WO2004087980A1 - Acier inoxydable pour applications a hautes temperatures - Google Patents

Acier inoxydable pour applications a hautes temperatures Download PDF

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Publication number
WO2004087980A1
WO2004087980A1 PCT/SE2004/000344 SE2004000344W WO2004087980A1 WO 2004087980 A1 WO2004087980 A1 WO 2004087980A1 SE 2004000344 W SE2004000344 W SE 2004000344W WO 2004087980 A1 WO2004087980 A1 WO 2004087980A1
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Prior art keywords
alloy
high temperature
alloys
temperature applications
content
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PCT/SE2004/000344
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English (en)
Inventor
Kenneth GÖRANSSON
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Sandvik Intellectual Property Ab
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Publication of WO2004087980A1 publication Critical patent/WO2004087980A1/fr

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    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • 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
    • C22C38/04—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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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 of producing a stainless steel alloy with improved oxidation resistance in high temperature applications by depositing an Al-base alloy on a substrate material, the use of said alloy and said alloy.
  • Ferritic Fe-Cr-AI alloys are used in many applications where resistance to oxidation and corrosive gases, salts and/or melts is necessary.
  • the biggest advantage of such an alloy lies in the ability to form a thin, adherent aluminium oxide film/scale on the surface after heat-treating.
  • the aluminium oxide film is necessary to protect the metal from rapid oxidation or corrosion.
  • protective films of aluminium oxide are superior to those films that can be formed by oxides of for example chromium or nickel.
  • Fe-Cr-AI alloys do not form single-phase aluminium oxide films, but they nonetheless usually have superior oxidation resistance to that of other types of alloys.
  • Thin foils of ferritic Fe-Cr-AI alloys are today used as carrier materials for catalytic converters in the purification of exhaust gases from internal combustion engines. Cyclic thermal stress is the usual working condition in this application. In order to form a protective oxide film/scale on the surface a minimum content of aluminium in the alloy is assumed to be necessary. The protective properties of this aluminium oxide are known to be improved, especially with respect to cyclic thermal stress, if the alloy contains small amounts of one or more or the so called reactive elements (RE), such as Mg, Ca, Zr, Hf or rare earth elements (REM), such as for example one of the lanthanide elements or Sc, Y.
  • the alloy can be produced by conventional methods, which comprise e.g.
  • the alloy can also be produced by using a pre-rolled strip with a lower aluminium content than the desired final content of aluminium of a catalytic converter carrier material and subsequently depositing a layer of an aluminium rich alloy on the surface of this material.
  • the deposition can be made in different ways, e.g. by dipping the strip in a molten Al alloy, by roll bonding (cladding) an Al alloy onto a ferritic steel, by coating by means of PVD-technology (Physical Vapour Deposition) or CVD-technology (Chemical Vapour Deposition).
  • the thickness of the strip together with the deposit may be the final shape and thickness, or the strip may be rolled down to a smaller thickness after the deposition has been performed.
  • the composite material comprising the ferritic alloy and aluminium alloy on one or both surfaces may be heat-treated to provide a homogeneous alloy, or an alloy with an increasing aluminium concentration towards the surface.
  • the mechanical properties of ferritic Fe-Cr-AI alloys, especially with increased content of Al, are known to be poor at high temperature.
  • Several ways of improving these properties are known, such as the production of fine dispersions of oxide or nitride phases by powder metallurgical processes. These processes involve expensive operations during production and are hence not suitable for the manufacturing of alloys that are to be produced in large quantities at low costs.
  • Another object of the present invention is to provide a production route for the alloy according to the invention by the deposition of an Al alloy onto a thin foil of a substrate alloy
  • Figure 1 shows the elongation to fracture for alloys according to the present invention compared with one comparative example plotted vs. temperature.
  • Figure 2 shows the Young ' s modulus plotted vs. temperature for the same samples as in Figure 1.
  • Figure 3a shows the tensile strength plotted vs. temperature for the same samples as in the preceding figures.
  • Figure 3b shows the tensile strength relative to that of the comparative example at the same temperature plotted vs. temperature for the same samples as in the preceding figures.
  • Figure 4a shows the yield strength plotted vs. temperature for the same samples as in the preceding figures.
  • Figure 4b shows the yield strength relative to that of the comparative example at the same temperature plotted vs. temperature for the same samples as in the preceding figures.
  • Figure 5 shows the result of the oxidation test of alloys of the present invention and a comparative example by plotting the mass change after oxidation at 1100°C of the samples plotted vs. time.
  • Figure 6 shows the result of the oxidation test of alloys of the present invention and a comparative example by plotting the mass change after oxidation at 1200°C of the samples plotted vs. time.
  • Figure 7 shows a section through the Fe-Ni-Cr-AI Thermo-calc phase diagram at 20 weight-% Cr and 5 weight-% Al.
  • Figure 8 shows the result of the oxidation test of alloys of the present invention and a comparative example by plotting the change in mass after oxidation at 1100°C of the samples plotted vs. time.
  • the contents of elements in the alloy produced by the method of depositing an Al-base alloy on a substrate of stainless steel should have the following limitations: the content of Cr should be limited to 15,0 to 25,0 wt-%, preferably to 20,0 to 22,0 wt-%.
  • the content of Ni should be limited to between 1 ,0 and 20,0 wt-%, preferably to 2,5 to 15,0 wt-%, most preferably to 5,0 to 12,5 wt-%.
  • the content of aluminium should be limited to 4,5 to 12,0 wt-%, preferably to 5,0 to 8,0 wt-%, most preferably to 5,0 to 7,0 wt-%.
  • the total content of the elements Mo and W should be limited up to 4,0 wt-%, preferably up to 3,0 wt-%. Another preferred content of the total of Mo and W is more than 1 wt-%.
  • the content of Mn should be limited up to 2,0 wt-%, preferably up to 0,5 wt-%.
  • the content of N will be limited up to 0,05 wt-% and should be held as low as possible.
  • the content of C should be limited up to 0,20 wt-%, preferably up to 0,15 wt-%.
  • This alloy can be produced by conventional methods such as melting, casting and hot rolling in dimensions down to approximately 1 mm.
  • the substrate alloy according to the invention can be in the form of for example a thin foil or strip, a wire or a plate.
  • the deposition of an Al alloy onto the substrate can be performed onto a substrate alloy which has suitable dimensions for the final product or, if necessary, be followed by further cold working and/or diffusion anneal.
  • the composition of the substrate alloy before deposition is as follows (all contents in weight-%):
  • the content of Cr in the substrate alloy should be limited to 16,0 to 27,0 wt-%, preferably to 20,0 to 24,0 wt-%.
  • the content of Ni should be limited to between 1 ,2 and 22,0 wt-%, preferably to 2,5 to 15,0 wt-%, most preferably to 5,0 to 14,0 wt-%.
  • the content of aluminium in the substrate alloy should be limited to 0 to 6 wt- %, preferably to 0,0 to 2 wt-%, most preferably to >0 to 1 ,0 wt-%.
  • the total content of the elements Mo and W should be limited up to 4,0 wt-%, preferably up to 3,0 wt-%.
  • the content of Mn should be limited up to 2,0 wt-%, preferably up to 0,5 wt-%.
  • the content of N in the substrate alloy will be limited up to 0,10 wt-%, preferably up to 0,05 wt-%.
  • the content of C should be limited up to 0,20 wt-%, preferably up to 0,15 wt-%.
  • Carbon forms carbides together with e.g. Nb or Cr. These carbides contribute to increasing the high temperature mechanical strength of the alloy and also reduce the tendency for grain growth during operation, a phenomenon known to cause embrittlement in ferritic alloys. Carbon, however can cause embrittlement during cold rolling of the alloy and is also likely to cause a deterioration of the oxidation resistance. Therefore, the carbon content is limited to maximum 0,2 wt-%.
  • Chromium Chromium can form an oxide, which protects the alloy from further oxidation.
  • at least 15,0 wt-% Cr is necessary to effectively form a protective oxide scale.
  • Cr further facilitates the formation of an aluminium oxide scale in alloys containing 4,5 wt-% Al or more, which is necessary if the alloys are to be used at temperatures higher than 1000°C.
  • An excessive amount of chromium in the alloy can cause embrittlement of the alloy during production, and the maximum chromium content of the substrate alloy is therefore limited to 27,0 wt-%.
  • Nickel Nickel is included in the alloy to form strengthening NiAI particles, the formation of which is considered to be the main strengthening effect in this alloy. Aluminium
  • Aluminium if it is present in concentrations of 4,5 wt-% or more, forms a protective aluminum oxide scale on the surface of the alloy when it is exposed to high temperature. This oxide protects the alloy from further oxidation. Therefore the minimum Al content of the final alloy is 4,5 wt-%.
  • a low Al content in the substrate alloy is desirable in order to avoid the formation of embrittling phases during manufacturing.
  • the presence of small amounts of Al in the substrate alloy reduces the necessary amount of Al that must be deposited onto the substrate in order to produce a final alloy containing at least 4,5 wt-% Al.
  • Molybdenum and tungsten act as a solid solution strengthening elements, giving the alloy a higher mechanical strength at high temperatures. As such, the two elements can replace each other entirely. If the total content of molybden and tungsten is more than 4,0 wt-%, the oxidation properties are greatly deteriorated.
  • Niobium Niobium is known to increase the stability of the NiAI phase and therefore can be useful in providing an increase in the dissolution temperature of NiAI.
  • Nb can increase the high temperature strength of the alloy according to the invention.
  • Nb also forms Nb(N,C), which provides additional creep strength and resistance to grain growth.
  • the effect of these elements is to reduce the oxidation rate of the alloy and to increase the resistance of the aluminium oxide to cracking and exfoliation during heating and cooling.
  • These elements can be added either in the substrate alloy or in the deposited Al alloy or in both, in order to optimise the oxidation resistance.
  • Nitrogen Nitrogen forms embrittling AIN with aluminium and should therefore be present in as small amounts as possible in an alloy produced by conventional methods. However, in an alloy produced by the deposition of Al onto a substrate alloy with a low Al content, the nitrogen level can be allowed to be as high as 0,1 wt-%. If present, N is known to increase the mechanical strength of alloys, both by solid solution strengthening and by the precipitation of nitrides or carbonitrides such as Cr 2 N or Nb(N,C).
  • the alloys were produced by induction melting.
  • the cast ingots were rolled to billets, which subsequently were hot-rolled down to a thickness of 3 mm.
  • Oxidation properties of the alloys were evaluated at 1100°C and 1200X in normal atmosphere. The samples were removed from the furnace at pre-set intervals and weighed in order to monitor the weight gain.
  • the large-scale microstructure of the alloys is identical to that of the comparative example.
  • SEM and TEM analyses show that alloys of these compositions contain nickel aluminide particles of a size of between 5 nm and 2 ⁇ m with the CsCI-type structure. The particles form evenly spaced within the ferrite grains.
  • the hardness of the material after hot rolling is high: in the range 400-520 HV1. By annealing, the hardness could be brought down from 490 to 320 HV1. Due to the high hardness of the material, cold rolling was deemed to be infeasible.
  • Figures 1 to 4 show the measured high temperature mechanical properties of the alloys A to D and the comparative example alloy.
  • the Young ' s moduli of the experimental alloys are generally higher than that of the comparative example.
  • One interesting effect is the measured increase of Young ' s modulus in the two 5,0 % Ni-alloys above 900°C.
  • the alloys according to the present invention have significantly greater mechanical strength than the comparative example. However at higher temperatures the difference between the alloys is within the experimental uncertainty of the equipment used, with two exceptions.
  • the strength of Alloy B and, in particular, Alloy D is significantly higher at 900°C and 1000°C than that of the other alloys.
  • the experimental alloys show consistently less elongation at fracture than the comparative example as shown in Fig. 1.
  • the high hardness of the material is partially due to the presence of Ni aluminides.
  • a calculated phase diagram section for the system Fe-Ni-20Cr-5AI is shown in Fig. 7. The phase diagram was calculated with Thermo-calc. It shows that NiAI is likely to be stable even at very low Ni contents in the alloy.
  • the dissolution temperature of NiAI is approximately 900 °C for a 5,0 wt- % Ni- alloy and 1050 °G for a 12,5 wt-% Ni-alloy. No austenite is expected to form below a total Ni content of 14,0 wt-%.
  • the lattice parameter mismatch between NiAI and ferrite in equilibrium is expected to be small, and precipitation of NiAI appears to occur coherently.
  • the presence of NiAI in the Alloy B in the hot tensile tests above 900°C explains the improved yield strength.
  • the unexpected temperature dependence of the Young ' s moduli between 900 and 1000 °C for two of the alloys can not be explained at the time being, however it may be connected with the dissolution of NiAI.
  • the actual numbers for the Young ' s moduli are however still much higher for the alloy according to the invention for the comparative example. It must be noted that measurement of the Young's modulus is less accurate at high temperatures than at room temperature.
  • the yield strength is improved for all compositions according to the invention below 800°C compared to the comparative example. At higher temperatures, the effect is less clear.
  • the strengthening effect of Mo appears to be small above 600°C with respect to the yield strength.
  • the improvement of the yield strength compared with the comparative example is highest at 600°C for alloy A.
  • this alloy is preferred in catalytic converters working at comparatively low temperatures.
  • the improvement of the yield strength is greatest for alloy D.
  • a Ni content of 7,0 wt-% is preferred.
  • high temperature fatigue tests as well as creep tests will probably be necessary.
  • the initial tests which have been performed and which are described in the present application indicate that these alloys are promising candidate materials for catalytic converter bodies in mechanically challenging applications, where a combination of high mechanical strength, high temperature properties and oxidation resistance is required.
  • the oxidation properties of the experimental alloys are unexpectedly good, in several cases superior to that of the comparative example, especially referring to the high content of Ni, which was assumed to have a negative effect on the oxidation properties and resistance. In other cases, spalling is found, although the rate of spallation is not too serious for possible use of the material in other applications than catalytic converters.
  • By adding in amounts of 2,5-15 wt-% and Mo+W ⁇ 4,0 wt-% it is possible to improve the h igh temperature strength compared to FeCrAI catalytic converter steel, without s ignificantly deteriorating the oxidation resistance.
  • the alloy may also be useful in other high temperature applications such as heating applications, e.g. in heat treating furnaces.
  • Example 2 shows the preferred composition with respect to mechanical properties and corrosion resistance, it does not show the preferred production route for an alloy that is to be used in the form of thin strips, e.g. in thickness below 150 ⁇ m in a catalytic converter.
  • Example 2 shows the preferred composition with respect to mechanical properties and corrosion resistance, it does not show the preferred production route for an alloy that is to be used in the form of thin strips, e.g. in thickness below 150 ⁇ m in a catalytic converter.
  • a preferred manufacturing method for the alloy is by coating an alloy with a low content of Al with pure Al and/or an aluminium-base alloy in one or more of the final steps in the production.
  • the coating may be applied by e.g. dipping, cladding or a CVD- or PVD-process.
  • the present example will show the usefulness of such a production route and further indicate a preferred composition of the substrate alloy.
  • the Al content of the substrate alloy should be below 2,0 wt-%, preferably below 1 ,0 wt-% in order not to produce embrittling NiAI precipitates during production.
  • Strips of alloys according to table 2 were produced by induction melting. The cast ingots were forged to billets, which were subsequently hot-rolled down to a thickness of 3 mm. The hot-rolled strips were then cold-rolled down to a smallest thickness of 50 ⁇ m, with intermediate annealing.
  • the mechanical property data collected in table 2 show that the substrate alloy according to the invention produced in this way can be annealed to give a soft, workable alloy, which can be cold worked down to a suitable thickness.
  • Example 3 A thin film of Al was deposited on strip samples of three of the alloys in example 2 in an evaporation process, to produce samples with a total Al content of 6,0 w-%, as shown in table 3. Parts of the strips were annealed in hydrogen gas for 10 minutes at 1100°C. Oxidation tests and hot tensile tests were performed on the annealed samples. The oxidation results for alloy 2C in the annealed condition are shown in figure 8 together with those of alloys A and D and the comparative example. Up to 220h, the oxidation resistance of alloy 2C, which does not contain any intentional additions of REM, was superior to that of all the other alloys, including alloy A, which has a similar nominal composition. This effect can not be explained at present. It can be expected that alloy 2C, if additionally alloyed with REM, would show even better oxidation resistance. Table 3. Properties of alloys according to the invention in the deposited condition
  • the alloys of the present invention are basically ferritic Fe-Ni-Cr-AI alloys strengthened by the presence of minute particles of nickel aluminides and if necessary further strengthened by the presence of substitutionally dissolved elements such as Mo or W. Owing to a high Al content and the presence of reactive elements, the resistance to oxidation at high temperatures is good.
  • this is a suitable alloy for use as a carrier material in metallic catalytic converters, especially such that are exposed to a combination of high temperature, cyclic thermal stress and mechanical load.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Catalysts (AREA)

Abstract

L'invention concerne un procédé pour produire un alliage contenant les éléments suivants (en % en poids): C = 0,20, Cr 15,0-25,0, Ni 1,0-20,0, Al 4,5-12,0, Mo+W = 4,0, Nb = 2,0, Mn = 2,0, Si = 2,0, Zr + Hf = 0,2, REM = 0,1, N = 0,05. Cet alliage présente une meilleure résistance à l'oxydation dans des applications à températures élevées grâce au dépôt d'un alliage à base d'AI sur un substrat composé des éléments suivants (en % en poids): C = 0,20, Cr 16,0-27,0, Ni 1,2-22,0, Al 0-6,0, Mo + W = 4,5, Nb = 2,2, Mn = 2,0, Si = 2,0, Zr + Hf = 0,2, REM = 0,1, N = 0,1, le reste étant du Fe et des impuretés résultant normalement de la production de l'acier ainsi que des produits additionnels. La présente invention porte également sur cette alliage et sur son utilisation.
PCT/SE2004/000344 2003-04-02 2004-03-09 Acier inoxydable pour applications a hautes temperatures WO2004087980A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
SE0300993-3 2003-04-02
SE0300993A SE527176C2 (sv) 2003-04-02 2003-04-02 Rostfritt stål för användning i högtemperaturapplikationer

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WO2004087980A1 true WO2004087980A1 (fr) 2004-10-14

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108779538A (zh) * 2016-10-21 2018-11-09 韩国科学技术院 高强度Fe-Cr-Ni-Al多相不锈钢及其制造方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4859649A (en) * 1987-02-27 1989-08-22 Thyssen Edelstahlwerke Ag Semi-finished products of ferritic steel and catalytic substrate containing same
EP0646657A1 (fr) * 1993-03-19 1995-04-05 Nippon Yakin Kogyo Co., Ltd. Acier ferritique inoxydable presentant une excellente resistance a l'oxydation
EP0667400A1 (fr) * 1994-02-09 1995-08-16 Allegheny Ludlum Corporation Alliage de fer-chrome-aluminium pratiquement exempt de molybdène résistant au fluage
US5866065A (en) * 1995-03-29 1999-02-02 Usinor Sacilor Ferritic stainless steel of use in particular for catalyst supports
US6197132B1 (en) * 1996-08-30 2001-03-06 Sandvik Ab Method of manufacturing ferritic stainless FeCrA1-steel strips
SE520617C2 (sv) * 2001-10-02 2003-07-29 Sandvik Ab Ferritiskt rostfritt stål, folie tillverkad av stålet, användning av stålet och folien, samt metod för att framställa stålet

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4859649A (en) * 1987-02-27 1989-08-22 Thyssen Edelstahlwerke Ag Semi-finished products of ferritic steel and catalytic substrate containing same
EP0646657A1 (fr) * 1993-03-19 1995-04-05 Nippon Yakin Kogyo Co., Ltd. Acier ferritique inoxydable presentant une excellente resistance a l'oxydation
US5480608A (en) * 1993-03-19 1996-01-02 Nippon Yakin Kogyo Co., Ltd. Ferritic stainless steel having an excellent oxidation resistance
EP0667400A1 (fr) * 1994-02-09 1995-08-16 Allegheny Ludlum Corporation Alliage de fer-chrome-aluminium pratiquement exempt de molybdène résistant au fluage
US5866065A (en) * 1995-03-29 1999-02-02 Usinor Sacilor Ferritic stainless steel of use in particular for catalyst supports
US6197132B1 (en) * 1996-08-30 2001-03-06 Sandvik Ab Method of manufacturing ferritic stainless FeCrA1-steel strips
SE520617C2 (sv) * 2001-10-02 2003-07-29 Sandvik Ab Ferritiskt rostfritt stål, folie tillverkad av stålet, användning av stålet och folien, samt metod för att framställa stålet

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108779538A (zh) * 2016-10-21 2018-11-09 韩国科学技术院 高强度Fe-Cr-Ni-Al多相不锈钢及其制造方法
US11649517B2 (en) 2016-10-21 2023-05-16 Korea Advanced Institute Of Science And Technology High-strength Fe—Cr—Ni—Al multiplex stainless steel and manufacturing method therefor

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SE0300993D0 (sv) 2003-04-02
SE0300993L (sv) 2004-10-03

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