Patent Grant
9476110
This application is the National Stage of PCT/DE2012/000153 filed on Feb. 17, 2012, which claims priority under 35 U.S.C. §119 of German Application Nos. 10 2011 012 210.9 filed on Feb. 23, 2011 and 10 2012 002 514.9 filed on Feb. 10, 2012, the disclosures of which are incorporated by reference. The international application under PCT article 21(2) was not published in English.
1. Field of the Invention
The invention relates to a nickel-chromium-iron-aluminum alloy having excellent high-temperature corrosion resistance, good creep resistance, and improved processability.
2. Description of the Related Art
Austenitic nickel-chromium-iron-aluminum alloys having different nickel, chromium, and aluminum contents have been used in furnace construction and in the chemical process industry for a long time. For this use, good high-temperature corrosion resistance and good heat resistance/creep resistance even at temperatures above 1000° C. is required.
In general, it should be noted that the high-temperature corrosion resistance of the alloys indicated in Table 1 increases with an increasing chromium content. All of these alloys form a chromium oxide layer (Cr2O3) with an Al2O3 layer that lies underneath and is more or less closed. Slight additions of strongly oxygen-affine elements such as Y or Ce, for example, improve the oxidation resistance. The chromium content is slowly consumed during the course of use in the region of application, to build up the protective layer. For this reason, the useful lifetime of the material is increased by means of a higher chromium content, because a higher content of chromium, as the element that forms the protective layer, delays the point in time at which the Cr content is below the critical limit and oxides other than Cr2O3 form, which are oxides that contain iron or that contain nickel, for example. A further increase in the high-temperature corrosion resistance can be achieved by means of addition of aluminum and silicon. Starting from a certain minimum content, these elements form a closed layer below the chromium oxide layer, and thereby reduce the consumption of chromium.
The heat resistance/creep resistance at the temperatures indicated is improved by means of a higher carbon content, among other things.
Examples of these alloys are listed in Table 1.
Alloys such as N06025, N06693 or N06603 are known for their excellent corrosion resistance in comparison with N06600, N06601 or N06690, because of the high aluminum content. Alloys such as N06025 or N06603 also demonstrate excellent heat resistance/creep resistance even at temperatures above 1000° C., because of the high carbon content. However, the processability, e.g. formability and weldability, are impaired by these high aluminum content values, whereby the impairment is all the greater, the higher the aluminum content (N06693). The same holds true to an increased degree for silicon, which forms intermetallic phases with nickel that melt at a low temperature. For N06025, for example, it was possible to achieve weldability by means of the use of a special welding gas (Ar with 2% nitrogen) (data sheet for Nicrofer 6025 HT, ThyssenKrupp VDM). The high carbon content in N06025 and N06603 results in a high content of primary carbides, which leads to crack formation, proceeding from the primary carbides, for example at high degrees of forming, as they occur during deep drawing, for example. Something similar happens during the production of seamless pipes. Here, too, the problem becomes worse with an increasing carbon content, particularly in the case of N06025.
EP 0 508 058 A1 discloses an austenitic nickel-chromium-iron alloy consisting of (in weight-%) C 0.12-0.3%, Cr 23-30%, Fe 8-11%, Al 1.8-2.4%, Y 0.01-0.15%, Ti 0.01-1.0%, Nb 0.01-1.0%, Zr 0.01-0.2%, Mg 0.001-0.015%, Ca 0.001-0.01%, N max. 0.03%, Si max. 0.5%, Mn max. 0.25%, P max. 0.02%, S max. 0.01%, Ni remainder, including unavoidable melting-related contaminants.
EP 0 549 286 discloses a high-temperature-resistant Ni—Cr alloy containing 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 that contains Mg, Ca, Ce, <0.5% in total Mg+Ca, <1% Ce, 0.0001-0.1% B, 0-0.5% Zr, 0.0001-0.2% N, 0-10% Co, remainder iron and contaminants.
From DE 600 04 737 T2, a heat-resistant nickel-based alloy has become known, containing ≦0.1% C, 0.01-2% Si, ≦2% Mn, ≦0.005% S, 10-25% Cr, 2.1-<4.5% Al, ≦0.055% N, in total 0.001-1% of at least one of the elements B, Zr, Hf, whereby the stated elements can be present in the following contents: B≦0.03%, Zr≦0.2%, Hf≦0.8%. Mo 0.01-15%, W 0.01-9%, whereby a total content Mo+W of 2.5-15% can exist, Ti 0-3%, Mg 0-0.01%, Ca 0-0.01%, Fe 0-10%, Nb 0-1%, V 0-1%, Y 0-0.1%, La 0-0.1%, Ce 0-0.01%, Nd 0-0.1%, Cu 0-5%, Co 0-5%, remainder nickel. For Mo and W, the following formula must be fulfilled:
2.5≦Mo+W≦15 (1)
The task on which the invention is based consists in designing an alloy, which, at sufficiently high nickel, chromium, and aluminum contents,
This task is accomplished by means of a nickel-chromium-aluminum-iron alloy having (in wt.-%) 12 to 28% chromium, 1.8 to 3.0% aluminum, 1.0 to 15% iron, 0.01 to 0.5% silicon, 0.005 to 0.5% manganese, 0.01 to 0.20% yttrium, 0.02 to 0.60% titanium, 0.01 to 0.2% zirconium, 0.0002 to 0.05% magnesium, 0.0001 to 0.05% calcium, 0.03 to 0.11% carbon, 0.003 to 0.05% nitrogen, 0.0005 to 0.008% boron, 0.0001-0.010% oxygen, 0.001 to 0.030% phosphorus, max. 0.010% sulfur, max. 0.5% molybdenum, max. 0.5% tungsten, remainder nickel and the usual process-related contaminants, wherein the following relationships must be fulfilled:
0<7.7C−x·a<1.0 (2)
with a=PN, if PN>0 (3a)
or a=0, if PN≦0 (3b)
and x=(1.0Ti+1.06Zr)/(0.251Ti+0.132Zr) (3c)
where PN=0.251Ti+0.132Zr−0.857N (4)
and Ti, Zr, N, C are the concentration of the related elements in mass-%.
Advantageous further developments of the object of the invention can be derived from the related dependent claims.
The spread range for the element chromium lies between 12 and 28%, whereby chromium contents can exist as follows as a function of the case of use, and are adjusted in the alloy as a function of the case of use.
Preferred ranges are reproduced as follows:
The aluminum content lies between 1.8 and 3.0%, whereby here, too, depending on the region of use of the alloy, aluminum contents can exist as follows:
The iron content lies between 1.0 and 15%, whereby, depending on the region of use, defined contents within the spread range can be adjusted:
The silicon content lies between 0.01 and 0.50%. Preferably, Si can be adjusted in the alloy within the spread region as follows:
The same holds true for the element manganese, which can be contained in the alloy at 0.005 to 0.5%. Alternatively, the following spread range is also possible:
The object of the invention preferably proceeds from the assumption that the material properties can essentially be adjusted with the addition of the element yttrium in contents of 0.01 to 0.20%. Preferably, Y can be adjusted in the alloy as follows, within the spread range:
Optionally, yttrium can also be replaced, completely or partially, by
Preferably, the substitute, in each instance, can be adjusted in the alloy as follows, within its spread range:
The titanium content lies between 0.02 and 0.60%. Preferably, Ti can be adjusted in the alloy as follows, within its spread range:
Optionally, titanium can be completely or partially replaced by
Preferably, the substitute can be adjusted in the alloy as follows, within the spread range:
Optionally, titanium can also be completely or partially replaced by
Preferably, the substitute can be adjusted in the alloy as follows, within the spread range:
The zirconium content lies between 0.01 and 0.20%. Preferably, Zr can be adjusted in the alloy as follows, within the spread range:
Optionally, zirconium can also be completely or partially replaced by
Magnesium is also contained in contents of 0.0002 to 0.05%. Preferably, the possibility exists of adjusting this element in the alloy as follows:
The alloy furthermore contains calcium in contents between 0.0001 and 0.05%, particularly 0.0005 to 0.02%.
The alloy contains 0.03 to 0.11% carbon. Preferably, this can be adjusted in the alloy as follows, within the spread range:
This applies in equal manner for the element nitrogen, which is contained in contents between 0.003 and 0.05%. Preferred contents can exist as follows:
The elements boron and oxygen are contained in the alloy as follows:
Preferred contents can exist as follows:
The alloy furthermore contains phosphorus in contents between 0.001 and 0.030%, and particularly contains 0.002 to 0.020%.
The element sulfur can exist in the alloy as follows:
Molybdenum and tungsten can be contained in the alloy, individually or in combination, with a content of maximally 0.50%, in each instance. Preferred contents can exist as follows:
If Zr is completely or partially substituted by Hf, the formulas 3c and 4 should be changed as follows:
x=(1.0Ti+1.06Zr+0.605Hf)/(0.251*Ti+0.132Zr+0.0672Hf) (3c-1)
where PN=0.251Ti+0.132Zr+0.0672Hf−0.857N (4-1)
Furthermore, the alloy can contain between 0.01 to 5.0% cobalt, which furthermore can also be restricted as follows:
Furthermore, maximally 0.1% vanadium can be contained in the alloy.
Finally, the elements copper, lead, zinc, and tin can also exist as contaminants, in contents as follows:
The content of copper can furthermore be restricted as follows:
The alloy according to the invention is preferably melted in open manner, followed by treatment in a VOD or VLF system. After being cast in blocks or as an extrusion, the alloy is hot-formed to the desired semi-finished product form, if necessary with intermediate annealing between 900° C. and 1270° C. for 2 h to 70 h. The surface of the material can be removed chemically and/or mechanically, if necessary (also multiple times) in between and/or at the end of cleaning. After the end of hot-forming, cold-forming can take place, if necessary, with forming degrees of up to 98%, to the desired semi-finished product form, if necessary with intermediate annealing between 800° C. and 1250° C. for 0.1 min to 70 h, if necessary under protective gas, such as argon or hydrogen, for example, followed by cooling in air, in the moved annealing atmosphere or in a water bath. Afterward, annealing in a temperature range of 800° C. to 1250° C. takes place for 0.1 min to 70 h, if necessary under protective gas, such as argon or hydrogen, for example, followed by cooling in air, in the moved annealing atmosphere, or in a water bath. If necessary, chemical and/or mechanical cleaning processes of the material surface can take place in between.
The alloy according to the invention can be produced and used well in the product forms of strip, sheet, rod, wire, pipe welded with a longitudinal seam, and seamless pipe.
The alloy according to the invention should preferably be used for use in furnace construction, for example as muffles for annealing furnaces, furnace rollers, or support frames.
A further area of application is use as a pipe in the petrochemical industry or in solar thermal power plants.
Likewise, the alloy can be used as a mantle in glow plugs, as a catalytic converter support foil, and as a component in exhaust gas systems.
The alloy according to the invention is well suited for the production of deep-drawn parts.
Tests Conducted:
Formability is determined in a tensile test according to DIN EN ISO 6892-1 at room temperature. In this connection, the elongation limit Rp0.2, the tensile strength Rm, and the elongation A to rupture are determined. The elongation A is determined on the ruptured sample, from the lengthening of the original measurement segment L0:
A=(LU−L0)/L0100%=ΔL/L0100%
With LU=measurement length after rupture.
Depending on the measurement length, the elongation to rupture is provided with indices:
For example, for A5 the measurement length is L0=5·d0 with d0=initial diameter of a round sample
The tests were conducted on round samples having a diameter of 6 mm in the measurement region and a measurement length L0 of 30 mm. Sample-taking took place transverse to the forming direction of the semi-finished product. The forming speed was 10 MPA/s at Rp0.2, and 6.7 10−3 1/s (40%/min) at Rm.
The value of the elongation A in the tensile test at room temperature can be taken to be a measure of deformability. A material that has good processability should have an elongation of at least 50%.
Here, weldability is assessed by way of the extent of the formation of hot cracks (see DVS bulletin 1004-1). The greater the risk of the formation of hot cracks, the poorer the weldability of the material. The hot-crack susceptibility was tested using the Modified Varestraint Transvarestraint Test (MVT test), at the Federal Institute for Material Research and Testing (see DVS bulletin 1004-2). In an MVT test, a WIG seam is laid on the surface of a material sample having the dimensions 100 mm×40 mm×10 mm, lengthwise, in fully mechanized manner, at a constant advancing speed. When the arc passes the center of the sample, a defined bending elongation is applied to the sample, in that the sample is bent about a matrix having a known radius, by means of dies. In this phase of bending, hot cracks form on the MVT sample, in a locally limited test zone. For the measurements, the samples were bent lengthwise relative to the welding direction (Varestraint). Experiments were conducted with 1% and 4% bending elongation, a total speed of 2 mm/s, with a stretching energy of 7.5 kJ/cm, under argon 5.4 and argon with 3% nitrogen, in each instance. The hot-crack resistance is quantified as follows: The lengths of all the solidification and remelting cracks that are visible on the sample under a light microscope at 25× magnification are added up. In the same manner, the cracks are determined by means of a decrease in formability (DDC=Ductility Dip Cracks). Using these results, the material can then be classified in the categories “not at risk for hot cracks,” “increasing tendency toward hot cracks,” and “at risk for hot cracks.”
All the materials that lie in the range of “not at risk for hot cracks” and “increasing tendency toward hot cracks” in the MVT test are considered to be weldable in the following investigations.
Corrosion resistance at higher temperatures was determined in an oxidation test at 1100° C., in air, whereby the test was interrupted every 96 hours and the measurement changes of the sample resulting from oxidation were determined (net mass change mN). The specific (net) mass change is the mass change with reference to the surface of the samples. Three samples of each batch were aged.
Heat resistance is determined in a hot tensile test according to DIN EN ISO 6892-2. In this connection, the elongation limit Rp0.2, the tensile strength Rm, and the elongation A to rupture are determined analogous to the tensile test, at room temperature (DIN EN ISO 6892-1).
The tests were conducted using round samples having a diameter of 6 mm in the measurement region, and an initial measurement length L0 of 30 mm. Sample-taking took place transverse to the forming direction of the semi-finished product. The forming speed was 8.33 10−5 1/s (0.5%/min) at Rp0.2 and 8.33 10−4 1/s (5%/min) at Rm.
The sample is placed into a tensile testing machine at room temperature, and heated to the desired temperature without stress by a tensile force. After the test temperature has been reached, the sample is held without stress for one hour (600° C.) or two hours (700° C. to 1100° C.), respectively, for temperature equalization. Afterward, a tensile stress is placed on the sample so that the desired elongation speeds are maintained, and the test begins.
Creep resistance is determined by way of a slow tensile test (SSRT=Slow Strain Rate Test). For this purpose, a hot tensile test according to DIN EN ISO 6892-2 is conducted at very low forming speeds of 1.0×10−6 1/s. This elongation speed already lies in the range of creep speeds, so that a ranking of materials with reference to creep resistance can be carried out using a comparison of elongation limit and, in particular, tensile strength determined with the slow tensile test.
The elongation limit Rp0.2, the tensile strength Rm, and the elongation A to rupture are determined analogous to the method described for the tensile test at room temperature (DIN EN ISO 6892-1). To reduce the testing times, the tests were stopped after approximately 30% elongation, if Rm has been reached, otherwise after the elongation A for Rm was exceeded. The tests were conducted using round samples having a diameter of approximately 8 mm in the measurement region and a measurement length L0 of 40 mm. Sample-taking took place transverse to the forming direction of the semi-finished product.
The sample is placed into a tensile testing machine at room temperature, and heated to the desired temperature without stress by a tensile force. After the test temperature has been reached, the sample is held without stress for two hours (700° C. to 1100° C.), for temperature equalization. Afterward, a tensile stress is placed on the sample so that the desired elongation speeds are maintained, and the test begins.
Examples:
Tables 2a and 2b show the composition of the alloys investigated.
The alloys N06025 and N06601 are alloys according to the state of the art. The alloy according to the invention is indicated with “E.” The analyses of the alloys N06025 and N06601 lie in the ranges indicated in Table 1. The alloy “E” according to the invention has a C content that lies in the center between N06025 and N06601. In Table 2a, PN and 7.7 C−x·a according to Formulas 2 and 4 are furthermore indicated. PN is greater than zero for all the alloys in Table 2a. 7.7 C−x·a, at 0.424, lies precisely in the preferred range 0<7.7 C−x·a<1.0 for the alloy according to the invention.
For the alloy according to the state of the art, N06025, 7.7 C−x·a is greater than 1.0 and therefore too great.
For the alloy according to the state of the art, N06601, 7.7 C−x·a is less than zero and therefore too small.
For these example batches, the following properties are compared:
Table 3 shows the results of the tensile test at room temperature. The alloy “E” according to the invention shows an elongation, at an elongation of over 80%, which is far greater than that of N06025 and N06601. This is not surprising for N06025, due to the high carbon content of 0.17% of the two example batches 163968 and 160483. Both batches show their poorer formability by an elongation less than 50%. For N06601, this is noteworthy, however, because the batches 314975 and 156656 have a carbon content of 0.045 and 0.053%, respectively, which is clearly lower then that of the alloy according to the invention, at 0.075%, and also, as expected, have an elongation greater than 50%. This shows that when the range for limits for 0<7.7 C−x·a<1.0 is adhered to, formability that goes beyond the state of the art is obtained.
Table 4 shows the results of the MVT tests. N06601 can be welded with both gases, argon and argon with 3% nitrogen, because all the measured total crack lengths for 1% bending elongation are less than 7.5 mm, and all the measured total crack lengths for 4% bending elongation are less than 30 mm. For N06025 and the alloy “E” according to the invention, the measured total crack lengths are greater than 7.5 mm (1% bending elongation) and 30 mm (4% bending elongation), respectively, so that these alloys cannot be welded with argon. For argon with 3% nitrogen, however, the measured total crack lengths clearly lie below 7.5 mm (1% bending elongation) and 30 mm (4% bending elongation), respectively, so that N06025 and the alloy “E” according to the invention can be welded with argon with 3% nitrogen.
Table 5 shows the results of the hot tensile tests at 600° C., 700° C., 800° C., 900° C., and 1100° C. The highest values both at Rp0.2 and at Rm are shown by N06025, as expected, and the lowest by N06601. The values of the alloy “E” according to the invention lie in between, whereby at 800° C., the values of the alloy “E” according to the invention are greater than those of N06025 both at Rp0.2 and at Rm. The elongation values in the hot tensile tests are sufficiently great for all the alloys. At 1100° C., no differences can be found any longer between the alloy “E” according to the invention and N06601, due to the measurement accuracy.
Table 6 shows the results of the slow tensile tests at 700° C., 800° C., and 1100° C. The highest values both at Rp0.2 and at Rm are shown, as expected, by N06025, and the lowest by N06601. The value of the alloy “E” according to the invention lie in between for Rp0.2; for Rm at 700° C. and 800° C., they are better or almost as good as N06025. The elongations in the slow tensile tests are sufficiently great for all the alloys. At 1100° C., no differences can be found any longer between the alloy “E” according to the invention and N06601, due to the measurement accuracy.
At 700° C. and 800° C., Rm from the slow tensile tests of N06025 and the alloy “E” according to the invention is comparable, i.e. it can be expected that at these temperatures, the creep resistance of N06025 and that of the alloy “E” according to the invention is comparable. This shows that for alloys in the preferred range 0<7.7 C−x·a<1.0 Rm, the creep resistance is comparable to that of Nicrofer 6025 HT, with simultaneously goad processability of the alloy “E” according to the invention in comparison with N06025.
The claimed limits for the alloy “E” according to the invention can therefore be explained as follows, in detail:
The costs for the alloy increase with a reduction in the iron content. Below 1%, the costs increase disproportionately, since a special pre-material has to be used. Therefore 1% Fe must be viewed as a lower limit for cost reasons.
With an increase in the iron content, the phase stability (formation of phases causing brittleness) is reduced, particularly at high chromium and aluminum contents. Therefore 15% Fe is a practical upper limit for the alloy according to the invention.
Overly low Cr contents means that the Cr concentration very quickly drops below the critical limit. Therefore 12% Cr is the lower limit for chromium. Overly high Cr contents worsen the processability of the alloy. Therefore 28% Cr must be viewed as an upper limit.
The formation of an aluminum oxide layer underneath the chromium oxide layer reduces the oxidation rate. Below 1.8% Al, the aluminum oxide layer contains too many gaps to fully develop its effect. Overly high Al contents impair the processability of the alloy. Therefore an Al content of 3.0% forms the upper limit.
Si is needed in the production of the alloy. Therefore a minimum content of 0.01% is required. Overly high contents in turn impair processability. The Si content is therefore limited to 0.5%.
A minimum content of 0.005% Mn is necessary to improve processability. Manganese is limited to 0.5%, because this element also reduces oxidation resistance.
As has already been mentioned, additions of oxygen-affine elements improve oxidation resistance. They do this in that they are installed into the oxide layer, and block 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-increasing effect of Y. The upper limit is placed at 0.20% for cost reasons.
Y can be completely or partially replaced by Ce and/or La, because these elements also, like Y, increase oxidation resistance. Replacement is possible starting with contents of 0.001%. The upper limit is placed at 0.20% Ce or 0.20% La for cost reasons.
Titanium increases the high-temperature resistance. At least 0.02% is needed to achieve an effect. From 0.6%, the oxidation behavior is worsened.
Titanium can be completely or partially replaced by niobium, because niobium also increases the high-temperature resistance. Replacement is possible from 0.001%. Higher contents greatly increase the costs. The upper limit is therefore set at 0.6%.
Titanium can also be completely or partially replaced with tantalum, because tantalum also increases the high-temperature resistance. Replacement is possible from 0.001%. Higher contents very greatly increase the costs. The upper limit is therefore set at 0.6%.
A minimum content of 0.01% Zr is necessary to obtain the effect of Zr that increases high-temperature resistance and oxidation resistance. The upper limit is placed at 0.20% Zr for cost reasons.
Zr can be completely or partially replaced by Hf, if necessary, because this element also, like Zr, increases the high-temperature resistance and the oxidation resistance. Replacement is possible from contents of 0.001%. The upper limit is set at 0.20% Hf for cost reasons.
Even very low Mg contents improve processing, by means of binding of sulfur, thereby avoiding the occurrence of NiS eutectics with a low melting point. Therefore a minimum content of 0.0002% is required for Mg. At overly high contents, intermetallic Ni—Mg phases can occur, which again clearly worsen processability. The Mg content is therefore limited to 0.05%.
Just like Mg, even very low Ca contents already improve processing by means of binding of sulfur, thereby avoiding the occurrence of NiS eutectics having a low melting point. For Ca, a minimum content of 0.0001% is therefore required. At overly high contents, intermetallic Ni—Ca phases can occur, which again clearly worsen processability. The Ca content is therefore limited to 0.05%.
A minimum content of 0.03% C is required for good creep resistance. C is limited to 0.11%, because this element reduces processability.
A minimum content of 0.003% N is required, thereby improving the processability of the material. N is limited to 0.05%, because this element reduces oxidation resistance.
Boron improves creep resistance. Therefore a content of at least 0.0005% should be present. At the same time, this surfactant element worsens oxidation resistance. Therefore max. 0.008% boron is established.
The oxygen content must be less than 0.010% to guarantee producibility of the alloy. Overly small oxygen contents cause increased costs. The oxygen content should therefore be greater than 0.0001%.
The content of phosphorus should be less than 0.030%, because this surfactant element impairs oxidation resistance. An overly low P content increases costs. The P content is therefore ≧0.001%.
The contents of sulfur should be set as low as possible, because this surfactant element impairs oxidation resistance. Therefore max. 0.010% S is established.
Molybdenum is limited to max. 0.5%, because this element reduces oxidation resistance.
Tungsten is limited to max. 0.5%, because this element also reduces oxidation resistance.
The following formula describes the interaction of C, N, Ti, Zr, and in the alloy:
0<7.7C−x·a<1.0 (2)
with a=PN, if PN>0 (3a)
or a=0, if PN≦0 (3b)
and x=(1.0Ti+1.06Zr)/(0.251Ti+0.132Zr) (3c)
PN=0.251Ti+0.132Zr−0.857N (4)
and Ti, Zr, N, C are the concentration of the related elements in mass-%.
If 7.7 C−x·a is greater than 1.0, so many primary carbides are formed, which impair formability. If 7.7 C−x·a is less than 0, heat resistance and creep resistance worsen.
Cobalt can be contained in this alloy up to 5.0%. Higher contents markedly reduce the oxidation resistance. An overly low cobalt content increases costs. The Co content is therefore ≧0.01%.
Vanadium is limited to max. 0.1%, because this element reduces oxygen resistance.
Copper is limited to max. 0.5%, because this element reduces oxygen resistance.
Pb is limited to max. 0.002%, because this element reduces oxygen resistance. The same holds true for Zn and Sn.
| Number | Date | Country | Kind |
|---|---|---|---|
| 10 2011 012 210 | Feb 2011 | DE | national |
| 10 2012 002 514 | Feb 2012 | DE | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/DE2012/000153 | 2/17/2012 | WO | 00 | 8/14/2013 |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2012/113373 | 8/30/2012 | WO | A |
| Number | Name | Date | Kind |
|---|---|---|---|
| 4784830 | Ganesan et al. | Nov 1988 | A |
| 5755897 | Brill | May 1998 | A |
| 5980821 | Brill | Nov 1999 | A |
| 6458318 | Nishiyama et al. | Oct 2002 | B1 |
| 6761854 | Smith et al. | Jul 2004 | B1 |
| 6852177 | Kubota et al. | Feb 2005 | B2 |
| 20100166594 | Hirata et al. | Jul 2010 | A1 |
| Number | Date | Country |
|---|---|---|
| 1 304 608 | Jul 1992 | CA |
| 1147560 | Apr 1997 | CN |
| 600 04 737 | Jun 2004 | DE |
| 0 508 058 | Oct 1992 | EP |
| 0 549 286 | Jun 1993 | EP |
| 0 549 286 | Jun 1993 | EP |
| 0 752 481 | Jan 1997 | EP |
| 63-026321 | Feb 1988 | JP |
| 63-312940 | Dec 1988 | JP |
| 07-050168 | Feb 1995 | JP |
| 07-114928 | May 1995 | JP |
| 2001-040443 | Feb 2001 | JP |
| 2002-180169 | Jun 2002 | JP |
| 2002-524658 | Aug 2002 | JP |
| 2003-247039 | Sep 2003 | JP |
| 2001-0007520 | Jan 2001 | KR |
| Entry |
|---|
| ThyssenKrupp VDM, Nicrofer 6025 HT—alloy 602 CA, Material Data Sheet No. 4037, Mar. 2007 Edition. |
| International Search Report of PCT/DE2012/000153, date of mailing Aug. 17, 2012. |
| Din En ISO 6892-1, Metallic materials—Tensile testing—Part 1: Method of test at room temperature, First edition Aug. 15, 2009, 72 pages. |
| Din En ISO 6892-2, Metallic materials—Tensile testing—Part 2: method of test at elevated temperature, May 2011, pp. 1-24. |
| DVS Bulletin 1004-1, Heiβriβprüfverfahren Grundlagen, Nov. 1996, pp. 1-4. |
| DVS Bulletin 1004-2, Heiβriβprüfverfahren mit fremdbeanspruchten Proben, Nov. 1996, pp. 1-8. |
| Number | Date | Country | |
|---|---|---|---|
| 20130323113 A1 | Dec 2013 | US |
