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EP3981889A1 - Procédé de production d'acier inoxydable - Google Patents

Procédé de production d'acier inoxydable Download PDF

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Publication number
EP3981889A1
EP3981889A1 EP20201101.1A EP20201101A EP3981889A1 EP 3981889 A1 EP3981889 A1 EP 3981889A1 EP 20201101 A EP20201101 A EP 20201101A EP 3981889 A1 EP3981889 A1 EP 3981889A1
Authority
EP
European Patent Office
Prior art keywords
stainless steel
cooling
quenching
annealing
steel
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.)
Pending
Application number
EP20201101.1A
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German (de)
English (en)
Inventor
Jan Y. Jonsson
James Oliver
Nataliya Limbach-Malyar
Peter HEDSTRÖM
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Outokumpu Oyj
Original Assignee
Outokumpu Oyj
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Outokumpu Oyj filed Critical Outokumpu Oyj
Priority to EP20201101.1A priority Critical patent/EP3981889A1/fr
Priority to KR1020237011656A priority patent/KR20230084496A/ko
Priority to PCT/EP2021/077932 priority patent/WO2022074229A1/fr
Priority to MX2023003545A priority patent/MX2023003545A/es
Priority to CN202180063438.2A priority patent/CN116323987B/xx
Priority to TW110137572A priority patent/TW202214876A/zh
Priority to JP2023518187A priority patent/JP7574423B2/ja
Priority to US18/247,822 priority patent/US20230340634A1/en
Publication of EP3981889A1 publication Critical patent/EP3981889A1/fr
Pending legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • B22D11/002—Stainless steels
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
    • C21C5/005—Manufacture of stainless steel
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
    • C21C5/52—Manufacture of steel in electric furnaces
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/28—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for plain shafts
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a method of suppressing embrittlement of steel.
  • the method comprises supressing embrittlement of duplex grades and ferritic grades with an external magnetic field.
  • the excellent properties of stainless steels are in part owed to the heat treatments performed during the final processing steps.
  • the heat treatments performed need to be closely controlled. While the heat treatment enhances these desired properties, it also can "sensitize" parts, when not performed adequately.
  • the risk for sensitization generally increases as the stainless steel grades becomes higher alloyed i.e. higher Cr and Mo levels. Resident times in the range of 700°C to 950°C for example, must be avoided to prevent the formation of sigma phase and chromium carbides both of which can reduce the corrosion resistance and mechanical properties of high alloyed austenitic and duplex stainless steel grades.
  • cooling after heat treatment is prefered to be performed by water quenching in water baths or water spraying depending on the product form.
  • another temperature region than should be avoided as much as possible is between 250°C to 500°C. Within this temperature region and phenomena known as spinodal decomposition can occur.
  • Spinodal decomposition is a degradation of duplex materials which drastically compromises the toughness.
  • the decomposition and embrittlement of the ferrite phase, in duplex and ferritic grades can occur to the extent that the impact toughness can be reduced by 50% after just holding for 3 minutes at temperature.
  • the decomposition still occurs but at a significantly lower rate, up to 10s of thousands of hours at temperature is required for the same level of negative impact on the properties.
  • JPH09217149A shows that 475°C embrittlement can occur during the cooling of thick gauge casts with grains size larger than 50 ⁇ m. They teach that an advanced cooling schedule is required to supress sigma phase, 475°C embrittlement and induced stress, including that the cooling rate needs to be higher than 10°C/min from 500°C to 300°C to limit 475°C embrittlement. Such a cooling approach is however, not possible in an in-line quenching process or practical in industrial scale batch annealing using large tanks for quenching.
  • 10°C/min is still too slow in some materials, e.g. in thick gauge materials having a grain size most more than 50 ⁇ m to avoid spinodal decomposition.
  • the highest possible cooling rate, at large plate thickness, due to material properties is still not fast enough to suppress 475°C embrittlement sufficiently.
  • JP2006212674A describes how ferritic grades can suffer from brittleness due to 475°C embrittlement in hot rolled coils if not adequately cooled during coiling.
  • a solution is proposed by starting the coiling at a specific temperature such that the tip of the coil enters the mandrel just above the embrittlement temperature range and thereafter is rapidly cooled during the coiling by the mandrel which has an in-built cooling function.
  • This approach is not pratically possible on plate material or bars for example.
  • CN108315549A claims a method for eliminating aging embrittlement of duplex stainless steel, which is subjected to an electric pulse treatment on aged duplex stainless steel, characterized in that the parameter range of the pulse processing is: frequency 1 to 200 Hz, pulse width 20 ⁇ s to 1 ms, current 10 to 2000 A, function Time 1 to 6h. This method is said to heal the aged duplex steel after long exposure to the 475°C regime, but does not prevent the occurrence during the processing of the steel.
  • the inventors have recently found that 475°C embrilttlement can even occur during the cooling/quenching step.
  • the properties of the materials subjected to 475°C embrittlement during cooling have been determined to be somewhat reduced in terms of impact toughness, albeit not to the same extent as isothermal aging at 475°C as described above.
  • the impact toughness can be lowered further to below acceptable levels, thus limiting plate thickness or quality of the delivered material. Supression of this embrittlement is therefore vital for achieveing high standard products.
  • a method of supressing embrittlement of stainless steel in a stainless steel production process comprising the steps of manufacturing stainless steel in a conventional stainless steel production process, annealing the stainless steel, cooling/quenching the steel and applying a magnetic field to the steel.
  • the magnetic field is applied to the steel in the cooling or quenching step.
  • the present invention relates to a method of supressing embrittlement of stainless steel in a stainless steel production process comprising the steps of manufacturing stainless steel in a conventional stainless steel manufacturing process, annealing stainless steel in an annealing step with an annealing temperature range of 900-1250°C, quenching the steel in a water bath, or in any other suitable quenching media/process, including air-cooling with or without forced air, through the critical temperature range of 350°C to 550°C and to below 350°C, particularly below 200°C, preferably 150 °C or below, suitably 100 °C and applying a magnetic field to the steel during either the annealing step or the cooling/quenching step or during both the annealing step and the cooling/quenching step.
  • FIG 1 shows that different cooling rates can influence the properties of the duplex stainless steels with regards to 475°C embrittlement.
  • the normal industrial process cooling (dashed line) gives a low impact toughness strength as some degree of spinodal decomposition already occurs during this cooling time period.
  • the impact toughness is significantly higher (table 1). This is since the spinodal decomposition has not had time to occur.
  • the impact toughness would logically be even lower than that for the process cooled sample.
  • FIG 2 The curves in Fig 2 represent different heat treatments and process conditions for super duplex material.
  • the material aged for 500 hours at 450°C has a large peak in intensity at around Q 0.007nm -1 indicating a relatively large amount of spinodal decomposition and probable embrittlement. After 6 hours at this temperature the peak intensity is less and shifted somewhat to a higher inverse wavelength (Q 0.01nm -1 ) showing that the phase separation is less as could be expected given the shorter exposure time. This trend continues for the sample held at 2 hours with a lesser but still very significant peak.
  • the material held at 450°C for 6 hours and 2 hours in the presence of a magnetic field (1.5T) shows no sign of phase separation as no peak intensity is observed from the background level. This shows that in the presence the magnetic field the 475°C embrittlement is fully suppressed in the isothermally aged condition up to at least 6 hours.
  • FIG 3 Show the same findings as for FIG 2 except for duplex grade 2205 rather than super duplex grade 2507.
  • duplex grades are less sensitive to the embrittlement than super duplex grades on account of the fact that they have less Cr.
  • Fig 3 still shows that at 450°C for 6 hours a significant degree of spinodal decomposition does exist and a somewhat affected nanostructure can be observed even after 30mins. Again, even for this grade in the presence of an external magnetic field the phase separation is significantly suppressed.
  • FIG 4 plots the SANS data (Intensity I(Q) [cm-1] vs. inverse wavelength Q [nm -1 ]) for samples cooled under different conditions.
  • the total exposure time to the 475°C temperature region is less than for the conditions in FIG 2 .
  • the general background intensities are different between the "slow” and “fast” cooled sample curves due to the difference in general microstructure e.g. different austenite spacing.
  • the slight curvature in intensity (data points show a higher intensity than the background reference line added to the plot) at about 0.01nm -1 measures a change in the nanostructure and indicates that the slow cooled sample shows an initial phase separation, whereas the fast cooled sample seems to be unaffected.
  • the process cooling rate of the slow cooled sample in FIG 4 was similar to the conditions of the slow cooled samples in FIG 1 (50-70°C/min and Table 1) which also had the low impact toughness. This tells that the production produced material can have some degree of phase separation and embrittlement already in the as received condition. The degree of phase separation and thus embrittlement would be more severe in air-cooled parts when the cooling rate would be much less than 50°C/min.
  • the "fast" cooled sample in FIG 4 was rapidly cooled (>500°C/min) faster than is possible under normal process quenching conditions. Therefore, in the real process it is not possible to cool thick plates, such as quarto plates, fast enough to avoid some initiation of embrittlement.
  • Application of an external magnetic field overcomes this problem and allows for material to be delivered free from spinodal decomposition/embrittlement.
  • the present invention relates to a method of supressing embrittlement of stainless steel in a stainless steel production process.
  • the process comprises the steps of providing an annealed stainless steel, cooling or quenching the steel in a cooling or quenching step; and applying a magnetic field to the stainless steel. Cooling/Quenching is most typically performed in batches in water baths (or heavy spraying in-line) or air cooled. The magnetic field is applied to the stainless steel during the cooling or quenching step. It has been found that embodiments of the invention are suitable for all types of stainless steel.
  • the step of providing an annealed stainless steel comprises stainless steels produced by all processes such as, but not limited to, melting of raw and / or scrap materials, casting stainless steel into ingots, slabs, blooms or atomized metallic powder or further processing the stainless steel by rolling, pressing or forming into billets, plates, sheets, strips, coils, bars, rods, wires, profiles and shapes, seamless and welded tubes and/or pipes, formed shapes, near net shape powder metallurgy and profiles, thereafter casting either by ingot casting or continuous casting to be susequently hot rolled and or cold rolled, or forged ready for final annealing in the temperarture range of 900°C to 1250°C.
  • the stainless steel melt can be used to produce metallic powder for isostatic pressing or additive manufacturing for annealing and cooling or quenching.
  • raw materials such as nickel and molybdenom are melted together with scrap metal in an electric arc furnace with or without vacuum oxygen decarburization.
  • Electric arc furnaces are particularly efficient for the purposes of embodiments of the present invention.
  • the stainless steel is tapped into a mould. Moulds may be made from various materials known to those skilled in the art. In one embodiment the stainless steel is tapped into a copper mould. In a further embodiment the stainless steel is continuously cast into slabs.
  • stainless steel manufacturing processes comprise an annealing step.
  • Such processes may comprise one or more annealing steps in the temperarture range of 900°C to 1250°C.
  • the annealing step has the purpose of homogenizing the stainless steel and softening and dissolving secondary phases. Secondary phases include, e.g. carbides, nitrides and intermetallics, like sigma phase.
  • the annealing step comprises raising the temperature of the steel to a temperature in excess of 900°C.
  • the annealing step may be carried out in batch furnaces for batch annealing or by in-line annealing, in embodiments.
  • Stainless steel manufacturing processes also include a cooling or quenching step.
  • the number of quenching steps is usually equal to the number of annealing steps.
  • the cooling or quenching step reduces the temperature of the steel to maintain the material properties of the steel.
  • the quenching step reduces the temperature of the steel from the annealing temperature to a temperature below which secondary phases or embrittlement can no longer form or occur i.e. 350°C or lower, particularly below 200°C, preferably 150 °C or below, suitably 100 °C or below by a quenching method selected from batch quenching in water tanks, in-line quenching, spraying and other suitable quenching techniques as used in the stainless steel industry when producing duplex stainless steels.
  • the quenching step reduces the termperature of the steel to room temperature or to a temperature in range of room temperature to 350°C.
  • room temperature means a temperature in the range of 20 to 25°C. Cooling to less than 20°C has no extra benefit.
  • a cooling step reduces the temperature of the steel by air-cooling either by forced air or natural cooling to room temperature.
  • the magnetic field has a field strength in the range of >0.2 T, preferably >1.0, most suitably 1.5-3.0T. Increasing the magnetic strength to greater than 3.0T has no extra benefit as the material will have reached magnetic saturation. By means of the magnetic field, embrittling of the stainless steel is supressed.
  • embodiments of the invention are suitable for all stainless steels.
  • the stainless steel is ferrite containing stainless steel or martensite containing stainless steel.
  • Impact toughness testing (Charpy impact tests) is a standardized testing method (for example in accordance to ISO 148-1:2016, ISO 17781 and well establised as a test method for determining the presence of detrimental phases for duplex grade such as described in ASTM A923 method B) ideally suited for determining if a material has been sensitized in some way, for example by 475°C embrittlement.
  • Impact toughness tests have been performed at -40°C on duplex grades that have been subjected to different cooling conditions from the normal annealing temperature as shown in Figure 1 .
  • a GLEEBLE instrument was used to simulate a typical cooling curve for thick plates materials when quenched in a water bath whereby the cooling through the critical temperature range 550-350°C was at a normal rate, dashed line in Figure 1 .
  • other samples were cooled under the same conditions down to 550°C and then rapidly quenched through the critical temperature range to completely eliminate the onset of 475°C embrittlement, solid line in Figure 1 .
  • the samples used for this GLEEBLE simultation and impact toughness testing were standard size 55x10x6mm with a v-notch for impact testing. 6mm thickness allowed for precise temperature control throughout the cooling step.
  • SANS Small-angle neutron scattering
  • 10x10x1mm was used. 1 mm thickness allows for a good signal strength and also avoids multiple scattering that can be otherwise experienced with thicker samples. 10x10mm dimensions are ideal for giving a homogenuous temperature across the whole sample in the cases where heated samples are required.
  • Fig 2 and 3 shows how the phase separation can clearly be detected using SANS for two different austenite-ferrite duplex stainless steels.
  • Materials that have been previously annealed and quenched have been held at 450°C for 6 and 500 hours.
  • the peak intensity increases and the position of the peak moves towards lower Q(nm -1 ) with increasing time showing that the spinodal decomposition proceeds with time. This is more evident in the Figure 2 compared to Figure 3 due to the higher alloying content, in particular chromium, of the super duplex grade in this Figure 2 .
  • Tests have also been performed on samples held at 475°C for up to 6 hours in the presence of an applied external magnetic field of strength 1.5T.
  • Fig 4 shows that under normal process quenching which is relatively slow cooled (approximately 60°C/min) as for thick plate material, some phase separation does exist, as indicated by the slight intensity peak in the as-received conditions, compared to the rapidly cooled material.
  • rapidly cooling >500°C/min as fast as the "fast sample” in figure 4 is not possible in many plates, thus the need for a means of suppressing the 475°C embrittlement, such as using a magnetic field, is desired.
  • an external magnetic field of >0.2T should be applied to the stainless steel to be cooled or quenched during the entire cooling or quenching process of the part, preferably applied during cooling or quenching from below 600°C.
  • the magnetic field is applied in such a way that the entire material to be cooled or quenched is encompassed by the magnetic field of >0.2T.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Articles (AREA)
  • Continuous Casting (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Soft Magnetic Materials (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Manufacturing Of Steel Electrode Plates (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP20201101.1A 2020-10-09 2020-10-09 Procédé de production d'acier inoxydable Pending EP3981889A1 (fr)

Priority Applications (8)

Application Number Priority Date Filing Date Title
EP20201101.1A EP3981889A1 (fr) 2020-10-09 2020-10-09 Procédé de production d'acier inoxydable
KR1020237011656A KR20230084496A (ko) 2020-10-09 2021-10-08 스테인리스 강을 생성하는 방법
PCT/EP2021/077932 WO2022074229A1 (fr) 2020-10-09 2021-10-08 Procédé de production d'acier inoxydable
MX2023003545A MX2023003545A (es) 2020-10-09 2021-10-08 Metodo de produccion de acero inoxidable.
CN202180063438.2A CN116323987B (en) 2020-10-09 2021-10-08 Stainless steel production method
TW110137572A TW202214876A (zh) 2020-10-09 2021-10-08 製造不鏽鋼之方法
JP2023518187A JP7574423B2 (ja) 2020-10-09 2021-10-08 ステンレス鋼の生成方法
US18/247,822 US20230340634A1 (en) 2020-10-09 2021-10-08 Method for producing stainless steel

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP20201101.1A EP3981889A1 (fr) 2020-10-09 2020-10-09 Procédé de production d'acier inoxydable

Publications (1)

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EP3981889A1 true EP3981889A1 (fr) 2022-04-13

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EP20201101.1A Pending EP3981889A1 (fr) 2020-10-09 2020-10-09 Procédé de production d'acier inoxydable

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US (1) US20230340634A1 (fr)
EP (1) EP3981889A1 (fr)
JP (1) JP7574423B2 (fr)
KR (1) KR20230084496A (fr)
MX (1) MX2023003545A (fr)
TW (1) TW202214876A (fr)
WO (1) WO2022074229A1 (fr)

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JP3322157B2 (ja) * 1997-03-31 2002-09-09 住友金属工業株式会社 Ｃｕを含有するフェライト系ステンレス鋼帯の製造方法
JP2006212674A (ja) 2005-02-04 2006-08-17 Jfe Steel Kk 高Ｃｒフェライト系ステンレス熱延鋼帯の巻取方法およびその装置
US20150071702A1 (en) * 2013-09-06 2015-03-12 Hitachi, Ltd. Structural body and production method for the same
CN105695671A (zh) * 2014-11-28 2016-06-22 重庆市巴南区仁荣机械厂 一种磁钢的热处理工艺
JP2017031493A (ja) * 2015-08-05 2017-02-09 新日鐵住金株式会社 ステンレス鋼管の製造方法
CN108315549A (zh) 2018-03-19 2018-07-24 北京科技大学 一种脉冲电流作用下老化双相不锈钢性能再生的方法
JP2018204040A (ja) * 2015-09-15 2018-12-27 株式会社日立製作所 二相ステンレス鋼製造物およびその製造方法

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