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WO2013018628A1 - Procédé de production d'acier inoxydable austénitique - Google Patents

Procédé de production d'acier inoxydable austénitique Download PDF

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Publication number
WO2013018628A1
WO2013018628A1 PCT/JP2012/068905 JP2012068905W WO2013018628A1 WO 2013018628 A1 WO2013018628 A1 WO 2013018628A1 JP 2012068905 W JP2012068905 W JP 2012068905W WO 2013018628 A1 WO2013018628 A1 WO 2013018628A1
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Prior art keywords
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temperature
stainless steel
hot rolling
content
Prior art date
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Ceased
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PCT/JP2012/068905
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English (en)
Japanese (ja)
Inventor
勇人 喜多
渋谷　将行
修二 吉田
朋之 須川
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.)
Nippon Steel Corp
Original Assignee
Nippon Steel and Sumitomo Metal Corp
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Filing date
Publication date
Application filed by Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Priority to KR1020147005051A priority Critical patent/KR101495483B1/ko
Priority to JP2013526850A priority patent/JP5418734B2/ja
Priority to EP12819669.8A priority patent/EP2737961B1/fr
Priority to CN201280046368.0A priority patent/CN103826766B/zh
Priority to SI201230842A priority patent/SI2737961T1/sl
Priority to US14/235,849 priority patent/US20140261917A1/en
Publication of WO2013018628A1 publication Critical patent/WO2013018628A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B1/026—Rolling
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
    • B21B2001/028—Slabs
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to a method for producing austenitic stainless steel exhibiting corrosion resistance against concentrated nitric acid. More specifically, the present invention relates to a method for producing a high Si-containing austenitic stainless steel that can be used in a high-temperature, high-concentration nitric acid environment.
  • the main components of the nitric acid production plant are exposed to a high temperature and high concentration nitric acid environment.
  • stainless steel is used as a corrosion resistant material for plants.
  • Stainless steel forms a stable passive film in nitric acid and exhibits excellent corrosion resistance.
  • high-temperature, high-concentration nitric acid is extremely oxidative, and general stainless steel causes transpassive corrosion.
  • the passive state corrosion the whole surface corrosion accompanied by elution of Cr 2 O 3 forming the passive state film and the intergranular corrosion occur near the grain boundary where sensitization (sensitivity of intergranular corrosion increases).
  • High Si austenitic stainless steels such as 17Cr-14Ni-4Si (Patent Document 1) and 11Cr-17Ni-6Si (Patent Document 2) are known as materials having corrosion resistance even in such an environment. These high-Si stainless steels exhibit excellent nitric acid corrosion resistance by re-oxidizing Si eluted by corrosion in the passive state region to form a silicate film.
  • One or more of Nb, Ta, Ti, and Zr are added to these high Si stainless steels.
  • These additive elements have an effect of fixing C in steel and suppressing sensitization. In particular, it is effective in suppressing sensitization of the weld heat affected zone, and has a remarkable effect in improving the intergranular corrosion resistance in high-concentration nitric acid.
  • the heating temperature of the slab in hot working is advantageously as high as possible from the viewpoint of productivity.
  • high Si stainless steel has a problem that cracking of the slab occurs during hot working when heated to a temperature higher than a predetermined temperature during hot working. This is because Si has a lower solid solubility in the austenite phase, and the higher the amount of Si, the more embrittled phases such as intermetallic compounds and ⁇ ferrite are generated at high temperatures, resulting in deterioration of high temperature ductility. Therefore, in order to stably produce high-Si stainless steel on an industrial scale, it is necessary to appropriately manage the heating temperature in hot working.
  • Patent Document 3 discloses an ingot of high Si stainless steel containing 5 to 8% Si (in this specification, “%” means “% by mass” unless otherwise specified) unless otherwise specified). Disclosed is a method of hot rolling or hot forging in a temperature range of 900 ° C. or higher after soaking in a temperature range satisfying 1100 ° C. and T (° C.) ⁇ 1470-35 ⁇ Si-5 ⁇ Ni (%). ing. As the Si content increases, a low-melting intermetallic compound is formed in the cast solidified structure, and when the soaking temperature rises, the intermetallic compound partially melts, so that cracking occurs during hot working. The soaking temperature is specified to prevent this cracking.
  • Non-Patent Document 1 describes the relationship between intermetallic compounds and hot workability in high-Si stainless steel (6.5Si-17Cr-22Ni-0.01Pd).
  • Si-- Ni-rich intermetallic compound crystallizes, and if it is present in a large amount, the hot workability is lowered, and
  • the high-Si stainless steel of Non-Patent Document 1 resulted in fracture due to partial melting of a low melting point Ni—Si intermetallic compound exceeding 1100 ° C. and crack propagation along the grain boundary. It is presumed that the heating temperature in the hot working is defined as 1100 ° C. or lower.
  • Patent Document 4 a high Si stainless steel slab containing 4 to 10% of Si and having S and O regulated to 30 ppm or less is soaked at 1100 ° C. to 1250 ° C. for 2 hours or more and hot-rolled. A method is disclosed in which hot rolling is terminated at 950 ° C. or higher and solution heat treatment is performed at 1000 ° C. or higher and 1200 ° C. or lower.
  • factors affecting the high-temperature ductility of high-Si austenitic stainless steel are (1) impurity elements of S and O, and (2) intermetallic compounds that precipitate during cooling of the slab, and It is disclosed that hot workability is improved by eliminating intermetallic compounds by reducing S and O and soaking slabs. Although the component of this intermetallic compound is not specified, it is presumed that it is a Ni—Si intermetallic compound having a low melting point as in Non-Patent Document 1.
  • the hot workability is improved by setting the heating temperature to be equal to or lower than the melting temperature of the Ni—Si intermetallic compound.
  • the heating temperature is set to be equal to or lower than the melting temperature of the Ni—Si intermetallic compound.
  • the solid solubility of C tends to be lowered and sensitized. Intergranular corrosion resistance was poor.
  • the high-Si stainless steels disclosed in Patent Documents 1 and 2 contain Nb, Ta, Ti, and Zr, thereby suppressing sensitization and greatly improving nitric acid corrosion resistance. There was a new problem that surface defects called wrinkles were likely to occur.
  • the object of the present invention is to reliably produce high-Si austenitic stainless steel with corrosion resistance suitable for use in a high-temperature, high-concentration nitric acid environment without generating lashes during the hot rolling process. It is to be.
  • the present inventors have developed a high Si-containing austenitic stainless steel suitable for use in a high-temperature, high-concentration nitric acid environment (hereinafter austenitic stainless steel).
  • austenitic stainless steel As a result of investigating conditions for reliably producing (sometimes simply referred to as stainless steel), the following items (i) to (iii) were clarified.
  • Ni—Si—X Nb, Ti, Zr
  • the melting point is approximately in the range of 1150 to 1200 ° C., and for example, Ni—Si—Nb is about 1160 ° C. from the results of the phase diagram calculation.
  • the present invention has a C: 0.04% or less, Cr: 7-20%, Ni: 10-22%, Si: 2.5-7%, Mn: 10% or less, sol. Al: 0.03% or less, P: 0.03% or less, S: 0.03% or less, N: 0.035% or less, a total of one or more of Nb, Ti, Ta, and Zr: 0.0
  • the method according to the present invention comprises heat-treating the austenitic stainless steel subjected to the hot rolling in a temperature range of 1100 to 1160 ° C., and then cooling at a cooling rate of 100 ° C./min or more.
  • a temperature range of 1100 to 1160 ° C. a temperature range of 1100 to 1160 ° C.
  • cooling at a cooling rate of 100 ° C./min or more.
  • a high Si content austenitic stainless steel suitable for use in a high-temperature, high-concentration nitric acid environment can be reliably produced without generating lashes during the hot rolling process.
  • FIG. 1 is a graph showing the results of a torsion test of the test steel 1.
  • FIG. 2 is a graph showing the relationship between ⁇ T of the test steel 1 and the rate of occurrence of whipping.
  • FIG. 3 is a graph showing the relationship between the heat treatment temperature of the test steel 1 after rolling, 0.2% proof stress, and elongation.
  • % related to the chemical composition of steel is “% by mass”. Moreover, the balance of the chemical composition of steel is Fe and impurities.
  • C [Chemical composition of steel] [C: 0.04% or less]
  • C is an element that increases the strength of steel, it is an element that deteriorates corrosion resistance, for example, forms Cr carbide at the grain boundary in the heat-affected zone of the weld and causes sensitization. Therefore, the C content is set to 0.04% or less.
  • the C content is preferably 0.03% or less, and more preferably 0.02% or less.
  • Cr 7-20%
  • Cr is a basic element for ensuring the corrosion resistance of stainless steel, and its content is 7% or more and 20% or less. If the Cr content is less than 7%, sufficient corrosion resistance cannot be obtained. On the other hand, if the Cr content is excessive, a co-existence of Si and Nb results in a two-phase structure in which a large amount of ferrite is precipitated, resulting in a decrease in workability and impact resistance. Therefore, the upper limit of the Cr content is 20%. To do.
  • the lower limit of the Cr content is preferably 10%, and more preferably 11%.
  • the upper limit of the Cr content is preferably 19%, and more preferably 18%.
  • Ni is a stabilizing element of the austenite phase and also has an effect of increasing the zero ductility temperature. Ni is contained in an amount of 10% to 22%. If the Ni content is less than 10%, the desired corrosion resistance and toughness cannot be obtained. If the Ni content exceeds 22%, the cost increases significantly.
  • the lower limit of the Ni content is preferably 12%, and more preferably 13%. Further, the upper limit of the Ni content is preferably 20%, and more preferably 16%.
  • Si is contained in an amount of 2.5% or more and 7% or less in order to enhance the corrosion resistance in concentrated nitric acid.
  • Si is contained in an amount of 2.5% or more.
  • the upper limit of the Si content is set to 7%.
  • the lower limit of the Si content is preferably 3.0%, and more preferably 3.5%.
  • the upper limit of the Si content is preferably 6%, and more preferably 5%.
  • Mn is a stabilizing element of the austenite phase and is also contained as a deoxidizing agent. If the Mn content exceeds 10%, the corrosion resistance decreases, hot cracking during welding, and further the workability decreases.
  • the upper limit of the Mn content is preferably 6%, and more preferably 4%. Moreover, in order to acquire the said effect of Mn reliably, it is preferable that Mn content is 0.5% or more, and it is further more preferable that it is 1.0% or more.
  • sol.Al 0.03% or less
  • Al is contained in the steel as a deoxidizing agent. However, since excessive inclusion of Al generates harmful inclusions, the content of sol.Al is set to 0.03% or less.
  • P and S are both elements harmful to corrosion resistance and weldability, and the lower the content of each, the better. Therefore, the P content is 0.03% or less, and the S content is 0.03% or less.
  • N 0.035% or less
  • N has a high affinity with Nb, Ti, Ta, and Zr, and inhibits the fixation of C by these elements. Therefore, the N content is preferably as low as possible. Therefore, the N content is set to 0.035% or less.
  • Nb, Ti, Ta and Zr all have an effect of fixing C and suppressing the decrease in intergranular corrosion resistance due to sensitization, and are particularly effective elements for improving the corrosion resistance of the weld heat affected zone. If the total content of these elements is less than 0.05%, the effect of improving the intergranular corrosion resistance cannot be obtained, and hot working cracks due to the formation of a low melting point Ni—Si intermetallic compound become large. On the other hand, if the total content of these elements exceeds 0.7%, workability is obtained. Therefore, the content of these elements is 0.05% or more and 0.7% or less in total of one or more kinds.
  • a hot rolling step of performing hot rolling 9Cr + 40Ni- ⁇ T ⁇ T in is heated to a heating temperature T h at 30 ° C. or higher, after heat treatment at preferably a temperature range of more 1100 ⁇ 1160 °C, 100 °C / min It consists of a heat treatment step (annealing step) for cooling at the above cooling rate.
  • Hot rolling process In order to clarify the optimum heating temperature range for hot rolling, the relationship between chemical composition and high temperature deformability was investigated by high temperature torsion test. Thereby, the zero ductility in hot rolling can be investigated.
  • one of the test pieces having a parallel part diameter of 8 mm and a length of 30 mm is fixed and held at a predetermined temperature, with a rotational speed of 300 rpm (strain speed of 4.2 sec ⁇ 1 ) and an axial force of 0 kgf in one direction.
  • the number of rotations until twisting was applied and breaking was taken as the number of twists.
  • FIG. 1 shows the relationship between the heating temperature and the number of twists as a result of conducting a high temperature return test using a test piece of high Si stainless steel having the chemical composition shown in Table 1 as test steel 1.
  • the number of twists showed a maximum at around 1100 ° C., and the number of twists decreased significantly at a temperature higher than that, and at 1275 ° C., it started to twist and broke at the same time. That is, it can be seen that the temperature at which the ductility of the high Si stainless steel shown as the test steel 1 in Table 1 becomes zero (hereinafter referred to as “zero ductility temperature”) is approximately 1275 ° C.
  • the high-temperature torsion test was conducted on high-Si stainless steels having various chemical compositions containing one or more of Nb, Ta, Ti, and Zr, and the zero ductility temperature was examined.
  • T 0 the zero ductility temperature
  • T 0 1135-90Si-2.9Cr + 40Ni (2)
  • the thickness was 4 mm by hot rolling. Thereafter, the scale was removed by pickling, and then the rate of occurrence of baldness was investigated by the following method.
  • the steel plate surface was divided into 100 mm unit meshes, and the ratio of the number of meshes with scabs in the total number of meshes investigated was defined as the scab generation rate (%). If the rate of occurrence of lashes is 5% or less, it is possible to proceed to the next step with a simple rework.
  • FIG. 2 shows the relationship between ⁇ T of the test steel 1 (Table 1) and the rate of occurrence of lashes.
  • [Delta] T is 30 ° C. or more, preferably such that 60 ° C. or higher may be set the heating temperature T h of the hot rolling.
  • the holding time to this heating temperature is not particularly limited.
  • the heating temperature is set in order to prevent the occurrence of baldness after rolling, so that the surface temperature of the slab may be a predetermined temperature.
  • the heating time required for this depends on the size of the slab, but in general, the heating time is preferably 60 minutes or more.
  • hot rolling can be performed if the hot rolling end temperature is 700 ° C. or higher. Desirably, the end temperature is set to 950 ° C. or higher.
  • Hot rolling can be performed in one or more stages. In the case of multi-stage rolling, if necessary, it can be heated between rolling stands.
  • the heating temperature at this time is not particularly required to be a temperature at which ⁇ T is 30 ° C. or higher, but is preferably a temperature at which ⁇ T is 30 ° C. or higher.
  • pickling is generally performed by a conventional method to remove oxide scale on the surface of the rolled material.
  • Heat treatment process Since the stainless steel plate obtained by hot rolling can adjust mechanical characteristics (elongation, yield strength) by performing a heat treatment for annealing, it is preferable to perform the heat treatment after the hot rolling.
  • the heat treatment temperature is increased, the proof stress is reduced although the elongation is increased.
  • the cooling rate after the heat treatment is slow, chromium carbide precipitates, and the corrosion resistance deteriorates. Therefore, it is necessary to set the heat treatment temperature and the subsequent cooling rate so as to achieve both elongation and yield strength and prevent sensitization.
  • FIG. 3 shows the relationship between the heat treatment temperature of the test steel 1, the 0.2% proof stress and the elongation.
  • the circle plot in the graph of FIG. 3 shows 0.2% yield strength (MPa), and the square plot shows elongation (%).
  • a high Si content austenitic stainless steel suitable for use in a high-temperature, high-concentration nitric acid environment can be reliably produced without generating lashes in the hot rolling process. can do.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention porte sur la production de l'acier. Selon l'invention, il est possible de produire fiablement un acier inoxydable austénitique qui possède une haute teneur en Si et présente une résistance à la corrosion suffisamment élevée pour que l'outil puisse être utilisé dans un environnement à haute température présentant une haute concentration d'acide nitrique sans qu'il se produise d'écaillage, en soumettant une brame d'acier inoxydable ayant une composition chimique qui contient 0,04 % ou moins de C, 7 à 20 % de Cr, 10 à 22 % de Ni, 2,5 à 7 % de Si, 10 % ou moins de Mn, 0,03 % ou moins de sol.Al, 0,03 % ou moins de P, 0,03 % ou moins de S, 0,035 % ou moins de N et 0,05 à 0,7 % du total d'un ou plusieurs éléments sélectionnés parmi Nb, Ti, Ta et Zr, le reste comprenant Fe et des impuretés, à un laminage à chaud par chauffage de la brame d'acier à une température de chauffage Th, la température de chauffage pendant le laminage à chaud étant Th et ΔT dans la formule (1) (Th= 1135 - 90Si - 2,9Cr + 40Ni - ΔT) étant de 30°C ou plus et en soumettant ensuite la brame d'acier à un traitement thermique par chauffage à une température de 1100 à 1160°C, puis refroidissement à une vitesse de refroidissement de 100°C/minute ou plus.
PCT/JP2012/068905 2011-07-29 2012-07-26 Procédé de production d'acier inoxydable austénitique Ceased WO2013018628A1 (fr)

Priority Applications (6)

Application Number Priority Date Filing Date Title
KR1020147005051A KR101495483B1 (ko) 2011-07-29 2012-07-26 오스테나이트계 스테인리스강의 제조 방법
JP2013526850A JP5418734B2 (ja) 2011-07-29 2012-07-26 オーステナイト系ステンレス鋼の製造方法
EP12819669.8A EP2737961B1 (fr) 2011-07-29 2012-07-26 Procédé de production d'acier inoxydable austénitique
CN201280046368.0A CN103826766B (zh) 2011-07-29 2012-07-26 奥氏体系不锈钢的制造方法
SI201230842A SI2737961T1 (sl) 2011-07-29 2012-07-26 Metoda za izdelavo avstenitnega nerjavnega jekla
US14/235,849 US20140261917A1 (en) 2011-07-29 2012-07-26 Method for manufacturing austenitic stainless steel

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011166361 2011-07-29
JP2011-166361 2011-07-29

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WO2013018628A1 true WO2013018628A1 (fr) 2013-02-07

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PCT/JP2012/068905 Ceased WO2013018628A1 (fr) 2011-07-29 2012-07-26 Procédé de production d'acier inoxydable austénitique

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US (1) US20140261917A1 (fr)
EP (1) EP2737961B1 (fr)
JP (1) JP5418734B2 (fr)
KR (1) KR101495483B1 (fr)
CN (1) CN103826766B (fr)
SI (1) SI2737961T1 (fr)
WO (1) WO2013018628A1 (fr)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103849715A (zh) * 2014-03-18 2014-06-11 河北师范大学 一种降低奥氏体不锈钢铸件磁性的热处理方法
JP2016079481A (ja) * 2014-10-20 2016-05-16 新日鐵住金株式会社 複合非金属介在物を含有する高Ｓｉオーステナイト系ステンレス鋼
JP2020104145A (ja) * 2018-12-27 2020-07-09 ヤマコー株式会社 高珪素ステンレス鋼の成形加工方法

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CN110257690B (zh) * 2019-06-25 2021-01-08 宁波宝新不锈钢有限公司 一种资源节约型奥氏体耐热钢及其制备方法

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JP2020104145A (ja) * 2018-12-27 2020-07-09 ヤマコー株式会社 高珪素ステンレス鋼の成形加工方法

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EP2737961A1 (fr) 2014-06-04
KR101495483B1 (ko) 2015-02-24
US20140261917A1 (en) 2014-09-18
CN103826766A (zh) 2014-05-28
JPWO2013018628A1 (ja) 2015-03-05
JP5418734B2 (ja) 2014-02-19
CN103826766B (zh) 2015-11-25
SI2737961T1 (sl) 2017-05-31
EP2737961A4 (fr) 2015-06-03
KR20140037969A (ko) 2014-03-27

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