EP1702083A1 - Verfahren zur herstellung eines austenitischen produkts und verwendung davon - Google Patents
Verfahren zur herstellung eines austenitischen produkts und verwendung davonInfo
- Publication number
- EP1702083A1 EP1702083A1 EP04809190A EP04809190A EP1702083A1 EP 1702083 A1 EP1702083 A1 EP 1702083A1 EP 04809190 A EP04809190 A EP 04809190A EP 04809190 A EP04809190 A EP 04809190A EP 1702083 A1 EP1702083 A1 EP 1702083A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- aluminium
- weight
- austenitic
- content
- 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.)
- Withdrawn
Links
- 238000000034 method Methods 0.000 title claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 title claims description 23
- 239000000956 alloy Substances 0.000 claims abstract description 94
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 93
- 239000000758 substrate Substances 0.000 claims abstract description 39
- 239000000463 material Substances 0.000 claims description 81
- 229910052782 aluminium Inorganic materials 0.000 claims description 53
- 239000004411 aluminium Substances 0.000 claims description 49
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical group [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 49
- 239000000203 mixture Substances 0.000 claims description 25
- 239000000047 product Substances 0.000 claims description 21
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 13
- 150000002910 rare earth metals Chemical class 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 12
- 230000003197 catalytic effect Effects 0.000 claims description 10
- 229910052726 zirconium Inorganic materials 0.000 claims description 10
- 229910052727 yttrium Inorganic materials 0.000 claims description 8
- 229910052684 Cerium Inorganic materials 0.000 claims description 7
- 229910052746 lanthanum Inorganic materials 0.000 claims description 7
- 239000012467 final product Substances 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 5
- 229910052706 scandium Inorganic materials 0.000 claims description 5
- 229910052772 Samarium Inorganic materials 0.000 claims description 4
- -1 e.g. Chemical class 0.000 claims description 3
- 235000015392 Sesbania grandiflora Nutrition 0.000 claims 1
- 244000275021 Sesbania grandiflora Species 0.000 claims 1
- 235000010210 aluminium Nutrition 0.000 description 46
- 230000003647 oxidation Effects 0.000 description 33
- 238000007254 oxidation reaction Methods 0.000 description 33
- 238000000576 coating method Methods 0.000 description 19
- 239000011248 coating agent Substances 0.000 description 16
- 239000011888 foil Substances 0.000 description 13
- 238000012360 testing method Methods 0.000 description 13
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 11
- 229910000838 Al alloy Inorganic materials 0.000 description 9
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 8
- 239000010410 layer Substances 0.000 description 7
- 238000000137 annealing Methods 0.000 description 6
- 238000007796 conventional method Methods 0.000 description 6
- 238000009792 diffusion process Methods 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 239000002184 metal Substances 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 229910052735 hafnium Inorganic materials 0.000 description 5
- 229910052759 nickel Inorganic materials 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 238000007792 addition Methods 0.000 description 4
- 230000003247 decreasing effect Effects 0.000 description 4
- 238000003754 machining Methods 0.000 description 4
- 229910052758 niobium Inorganic materials 0.000 description 4
- 229910052757 nitrogen Inorganic materials 0.000 description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- 238000005452 bending Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 239000003054 catalyst Substances 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 238000001336 glow discharge atomic emission spectroscopy Methods 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 230000001681 protective effect Effects 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 238000009834 vaporization Methods 0.000 description 3
- 230000008016 vaporization Effects 0.000 description 3
- 229910017083 AlN Inorganic materials 0.000 description 2
- PIGFYZPCRLYGLF-UHFFFAOYSA-N Aluminum nitride Chemical compound [Al]#N PIGFYZPCRLYGLF-UHFFFAOYSA-N 0.000 description 2
- 229910017060 Fe Cr Inorganic materials 0.000 description 2
- 229910002544 Fe-Cr Inorganic materials 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- UPHIPHFJVNKLMR-UHFFFAOYSA-N chromium iron Chemical compound [Cr].[Fe] UPHIPHFJVNKLMR-UHFFFAOYSA-N 0.000 description 2
- 229910017052 cobalt Inorganic materials 0.000 description 2
- 239000010941 cobalt Substances 0.000 description 2
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 2
- 238000007598 dipping method Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 238000004626 scanning electron microscopy Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 241000365446 Cordierites Species 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 239000011149 active material Substances 0.000 description 1
- 229960005363 aluminium oxide Drugs 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000000332 continued effect Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 235000000396 iron Nutrition 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000005240 physical vapour deposition Methods 0.000 description 1
- 238000009853 pyrometallurgy Methods 0.000 description 1
- 238000004544 sputter deposition Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- 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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Definitions
- the present invention relates to a method for the manufacture of an austenitic product having elevated content of aluminium, and the use thereof in applications where high temperature resistance in the form of oxidation resistance and improved mechanical properties are required.
- ferritic FeCrAI materials With increasing application temperatures for steel materials in various high- temperature applications, today's ferritic materials have, more precisely ferritic FeCrAI materials, occasionally turned out to be mechanically weak in order to resist the stresses that arise upon use at high temperatures in the form of fast changes of temperature, gas flows varying in temperature, direction and/or composition, and mechanical stresses, such as, e.g., vibrations.
- EP-B 1-1235682 discloses the use of an austenitic nickel base or cobalt base alloy that is coated with aluminium or aluminium alloy and rolled to finished dimension. In such a way, by means of a heat treatment at temperatures above 600 °C, foil of a min. thickness of approx. 50 ⁇ m can be manufactured, which has been tested to approximately 1100 °C. At 1100 °C, the mass of the sample increased by up to 7,6 % after 400 h.
- the disadvantage is, in comparison with conventional FeCrAI material, the relatively high oxidation rate, which is regarded to be the decisive factor for the service life of the catalyst supporting material.
- Austenitic alloys generally have higher mechanical strength at the same high temperatures than ferritic alloys. Austenitic materials of high aluminium content have a considerable improved oxidation resistance in comparison with austenitic materials of lower aluminium contents by virtue of the material having a very low ductility at typical hot-working temperatures, i.e., at 750 to 1200 °C.
- a metallic material for catalysts with elevated working temperatures and in increased mechanical load has to meet the following requirements: an improved mechanical strength in relation to materials used today, as is disclosed in US-B- 5,578,265 and furthermore considerably better oxidation resistance than the austenitic, high-strength materials disclosed in EP-B1-1235682.
- a foil material of a thickness of 50 ⁇ m should not increase in weight more than 6 % after 400 h of oxidation in air at 1100 °C, preferably the increase in weight should be below 4 %.
- An Al alloyed austenitic steel or nickel or cobalt base alloy of more than 4,5 % of Al can be expected to have sufficiently satisfactory mechanical properties and may, for a foil having a thickness of 50 ⁇ m, during certain circumstances attain an increase in weight corresponding to 6 % after 400 h at 1100 °C, but by virtue of utmost limited hot workability at Al contents above 4,5 % by weight, such products are not possible to produce as thin strips by means of conventional methods. Furthermore, the oxidation resistance of such materials are still inferior compared to ferritic materials used today.
- Figure 1 shows results of hot ductility testing, so-called Gleeble testing, the reduction of area to fracture being measured as a function of the test temperature.
- Figure 2 shows the oxidation rate in air at 1000 °C of examples C and D in comparison with comparison example 1.
- Figure 3 shows the oxidation rate in air at 1100 °C of example C and comparison example 1.
- Figure 4 shows the oxidation rate in air at 1100 °C of examples C, E and F as well as of comparison example 1 having the thicknesses of 50 ⁇ m and 3 mm, and comparison example 3.
- Figure 5 shows the content of aluminium in an Al-coated material after annealing times of different length at 1050 °C, plotted as a function of the distance from the surface.
- an austenitic product that is manufactured by coating an austenitic substrate alloy with the following composition (in % by weight): 20-70 % of Ni, 15-27 % of Cr, 0-5 % of Al, 0- 4 % of Mo and/or W, 0-2 % of Si, 0-3 % of Mn, 0-2 % of Nb, 0-0,5 % of Y, Zr and/or Hf, 0-0,5 % of Ti, 0-0,1 % of one or more rare earth metals (REM) such as, e.g., Ce, La, Sm, 0-0,2 % of C, 0-0,1 % of N, balance Fe and normally occurring impurities, with an aluminium composition such as aluminium or an aluminium-based alloy such as is described below.
- REM rare earth metals
- a preferred composition of the substrate material is (in % by weight) 25-70 % of Ni, 18-25 % of Cr, 1-4 % of Al, 0 ⁇ % of Mo and/or W, 0-2 % of Si, 0-3 % of Mn, 0-2 % of Nb, 0-0,5 % of Y, Zr and/or Hf, 0-0,5 % of Ti, 0-0,1 % of one or more rare earth metals (REM) such as, e.g., Ce, La, Sm, 0-0,1 % of C, 0- 0,05 % of N, balance Fe and normally occurring impurities.
- REM rare earth metals
- the content of aluminium of the final product as well as its mechanical properties and oxidation resistance can be optimized independently of each other.
- the final alloy After coating the substrate material with aluminium or an aluminium-based alloy, the final alloy has a composition consisting of (in % by weight) 25-70 % of Ni, 15-25 % of Cr, 4,5-12 % of Al, 0-4 % of Mo and/or W, 0-4 % of Si, 0-3 % of Mn, 0-2 % of Nb, 0-0,5 % of Ti, 0-0,5 % of Y, Sc, Zr and/or Hf, 0-0,2 % of one or more rare earth metals (REM) such as, e.g., Ce, La, Sm, 0-0,2 % of C, 0-0,1 % of N, balance Fe and normally occurring impurities.
- REM rare earth metals
- the austenitic substrate material has in itself a good high-temperature strength, which is increased by the presence of precipitations of Ni (Nb, Al) and, if required, also by Mo and/or W in solid solution. Additionally increased mechani- cal stability and resistance to grain growth may be given by the presence of precipitations of carbides and/or nitrides of any one or some of the elements Ti, Nb, Zr, Hf.
- Carbon in solid solution or as carbides contributes to an increased mechanical strength at high temperatures. Simultaneously, higher contents of carbon in the substrate material imply deteriorated properties upon cold working. Therefore, the maximal content of carbon in the substrate should be limited to 0,2 % by weight.
- Nitrogen in solid solution or as nitrides contributes to an increased mechanical strength at high temperatures. Simultaneously, higher contents of nitrogen in the substrate material imply that embrittling aluminium nitride may be formed in the production of the substrate or after coating with aluminium or an aluminium- based alloy. Therefore, the maximal content of nitrogen in the substrate should be limited to 0,1 % by weight.
- the austenitic alloy manufactured according to the invention is used in a coated and not heat-treated state or after a diffusion annealing.
- the most favourable compositions for the substrate alloy are obtained if it contains 1-4 % by weight of Al.
- This content of aluminium gives the finished alloy an improved oxidation resistance and an improved production economy without entailing an increased risk of production disturbances in comparison with the manufacture of a material of low content of aluminium.
- the material should in total contain more than 4,5 % by weight of Al.
- the coating with aluminium or an aluminium-based alloy should take place within a temperature range of the substrate that is lower than the melting point of the aluminium, i.e., at a temperature between 100 °C and 600 °C, preferably 150 °C-450 X.
- Addition of Zr and/or Hf and REM and/or Y and/or Sc gives an increased resistance to peeling and flaking of the formed oxide.
- the finished product's contents of said elements may be supplied by addition in the substrate alloy and/or in the aluminium-based alloy that are used in the coating.
- compositions of the alloy according to the invention could be manufactured by conventional metallurgy. However, unlike this, in production by means of the process according to the present invention, a material can be obtained, the microstructure of which is controlled and the oxidation properties and mechanical properties of which are optimal. It is an additional advantage of the process according to the present invention that the total content of aluminium of the final product is not limited by the embrittling effect that contents of aluminium above approx. 4,5 % by weight may give upon later cold and/or hot working.
- the method to coat a substrate material with aluminium or an aluminium-based alloy according to the invention gives a final product, the contents of which of, e.g., Mo, C, Nb can be considerably higher than in a con- ventionally manufactured material without the presence of said elements resulting in any noticeable deterioration of the oxidation properties.
- the proper coating of the substrate alloy with aluminium or an aluminium-based alloy may be effected by processes such as, e.g., dipping in melt, electrolytic coating, rolling together strips of aluminium or an aluminium alloy from a gas phase by so-called CVD or PVD technique.
- the coating with aluminium or aluminium-based alloy can be carried out after the substrate alloy has been rolled or in another way been machined to desired product dimension.
- a diffusion annealing may be carried out in order to provide a homo- genization of the material and then plastic machining in one or more steps may be carried out in order to provide the final product.
- Plastic machining such as, e.g., rolling or drawing may also be effected directly on a coated product of larger dimensions than the desired final dimension. In this case, the plastic machining may be followed by annealing.
- the content of aluminium in the final product can be varied by means of different factors: the thickness of the substrate material in relation to the thickness of the coating, the content of aluminium in the substrate material as well as the content of aluminium of the coating.
- the total content of aluminium in the finished product always has to be at least 4,5 % by weight in order to secure sufficient properties.
- the product may be used in the form of an annealed, homogeneous material or a laminate or a material having a concentration gradient of Al with the Al content being higher at the surface than in the centre of the material.
- the aluminium alloy contains 0-25 % of Si and/or 0-2 % by weight of one or more of the elements Ce, La, Sc, Y, Zr, Hf and/or 0-5 % by weight of one or more of the elements Mg, Ti, Cr, Mn, Fe, Ni, Co and/or 0-1 % by weight of one or more of the elements B, Ge, preferably the aluminium alloy should contain at least 90 % of Al, 0-10 % of Si and/or 0-2 % by weight of one or more of the elements Ce, La, Sc, Y, Zr, Hf, more preferably the aluminium alloy should contain at least 95 % of Al, 0-5 % of Si and/or 0-2 % by weight of one or more of the elements Ce, La, Sc, Y, Zr, Hf.
- Table 1 indicates examples of compositions of examined alloys.
- the alloys according to examples A and B as well as the Comparative examples 1 , 2 and 3 were manufactured in the conventional way by pyrometallurgy and hot working.
- Comparison example 1 is an alloy that today is used as supporting material in catalytic converters and that has acceptable oxidation resistance for this use.
- Comparison example 2 is an austenitic alloy of high Al content, manufactured by conventional methods. The yield upon hot working of said alloy was only approximately 10 %, i.e., 90 % of the material had such internal defects in the form of, e.g., cracks that it could not be used for further working.
- the alloys according to examples A and B have compositions that are suitable to be used as substrate materials in a coating process where a thin layer of aluminium or an aluminium-based alloy is deposited on said substrate. From the alloys according to Examples A and B as well as comparison example 1 , 50 ⁇ m thick strips were manufactured via hot rolling and cold rolling. The yield in the production of the alloys in examples A and B was the same as comparison example 1. In order to avoid formation of aluminium nitride, the content of nitrogen in the substrate materials is low. In order to limit this tendency further, Ti, Nb and/or Zr and/or Hf were added. Addition of these elements results in the formation of nitrides that are more stable than AIN, which entails a reduced formation of the latter.
- compositions are chosen in order to enable efficient production of thin strips of the substrate material.
- the content of carbon is below 0,10 %, which allows satisfactory metarial yields in cold working processes.
- the necessary amount of Al that has to be deposited on the substrate is decreased with the purpose of achieving sufficient Al content in the finished product.
- the substrate alloys have a very good high-temperature strength; e.g., at 700 °C the ultimate strength of the alloys according to examples A and B is up to 3 times larger than of the conventional material in comparison example 1, and at this temperature the yield point in tension is 2,8 to 5 times larger than of comparison example 1.
- the yield point in tension of the alloy according to examples A and B is approximately 5 times larger of for comparison example 1 , while the ultimate strength is at least 3,5 times higher than of comparison example 1.
- the two substrate alloys used in Examples A and B meet the requirements of sufficient mechanical strength and manufacturability as thin foil.
- Figure 1 shows results of hot ductility testing, so-called Gleeble testing, where the reduction of area to fracture is measured as a function of the test temperature, for the alloys according to Examples A and B and for comparison example 2.
- the reduction of area to fracture should exceed 40 %.
- the average reduction of area to fracture should be at least 70 % at a temperature difference of 100 °C.
- the alloys according to Examples A and B are both sufficiently ductile at room temperature and at elevated temperatures in order to be able to be cold-rolled to very thin strips with satisfactory productivity, which is seen in that they could be manufactured without problems down to material thicknesses of 50 ⁇ m, and are thereby good candidate materials to be used as substrate materials for a coating with aluminium or an aluminium-based alloy Al.
- the alloys in examples C and D were manufactured by coating the two surfaces of cold-rolled, 50 ⁇ m thick, strips of the alloy according to examples A and B, respectively, by vaporization or sputtering with Al in such an amount that the total Al content corresponded to 5,5-6 % (see table 3).
- the coating was effected by a certain heating of the substrate material, however not to such a high temperature that melted Al was present on the substrate.
- the coating with Al or Al alloy according to the invention should accordingly be effected within a temperature range of the substrate of 100 °C-660 °C, preferably in the temperature range of 150-450 °C.
- the alloy according to comparison example 2 which has approximately the same total composition as the alloy in example C, could, as has been men- tioned previously, be forged, but only with a very low material yield.
- the limited hot ductility entails that this alloy hardly can be manufactured in the form of thin strips.
- the same alloy has, as is seen in table 2, a very good heat resistance; e.g., the ultimate strength at both 700 °C and 900 °C is 3 to 4 times larger than of the conventional material in comparison example 1 , and the yield point in tension is more than 4 times as large at both test temperatures.
- the thickness of the Al layer obtained on 50 ⁇ m thick strip according to example C was measured by GDOES (Glow Discharge Optical Emission Spectroscopy), a method that enables accurate measuring of compositions and thicknesses of thin surface layers. The analysis showed that the sample had a total Al content of 5-6 % by weight. These samples were oxidized in air at 1000 °C for up to 620 h. The results are shown in Figure 2.
- the alloy according to Example C has an oxidation resistance that is comparable with the conventionally manufactured Fe-Cr-AI alloy of the same thickness (comparison example 1) and has a significantly better oxidation resistance than the alloy according to example D. After 400 h, the alloy according to example C has increased 2,3 % in weight, while the alloy according to example D increased 5 % in weight. After the same time, comparison example 1 has increased approx. 2,2 % in weight.
- the alloy according to Example C was oxidation tested at 1100 °C together with comparison example 1 , which is shown in Figure 3.
- the two materials were tested in the form of foil of a thickness of 50 ⁇ m. After up to 300 h of test time, the two materials are equally good.
- both the alloy according to Example C and comparison example 1 have increased less than 6 % in weight: the alloy according to example C by 5,9 % and comparison example 1 by 4,3 %.
- the alloy according to Example C meets the requirement of sufficient oxidation resistance for use in catalytic converters, maximum 6 % increase in weight in 50 ⁇ m thickness upon oxidation in 400 h at 1100 °C.
- Examples E and F are the alloys according to examples C and D, respectively, that have been annealed at 1200 °C for 20 min with the purpose of providing an equalising of the Al content in the material (see table 4).
- the ductility of the material was assessed by means of a bending test where the smallest bending radius that the material could be bent to without fracturing was determined (see table 4).
- the narrowest radius that the material was tested at was 0,38 mm. None of the materials exhibited any damage after this bending.
- the radius is smaller than the one used in the production of catalytic converters. Thereby, strips manufactured according to the invention have a fully sufficient ductility to allow the use thereof in catalytic converters.
- example E has an ultimate strength of 166 MPa (see table 2), which is more than four times larger than the material according to comparison example 1 used at present, and fur- thermore somewhat higher than a conventionally manufactured material according to comparison example 2, having a similar composition as alloys that have been manufactured in accordance with the invention. Table 4. Results of test of coated and diffusion-annealed samples
- the alloys according to Examples C and E have almost the same composition as the alloy in comparison example 2, and also here, a similar effect of different sample thickness would be expected, as for comparison example 1.
- the relative improvement in oxidation resistance with decreasing sample thickness of the alloy according to the invention is considerably larger than it is of comparison example 1 (see table 5). This may be regarded to be a highly unexpected and valuable effect of the method according to the invention.
- Example F has equally good oxidation resistance as Example C or comparison example 1 in the form of foil. Testing was interrupted after 220 h for the alloy according to Example F. However, comparison between the increase in weight up to 220 h at 1100 °C of examples E and F shows that the alloy according to Example E has the most suitable combination of composition and way of production as regards oxidation resistance.
- a 50 ⁇ m thick strip of the alloy according to example A was coated with Al by means of vaporization.
- Various samples were annealed for different times at 1050 °C in Ar gas.
- Concentration profiles of Al in the material were determined by GDOES. The results are shown in figure 5. It is clear that an Al enriched area is left near the surface of the strip also after 8 h of heat treatment. This area seems only to be consumed slowly by Al diffusion inwardly in the strip.
- a 50 ⁇ m thick strip of the alloy according to example A was coated with Al by means of vaporization.
- a sample was annealed for 50 min at 1150 °C in Ar gas.
- the micro structure was analysed by means of SEM (scanning electron microscopy).
- Figure 6 shows the area closest to the sample surface. Farthest out, a Fe-Cr rich layer (cf. "0" in figure 6) is formed, inside this, a Ni and Al enriched area (cf. "1" in figure 6).
- Layer “2" corresponds to a diffusion zone of slowly decreasing Al content with increasing distance from the surface.
- the composition is the same as in the substrate material.
- Catalytic conversion is since a number of years a requirement in most industri- alised countries.
- the catalytically active material is carried mechanically by a supporting material.
- the requirements on the supporting material are, among other things, that it should have a large surface, withstand temperature varia- tions and have sufficient mechanical strength and oxidation resistance at the operating temperature of the catalytic converter.
- Ceramic and metallic Two main types of supporting materials are used today: ceramic and metallic.
- the ceramic supporting materials which frequently are manufactured from cordierit, are not affected by oxidation, however their brittleness means that the resistance to impacts and other mechanical stresses as well as to temperature variations such as fast changes of temperature is very limited.
- metallic supporting materials generally are based on thin strips of ferritic Fe-Cr-AI alloys with additions of small amounts of reactive elements such as rare earth metals (REM) or Zr or Hf.
- REM rare earth metals
- Zr or Hf reactive elements
- the supporting material should be as thin as possible, usually between 10 ⁇ m and 200 ⁇ m.
- a common strip thickness is 50 ⁇ m, but considerably enhanced efficiency of the catalytic converter by virtue of an increased surface/volume- ratio and/or decreased fall of pressure over the catalytic converter can be expected upon a reduction of the strip thickness to 30 ⁇ m or 20 ⁇ m.
- the high ductility of the metal gives a good resistance to mechanical and thermal fatigue. Aluminium in contents above approx. 4,5 % by weight gives, together with the reactive elements, the material the possibility of forming a thin, protective, alu- minium oxide upon heating. Furthermore, the reactive elements make the oxide getting a considerably reduced tendency to peel, i.e., come loose from the metal upon cooling or mechanical deformation.
- conventional Fe-Cr-AI alloys have a large disadvantage: they are mechanically very weak at high temperatures, and therefore tend to be greatly deformed also upon small stresses by virtue of, e.g., acceleration, changes of pressure, mechanical impacts or changes of temperature.
- the invention is not limited to products in small dimensions, such as thin strips or thin wire. Since an austenitic material having a content of aluminium that is larger than 4,5 % by weight cannot be produced with sufficient productivity and material yield by hot working, it is valuable to be able to manufacture such an alloy in thicker dimensions by the coating method described in the present invention. This may be effected, e.g., by manufacturing a product in the form of, e.g., sheet-metal plate, strip, foil or a seamless tube, in a substrate alloy, and then said product is coated, on one or both surfaces with an aluminium alloy in such an amount that the total content of aluminium of the material exceeds 4,5 % by weight.
- a seamless tube having the composition according to example A may be manufactured by means of conventional methods to the following dimensions: outer diameter 60,33 mm, wall thickness 3,91 mm.
- outer diameter 60,33 mm, wall thickness 3,91 mm In order to be able to achieve a total content of aluminium of at least 4,5 % by weight in such a tube, it needs to be coated with aluminium on the inner and outer surface with a thickness of at least 0,1 mm.
- Such an amount may be applied to the surfaces of the tube by conventional methods, e.g., by dipping in a melt of an aluminium alloy. If a homogeneous material is desired, a longer heat treatment at high temperature is required, suitably at least 1000 °C.
- the finished product should suitably be manufactured in a partly homogenized form, where the material has an aluminium gradient that increases towards the surfaces, e.g., by a heat treatment where the material slowly is heated to 1100 °C and is heat-treated at this temperature for between 5 min and 10 h, depending on the desired aluminium distribution.
- a heat treatment where the material slowly is heated to 1100 °C and is heat-treated at this temperature for between 5 min and 10 h, depending on the desired aluminium distribution.
- the content of aluminium in the substrate material should be as high as possible, without causing production disturbances in the manufacture of the substrate.
- a suitable content of aluminium in the substrate material is 2-4 % by weight.
- This method can be used to manufacture a finished product or to manufacture a starting material for contin- ued plastic machining at low temperature, e.g., a tubular blank for vocational step rolling.
- the alloy produced according to the invention may also be used in other high temperature applications, such as applications requiring a high oxidation resistance and good mechanical properties.
- it could be used in heat exchangers or as protective plates.
- it could be used in other environments such as in reducing atmosphere. In this latter case it could be advantageous in some cases to pre-oxidise the product before use in order to assure a stable and dense Al-containing oxide on the surface.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
- Catalysts (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE0303608A SE527174C2 (sv) | 2003-12-30 | 2003-12-30 | Metod för tillverkning av en austenitisk rostfri stållegering genom beläggning med aluminium samt dess användning i högtemperaturapplikationer |
PCT/SE2004/002017 WO2005064031A1 (en) | 2003-12-30 | 2004-12-15 | Method for the manufacture of an austenitic product as well as the use thereof |
Publications (1)
Publication Number | Publication Date |
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EP1702083A1 true EP1702083A1 (de) | 2006-09-20 |
Family
ID=30768915
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP04809190A Withdrawn EP1702083A1 (de) | 2003-12-30 | 2004-12-15 | Verfahren zur herstellung eines austenitischen produkts und verwendung davon |
Country Status (7)
Country | Link |
---|---|
US (1) | US20080038143A1 (de) |
EP (1) | EP1702083A1 (de) |
JP (1) | JP2007518879A (de) |
KR (1) | KR20060111662A (de) |
CN (1) | CN1902334A (de) |
SE (1) | SE527174C2 (de) |
WO (1) | WO2005064031A1 (de) |
Families Citing this family (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US7413778B2 (en) * | 2005-12-05 | 2008-08-19 | General Electric Company | Bond coat with low deposited aluminum level and method therefore |
CA2743129C (en) * | 2008-11-19 | 2017-10-24 | Sandvik Intellectual Property Ab | Aluminium oxide forming nickel based alloy |
CN102230141B (zh) * | 2010-04-28 | 2013-01-16 | 鞍钢集团矿业公司 | 链篦机篦板用耐热钢 |
US9790578B2 (en) * | 2013-05-17 | 2017-10-17 | Komatsu Ltd. | Steel for tracked undercarriage component, and track link |
CN103667939B (zh) * | 2013-11-07 | 2016-02-10 | 安徽省智汇电气技术有限公司 | 一种滚珠轴承用锰钢材料及其制备方法 |
JP6930759B2 (ja) * | 2017-03-14 | 2021-09-01 | 国立大学法人東北大学 | 鉄基耐熱合金 |
CN107254641B (zh) * | 2017-06-02 | 2019-03-19 | 江阴国润机械有限公司 | 耐高温氧化炉排片及其浇注模具和浇注工艺 |
GB201713066D0 (en) * | 2017-08-15 | 2017-09-27 | Paralloy Ltd | Oxidation resistant alloy |
US10481052B2 (en) | 2018-03-28 | 2019-11-19 | Ford Global Technologies, Llc | Quality control process to assess the aluminized coating characteristics of hot stamped parts |
WO2020067444A1 (ja) * | 2018-09-27 | 2020-04-02 | 日本製鉄株式会社 | オーステナイト系合金 |
CN113151747A (zh) * | 2021-04-27 | 2021-07-23 | 中国核动力研究设计院 | 一种耐高温腐蚀的含铝奥氏体不锈钢及制备方法 |
CN114318169B (zh) * | 2021-11-16 | 2022-11-25 | 上海交通大学 | 耐超临界水/超临界二氧化碳腐蚀的含铝奥氏体不锈钢 |
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JPS5421930A (en) * | 1977-07-20 | 1979-02-19 | Toyo Kogyo Co | Oxidationnand deformationnresistant material for use as parts in internal combustion engine exhaust system |
JPS5856026B2 (ja) * | 1979-01-20 | 1983-12-13 | 日立造船株式会社 | アルミニウム被覆ステンレス鋼の製造方法 |
US4535034A (en) * | 1983-12-30 | 1985-08-13 | Nippon Steel Corporation | High Al heat-resistant alloy steels having Al coating thereon |
US4752599A (en) * | 1986-03-31 | 1988-06-21 | Nippon Steel Corporation | Method for producing a base of a catalyst carrier for automobile exhaust gas-purification |
US4829655A (en) * | 1987-03-24 | 1989-05-16 | W. R. Grace & Co.-Conn. | Catalyst support and method for making same |
JP2593319B2 (ja) * | 1987-10-09 | 1997-03-26 | 株式会社アサヒ電子研究所 | ファイル等被検索物の個別検索装置 |
JPH03260034A (ja) * | 1990-03-09 | 1991-11-20 | Nippon Steel Corp | 自動車排ガス触媒担体用ステンレス鋼箔及びその製造方法 |
JPH0375353A (ja) * | 1989-08-15 | 1991-03-29 | Nippon Yakin Kogyo Co Ltd | Al含有ステンレス鋼箔の製造方法 |
JPH04147965A (ja) * | 1990-10-08 | 1992-05-21 | Kobe Steel Ltd | 蒸着a1めっき鋼材の製造方法 |
FI89463C (fi) * | 1991-01-03 | 1993-10-11 | Kemira Oy | Anvaendning av en nickelbaserad, aluminium innehaollande metallegering som substratmaterial foer en avgaser renande katalysator |
JP2943021B2 (ja) * | 1991-01-31 | 1999-08-30 | 日本冶金工業株式会社 | 表層にNiAl金属間化合物を有するオーステナイト鋼板帯の製造方法 |
US5578265A (en) * | 1992-09-08 | 1996-11-26 | Sandvik Ab | Ferritic stainless steel alloy for use as catalytic converter material |
JPH06271993A (ja) * | 1993-03-19 | 1994-09-27 | Sumitomo Metal Ind Ltd | 耐酸化性に優れたオーステナイト系ステンレス鋼 |
DE69516069T2 (de) * | 1994-09-30 | 2000-10-12 | General Electric Co., Schenectady | Verfahren zum Reinigen von Substraten und Herstellen von Schutzschichten |
DE19957646A1 (de) * | 1999-11-30 | 2001-05-31 | Krupp Vdm Gmbh | Verfahren zur Herstellung einer warmfesten Legierung mit guter Hochtemperaturoxidationsbeständigkeit |
US6585864B1 (en) * | 2000-06-08 | 2003-07-01 | Surface Engineered Products Corporation | Coating system for high temperature stainless steel |
US6730264B2 (en) * | 2002-05-13 | 2004-05-04 | Ati Properties, Inc. | Nickel-base alloy |
-
2003
- 2003-12-30 SE SE0303608A patent/SE527174C2/sv not_active IP Right Cessation
-
2004
- 2004-12-15 KR KR1020067013300A patent/KR20060111662A/ko not_active Application Discontinuation
- 2004-12-15 WO PCT/SE2004/002017 patent/WO2005064031A1/en active Application Filing
- 2004-12-15 EP EP04809190A patent/EP1702083A1/de not_active Withdrawn
- 2004-12-15 CN CNA2004800392746A patent/CN1902334A/zh active Pending
- 2004-12-15 US US10/584,903 patent/US20080038143A1/en not_active Abandoned
- 2004-12-15 JP JP2006546924A patent/JP2007518879A/ja active Pending
Non-Patent Citations (1)
Title |
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See references of WO2005064031A1 * |
Also Published As
Publication number | Publication date |
---|---|
SE0303608D0 (sv) | 2003-12-30 |
JP2007518879A (ja) | 2007-07-12 |
WO2005064031A1 (en) | 2005-07-14 |
CN1902334A (zh) | 2007-01-24 |
SE0303608L (sv) | 2005-07-01 |
US20080038143A1 (en) | 2008-02-14 |
KR20060111662A (ko) | 2006-10-27 |
SE527174C2 (sv) | 2006-01-17 |
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