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WO2019059095A1 - Tôle d'acier, et procédé de fabrication de celle-ci - Google Patents

Tôle d'acier, et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2019059095A1
WO2019059095A1 PCT/JP2018/034011 JP2018034011W WO2019059095A1 WO 2019059095 A1 WO2019059095 A1 WO 2019059095A1 JP 2018034011 W JP2018034011 W JP 2018034011W WO 2019059095 A1 WO2019059095 A1 WO 2019059095A1
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WO
WIPO (PCT)
Prior art keywords
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steel
steel plate
amount
component composition
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.)
Ceased
Application number
PCT/JP2018/034011
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English (en)
Japanese (ja)
Inventor
茂樹 木津谷
博司 池田
植田　圭治
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.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
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 JFE Steel Corp filed Critical JFE Steel Corp
Priority to KR1020207007547A priority Critical patent/KR102363482B1/ko
Priority to SG11202002379QA priority patent/SG11202002379QA/en
Priority to MYPI2020001389A priority patent/MY193070A/en
Priority to EP18858881.8A priority patent/EP3686306B1/fr
Priority to JP2019502271A priority patent/JP6760476B2/ja
Priority to CN201880060450.6A priority patent/CN111108225B/zh
Publication of WO2019059095A1 publication Critical patent/WO2019059095A1/fr
Priority to PH12020550108A priority patent/PH12020550108A1/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/0247—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
    • 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
    • C21D8/0273—Final recrystallisation annealing
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a steel plate suitable for structural steel used in a cryogenic environment such as a tank for liquefied gas storage, in particular, a steel plate excellent in corrosion resistance in a saltwater corrosive environment, and a method of manufacturing the same.
  • the hot rolled steel sheet When the hot rolled steel sheet is provided to the structure for liquefied gas storage, the use environment becomes extremely low temperature, so the hot rolled steel sheet is required to have not only strength but also toughness at very low temperature.
  • a hot-rolled steel plate used for storage of liquefied natural gas needs to secure excellent toughness at -164 ° C. or less, which is the boiling point of liquefied natural gas. If the low temperature toughness of the steel material is poor, there is a risk that the safety as a cryogenic storage tank structure can not be maintained, so there is a strong demand for improvement of the low temperature toughness of the steel material to be applied.
  • Patent Document 1 by adding 15 to 35% of Mn, 5% or less of Cu, and an appropriate amount of C and Cr, the machinability and Charpy impact characteristics at -196 ° C of the heat-of-heat affected zone Steel materials with improved are disclosed.
  • Patent Document 2 C: 0.25 to 0.75%, Si: 0.05 to 1.0%, Mn: more than 20% and 35% or less, Ni: 0.1% or more and 7.0%
  • a high-Mn steel material is disclosed in which the low-temperature toughness is improved by adding less than 0.1% of Cr and less than 8.0%.
  • Patent Document 3 contains 0.001 to 0.80% of C, 15 to 35% of Mn, and the elements such as Cr, Ti, Si, Al, Mg, Ca, and REM are added to the mother material.
  • a high Mn steel is disclosed that improves the cryogenic toughness and properties of the material and welds.
  • Patent Literatures 1, 2 and 3 are from the viewpoint of manufacturing cost to achieve strength and low temperature toughness and from the viewpoint of corrosion resistance when the austenitic steel described above is placed in a salty corrosion environment, There is still room for consideration.
  • An object of the present invention is to provide a high Mn steel excellent in corrosion resistance, particularly in a salt corrosion environment, in view of the problems.
  • the present inventors conducted intensive studies on various factors that determine the component composition and manufacturing conditions for high-Mn steel in order to achieve the above problems, and reached the following findings. .
  • P is an element which is likely to segregate with Mn in the solidification process of the billet and lowers the grain boundary strength of the portion intersecting with such a segregated portion. Therefore, it is necessary to reduce impurity elements such as P.
  • the present invention has been made by further examining the above findings, and the summary thereof is as follows. 1. In mass%, C: 0.20% or more and 0.70% or less, Si: 0.05% or more and 1.00% or less, Mn: 15.0% to 35.0%, P: 0.030% or less, S: 0.0200% or less, Al: 0.010% or more and 0.100% or less, Cr: 0.5% or more and 8.0% or less and N: 0.0010% or more and 0.0300% or less, and has a component composition of the balance Fe and unavoidable impurities, and 60% or more of the contained Cr Steel plate which is solid solution Cr.
  • the above component composition is, further, in mass%, Nb: 0.003% or more and 0.030% or less,
  • the above component composition is, further, in mass%, Cu: 0.01% or more and 0.50% or less, Ni: 0.01% or more and 0.50% or less, Sn: 0.01% or more and 0.30% or less, Sb: 0.01% or more and 0.30% or less, Mo: 0.01% or more and 2.0% or less and W: 0.01% or more and 2.0% or less.
  • Cu 0.01% or more and 0.50% or less
  • Ni 0.01% or more and 0.50% or less
  • Sn 0.01% or more and 0.30% or less
  • Sb 0.01% or more and 0.30% or less
  • Mo 0.01% or more and 2.0% or less
  • W 0.01% or more and 2.0% or less
  • the above component composition is, further, in mass%, Ca: 0.0005% or more and 0.0050% or less,
  • the steel sheet according to the above 1, 2 or 3 containing one or more selected from Mg: 0.0005% or more and 0.0100% or less and REM: 0.0010% or more and 0.0200% or less.
  • “excellent in corrosion resistance” is a test based on the Slow Strain Rate Test Method based on NACE Standard TM0111-2011, and is immersed in artificial seawater (chloride ion concentration 18000 ppm) at a temperature of 23 ° C. Strain rate: It means that the breaking stress is 400 MPa or more when the constant velocity tension test is performed at 4 ⁇ 10 ⁇ 7 inch / s.
  • the steel plate excellent in corrosion resistance, especially corrosion resistance in a salt corrosion environment can be provided. Therefore, by using the steel plate of the present invention for a steel structure used in a cryogenic environment, such as a tank for liquefied gas storage tank, for example, the safety and the life of the steel structure are greatly improved. Will bring about the effects of Moreover, since the steel plate of this invention is cheap compared with the existing material, it also has the advantage which is excellent in economical efficiency.
  • C 0.20% or more and 0.70% or less C is effective for increasing the strength, and is an inexpensive austenite stabilizing element and an important element for obtaining austenite. In order to obtain the effect, C needs to contain 0.20% or more. On the other hand, if the content exceeds 0.70%, excessive precipitation of Cr carbide and Nb, V, Ti carbides is promoted, so the low temperature toughness decreases and it becomes a starting point of occurrence of corrosion. Therefore, C is set to 0.20% or more and 0.70% or less. Preferably, it is 0.25% or more and 0.60% or less.
  • Si acts as a deoxidizing material and is not only necessary for steel making, but also has the effect of making a solid solution in steel and strengthening the steel plate by solid solution strengthening. Have. In order to obtain such an effect, Si needs to be contained 0.05% or more. On the other hand, if the content is more than 1.00%, the weldability and the surface properties may be deteriorated and the stress corrosion cracking resistance may be reduced. Therefore, Si is set to 0.05% or more and 1.00% or less. Preferably, it is 0.07% or more and 0.50% or less.
  • Mn 15.0% to 35.0%
  • Mn is a relatively inexpensive austenite stabilizing element. In the present invention, it is an important element to achieve both strength and cryogenic toughness. In order to obtain the effect, Mn needs to contain 15.0% or more. On the other hand, when the content exceeds 35.0%, the effect of improving the cryogenic toughness saturates, resulting in an increase in alloy cost. In addition, weldability and cuttability are degraded. Furthermore, it promotes segregation and promotes the occurrence of stress corrosion cracking. Therefore, the Mn content is 15.0% or more and 35.0% or less. Preferably, it is in the range of 18.0% or more and 28.0%.
  • P 0.030% or less
  • P When P is contained in excess of 0.030%, it segregates at grain boundaries to lower the grain boundary strength, and becomes a generation origin of stress corrosion cracking. For this reason, it is desirable to make it as upper limit 0.030%, and to reduce as much as possible.
  • steelmaking requires much cost and the economy is impaired, so the content of 0.001% or more is acceptable.
  • S degrades the low temperature toughness and ductility of the base material, so the upper limit of 0.0200% is desirable, and it is desirable to reduce as much as possible. Therefore, S is 0.0200% or less, preferably 0.0180% or less. On the other hand, in order to make it less than 0.0001%, steelmaking requires much cost and the economy is lost, so the content of 0.0001% or more is acceptable.
  • Al acts as a deoxidizer, and is most widely used in the molten steel deoxidation process of steel sheet.
  • solid solution N in steel is fixed to form AlN, which has the effect of suppressing coarsening of crystal grains. At the same time, it has an effect of suppressing the deterioration of toughness due to the reduction of solid solution N.
  • Al needs to contain 0.010% or more.
  • the content is more than 0.100%, coarse nitrides may be formed to be a starting point of corrosion or fracture, and stress corrosion cracking resistance may be reduced.
  • it in order to diffuse to a weld metal part at the time of welding and to deteriorate the toughness of a weld metal, it makes it 0.100% or less.
  • it is 0.020% or more and 0.070% or less.
  • Cr Cr 0.5% or more and 8.0% or less and 60% or more of contained Cr is solid solution
  • Cr Cr has the effect of delaying the initial corrosion reaction on the surface of the steel sheet in a saltwater corrosion environment by containing an appropriate amount of content, and this effect is important to reduce the amount of hydrogen penetration into the steel sheet and to improve stress corrosion cracking resistance Element.
  • the corrosion resistance can be improved by increasing the amount of Cr, it can not be avoided that Cr precipitates in the form of nitride, carbide, carbonitride, etc. during rolling, and such precipitates
  • the stress corrosion cracking resistance may be lowered as a starting point of corrosion or destruction. Therefore, the amount of Cr is set to 0.5% or more and 8.0% or less.
  • the amount of solid solution of Cr is important, and Cr is It turned out that it exhibits reliably when 0.3% or more exists in a solid solution state.
  • the lower limit of the solid solution ratio of Cr which can be stably secured by a small change of production conditions is 60%.
  • a Cr content of at least 0.5% is required.
  • the amount of solid solution Cr is preferably 1.0% or more and 6.0% or less, more preferably 1.2% or more and 5.5% or less.
  • the solid solution state is a state in which solute atoms exist as atoms without forming precipitates and the like.
  • N is an austenite stabilizing element and is an element effective for improving the cryogenic toughness. In addition, it combines with Nb, V, and Ti, precipitates finely as nitride or carbonitride, and has an effect of suppressing stress corrosion cracking as a trap site of diffusible hydrogen. In order to obtain such an effect, N needs to contain 0.0010% or more.
  • N is set to 0.0010% or more and 0.0300% or less. Preferably, it is 0.0020% or more and 0.0150% or less.
  • Nb 0.003% or more and 0.030% or less
  • V 0.01% or more and 0.10% or less
  • Ti 0.003% or more and 0.040% or less
  • Nb is an element having an effect of suppressing stress corrosion cracking because it is precipitated as a carbonitride and the generated carbonitride functions as a trap site for diffusible hydrogen. . In order to acquire such an effect, it is preferable to contain Nb at 0.003% or more. On the other hand, if the content is more than 0.030%, coarse carbonitrides may be precipitated to be the starting point of destruction. In addition, the precipitate may be coarsened to deteriorate the base material toughness. For this reason, when it contains Nb, it is preferable to set it as 0.003% or more and 0.030% or less. More preferably, it is 0.005% or more and 0.025% or less, and further preferably 0.007% or more and 0.022% or less.
  • V 0.01% or more and 0.10% or less
  • V is an element having an effect of suppressing stress corrosion cracking because it is precipitated as a carbonitride and the produced carbonitride functions as a trap site for diffusible hydrogen. .
  • V it is preferable to contain V by 0.01% or more.
  • the content is more than 0.10%, coarse carbonitrides may be precipitated to be a starting point of destruction.
  • the precipitate may be coarsened to deteriorate the base material toughness.
  • V it is preferable to set it as 0.01% or more and 0.10% or less. More preferably, it is 0.02% or more and 0.09% or less, and further preferably 0.03% or more and 0.08% or less.
  • Ti 0.003% or more and 0.040% or less Ti is precipitated as a nitride or carbonitride, and the formed nitride or carbonitride functions as a trap site for diffusible hydrogen, so stress corrosion cracking is suppressed. It is an element having an effect. In order to acquire such an effect, it is preferable to contain Ti by 0.003% or more. On the other hand, if the content exceeds 0.040%, the precipitates may be coarsened to deteriorate the base material toughness. In addition, coarse carbonitrides may be precipitated to be the starting point of destruction. For this reason, when it contains Ti, it is preferable to set it as 0.003% or more and 0.040% or less. More preferably, they are 0.005% or more and 0.035% or less, and more preferably 0.007% or more and 0.032% or less.
  • Cu 0.01% to 0.50%
  • Ni 0.01% to 0.50%
  • Sn 0.01% to 0.30%
  • Sb 0.01% to 0.30%
  • Mo 0.01% or more and 2.0% or less
  • W 0.01% or more and 2.0% or less may be contained alone or in combination of two or more.
  • Cu, Ni, Sn, Sb, Mo and W are elements that improve the corrosion resistance of a high Mn steel in a saltwater corrosive environment by complex addition with Cr.
  • Cu, Sn and Sb have the effect of suppressing the hydrogen generation reaction which is the cathode reaction by increasing the hydrogen overvoltage of the steel material.
  • Ni forms a precipitate coating on the steel material surface, Cl - physically inhibit the transmission of the corrosive anions such as base steel.
  • Cu, Ni, Sn, Sb, Mo and W are released as metal ions from the surface of the steel during corrosion, and by densifying the corrosion product, the steel interface (the interface between the rust layer and the base iron) Inhibit permeation of corrosive anions.
  • Mo and W are released as Mo 4 2- and WO 4 2- , respectively, and adsorbed in the corrosion product or on the surface of the steel sheet to give cation selective permeability, and the permeation of corrosive anions to ground iron To suppress.
  • the amount of Cu is in the range of 0.01% to 0.50%
  • the amount of Ni is in the range of 0.01% to 0.50%
  • the amount of Sn is in the range of 0.01% to 0.30%
  • the amount of Sb is in the range of 0.01% to 0.30%
  • the amount of Mo is in the range of 0.01% to 2.0%
  • the amount of W is in the range of 0.01% to 2.0%. Is preferred.
  • the amount of Cu is 0.02% or more and 0.40% or less
  • the amount of Ni is 0.02% or more and 0.40% or less
  • the amount of Sn is 0.02% or more and 0.25% or less
  • the amount of Sb is 0 .02% or more and 0.25% or less
  • Mo content is 0.02% or more and 1.9% or less
  • W content is 0.02% or more and 1.9% or less.
  • Ca, Mg and REM are elements useful for controlling the form of inclusions and can be contained as necessary.
  • the control of the form of inclusions means that the spread sulfide-based inclusions are made into particulate inclusions. The ductility, toughness and resistance to sulfide stress corrosion cracking are improved through shape control of the inclusions.
  • the amount of Ca is 0.0010% to 0.0040%
  • the amount of Mg is 0.0010% to 0.0040%
  • the amount of REM is 0.0020% to 0.0150%.
  • the temperature means the temperature at the thickness center of the steel plate.
  • the reason for heating the steel material to 1000 ° C. or higher is to dissolve carbonitrides in the structure so as to make the crystal grain size etc. uniform. That is, when the heating temperature is less than 1000 ° C., desired characteristics can not be obtained because the carbonitrides do not sufficiently form a solid solution.
  • heating in excess of 1300 ° C. requires excessive energy in addition to material deterioration due to coarsening of the crystal grain size, and productivity decreases, so the upper limit of the heating temperature is 1300 ° C.
  • the temperature is in the range of 1050 ° C. to 1250 ° C., and more preferably in the range of 1070 ° C. to 1250 ° C.
  • the reduction ratio in hot rolling is limited to 3 or more.
  • the upper limit needs to be 30 for the reason described later.
  • the reduction ratio is defined by the thickness of the material to be rolled / the thickness of the steel plate after rolling.
  • Rolling finish temperature 750 ° C or higher
  • the rolling finishing temperature is less than 750 ° C.
  • the amount of precipitated carbide during rolling significantly increases, and even if the staying time at 600 ° C. or more and 950 ° C. or less is 30 minutes or less, the amount of solid solution Cr may not be secured. descend.
  • the rolling finish temperature is set to 750 ° C. or higher.
  • the upper limit is preferably 1050 ° C. or less from the viewpoint of suppressing significant coarsening of crystal grains.
  • the length of the material to be rolled is 5000 mm or less, and the reduction ratio from the material to be rolled is 30 or less as described above. limit.
  • the rolling time becomes long, and as a result, the staying time in the range of 950 ° C. or less and 600 ° C. or more exceeds 30 minutes.
  • Average cooling rate at 700 ° C. or less and 600 ° C. or more 3 ° C./s or more
  • the average cooling rate at 700 ° C. or less and 600 ° C. or more is less than 3 ° C./s, a large amount of precipitates such as Cr carbides are formed, so the average cooling rate is limited to 3 ° C./s or more.
  • it is so good that average cooling rate is quick it is not necessary to provide the upper limit.
  • the No. 1 to 28 steels shown in Table 1 are melted and made into slabs, and the steel plates of 6 mm to 50 mm in thickness are manufactured according to the manufacturing conditions shown in Table 2 and the thick steel plates of sample Nos. 1 to 34 are manufactured. And subjected to the following test.
  • the corrosion resistance test was performed in accordance with the SlowStrain Rate Test Method (hereinafter, SSRT test) according to NACE Standard TM0111-2011.
  • the specimen shape was immersed in artificial seawater (chloride ion concentration: 18000 ppm) at a temperature of 23 ° C. using a Type A round bar-notched specimen, and an isochronous tensile test was performed at a strain rate of 4 ⁇ 10 ⁇ 7 inch / s. .
  • the breaking stress of 400 MPa or more is excellent in stress corrosion cracking resistance.
  • Table 2 The results obtained by the above are shown in Table 2.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Chemical Treatment Of Metals (AREA)

Abstract

L'invention fournit un acier riche en Mn qui présente une excellente résistance à la corrosion, tout particulièrement dans un environnement soumis à la corrosion par le sel. Plus précisément, l'objet de l'invention possède une composition qui comprend Ｃ：０,２０％ ou plus à ０,７０％ ou moins, Ｓｉ：０,０５％ ou plus à １,００％ ou moins, Ｍｎ：１５,０％ ou plus à ３５,０％ ou moins, Ｐ：０,０３０％ ou moins, Ｓ：０,０２００％ ou moins, Ａｌ：０,０１０％ ou plus à ０,１００％ ou moins, Ｃｒ：０,５％ ou plus à ８,０％ ou moins et Ｎ：０,００１０％ ou plus à ０,０３００％ ou moins, le reste étant constitué de Fe et des impuretés inévitables, et 60% ou plus de la teneur en Cr consistant en un Cr en solution.
PCT/JP2018/034011 2017-09-20 2018-09-13 Tôle d'acier, et procédé de fabrication de celle-ci Ceased WO2019059095A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
KR1020207007547A KR102363482B1 (ko) 2017-09-20 2018-09-13 강판 및 그 제조 방법
SG11202002379QA SG11202002379QA (en) 2017-09-20 2018-09-13 Steel plate and method for manufacturing same
MYPI2020001389A MY193070A (en) 2017-09-20 2018-09-13 Steel plate and method for manufacturing same
EP18858881.8A EP3686306B1 (fr) 2017-09-20 2018-09-13 Tôle d'acier, et procédé de fabrication de celle-ci
JP2019502271A JP6760476B2 (ja) 2017-09-20 2018-09-13 鋼板およびその製造方法
CN201880060450.6A CN111108225B (zh) 2017-09-20 2018-09-13 钢板及其制造方法
PH12020550108A PH12020550108A1 (en) 2017-09-20 2020-03-19 Steel plate and method for manufacturing same

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JP2022505582A (ja) * 2018-10-25 2022-01-14 ポスコ 耐腐食性に優れた極低温用オーステナイト系高マンガン鋼材及びその製造方法

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CN116981539A (zh) * 2021-03-01 2023-10-31 杰富意钢铁株式会社 Tig焊接头

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JPWO2020036090A1 (ja) * 2018-08-15 2020-08-20 Ｊｆｅスチール株式会社 鋼板およびその製造方法
JP2022505582A (ja) * 2018-10-25 2022-01-14 ポスコ 耐腐食性に優れた極低温用オーステナイト系高マンガン鋼材及びその製造方法
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KR20200041938A (ko) 2020-04-22
SG11202002379QA (en) 2020-04-29
EP3686306A1 (fr) 2020-07-29
PH12020550108A1 (en) 2020-12-07
KR102363482B1 (ko) 2022-02-15
CN111108225B (zh) 2021-09-24
EP3686306B1 (fr) 2024-02-28
JPWO2019059095A1 (ja) 2019-11-14

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