EP2172574B1 - Acier inoxydable austénoferritique d'excellente résistance à la corrosion et transformabilité, et procédé pour la fabrication dudit - Google Patents

Acier inoxydable austénoferritique d'excellente résistance à la corrosion et transformabilité, et procédé pour la fabrication dudit Download PDF

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EP2172574B1
EP2172574B1 EP08792317.3A EP08792317A EP2172574B1 EP 2172574 B1 EP2172574 B1 EP 2172574B1 EP 08792317 A EP08792317 A EP 08792317A EP 2172574 B1 EP2172574 B1 EP 2172574B1
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austenite
corrosion resistance
phase
uniform elongation
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EP2172574A1 (fr
EP2172574A4 (fr
Inventor
Masaharu Hatano
Akihiko Takahashi
Eiichiro Ishimaru
Ken Kimura
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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Priority claimed from JP2007202016A external-priority patent/JP5156293B2/ja
Priority claimed from JP2007222259A external-priority patent/JP5213386B2/ja
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Priority to EP18188353.9A priority Critical patent/EP3434802B1/fr
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Publication of EP2172574A4 publication Critical patent/EP2172574A4/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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • 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
    • C21D8/0236—Cold 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
    • 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
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to ferritic-austenitic stainless steel excellent in corrosion resistance and workability and a method of production of the same. According to the present invention, it is possible to produce ferritic-austenitic stainless steel excellent in corrosion resistance and workability without including a large amount of the expensive and rare element of Ni, so it is believed this can contribute to resource conservation and environmental protection.
  • Stainless steel may be broadly divided into austenitic stainless steel, ferritic stainless steel, and two-phase (ferritic-austenitic) stainless steel.
  • Austenitic stainless steel contains expensive Ni in 7% mass or more. Many types are excellent in workability.
  • Ferritic stainless steel contains almost no Ni and generally has considerably lower workability than austenitic stainless steel.
  • two-phase (ferritic-austenitic) stainless steel has a comparatively small Ni content. It is considered that many types have an intermediate position in workability, corrosion resistance, etc. between austenitic stainless steel and ferritic stainless steel.
  • ferritic stainless steel is economically superior to austenitic stainless steel, which contains a large amount of Ni.
  • ferritic stainless steel is very inferior to austenitic stainless steel with respect to workability, particularly in material elongation and uniform elongation.
  • austenitic-ferritic stainless steel which is positioned between austenitic and ferritic steel, has come under the spotlight in recent years.
  • austenitic-ferritic stainless steel such as SUS 329J4L contains over 5% of Ni. Further, it contains several percent of Mo - which is rarer and more expensive than Ni. Therefore, there is still a problem in terms of spread of use and economy.
  • austenitic-ferritic stainless steel using Mo as an optional additive element and limiting the amount of Ni to more than 0.1% and less than 1% has been disclosed in Japanese Patent Publication ( A) No. 11-071643 or to 0.5% to 1.7% has been disclosed in WO/02/27056 .
  • These austenitic-ferritic stainless steels are directed at lower Ni content, so contain N in an amount exceeding 0.1% and Mn in an amount substantially exceeding 3.7%.
  • Japanese Patent Publication ( A) No. 2006-169622 and Japanese Patent Publication ( A) No. 2006-183129 disclose austenitic-ferritic stainless steels aimed at improvement of total elongation and deep drawability by limiting the Ni amount to substantially 3% or less and adjusting the austenite phase C+N and ingredient balance. Further, Japanese Patent Publication ( A) No. 10-219407 . discloses ferritic stainless steel excellent in ductility having an amount of N of substantially less than 0.06, having a ferrite phase as the matrix phase, and having a residual austenite phase of less than 20%.
  • Japanese Patent Publication ( A) No. 10-219407 describes technology that uses stainless steel having a ferrite phase as its principal constituent phase and containing a residual austenite phase to improve the tensile elongation at break by the TRIP phenomenon.
  • Japanese Patent Publication ( A) No. 11-071643 describes a method defining the stability of an austenite phase to improve the tensile elongation.
  • Japanese Patent Publication ( A) No. 2006-169622 discloses the art of defining the percentage of the austenite phase and amounts of C and N in the austenite phase to improve the total elongation in a tensile test.
  • Japanese Patent Publication ( A) No. 10-219407 as shown in the examples, the values of the tensile elongation at break are 34 to 42%, that is, the elongation at break is not necessarily high. Further, even if steel sheet or plate does not break and "fracture" in actual shaping, it is often judged unworkable when necking occurs. That is, rather than the "elongation at break” in a tensile test, the uniform deformation limit, that is, the "uniform elongation", determines the workability, but what extent of level the uniform elongation is at is unknown. Japanese Patent Publication 11-071643 describes a tensile elongation at break of up to a 46% maximum. Further, Japanese Patent Publication ( A) No. 2006-169622 describes an elongation at break of up to a 71% maximum in the examples. However, even these citations do not describe at all the uniform elongation which governs the actual workability.
  • Japanese Patent Publication ( A) No. 2006-200035 and Japanese Patent Publication ( A) No. 2006-233308 disclose improvements in the crevice corrosion resistance and intergranular corrosion resistance of austenitic-ferritic stainless steels similar to Japanese Patent Publication ( A) No. 2006-169622 and Japanese Patent Publication ( A) No. 2006-183129 .
  • Japanese Patent Publication ( A) No. 2006-200035 describes suppression of crevice corrosion in a coastal environment exposure test for an austenitic-ferritic stainless steel in which an amount of Mn is limited to less than 2% and an amount of Ni of over 0.5% is added.
  • Japanese Patent Publication ( A) No. 2006-233308 describes an austenitic-ferritic stainless steel containing Mn in over 2% and less than 4% and having an amount of Ni of substantially less than 0.6% in which grain boundary cracking after boiling in a sulfuric acid/cupric sulfate solution is suppressed.
  • Japanese Patent Publication ( A) No. 5-247594 discloses two-phase stainless steel with improved resistance to weather under near coastal conditions.
  • This two-phase stainless steel contains an amount of Mn substantially over 4% or an amount of Mn less than 4% and an amount of Ni over 3%.
  • the present invention was made in view of the current state of the prior art and has as its object to provide ferritic-austenitic stainless steel oriented at lower Ni which is excellent in corrosion resistance, particularly corrosion resistance in a neutral chloride environment, and which has a high "uniform elongation", the factor governing workability, and a method of production of the same.
  • ferritic-austenitic stainless steel which has a corrosion resistance in a neutral chloride environment equal to or greater than SUS 304, which has excellent uniform elongation, and which is excellent in corrosion resistance and workability can be obtained and thereby completed the present invention.
  • the inventors engaged in research on the effects of the ingredients, phase balance, and final annealing condition on the corrosion resistance and workability of ferritic-austenitic stainless steel oriented toward lower Ni.
  • ferritic-austenitic stainless steel excellent in corrosion resistance and workability provided with a corrosion resistance in a neutral chloride environment equal to or greater than SUS 304, that is, of a pitting potential Vc'100 in a 30°C, 3.5% NaCl aqueous solution of 0.3V (Vv.s.AGCL) or more, and provided with an excellent material elongation, particularly an excellent uniform elongation of a uniform elongation in a tensile test of 30% or more.
  • the inventors will explain the first findings, which are partially the present invention.
  • the inventors engaged in intensive research on the effects of the ingredients and phase balance on the corrosion resistance and the workability of ferritic-austenitic stainless steel oriented to lower Ni and the effects of the final annealing conditions on the corrosion resistance and thereby completed the present invention. Below, they will explain representative test results.
  • the inventors hot rolled a stainless steel ingot obtained by vacuum melting ferritic-austenitic stainless steel having the ingredients shown in Table 1 to produce 5 mm thick hot rolled plate. They annealed the hot rolled plate at 1000°C, pickled it, then cold rolled it to prepare 1 mm thick cold rolled sheet. They annealed the cold rolled sheet at 1000°C, then cooled it by forced air cooling from 1000°C to 200°C at an average cooling rate in a range of 35 to 40°C/secs. The cold rolled annealed sheet was used for measurement of the volume fraction of the austenite ( ⁇ ) phase, measurement of the pitting potential, and a JIS 13B tensile test.
  • the volume fraction of the ⁇ phase was found by measurement of a phase map that identifies the crystal structure of fcc and bcc by using the EBSP method at the sheet cross-section.
  • the Vc'100 Vv.s.AGCL
  • the measurement value of the pitting potential was made the average of n3.
  • JIS 13B tensile test a tensile test piece was taken from the rolling direction, and the uniform elongation until necking occurred was measured at a tension rate of 20 mm/min (range of tension rate defined in JIS Z 2241).
  • Table 1 shows, in addition to the steel ingredients, the measurement results of the ⁇ fraction, Vc'100, and uniform elongation.
  • Steel No. 1 has a pitting potential of 0.38V, a uniform elongation of 35%, and corrosion resistance in a neutral chloride environment equal to or greater than SUS 304.
  • SUS 430LX with workability improved through a shift to ultra low C and N, the uniform elongation was greatly improved.
  • Steel Nos. 2 to 6 have uniform elongations sufficiently higher than SUS 430LX, but have pitting potentials equal to or less than SUS 430LX or greatly inferior compared to SUS 304.
  • the ingredients of steels with inferior pitting potentials are characterized by having (i) an amount of Si which is a high over 1% (Steel No. 2), (ii) an amount of Mn which is a high 3.8% (Steel No. 3), (iii) an amount of N which is a high 0.15% (Steel No. 4), (iv) a pitting indicator (PI value) which is less than 18% (Steel No. 5), and (v) an amount of N which is a high 0.16% and a ⁇ fraction which is over 50% (Steel No. 6).
  • FIG. 1 shows the relationship of the cooling rate in the final annealing and the pitting potential of the Steel No. 1.
  • a pitting potential equal to or greater than SUS 304 (0.3V or more)
  • it is necessary to restrict the cooling rate to 3°C/sec or more.
  • steel cooled by the method of holding at 500°C for 1 minute has the feature of having a pitting potential higher than when continuously cooling by a cooling rate of 5°C/sec without holding.
  • the inventors analyzed the structure in detail using an optical microscope, SEM (scan electron microscope), and TEM (transmission electron microscope) .
  • the inventors engaged in a detailed structural analysis by the method of measurement of a phase map identifying the fcc and bcc crystal structures at the sheet cross-section by the EBSP method, measured the pitting potential by the method of measuring the Vc'100 (Vv.s.AGCL) on a #500 polished surface as an evaluation surface in a 30°C, 3.5% NaCl aqueous solution (note that the measurement value of the pitting potential was made the average of n3), and, according to a JIS 13B tensile test, obtained a tensile test piece from the rolling direction and measured the uniform elongation until necking occurred by a tension rate of 20 mm/min (range of tension rate defined in JIS Z 2241). As a result, the inventors arrived at the following findings explaining the test results of Table 1 and FIG. 1 .
  • the inventors investigated the factors of metal structure governing uniform elongation in relation to the above problems by producing various ferritic-austenitic stainless steels in the laboratory, hot rolling them, then annealing and cold rolling them to produce thin-gauge steel sheet. They investigated the relationship of the metal structures of the obtained thin-gauge steel sheet and the uniform elongation after the tensile tests and as a result obtained the following findings concerning the characteristics of austenite grain in steels with high uniform elongation.
  • the inventors will explain details of these next.
  • the inventors produced 10 types of steel having compositions of 0.006 to 0.030% C, 0.10 to 0.85% Si, 1.0 to 3.0% Mn, 0.022 to 0.039% P, 0.0002 to 0.0035% S, 20.1 to 21.0% Cr, and 0.08 to 0.12% N, then hot rolled them, then annealed and cold rolled them to produce thin-gauge steel sheets. During this, they changed the hot rolling conditions, annealing temperatures, and other production conditions. They obtained JIS 13B tensile test pieces from the obtained 1 mm thick thin-gauge steel sheets parallel to the rolling direction and measured their uniform elongations by a method based on JIS Z 2241. The tension rate was made 10 mm/min.
  • FIG. 2(a) shows the BCC phase
  • FIG. 2(b) the FCC phase, each shown by the white color.
  • the inventors measured the grain sizes and aspect ratios of the grains of the austenite grains (FCC phase) and measured the distance between nearest grains for the austenite grains. For the distance between nearest grains, they used the smallest value of the distance between the center positions of austenite grains as the distance between nearest grains of those grains. For the center position of each crystal grain, they made the position of 1/2L and 1/2H, where the rolling direction length of the grain is L and the thickness direction length of the sheet is H, the center position. They measured the distance between nearest grains for each of 100 austenite grains and found their average value.
  • the inventors used EPMA to investigate the chemical composition in the austenite grains. From the obtained chemical composition, they calculated an Md value as an indicator of the stability of the austenite phase.
  • Md is an indicator expressing the austenite stability calculated by the following formula (2).
  • the coefficients in the formula were based on the formula of Nohara et al. (see Journal of the ISIJ 63 (1977) p. 772).
  • the [ ] in the formula indicates a composition measured by EPMA for each element.
  • quantification in the austenite phase is difficult by EPMA, so the average composition ⁇ ⁇ is shown.
  • the Md value is determined by the chemical composition in the austenite grains. Therefore, by changing the chemical composition in the austenite grains by, for example, the annealing temperature, annealing time, or the like, the Md value can be adjusted.
  • N, Cu, Ni, and Mn concentrate at the austenite phase, that is, are elements which have higher concentrations in the austenite phase than concentrations in the ferrite phase, so by increasing the amounts of addition of these, the Md value can be lowered.
  • the composition of the austenite phase is not an equilibrium composition determined by the annealing temperature. This is because time is needed for diffusion for the elements to be distributed to the austenite phase and ferrite phase at a certain annealing temperature. Therefore, increasing the holding time at the final annealing process will enable the equilibrium composition to be approached (the concentration in the austenite phase of N, Cu, Ni, and Mn rising), so making the holding time longer is also an effective method of lowering the Md value. However, with a holding time of 30 minutes, the equilibrium composition will substantially be reached.
  • C is an element lowering the Md value. By increasing the amount of addition, the Md value can be lowered. Further, C is also an element that concentrates in the austenite phase, however, measurement of the concentration in the austenite phase is difficult. In the present invention, in the formula for calculation of the Md value, the average composition of C is used. Therefore, the holding time of the annealing has no effect on the Md value of the present invention.
  • the Md value is determined by the chemical composition in the austenite grains.
  • the chemical composition in the austenite grains also changes depending on the austenite fraction. That is, when the austenite fraction is low, the concentration of austenite forming elements in the austenite phase becomes higher, so the Md value tends to fall. On the other hand, when the austenite fraction is low, the concentration of austenite forming elements in the austenite phase becomes lower, so the Md value rises. Further, the austenite fraction changes depending on the temperature. In the ingredients set forth in the present invention, the austenite fraction is the highest at 1000°C to 1150°C. At temperatures higher or lower than that, the austenite fraction decreases.
  • the higher the absolute value of the uniform elongation the higher the workability, however, if the uniform elongation is 30% or more, the level becomes higher compared to ferritic stainless steel, while if 40% or more, it is possible to work the steel into nearly the same shape as with austenitic stainless steel with good workability.
  • the invetors investigated the relationship between the volume fraction (austenite fraction) of the austenite phase and the uniform elongation for all datad.
  • the relationship between the austenite phase and the uniform elongation during a tensile test is shown in FIG. 3 .
  • the austenite fraction there is a range of suitability of the austenite fraction with respect to the uniform elongation. If too high or too low, the uniform elongation will drop. To secure a uniform elongation of 30% or more, it is necessary to make the austenite fraction 10% to less than 50%.
  • the range is preferably 15 to 40%.
  • the relationship between the Md value and the uniform elongation for data where the austenite fraction is 10% to less than 50% is shown in FIG. 4 .
  • the uniform elongation is a high value of 34 to 44%.
  • Such a high uniform elongation cannot be obtained outside this range.
  • the variation in uniform elongation is too large. There may also be other structural factors that affect the uniform elongation.
  • the grain size and shape of the austenite grains may also affect the uniform elongation, so the inventors measured, for the -10 to +110 Md value data in FIG. 4 , the "ratio of austenite grains with a grain size of 15 ⁇ m or less and a shape aspect ratio of less than 3 in the total number of austenite grains" X1 (%) was measured and investigated its relationship to the uniform elongation u-EL(%). The results are shown in FIG. 5 . As shown in FIG. 5 , the higher this ratio, the higher the uniform elongation tends to be. When the ratio is 90% or more, even better uniform elongation can be obtained.
  • C is an element raising the volume fraction of the austenite phase and concentrating in the austenite phase to raise the austenite phase stability. To obtain the above effects, it is included in 0.001% or more. However, if over 0.1%, the heat treatment temperature for making C form a solid solution becomes remarkably high and the steel will become susceptible to sensitization due to carbide grain boundary precipitation. Therefore, the content is made 0.1% or less, preferably 0.05% or less.
  • Cr is an element necessary to secure the corrosion resistance.
  • its lower limit is made 17%.
  • the content is made 25% or less. From the viewpoints of the corrosion resistance, workability, and production, the content is preferably 19 to 23%, more preferably 20 to 22%.
  • Si is sometimes added as a deoxidizing element. To obtain the above effect, it is included in 0.01% or more. However, if over 1%, it becomes difficult to secure the object of the first findings of corrosion resistance. Therefore, the content is made 1% or less. Excessive addition leads to an increase in refining costs as well. From the viewpoint of corrosion resistance and production, the content is preferably 0.02 to 0.6%, more preferably 0.05 to 0.2%.
  • Mn is an element raising the volume fraction of the austenite phase and concentrating in the austenite phase to raise the austenite phase stability. Further, it is also an element effective as a deoxidizing agent. To obtain the above effect, it is included in 0.5% or more. However, if over 3.7%, it becomes difficult to secure the object of the first findings of corrosion resistance. Therefore, the content is made 3.7% or less. From the viewpoints of corrosion resistance, workability, and production, the content is preferably 2 to 3.5%, more preferably 2.5 to 3.3%.
  • N is an element raising the volume fraction of the austenite phase and concentrating in the austenite phase to stabilize the austenite phase. Further, it is an element forming a solid solution with the austenite phase and raising pitting resistance. To obtain the above effects, its lower limit is made 0.06%. However, if 0.15% or more is added, the chromium nitride contained in the steel material will exceed 0.1 mass% and most of the chromium nitride will precipitate at the crystal grain boundaries, so this will become a factor forming a chrome-depleted layer. Therefore, securing the object of the first findings of corrosion resistance, will become difficult.
  • the content is made less than 0.15%. Further, adding N causes the occurrence of blowholes during melting and causes the hot workability to drop. From the viewpoints of corrosion resistance, workability, and production, the content is preferably 0.07 to 0.14%, more preferably 0.08 to 0.12%.
  • Ni is an austenite forming element and is effective in securing the objects of the first findings of corrosion resistance and workability.
  • the content is made 0.6% or more to achieve the above effects.
  • a content exceeding 3% leads to a rise in material costs and makes it difficult to achieve effects that match the costs. Therefore, when adding it, its content is 3% or less.
  • the content is preferably 0.7 to 2.8%, more preferably 0.9 to 2.0%.
  • Cu like Mn and Ni, is an austenite forming element and is effective in securing mainly the objects of the first findings of corrosion resistance and workability. Particularly, it is an element effective in improving corrosion resistance added in combination with Ni. When adding it, it is made 0.1% or more to obtain the above effect added in combination with Ni. A content exceeding 3% leads to a rise in material costs and makes it difficult to achieve effects that match the costs. Therefore, when adding it, the content is made 3% or less. From the viewpoints of corrosion resistance, workability, and economy, the content is preferably 0.3 to 1%, more preferably 0.4 to 0.6%.
  • Mo can be appropriately added to improve the corrosion resistance. To obtain the above effect, addition of 0.2% or more is preferable. However, a content exceeding 1% sometimes detracts from the economy. Therefore, when adding it, the content is made 1% or less. From the viewpoints of corrosion resistance and economy, the content is preferably 0.2 to 0.8%.
  • Ti and Nb can be appropriately added to suppress sensitization due to C and N and thereby improve the corrosion resistance. To obtain the above effect, addition of 0.01% or more for each is preferable.
  • the content of each is respectively made 0.5% or less.
  • the content of each is more preferably 0.03 to 0.3%, further preferably 0.05 to 0.1%.
  • Al is a powerful deoxidizing agent and can be appropriately added. To obtain the above effect, addition of 0.001% or more is preferable. However, a content exceeding 0.2% sometimes is a factor in forming nitrides and causing surface damage and a drop in corrosion resistance. Therefore, when adding it, the content is made 0.2% or less. From the viewpoint of production and corrosion resistance, the content is more preferably 0.005 to 0.1%.
  • B, Ca, and Mg can be appropriately added to improve the hot workability.
  • addition for each of 0.0002% or more is preferable.
  • a content for each exceeding 0.01% sometimes causes the corrosion resistance to drop remarkably. Therefore, when adding these, the content for each is made 0.01% or less.
  • the content for each is more preferably 0.0005 to 0.005%.
  • the stainless steel according to the first findings may contain, other than the above ingredients, P and S as part of the unavoidable impurities in the ranges below.
  • P and S are elements harmful to hot workability and corrosion resistance.
  • the content of P is preferably 0.1% or less, more preferably 0.05% or less. Excessive reduction leads to an increase in refining and material costs, so the lower limit is preferably 0.005%.
  • the content of S is preferably 0.01% or less, more preferably 0.005% or less. Excessive reduction leads to an increase in refining and material costs, so the lower limit is preferably 0.0005%.
  • the ferritic-austenitic stainless steel according to the first findings has the above ingredients and is improved in corrosion resistance and workability by having a defined volume fraction of the austenite phase (hereinafter, " ⁇ fraction") .
  • the ⁇ fraction can be found by the EBSP method.
  • the EBSP method as for example described in Microscopy; Seiichi Suzuki, Vol. 39, No. 2, 121 to 124 , designates the crystal system data of the austenite phase (fcc) and ferrite phase (bcc) and displays a phase distribution map in which a color is given to each phase. Due to this, the state of dispersion of the austenite phase can be understood and the ⁇ fraction found.
  • the test piece is a sheet cross-section, and measurement is at a magnification of 500X and step size of 10 ⁇ m.
  • the upper limit of the ⁇ fraction is made 50% or less to secure the object of the first findings mentioned above of corrosion resistance.
  • the lower limit of the ⁇ fraction is made 15% or more, more preferably 20% or more.
  • the content is more preferably 30 to 40% in range.
  • the state of dispersion of the austenite phase is not particularly defined, but from the viewpoint of improving the uniform elongation of the material, it is preferable that, rather than have a ferritic-austenitic phase layer-type structure, the ferrite phase be made the matrix phase and 100 ⁇ m elliptic to circular austenite phases be dispersed, more preferably austenite phases less than 50 ⁇ m be dispersed.
  • the ferritic-austenitic stainless steel having the ingredients of the first findings and the above metal structure can have a pitting potential, an indicator of the corrosion resistance, of 0.3V or more and a uniform elongation, an indicator of the workability, increased from 30% to 50% and can give a corrosion resistance in a neutral chloride environment equal to or greater than SUS 304 and a workability significantly higher than SUS 430LX and close to SUS 304.
  • the measurement conditions of the pitting potential and uniform elongation are similar to those mentioned above and are as follows. For the pitting potential, Vc'100 (Vv.s.AGCL) was measured on a #500 polished surface as the evaluation surface in a 30°C, 3.5% NaCl aqueous solution.
  • the measurement value of the pitting potential was made the average value of n3.
  • a tensile test piece was taken from the rolling direction and the uniform elongation until necking occurred was measured at a tension rate of 20 mm/min (range of tension rate specified in JIS Z 2241).
  • the hot rolled steel material used for production is not particularly limited so long as it has the above ingredients.
  • the final annealing following the cold working comprises heating and holding at 950 to 1150°C. When less than 950°C, recrystallization of the worked structure sometimes is insufficient. When over 1150°C, the grain size becomes larger and sometimes the structure becomes not a ferritic-austenitic phase layer-type structure, but one greatly deviating from the preferred one where the ferrite phase is the matrix phase and elliptical to circular austenite phases less than 100 ⁇ m are dispersed. Further, sometimes the ⁇ fraction decreases and good elongation is not able to be obtained. To obtain a preferable structure for achieving corrosion resistance and workability, the range is more preferably 980 to 1100°C, further preferably 980 to 1050°C.
  • the cooling following the final annealing not part of the present invention is performed at an average cooling rate from the heating temperature to 200°C of 3°C/sec or more. When less than 3°C/sec, the corrosion resistance drops due to the sensitization based on grain boundary precipitation of Cr nitrides.
  • the upper limit of the cooling rate is not particularly defined, but in the case of gas cooling, it is approximately 50°C/sec. In the case of water cooling, it is 300 to 500°C/sec.
  • the rate is preferably 10 to 40°C/sec, more preferably 25 to 35°C/sec.
  • the steel material is hold at a 200 to 600°C temperature region for 1 minute or more.
  • the N present in an oversaturated state near the crystal grain boundaries diffusing into the austenite phase with its large solid solubility limit and forming a solid solution t the time of holding at that temperature region, the grain boundary precipitation of Cr nitrides leading to a drop in pitting potential is suppressed. That is, the drop in the corrosion resistance caused by sensitization can be suppressed.
  • the upper limit is made 600°C. If less than 200°C, N diffusion will take a long time, making achievement of the above effect difficult. Therefore, the lower limit is made 200°C, more preferably in the range of 300 to 550°C, further preferably 400 to 550°C.
  • the holding time is made 1 minute or more in order to obtain above effect.
  • the upper limit is not particularly defined, but when using an industrial continuous annealing facility, a long holding time leads to a drop in productivity, so the time is preferably 5 minutes or less, more preferably 3 minutes or less.
  • ferritic-austenitic stainless steel excellent in corrosion resistance and workability having a ferrite phase as the matrix phase, having a volume fraction of an austenite phase of 15 to 50%, having a pitting potential Vc'100 of 0.3V (Vv.s.AGCL) or more in a 30°C, 3.5% NaCl aqueous solution, and having a uniform elongation in a tensile test of 30% or more.
  • the C is an element having a large effect on the stability of the austenite phase.
  • the upper limit was made 0.100%.
  • the lower the C the more preferable, however, if taking the ability of current facilities into consideration, lowering the amount of C to less than 0.002% would lead to a large increase in costs, so the lower limit is preferably this value, more preferably 0.002 to 0.8%.
  • Si is used as a deoxidizing element and sometimes is added to improve the oxidation resistance.
  • the upper limit is preferably this value, more preferably 1.6% or less.
  • the lower limit was made 0.05, preferably 0.08%.
  • Mn concentrates at the austenite phase and has an important role in changing the stability of the austenite phase.
  • the upper limit was made 5.00%. Less than 0.05% causes an increase in costs in the refining process, so this value was made the lower limit. From the viewpoint of corrosion resistance, a lower value is preferable, so the upper limit is more preferably 3.00%, further preferably 2.80%.
  • P is an element which is unavoidably included. Further, it is contained in Cr and other materials. Therefore, reducing it is difficult, however, if a large amount is contained, it causes the workability to drop, so the upper limit was made less than 0.050%. However, the lower it is, the more preferable, so making it 0.035% or less is preferable.
  • S is an element which is unavoidably included. It bonds with Mn to form inclusions and sometimes becomes the starting point of rust, therefore the upper limit was made less than 0.010%. The lower it is, the more preferable from the viewpoint of corrosion resistance, so making it 0.0020% or less is preferable.
  • Cr is an element necessary for securing the corrosion resistance. An addition of 17% or more is necessary. However, large addition causes hot working cracks and leads to an increase in refining process costs, so the upper limit was made 25%, preferably 17 to 22%.
  • N is an element having a large effect on the stability of the austenite phase. Further, if existing in a solid solution, it has the effect of improving corrosion resistance, so 0.010 or more is added. However, if over 0.150% is added, sometimes the uniform elongation will drop. Also, Cr nitrides will precipitate easily and cause the corrosion resistance to conversely drop. Therefore, the upper limit was made this value, preferably 0.03 to 0.13%.
  • Ni is an austenite stabilizing element and is important for adjusting the stability of the austenite phase. Further, it has the effect of suppressing hot working cracks, so when wishing to obtain these effects, 0.10% or more may be added. Addition over 5.00% causes an increase in material costs and, further, sometimes makes achievement of an austenitic-ferritic two-phase structure difficult, so the upper limit was made this value, preferably 3.00% or less.
  • Cu like Ni, is an austenite stabilizing element and is important for adjusting the stability of the austenite phase. Further, it has the effect of improving corrosion resistance, so 0.10% or more may be added. However, addition over 5.00% promotes cracks during hot working and, further, lowers the corrosion resistance, so the upper limit was made this value.
  • Mo is an element improving corrosion resistance, so may be selectively added. Addition of 0.10% or more enables the effect of improving corrosion resistance to be obtained, so addition of this value or more is preferable. However, addition over 5.00% lowers the uniform elongation and greatly increases the material costs, so the upper limit was made this value.
  • Nb has the effect of preventing coarsening of the weld heat affected zone, so to obtain good effects even when added, addition of 0.03% or more is required. This therefore may be added with the lower limit as this value. However, addition over 0.50% lowers the uniform elongation, so the upper limit was made this value.
  • Ti like Nb, may be added in 0.03% or more so as to prevent coarsening of the weld heat affected zone and further make the solidified structure finer equiaxial crystalline. However, addition over 0.50% lowers the uniform elongation, so the upper limit was made this value.
  • Mg has an effect of not only deoxidation, but also making the solidified structure finer and therefore is sometimes added. To obtain these effects, addition of 0.0002% or more is necessary, so this may be added with the lower limit as this value. Further, addition over 0.0030% causes an increase in costs in the steelmaking process, so the upper limit was made this value.
  • volume fraction of austenite phase of 10% to less than 50% As shown by the results of the study above, to obtain a good uniform elongation, a ratio of austenite phase of 10% or more is required, so the lower limit was made this value. Further, the uniform elongation does not necessarily become higher the higher the austenite fraction. If over 50%, the uniform elongation conversely drops, so the upper limit was made this value. It is preferable to measure the austenite fraction with a method classifying phases using EBSP, extracting only the austenite grains, then measuring the area ratio. The measurement range at this time is 200 ⁇ m ⁇ 200 ⁇ m or more.
  • the austenite fraction is important as an indicator of workability (uniform elongation).
  • the reasons for this are thought to be as follows.
  • the austenite phase causes work-induced martensite transformation during work and contributes to an increase in the uniform elongation. If the amount transformed at this time is small, the uniform elongation becomes smaller. Further, the reason why the uniform elongation is low when the austenite fraction is over 50% is not currently clear, but it is believed that it is because deformation concentrates in the ferrite phase which is softer in comparison to the austenite phase.
  • the chemical composition in the austenite phase forming the basis of the calculation of the Md is measured by EPMA.
  • [ ] in the above Md formula shows the composition (mass%) in the austenite phase measured by EPMA for each element.
  • the average composition (mass%) is shown.
  • the Md value is an indicator representing the stability of the austenite phase, that is, it can be said to represent the amount of strain needed to cause work-induced martensite transformation. If the amount of strain is too small, work-induced martensite transformation finishes at the initial steps of working and sufficient ductility cannot be maintained at the later steps of working important for determining success of working. Further, if the amount of strain is too large, uniform deformation finishes before reaching that amount of strain and work-induced martensite transformation cannot be applied effectively. Therefore, there is a suitable range of Md value for generating work-induced martensite transformation during work.
  • Ratio of austenite grains with a grain size of 15 ⁇ m or less and a shape aspect ratio of less than 3 accounting for 90% or more of the total number of austenite grains As metal structural features of the austenite grains when good uniform elongation is obtained, the grains are fine and not flattened in the rolling direction. Specifically, the ratio of austenite grains with a grain size of 15 ⁇ m or less and a shape aspect ratio of less than 3 account for 90% or more of the total number of austenite grains. When there are many crystal grains with a grain size over 15 ⁇ m, the uniform elongation drops, so the upper limit was made this value. Further, it is not particularly necessary to define the lower limit, however, making it 1 ⁇ m or less greatly increases costs in the production process, so the lower limit is preferably made 1 ⁇ m.
  • the shape of crystal grains is also an important factor.
  • the aspect ratio of each grain was measured.
  • the ratio of crystal grains with an aspect ratio of less than 3 becomes important.
  • the condition of the aspect ratio defined as a structural factor was made less than 3.
  • the aspect ratio is measured by dividing the length of the longest side of each grain by the length orthogonal to it. Therefore, the lower limit of the aspect ratio is 1.
  • the number of crystal grains for measuring the grain size and aspect ratio is 100 or more.
  • austenite grain size and grain shape affect the uniform elongation, but the reasons for this are currently unknown. However, it is believed that there have an effect on the mode of deformation in the austenite grains (dislocation density, deformation zone, twinning presence, etc.) and that this changes the work-induced martensite transformation behavior.
  • Average distance between nearest austenite grains of 12 ⁇ m or less The distance between nearest austenite grains also affects the uniform elongation, so the average distance was made 12 ⁇ m or less. If over 12 ⁇ m, the uniform elongation drops, so the upper limit was made this value. Further, the lower limit is not particularly defined.
  • the distance between nearest grains is determined by defining the point where the center line of the rolling direction length of each austenite grain intersects the center line of the sheet thickness direction length as the center position of a crystal grain and defining the smallest value of the distances between center positions of grains as the distance between nearest grains of that grain. The average of the results of measurements for 100 crystal grains or more is defined as the "average distance between nearest austenite grains".
  • the uniform elongation is an important indicator representing the workability in the present invention.
  • the uniform elongation is measured by taking a JIS 13 B tensile test piece parallel to the rolling direction and following the method based on JIS Z 2241.
  • the state of the ferrite grains is not particularly defined in the second findings, which are not part of the present invention, however, when the ferrite phase is coarse in grain size, the above distance between austenite grains becomes larger, so the grain size is preferably at average of 25 ⁇ m or less. Further, when the shape aspect ratio is large as well, the distance between austenite grains becomes large, so the ratio is preferably less than 3.
  • hot rolling material a steel slab obtained by continuous casting is used.
  • the heating temperature T1 before hot rolling is made 115C°C to less than 1250°C.
  • edge cracking occurs in hot rolling, so the lower limit was made this value.
  • the heating temperature is made over 1250°C, it is easy for the austenite grain size after final annealing to become larger, the steel slab deforms inside the heating furnace, and defects are likely to occur during hot rolling, so the upper limit was made this value.
  • the reduction rate and time between passes both greatly affect the recrystallization behavior, but to obtain austenite grains that are fine and have small aspect ratios after cold rolling and annealing, it is necessary for the reduction rate during hot rolling to be 30% or more and the holding time following it to be 30 sec or more.
  • the total rolling rate of hot rolling was made 96% or more.
  • the crystal grains after cold rolling and annealing become coarser.
  • the distance between austenite grains becomes larger, so the uniform elongation becomes insufficient.
  • the annealing temperature of the hot rolled sheet is between the heating temperature T1-100°C before hot rolling and T1°C.
  • T1-100°C the aspect ratio of the crystal grains after cold rolling and annealing becomes larger.
  • T1°C or more the grain size after cold rolling and annealing becomes coarser, the metal structure of the object is not obtained, and the uniform elongation during the tensile test drops.
  • the cold rolling and annealing may be repeatedly performed, i.e., so called two-time cold rolling may be performed. It is necessary to make the process annealing temperature at this time T1-100°C to T1°C in the same way as hot rolled sheet annealing.
  • the final annealing temperature is 1000°C to 1100°C. This is because when less than 1000°C, the shape aspect ratios of the austenite and ferrite grain become bigger, the Md value deviates from the appropriate range, and the uniform elongation drops. Further, when over 1100°C, the ⁇ fraction drops, the Md value deviates from the appropriate range, or the grain size becomes too large
  • Ferritic-austenitic stainless steel 250 mm thick cast slabs having the ingredients shown in Table 2 were produced and hot rolled into hot rolled steel plates with 5.0 mm plate thicknesses.
  • Steel No. 1 to Steel No. 23 have ingredients as defined in the present invention.
  • Steel No. 24 to 29 have ingredients deviating from the ingredients as defined in the present invention.
  • These hot rolled steel plates were annealed and pickled, then cold rolled to 1 mm thicknesses and final annealed. The final annealing was also performed under conditions deviating from the definitions of the present invention for comparison.
  • ⁇ phase volume fraction ( ⁇ fraction), pitting potential, and uniform elongation.
  • the ⁇ fraction was found by the EBSP method described in paragraph 0046.
  • the V'c100 (Vv.s.AGCL) was measured for a #500 polished surface in a 30°C, 3.5% NaCl aqueous solution.
  • the measurement value of the pitting potential was made the average value of n3.
  • a JIS 13 B test piece was taken from the rolling direction and the value was measured at a tension rate of 20 mm/min (range of the tension rate defined in JIS Z 2241).
  • the relationship of the production conditions and the ⁇ fraction and characteristics of the final annealed sheets are shown in Table 3.
  • the "Cooling rate 1" shows the average cooling rate from the annealing temperature to 200°C. However, when held during cooling, the average cooling rate from the annealing temperature to the holding temperature is shown. Further, the “Cooling rate 2" shows the average cooling rate from the holding temperature to ordinary temperature when holding during cooling.
  • Inventive Examples nos. 9 to 11 have the ingredients of the present invention and were final annealed as defined in the present invention. These inventive Examples satisfy the ⁇ fraction 15 to 50% defined in the present invention and have 0.3V or more pitting potentials and 30% or more uniform elongations. Due to this, by subjecting the ferritic-austenitic stainless steels having the ingredients defined in the present invention to the final annealing defined in the present invention, a corrosion resistance equal to or greater than SUS 304 in a neutral chloride environment is provided and a ductility sufficiently high compared to SUS 430LX and comparable to SUS 304 is obtained. Particularly, Nos.
  • 9 to 11 are examples in which, as the final annealing condition, the steels are held for approximately two minutes at a specified temperature of the 200 to 600°C temperature region with final annealing, then cooled from the holding temperature to room temperature.
  • the pitting potential Vc'100 shows good values.
  • Examples nos. 12 to 14 (not within the claims) have the ingredients defined in the present invention, but deviate from the final annealing conditions defined in the present invention. They did not give the pitting potential and uniform elongation of the objects of the present invention.
  • Comparative Examples nos. 36 to 41 have ingredients deviating from the definition of the present invention. Even if subjected to final annealing as shown in Table 3, they did not give the pitting potential and uniform elongation of the present invention.
  • the steels shown in Table 4 were produced, then were hot rolled, then the hot rolled plates were annealed, cold rolled, and final annealed to produce 1.0 mm thick thin-gauge steel sheets.
  • the metal structure can be changed by changing the material thickness, heating temperature of hot rolling, rolling pass schedule, rolling pass time, hot rolled sheet annealing temperature, and final annealing temperature and time. However, this time, the final annealing temperature was changed, and the annealing time was made 60 seconds.
  • the obtained product sheets were subjected to tensile tests and the uniform elongation was measured.
  • Condition 1a is an example where extremely good uniform elongation is obtained.
  • T2 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • condition 1c T1 does not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 2b is an example where extremely good uniform elongation is obtained.
  • T3 does not satisfy the second findings range, so the ⁇ fraction and X2 deviate from the second findings.
  • T3 does not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 3b is an example where extremely good uniform elongation is obtained.
  • N does not satisfy the second findings range, so X1 deviates from the second findings.
  • T1 and R do not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 4b is an example where extremely good uniform elongation is obtained.
  • T2 does not satisfy the second findings range, so X2 deviates from the second findings.
  • Condition 5a is an example where extremely good uniform elongation is obtained.
  • T2 and T3 do not satisfy the second findings range, so the ⁇ fraction and X1 deviate from the second findings.
  • T1 does not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 6b is an example where extremely good uniform elongation is obtained.
  • T2 and T3 do not satisfy the second findings range, so Md and X2 deviate from the second findings.
  • T3 does not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 7b is an example where extremely good uniform elongation is obtained.
  • N does not satisfy the second findings range, so X1 deviates from the second findings.
  • condition 8a T1, N, R, and T3 do not satisfy the second findings range, so the ⁇ fraction, Md, and X2 deviate from the second findings.
  • Condition 8b is an example where extremely good uniform elongation is obtained.
  • condition 8c T2 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • Condition 9a is an example where extremely good uniform elongation is obtained.
  • T2 does not satisfy the second findings range, so X1 deviates from the second findings.
  • T1 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • Condition 10b is an example where extremely good uniform elongation is obtained.
  • T3 does not satisfy the second findings range, so Md and X2 deviate from the second findings.
  • condition 11a T3 does not satisfy the second findings range, so ⁇ fraction and X1 deviate from the second findings.
  • Condition 11b is an example where extremely good uniform elongation is obtained.
  • condition 11c N does not satisfy the second findings range, so X1 deviates from the second findings.
  • condition 12a T1 and N do not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 12b is an example where extremely good uniform elongation is obtained.
  • condition 12c T2 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • Condition 13a is an example where extremely good uniform elongation is obtained.
  • T2 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • condition 13c T1 and N do not satisfy the second findings range, so X1 deviates from the second findings.
  • Condition 14a is an example where extremely good uniform elongation is obtained.
  • T2 does not satisfy the second findings range, so X1 and X2 deviate from the second findings.
  • condition 14c T1 does not satisfy the second findings range, so X1 deviates from the second findings.
  • ferritic-austenitic stainless steel excellent in corrosion resistance and workability having a corrosion resistance equal to or greater than SUS 304 in a neutral chloride environment can be produced.
  • ferritic-austenitic-based stainless thin-gauge steel sheet excellent in workability, particularly in uniform elongation, can be obtained without having to include a large amount of Ni.
  • the present invention can be applied to parts where conventionally austenitic stainless steel sheets containing large amounts of Ni have been used, for example, kitchen appliances, home electric appliances, electronic equipment, etc. used in a neutral chloride environment, and other broad fields, so from the viewpoint of Ni resource conservation, it greatly contributes to the environment.

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Claims (1)

  1. Procédé de production d'un acier inoxydable austéno-ferritique d'excellente résistance à la corrosion et d'excellente transformabilité, comprenant
    le forgeage à chaud ou le laminage à chaud d'un lingot d'acier inoxydable ayant des composés d'acier constitués, en % en poids, de
    C : de 0,001 à 0,1 %,
    Cr : de 17 à 25 %,
    Si : de 0,05 à 1 %,
    Mn : de 0,5 à 3,7 %, et
    N : de 0,06 % à moins de 0,15 %,
    éventuellement, à la fois de
    Ni : de 0,6 à 3 % et
    Cu : de 0,1 à 3 %, et
    en outre éventuellement de un ou plusieurs des suivants :
    Mo : 1 % ou moins,
    Nb : 0,5 % ou moins,
    Ti : 0,5 % ou moins,
    Al : 0,1 % ou moins,
    B : 0,01 % ou moins,
    Ca : 0,01 % ou moins,
    Mg : 0,01 % ou moins,
    P : 0,1 % ou moins, et
    S : 0,01 % ou moins ;
    le reste étant du Fe et d'inévitables impuretés, et
    ayant un indicateur de piqûre (valeur PI) représenté par la formule (a) suivante supérieur à 18 %, Indicateur de piqûre valeur PI = Cr + 3 Mo + 10 N − Mn
    Figure imgb0012
    pour obtenir un matériau d'acier laminé à chaud, le recuit du matériau d'acier laminé à chaud, et
    ensuite la répétition de l'usinage à froid et du recuit, ledit procédé de production d'un matériau d'acier étant caractérisé par
    la mise en oeuvre du recuit final par chauffage et maintien du matériau de 950 à 1150°C,
    puis le passage à une vitesse de refroidissement moyenne jusqu'à 600°C de 3°C/s ou plus,
    le maintien du matériau dans une région de températures de 200 à 600°C pendant 1 minute ou plus, et
    ensuite le passage à la vitesse de refroidissement moyenne de la température de maintien à la température ambiante de 3°C/s ou plus,
    pour obtenir une phase matricielle de type phase ferritique et obtenir une fraction en volume de phase austénitique de 15 à 50 %.
EP08792317.3A 2007-08-02 2008-08-01 Acier inoxydable austénoferritique d'excellente résistance à la corrosion et transformabilité, et procédé pour la fabrication dudit Active EP2172574B1 (fr)

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ES2717840T3 (es) 2019-06-25
EP2172574A1 (fr) 2010-04-07
EP2172574A4 (fr) 2017-06-07
EP3434802B1 (fr) 2020-07-01
US20130118650A1 (en) 2013-05-16
KR101253326B1 (ko) 2013-04-11
KR20100011989A (ko) 2010-02-03
WO2009017258A1 (fr) 2009-02-05
CN101765671A (zh) 2010-06-30
KR101185978B1 (ko) 2012-09-26
CN101765671B (zh) 2012-01-11
ES2817436T3 (es) 2021-04-07
US20100126644A1 (en) 2010-05-27
EP3434802A1 (fr) 2019-01-30

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