness of 13 mm or 6 mm.
  • the temperature control during hot rolling was such that the sheets were recrystallized.
  • the large-scale molten comparative batches were melted by VIM and poured into blocks. These blocks were remelted ESU. These blocks were between 1100 ° C and 1250 ° C for 0.1 min to 70 h, optionally under inert gas, such as. As argon or hydrogen, followed by cooling in air, annealed in the moving annealing atmosphere or in a water bath and by hot rolling and further intermediate annealing between 100 ° C and 1250 ° C for 0.1 to 20 hours to a final diameter between 17 and 40 mm hot rolled. The temperature control during hot rolling was such that the sheets were recrystallized. All alloy variants typically had a grain size of 21 to 52 pm (see Table 6).
  • Table 6 shows Vickers hardness HV30 before and after cure annealing.
  • the hardness HV30 in the cured state is in the range of 366 to 416 for all alloys except batch 250330.
  • the batch 250330 has a somewhat lower hardness of 346 HV30.
  • Table 7 shows the means ⁇ standard deviations of the measurements taken. If the standard deviation is missing, this is a single value.
  • the composition of the batches is roughly described in Table 7 in the column Alloy for orientation.
  • the maximum values for the volume loss of the alloys according to the invention from the inequalities (4a) for 600 or 800X and (4b) for 25 ° C and 300 ° C registered
  • Figure 1 shows the volume loss of the prior art NiCr20TiAI Charge 320776 pin as a function of test temperature measured at 20N, 1 mm sliding path, 20 Hz and with the force measuring module (a).
  • the experiments at 25 and 300 ° C were carried out for one hour and the experiments at 600 and 800 ° C were carried out for 10 hours.
  • the volume loss decreases strongly with the temperature up to 600 ° C, d. H. the wear resistance noticeably improves at higher temperatures.
  • In the high temperature range at 600 and 800 ° C there is a comparatively low volume loss and thus a low wear, which is based on the formation of a so-called “glaze” layer between pin and disc.This "Glaze” layer consists of compacted metal oxides and material of pin and Disc.
  • Figure 2 shows the volume loss of the prior art NiCr20TiAI Charge 320776 pen as a function of test temperature measured at 20N, 1 mm sliding path, 20 Hz, and with the force measuring module (s).
  • lot 320776 qualitatively the same behavior as with the force modulus (a) shows: the volume loss decreases strongly with temperature up to 600 ° C, whereby the values at 600 and 800 ° C are still smaller than those with the force measuring module ( a) measured.
  • the values measured at Steinte 6 are also entered in Fig. 2.
  • Figure 4 shows the volume loss of the pen for different laboratory batches compared to NiCr20TiAI, lot 320776 and Steinte 6 at 25 ° C after 1 hour measured at 20 N, glide path 1 mm, 20 Hz with force measuring module (a) and (n).
  • the values with force measuring module (s) were systematically smaller than those with force measuring module (a).
  • NiCr20TiAI as laboratory batch 250212 and as large-scale batch 320776 had a volume loss similar to the measurement accuracy.
  • the laboratory batches can thus be compared directly with the large-scale batches in terms of wear measurements.
  • the charge 250325 with approx. 6.5% Fe showed at 25 ° C a volume loss smaller than the maximum value from (4b) for both force measuring modules (see Table 7).
  • the volume loss of charge 250206 with 1 1% Fe tended to be in the upper spread of lot 320776, but the mean was also less than the maximum value of (4a).
  • Charge 250327 with 29% Fe showed a slightly increased volume loss in the measurements with force measuring module (s), but the average value was also smaller than the maximum value from (4b) for both force measuring modules.
  • the invention Co-containing laboratory batches showed on the other hand tend to have a reduced volume loss in batch 250209 (9.8% Co) with load module (s) with 1, 04 ⁇ 0.01 mm 3 is straight out of the stray field from batch 320776 out.
  • Figure 5 shows the volume loss of the pin for alloys with different carbon contents compared to NiCr20TiAI, lot 320776 at 25 ° C measured at 20 N, glide path 1 mm, 20 Hz with force measuring module (a) after 10 hours. Neither a reduction of carbon content to 0.01% for lot 250211 nor an increase to 0.211% for lot 250214 showed a change in volume loss as compared to lot 320776.
  • Figure 6 shows the volume loss of the pin for various alloys compared to NiCr20TiAI, lot 320776 at 300 ° C at 20N, glide path 1mm, 20Hz after 1 hour as measured with force measuring modules (a) and (n).
  • the values with force measuring module (s) are systematically smaller than those with force measuring module (a). Taking this into account below, it can be seen that at 300 ° C Steinte 6 was worse than batch 320776.
  • Co-containing laboratory melts 250329 and 250330 showed no reduction in wear volume as at room temperature, but this was in the range of the wear volume of NiCr20TiAI, batch 320776 and thus showed no increase as in Steinte 6.
  • the volume loss of all 3 Co-containing batches 250209 according to the invention, 250329 and 250330 were well below the maximum value of criterion (4b).
  • the Fe-containing laboratory melts 250206 and 250327 showed a volume loss which decreased with the increasing Fe content, which was thus below the maximum value (4b).
  • the laboratory batch 250326 with the Cr content of 30% had a volume loss in the range of the charge NiCr20TiAI, 320776.
  • Figure 7 shows the volume loss of the pin for different alloys compared to NiCr20TiAI, lot 320776 at 600 ° C measured at 20 N, glide path 1 mm, 20 Hz and with force measuring module (a) and (n) after 10 hours.
  • the values with force measuring module (s) were systematically smaller than those with force measuring module (a).
  • the reference laboratory batch 250212 also had the high temperature range of wear to NiCr20TiAI with 0.066 ⁇ 0.02 mm 3, a similar volume loss, such as the large-scale batch 320776 with 0.053 ⁇ 0.0028 mm 3.
  • the laboratory batches can thus be compared with the large-scale batches in terms of wear measurements even in this temperature range.
  • Steinte 6 showed a volume loss of 0.009 ⁇ 0.002 mm 3 (force measuring module (s)), which was reduced by a factor of 3. Furthermore, it was found that neither a reduction of the carbon content to 0.01% for batch 250211 nor an increase to 0.211% for batch 250214 resulted in a change in the volume loss compared to batch 320776 and 250212 (force measuring module (a)). , Also, the addition of 1.4% manganese on Charge 250208 and 4.6% tungsten on Charge 250210, respectively, did not result in any significant change in volume loss as compared to Charge 320776 and 250212.
  • Figure 8 shows the volume loss of the pin for the different alloys compared to NiCr20TiAI lot 320776 at 800 ° C with 20 N for 2 hours followed by 100 N for 3 hours, all with 1 mm sliding path, 20 Hz measured with force measuring module (s). Also at 800 ° C, it was confirmed that in the high temperature region of wear, the reference laboratory batch 250212 to NiCr20TiAI at 0.292 ⁇ 0.016 mm 3 had a comparable volume loss as the large scale batch 320776 with 0.331 ⁇ 0.081 mm 3 . The laboratory batches could thus be compared directly with the large-scale batches in terms of wear measurements even at 800 ° C.
  • a further reduction of volume loss in comparison to the batch 320,776th showed 0.057 + 0.007 mm 3 in the 250327 29% Fe, the volume loss was 0.043 ⁇ 0.02 mm 3.
  • the volume loss of the pin in the wear test could be greatly reduced in the alloys of the invention by a Co content between> 3 and 40%, so that it at one of the two temperatures 600 or 800 ° C was less than or equal to 50% of the volume loss of NiCr20TiAI (4a).
  • the alloy according to the invention with a Co content of> 3 to 40% also fulfilled the inequalities (4b) at 25 ° C. and 300 ° C.
  • batch 250326 with 30% Cr showed a reduction in volume loss to 0.042 + 0.011 mm 3 at 800 ° C and both to 0.026 mm 3 at 600 ° C below the respective maximum value from (4a).
  • the volume loss of 0.2588 mm 3 was also below the maximum value of (4a), as well as at 25 ° C with on 1, 41 + 0.18 mm 3 (force measuring module (s)), so that chromium contents between 18 and 31% are particularly beneficial for wear at higher temperatures.
  • NiCr20TiAl alloys lots 320776 and 250212, had a total Cr + Fe + Co of 20.3% and 20.2%, both less than 25%, and met criteria (4a) and (4b) for a very good wear resistance, but especially the criteria (4a) for a good high temperature wear resistance not. Also, lots 250211, 250214, 250208 and 250210, in particular, did not meet the criteria (4a) for good high-temperature wear resistance and had a total Cr + Fe + Co of 20.4%, 20.2%, 20.3% and 20, respectively , 3% all less than 25%.
  • the batches 250325, 250206, 250327, 250209, 250329, 250330 and 250326 with Fe and Co additions or an increased Cr content in particular the batches 250209, 250329 and 250330 according to the invention, in each case met the criteria (4a) for 800 ° C, sometimes even additionally for 600 ° C and had a total Cr + Fe + Co of 26.4%, 30.5%, 48.6%, 29.6%, 50.0%, 59.3%, respectively 30.3% all larger 25%. They fulfilled equation (1) for very good wear resistance. Temperature strength / creep
  • Figure 10 shows the yield strength R p0 2 and the tensile strength R m for 600 ° C
  • Figure 11 for 800 ° C.
  • Batches 321863, 321426 and 315828 smelted on an industrial scale had values between 841 and 885 MPa at 600 ° C. for the yield strength R p o2 and between 472 and 481 MPa at 800 ° C.
  • the reference batch 250212, with a similar analysis as the large-scale batches had a slightly higher aluminum content of 1, 75%, at 600 ° C to a slightly greater yield strength R p0 2 on 866 MPa and 800 ° C of 491 MPa led.
  • the yield strengths R p0 , 2 of all laboratory lots (L), including the batches (E) according to the invention, and all large-scale batches (G) were greater than 650 MPa, so the criterion ( 5a).
  • An alloy content of> 3.0% to 40% Co in The alloy according to the invention is therefore advantageous in order in particular to obtain a yield strength R p0 , 2 at 800 ° C. of greater than 390 MPa (5b) or even greater than 450 MPa (5c).
  • a certain amount of iron may be advantageous in the alloy for cost reasons.
  • Batch 250327 with 29% Fe barely met the inequality (5b) because, like the consideration of the laboratory batch 250212 (reference, similar to the large-scale batches Fe less than 3%) or also the large-scale batches and the batches according to the invention 250325 (6.5 % Fe), 250206 (11% Fe) and 250327 (29% Fe) showed that an increasing alloy content of Fe reduced the yield strength R p o, 2 in the tensile test (see also Figure 1 1). Therefore, an alloy content of 20% Fe is to be regarded as an upper limit for the alloy according to the invention.
  • the laboratory batch 250326 showed that with an addition of 30% Cr, the insertion limit R p0 , 2 in the tensile test at 800 ° C to 415 MPa reduced, which was still well above the minimum value of 390 MPa. Therefore, an alloy content of 31% Cr is to be regarded as an upper limit for the alloy according to the invention.
  • Table 9 shows the specific mass changes after an oxidation test at 800 ° C in air after 6 cycles of 96 h for a total of 576 h. Given in Table 9 is the specific gross mass change, the net specific mass change and the specific mass change of the chipped oxides after 576 hours.
  • the sample batches of the alloys according to the prior art NiCr20TiAI, batch 321426 and 250212 showed a specific gross mass change of 9.69 or 10.84 g / m 2 and a specific net mass change of 7.81 or 10.54 g / m 2 . Lot 321426 showed minor flakes.
  • Lots 250209 (Co 9.8%) and 250329 (Co 30%) of the present invention had a specific gross mass change of 10.05 and 9.91 g / m 2 and a net specific mass change of 9.81 and 9, respectively , 71 g / m 2 , which were in the range of NiCr20TiAI reference alloys and, as required, were no worse than these.
  • batch 250330 of the invention (29% Co, 10% Fe) behaved with a specific gross mass change of 9.32 g / m 2 and a net specific mass change of 8.98 g / m 2 .
  • a Co content of> 3 to 40% thus does not adversely affect the oxidation resistance.
  • Batch 250326 with an increased Cr content of 30% had a specific gross mass change of 6.74 g / m 2 and a specific net change in mass of 6.84 g / m 2, which were below the range of the reference NiCr20TiAI alloys.
  • All of the alloys shown in Table 5b contain Zr, which contributes as a reactive element to improve corrosion resistance.
  • further reactive elements such as Y, La, Ce, cerium mischmetal, Hf can be added, which exhibit a Zr-like activity.
  • 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 a closed chromium oxide layer can no longer form. Therefore, 18% Cr is the lower limit for chromium. Too high Cr contents increase the solvus temperature ⁇ 5 ⁇ too much, so that the processability deteriorates markedly. That's why 31% is considered the upper limit.
  • Titanium enhances the high temperature strength at temperatures in the range up to 900 ° C by promoting the formation of the ⁇ 'phase. At least 1, 0% is necessary to obtain sufficient strength. Too high a titanium content increases the solvus temperature ⁇ 8 ⁇ ⁇ too much, so that the processability deteriorates significantly. Therefore, 3.0% is considered the upper limit.
  • Aluminum increases the high temperature strength at temperatures in the range up to 900 ° C by promoting the formation of the y 'phase. At least 0.6% is necessary to obtain sufficient strength. Too high an aluminum content increases the solvus temperature T s too much, so that the processability deteriorates significantly. Therefore, 2.0% is considered the upper limit.
  • Carbon improves creep resistance.
  • a minimum content of 0.005% C is required for good creep resistance.
  • Carbon is limited to a maximum of 0.10%, since this element reduces the processability due to the excessive formation of primary carbides.
  • a minimum content of 0.0005% N is required for cost reasons.
  • N is limited to a maximum of 0.050%, since this element reduces the processability by the formation of coarse carbonitrides.
  • the content of phosphorus should be less than or equal to 0.030%, since this surfactant affects the oxidation resistance. Too low a phosphorus content increases the costs. The phosphorus content is therefore> 0.0005%.
  • the levels of sulfur should be adjusted as low as possible, since this surfactant affects oxidation resistance and processability. It will therefore max. 0.010% S set.
  • the oxygen content must be less than or equal to 0.020% to ensure the manufacturability of the alloy.
  • Si content is therefore limited to 0.70%.
  • Mg contents and / or Ca contents improve the processing by the setting of sulfur, whereby the occurrence of low-melting NiS Eutektika is avoided. If the contents are too high, intermetallic Ni-Mg phases or Ni-Ca phases may occur, which again significantly impair processability.
  • the Mg content or the Ca content is therefore limited to a maximum of 0.05%.
  • Molybdenum is reduced to max. 2.0% limited as this element reduces oxidation resistance.
  • Tungsten is limited to max. 2.0%, since this element also reduces oxidation resistance and has no measurable positive effect on wear resistance at the carbon contents possible in wrought alloys.
  • Niobium increases the high-temperature strength. Higher levels increase costs very much. The upper limit is therefore set at 0.5%.
  • 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.
  • Iron increases wear resistance, especially in the high temperature range. Also, it reduces the cost. It may therefore optionally be between 0 and 20% in the alloy. Excessive iron content reduces the yield strength too much, especially at 800 ° C. Therefore, 20% is to be considered as the upper limit.
  • the alloy may also contain Zr to improve high temperature strength and oxidation resistance.
  • the upper limit is set at 0.20% Zr for cost reasons because Zr is a rare element.
  • 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.
  • Nickel stabilizes the austenitic matrix and is required to form the ⁇ 'phase, which is the hot strength / creep resistance. At a nickel content below 35% the hot strength / creep strength is reduced too much, which is why 35% is the lower limit.
  • the oxidation resistance can be further improved by adding oxygen-affine elements such as yttrium, lanthanum, cerium, hafnium. They do this by incorporating them into the oxide layer and blocking the diffusion paths of the oxygen there on the grain boundaries.
  • the upper limit of yttrium is set at 0.20% for cost reasons, since yttrium is a rare element.
  • the upper limit of lanthanum is set at 0.20% for cost reasons, since lanthanum is a rare element.
  • cerium is set at 0.20% for cost reasons, since cerium is a rare element. Instead of Ce and or La also cerium mischmetal can be used. The upper limit of cerium mischmetal is set at 0.20% for cost reasons.
  • the upper limit of hafnium is set at 0.20% for cost reasons, since hafnium is a rare element.
  • the alloy may also contain tantalum, since tantalum also increases high-temperature strength by promoting ⁇ 'phase formation. Higher levels increase costs very much as tantalum is a rare element. The upper limit is therefore set at 0.60%.
  • Pb is set to max. 0.002% limited because this element reduces the oxidation resistance and the high temperature strength. The same applies to Zn and Sn.
  • Table 2 Reference values for the tensile strength at elevated temperatures of the nickel alloys for exhaust valves mentioned in DIN EN 10090. (+ AT solution annealed: 1000 to 1080 ° C air or water cooling, + precipitation hardened precipitates: 890 to 710/16 h air; 1 ) The values given here are close to the lower scatter band)
  • Table 3 Reference values for the 0.2% yield strength at elevated temperatures of the nickel alloys for exhaust valves mentioned in DIN EN 10090. (+ AT solution annealed: 1000 to 1080 ° C air or water cooling, + precipitation hardened precipitates: 890 to 710/16 h air; 1 ) the values given here are close to the lower scatter band)
  • Table 4 Reference values for the creep rupture strength after 1000 hours at elevated temperatures of the nickel alloys for exhaust valves specified in DIN EN 10090 (+ AT Solution annealed: 1000 to 1080 ° C air or water cooling, + P
  • precipitation hardened 890 to 710/16 h air; 1 ) averages of the previously recorded spread
  • Table 5a Composition of large-scale and laboratory batches, Part 1. All concentration data in mass% (T: alloy according to the prior art, E: alloy according to the invention, L: smelted on a laboratory scale, G: melted on an industrial scale)
  • Table 6 Results of the particle size determination and the hardness measurement HV30 at room temperature (RT) before (HV30_r) and na (HV30_h) the curing annealing (850 ° C for 4 h / air cooling followed by annealing 700 ° C for 16 h / air cooling); KG grain size.
  • T alloy according to the prior art
  • E alloy according to the invention
  • L melted on a laboratory scale, melted on an industrial scale
  • Table 7 Wear volume of the pin in mm 3 at a load of 20 N with a sliding path of one mm, a frequency of 20 Hz and a relative humidity of approx. 45% of the large-scale and laboratory batches.
  • 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
  • the mean values ⁇ standard deviation are indicated. If the standard deviation is missing, this is a single value.
  • Table 8 Results of tensile tests at room temperature (RT), 600 ° C and 800 ° C.
  • the forming speed was R p0 , 2 8,33 10 "5 1 / s (0,5% / min) and R m 8,33 10 ⁇ 1 / s (5% / min);
  • KG particle size (T : Alloy according to the prior art, E: alloy according to the invention, L: smelted on a laboratory scale, G: smelted on an industrial scale) *) Measurement error
  • Table 9 Results of the oxidation tests at 800 ° C in air after 576 h. (T: alloy according to the prior art, alloy according to the invention, L: melted on a laboratory scale, G: melted on an industrial scale)
  • Figure 1 Volume loss of the pin made of NiCr20TiAI lot 320776 after the
  • Figure 3 Volume loss of the pin made of NiCr20TiAI lot 320776 after the
  • Fig. 1 1 Yield strength R p0 , 2 and tensile strength R m for the alloys from table
  • Fig. 12 Yield strength R p o, 2 and fh calculated according to formula 2 for the alloys from table 8 at 800 ° C. (L: melted on a laboratory scale, G: melted on an industrial scale).

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Abstract

L'invention concerne un alliage de corroyage thermodurcissable de nickel-chrome-cobalt-titane-aluminium présentant une résistance à l'usure satisfaisante, tout en présentant une résistance au fluage très satisfaisante, une résistance à la corrosion sous haute température satisfaisante et une aptitude au façonnage satisfaisante. Ledit alliage comprend (en % en masse) >18 à 31 % de chrome, 1,0 à 3,0 % de titane, 0,6 à 2,0 % d'aluminium, >3,0 à 40 % de cobalt, 0,005 à 0,10 % de carbone, 0,0005 à 0,050 % d'azote, 0,0005 à 0,030 % de phosphore, max. 0,010 % de soufre, max. 0,020 % d'oxygène, max. 0,70 % de silicium, max. 2,0 % de manganèse, max. 0,05 % de magnésium, max. 0,05 % de calcium, max. 2,0 % de molybdène, max. 2,0 % de tungstène, max. 0,5 % de niobium, max. 0,5 % de cuivre, max. 0,5 % de vanadium, si nécessaire 0 à 20 % de Fe, si nécessaire 0 à 0,20 % de Zr, si nécessaire 0,0001 à 0,008 % de bore, le reste étant du nickel et les impuretés habituelles liées au procédé, la teneur en nickel étant supérieure à 35 %. La relation Cr + Fe + Co ≥ 25 % (1) doit être satisfaite afin d'obtenir une résistance à l'usure satisfaisante et la relation fh ≥ 0 (2a), avec fh = 6,49 + 3,88 Ti + 1,36 AI - 0,301 Fe + (0,759 - 0,0209 Co) Co - 0,428 Cr - 28,2 C (2), doit être satisfaite afin qu'une résistance suffisante soit donnée à des températures plus élevées, Ti, AI, Fe, Co, Cr et C représentant la concentration des éléments concernés en % en masse et fh étant donnée en %.
EP15704947.9A 2014-02-04 2015-01-12 Alliage nickel-chrome-cobalt-titane-aluminium présentant une résistance à l'usure, une résistance au fluage, une résistance à la corrosion élevées et une usinabilité Active EP3102710B1 (fr)

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PCT/DE2015/000007 WO2015117583A1 (fr) 2014-02-04 2015-01-12 Alliage thermodurcissable de nickel-chrome-cobalt-titane-aluminium présentant une résistance à l'usure, une résistance au fluage, une résistance à la corrosion et une aptitude au façonnage satisfaisantes

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SI3102710T1 (sl) 2018-12-31
DE102014001330B4 (de) 2016-05-12
KR20160137511A (ko) 2016-11-30
BR112016011895B1 (pt) 2021-02-23
CN105899693B (zh) 2018-04-10
DE102014001330A1 (de) 2015-08-06
KR101824867B1 (ko) 2018-02-02
CN105899693A (zh) 2016-08-24
EP3102710B1 (fr) 2018-08-29
US10870908B2 (en) 2020-12-22
US20160319402A1 (en) 2016-11-03
JP2017508884A (ja) 2017-03-30
BR112016011895A2 (pt) 2017-09-19
WO2015117583A1 (fr) 2015-08-13

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