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WO2011152475A1 - Tôle d'acier inoxydable de construction ayant une excellente résistance à la corrosion dans la partie soudée, et son procédé de production - Google Patents

Tôle d'acier inoxydable de construction ayant une excellente résistance à la corrosion dans la partie soudée, et son procédé de production Download PDF

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Publication number
WO2011152475A1
WO2011152475A1 PCT/JP2011/062640 JP2011062640W WO2011152475A1 WO 2011152475 A1 WO2011152475 A1 WO 2011152475A1 JP 2011062640 W JP2011062640 W JP 2011062640W WO 2011152475 A1 WO2011152475 A1 WO 2011152475A1
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value
stainless steel
mass
steel sheet
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PCT/JP2011/062640
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English (en)
Japanese (ja)
Inventor
太田　裕樹
藤田　健一
加藤　康
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JFE Steel Corp
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JFE Steel Corp
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Priority to BR112012030684-7A priority Critical patent/BR112012030684B1/pt
Priority to RU2012157554/02A priority patent/RU2522065C1/ru
Priority to CN201180026476.7A priority patent/CN102933732B/zh
Priority to KR1020127032216A priority patent/KR101409291B1/ko
Priority to CA2799696A priority patent/CA2799696C/fr
Priority to EP11789877.5A priority patent/EP2578715B1/fr
Priority to ES11789877.5T priority patent/ES2643150T3/es
Priority to AU2011259992A priority patent/AU2011259992B2/en
Priority to US13/698,483 priority patent/US20130126052A1/en
Publication of WO2011152475A1 publication Critical patent/WO2011152475A1/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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B9/00—Measures for carrying out rolling operations under special conditions, e.g. in vacuum or inert atmosphere to prevent oxidation of work; Special measures for removing fumes from rolling mills
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention is a structural stainless steel plate excellent in corrosion resistance of a welded portion suitable as a body use material of a freight car (railway wagon) carrying, for example, coal or iron ore (railway wagon) ( structural stainless steel sheet) and a manufacturing method thereof.
  • Stainless steel is often used as a body material for freight cars (rail wagons) that carry coal and iron ore. Since the mined coal contains a lot of sulfur content, the material for the rail wagon body is sulfate corrosion resistance, especially intergranular corrosion resistance of the weld. resistance) is required.
  • Patent Document 1 discloses a Ti-containing ferritic stainless steel having excellent welded portion toughness.
  • the technique of Patent Document 1 has a problem that the toughness and corrosion resistance of the welded portion are not sufficient because the component design is performed so that the structure of the welded portion has a ferrite phase.
  • Patent Document 2 and Patent Document 3 by controlling the phase fraction at high temperature, an appropriate amount of martensitic phase is generated in the welded portion, and the workability of the welded portion ( Techniques for improving workability and corrosion resistance are disclosed.
  • Patent Document 4 discloses stainless steel suitable for a welding method using carbon dioxide gas.
  • one of the inventors previously used a structural stainless steel sheet that has improved the corrosion resistance of the welded part by optimizing the component composition using parameters that can accurately predict the structure of the welded part. Proposed (Patent Document 5).
  • Patent Documents 2 to 5 do not necessarily have sufficient considerations regarding the optimum component range. In particular, they are hardly considered for manufacturability, and cracks are generated in the slab stage and surface defects called “scab” are generated. Remarkably, it is difficult to avoid an increase in cost due to a decrease in yield ratio.
  • the present invention has been made in view of such circumstances, and an object thereof is to provide a structural stainless steel plate that can be produced at low cost and with high efficiency and has excellent corrosion resistance of a welded portion.
  • one of the inventors of the present invention is able to adjust the content of chemical components, particularly Mn and Ti, and the balance of each component to an appropriate range. It was found that intergranular corrosion caused by Cr deficiency in steel can be suppressed, and that the weld heat affected zone can be made mainly of martensite.
  • the parameter (F value) as shown in Patent Document 5 has been proposed. And based on these findings, the present inventors have continued detailed studies especially on manufacturability.
  • the present invention in mass%, C: 0.01 to 0.03%, N: 0.01 to 0.03%, Si: 0.10 to 0.40%, Mn: 1.5 to 2 0.5%, P: 0.04% or less, S: 0.02% or less, Al: 0.05 to 0.15%, Cr: 10 to 13%, Ni: 0.5 to 1.0%, Ti : 4 ⁇ (C + N) (however, C and N indicate their content (mass%)) or more and 0.3% or less, V: 0.05% or less, Ca: 0.0030% or less , O: Restricted to 0.0080% or less, and further, F value and FFV value represented by the following formula satisfy F value ⁇ 11, FFV value ⁇ 9.0, and the balance is made of Fe and inevitable impurities
  • the structural stainless steel plate excellent in the corrosion resistance of a welding part characterized by this is provided.
  • F value Cr + 2 * Si + 4 * Ti-2 * Ni-Mn-30 * (C + N)
  • FFV value Cr + 3 * Si + 16 * Ti + Mo + 2 * Al-2 * Mn-4 * (Ni + Cu) -40 * (C + N) + 20 * V
  • each element symbol is the content (mass%) of these elements.
  • the present invention also provides a structural stainless steel sheet with excellent weld corrosion resistance, characterized by containing Cu: 1.0% or less in addition to the above components in terms of mass%.
  • the present invention also provides a structural stainless steel sheet with excellent weld corrosion resistance, characterized by containing, in addition to the above-mentioned components, Mo: 1.0% or less in terms of mass%.
  • C 0.01 to 0.03%
  • N 0.01 to 0.03%
  • Si 0.10 to 0.40%
  • Mn 1.5 to 2 0.5%
  • P 0.04% or less
  • S 0.02% or less
  • Al 0.05 to 0.15%
  • Cr 10 to 13%
  • Ni 0.5 to 1.0%
  • Ti 4 ⁇ (C + N) (where C and N indicate their content (mass%)) or more and 0.3% or less
  • V 0.05% or less
  • Ca 0.0030% or less
  • O regulated to 0.0080% or less
  • the present invention also provides a method for producing a structural stainless steel sheet, characterized in that the hot-rolled sheet is annealed at a temperature of 600 to 1000 ° C. without being annealed, and is pickled.
  • F value Cr + 2 * Si + 4 * Ti-2 * Ni-Mn-30 * (C + N)
  • FFV value Cr + 3 * Si + 16 * Ti + Mo + 2 * Al-2 * Mn-4 * (Ni + Cu) -40 * (C + N) + 20 * V
  • each element symbol is the content (mass%) of these elements.
  • the present invention also provides a method for producing a structural stainless steel sheet having excellent weld corrosion resistance, characterized by containing, in addition to the above components, Cu: 1.0% or less in terms of mass%.
  • the present invention also provides a method for producing a structural stainless steel sheet having excellent weld corrosion resistance, characterized by containing Mo: 1.0% or less in addition to the above components in terms of mass%.
  • a structural stainless steel plate excellent in corrosion resistance of a welded portion which can be produced at low cost and with high efficiency, and is suitable as a body use material of a freight car (rail wagon) carrying coal or iron ore, for example. It is done.
  • % display is mass%.
  • C and N must each be contained in an amount of 0.01% or more in order to obtain the strength required for a structural stainless steel plate.
  • C and N exceeds 0.03%, Cr carbide or Cr carbonitride tends to precipitate, and the corrosion resistance, particularly the corrosion resistance of the weld heat affected zone is lowered. Further, the weld heat affected zone is hardened and the toughness is also lowered. Therefore, the C and N contents are both in the range of 0.01 to 0.03%. More preferably, C is 0.015 to 0.025%, and N is 0.012 to 0.02%.
  • Si 0.10 to 0.40%
  • Si is an element used as a deoxidizing agent, and it is necessary to contain 0.10% or more in order to obtain the effect.
  • the content exceeds 0.40%, the toughness of the hot-rolled steel sheet is lowered.
  • the Si content is in the range of 0.10 to 0.40%.
  • the lower limit is 0.20% and the upper limit is 0.30%.
  • Mn is an element useful as a deoxidizer and as a strengthening element for securing the necessary strength as a structural stainless steel plate, and is also an austenite stabilizing element at high temperatures.
  • it is an important element for controlling the microstructure of the weld heat affected zone to a martensite structure having a desired volume ratio.
  • the content is required to be 1.5% or more.
  • the Mn content is in the range of 1.5 to 2.5%. More preferably, it is in the range of 1.8 to 2.5%. More preferably, it is in the range of 1.85 to 2.0%.
  • P is preferably smaller in terms of hot workability, and the allowable upper limit of the content is 0.04%. More preferably, it is 0.035% or less.
  • S 0.02% or less S is preferably smaller in terms of hot workability and corrosion resistance, and the allowable upper limit of the content is 0.02%. Preferably it is 0.005% or less.
  • ⁇ Al 0.05-0.15%
  • Al is generally contained for deoxidation, but in the present invention, it is found that it works effectively to suppress the production of cracks, particularly at the slab stage, and exerts such a function. Therefore, an appropriate amount is included.
  • V, Ca, and O In order to suppress the occurrence of slab cracking, it is necessary to reduce V, Ca, and O and further optimize the FFV value, as described later, in addition to Al content.
  • the mechanism by which slab cracking is improved by the inclusion of Al is not necessarily clear, but is presumed to be due to the effects of optimizing the phase fraction and controlling the inclusion form. In order to acquire such an effect, it is necessary to contain 0.05% or more of Al.
  • the Al content is set in the range of 0.05 to 0.15%. More preferably, it is in the range of 0.080 to 0.150%. More preferably, it is in the range of 0.085 to 0.120%.
  • ⁇ Cr 10-13%
  • Cr is an essential element for forming a passive film and ensuring the corrosion resistance, particularly the corrosion resistance of the weld heat affected zone. In order to obtain the effect, it is necessary to contain 10% or more. On the other hand, if Cr is contained in excess of 13%, not only the cost is increased, but it becomes difficult to secure a sufficient austenite phase at a high temperature in the welded portion, and the necessary amount for the welded heat affected zone after welding. It becomes difficult to obtain a martensitic structure of the rate. As a result, the intergranular corrosion resistance is lowered in the weld heat affected zone. Therefore, the Cr content is in the range of 10 to 13%. Preferably, it is 10.5 to 12.5%.
  • Ni 0.5-1.0%
  • Ni is contained in an amount of 0.5% or more for the purpose of ensuring strength and toughness.
  • Ni is an expensive element, and its upper limit is set to 1.0% from the viewpoint of economy.
  • Ni is an austenite stabilizing element at a high temperature, similar to Mn, and is useful in controlling the microstructure of the weld heat affected zone to a martensitic structure having a desired volume fraction. Since the effect can be sufficiently obtained by adding Mn, the Ni content is suitably in the range of 0.5 to 1.0%. More preferably, it is in the range of 0.60 to 1.0%. More preferably, it is in the range of 0.60 to 0.90%.
  • Ti 4 ⁇ (C + N) or more, 0.3% or less Ti is an important element for obtaining excellent weld corrosion resistance in the present invention, and particularly improves the intergranular corrosion resistance of the weld heat affected zone. It is an essential element. Ti precipitates and fixes C and N in steel as Ti carbide, nitride, or carbonitride (hereinafter, three types of carbide, nitride, and carbonitride are collectively referred to as carbonitride). It has the effect of suppressing the formation of Cr carbonitrides and the like.
  • the weld heat-affected zone of the steel sheet has a structure composed of ferrite and martensite.
  • the problem is a decrease in corrosion resistance in the ferrite phase part accompanied by precipitation of carbonitrides and the like during cooling. is there.
  • Cr deficiency is generated in the vicinity of the grain boundary due to precipitation of Cr carbonitride or the like in the weld heat-affected zone during welding, and particularly the intergranular corrosion resistance in the ferrite phase portion is reduced.
  • This problem is solved by containing Ti. In order to exert such effects, the Ti content needs to be 4 ⁇ (C + N) or more (however, C and N indicate their content (mass%)).
  • content of Ti shall be 4 * (C + N) or more and 0.3% or less. More preferably, it is in the range of 0.180 to 0.230%, and it is effective to reduce C and N so that the Ti content simultaneously satisfies 4 ⁇ (C + N) or more.
  • V, Ca, and O are as follows. It is important to reduce.
  • V 0.05% or less
  • V is often contained as an impurity such as Cr raw material, and may be included unintentionally, but in order to suppress the occurrence of cracks particularly in the slab stage, It is necessary to strictly control the content. From such a viewpoint, the V content needs to be 0.05% or less. A preferred range is 0.03% or less, and a more preferred range is less than 0.03%. By setting the content to 0.01% or less, a greater cracking suppression effect can be obtained, but it is economically disadvantageous because raw material selection is required.
  • Ca generates inclusions having a low melting point, and causes surface defects caused by inclusions in particular. For this reason, in this invention, it is necessary to restrict
  • the Ca content is preferably as low as possible, and is preferably 0.0010%, and more preferably 0.0002% or less, but it is economically disadvantageous because it requires selection of raw materials.
  • O 0.0080% or less O is required to reduce the content in order to suppress generation of oxide inclusions and ensure high productivity, and the upper limit is set to 0.0080%. . Preferably, it is 0.0060% or less.
  • the corrosion resistance and productivity are greatly improved by setting the F value and the FFV value shown below within appropriate ranges.
  • ⁇ F value ⁇ 11 F value is expressed as Cr + 2 ⁇ Si + 4 ⁇ Ti-2 ⁇ Ni-Mn-30 ⁇ (C + N) (where each element symbol is the content (% by mass) of these elements), and the welding heat during welding It is a parameter for estimating the microstructure of the affected part, more specifically, a parameter for estimating the volume ratio of the martensite structure (the residual ratio of the ferrite structure). In parts exposed to high temperatures, such as weld heat affected zone, a part of them transforms to austenite (or a part of them further to ⁇ ferrite), and this phase transforms to martensite during the cooling process. To do.
  • the ratio is affected by the quantitative balance between the ferrite stabilizing element (ferrite-forming elements) and the austenite stabilizing element (austenite-forming elements).
  • Elements with positive coefficients (Cr, Si, Ti) in the formula showing the F value are ferrite stabilizing elements, and elements with negative coefficients (Ni, Mn, C, N) are austenite stabilizing elements. That is, as the F value increases, the ferrite structure tends to remain (the volume ratio of the ferrite structure is large, that is, the volume ratio of the martensite structure decreases), and as the F value decreases, the ferrite structure hardly remains (the volume ratio of the ferrite structure is small). That is, the volume ratio of the martensite structure is large.
  • Patent Document 5 the relationship between the F value and the volume ratio of the martensitic structure of the weld heat affected zone is investigated, and the corrosion resistance in the vicinity of the weld heat affected zone is evaluated by a sulfuric acid-copper sulfate corrosion test.
  • the F value is set to 11 or less (martensite volume ratio: 40% or more) in order to improve the corrosion resistance of the weld heat-affected zone as in the case of Patent Document 5 in the present invention.
  • the F value is preferably 10.5 or less (martensite volume ratio 60% or more), more preferably 10 or less.
  • the lower limit of the F value is preferably 5.0 or more. A more preferable range is 6.0 or more.
  • FFV value ⁇ 9.0 FFV value is Cr + 3 * Si + 16 * Ti + Mo + 2 * Al-2 * Mn-4 * (Ni + Cu) -40 * (C + N) + 20 * V (however, each element symbol is content (mass%) of these elements) In the present invention, it is newly derived as an index indicating manufacturability.
  • This FFV value takes into account the phase balance during hot rolling, and the value should be reduced after adjusting the components as described above, especially by restricting the Al content and the upper limit of V, Ca, and O. Thus, the occurrence of surface defects due to cracks and inclusions in the slab stage can be remarkably reduced.
  • a major feature of the present invention is that it has succeeded in greatly reducing the yield drop due to the occurrence of surface defects by optimizing a new parameter that takes into account the amount of Al that was not taken into account when the F value was devised. It is.
  • the mechanism for improving the manufacturability by optimizing the FFV value is not necessarily clarified, the manufacturability is remarkably improved by setting the FFV value to 9.0 or less. Therefore, the FFV value is set to 9.0. The following. Preferably, it is 8.5 or less.
  • the lower limit of the FFV value is preferably 5.0 or more. A more preferable range is 6.0 or more.
  • FIG. 1 shows the relationship between the FFV value and the surface defect occurrence rate. It can be seen that the occurrence rate of the defects can be remarkably suppressed by setting the FFV value calculated from the length of the portion where the defects are generated to an appropriate range of 9.0 or less with respect to the total coil length.
  • Cu in addition to the above-described components, Cu can be contained in the following range as necessary.
  • Cu 1.0% or less
  • Cu is an element that improves the corrosion resistance, and in particular, an element that reduces crevice corrosion. For this reason, it can be added when high corrosion resistance is required. However, if the content exceeds 1.0%, the hot workability is deteriorated, the phase balance at high temperature is lost, and it is difficult to obtain a desired structure in the weld heat affected zone. Therefore, when Cu is contained, the upper limit is made 1.0%. In order to sufficiently exhibit the effect of improving corrosion resistance, it is effective to contain 0.3% or more. A more preferable range is 0.3 to 0.5%.
  • Mo 1.0% or less Mo is an element that improves corrosion resistance, and can be added when particularly high corrosion resistance is required. However, if the content exceeds 1.0%, the workability in the cold state is deteriorated, and the rough surface in the hot rolling occurs, so that the surface quality is extremely lowered. Therefore, when Mo is contained, the upper limit is made 1.0%. In order to sufficiently exhibit corrosion resistance, it is effective to contain 0.03% or more. A more preferable range is 0.1 to 1.0%.
  • the present invention based on the conventional knowledge such as the improvement of ductility by containing 0.005% or less B in addition to improving the corrosion resistance by containing Cu or Mo by 1.0% or less as described above. In this case, it is important to consider the phase balance at a high temperature.
  • Nb is a strong stabilizing element, and is not added in the present invention because it is combined with C and N to greatly collapse the phase balance.
  • the balance other than the elements specified above is Fe and inevitable impurities.
  • the martensite volume ratio of the weld heat affected zone becomes 40% or more by setting the F value to 11 or less. More preferably, by setting the F value to 10.5 or less, the martensite volume fraction of the weld heat affected zone becomes 60% or more. More preferably, it is 10 or less, and the martensite volume ratio in this case is 80% or more.
  • the base material portion has a ferrite structure with a volume ratio of 50% or more. The remaining structure is a structure in which a martensite phase and a residual ⁇ phase exist, particularly in a state of being hot-rolled, and partially includes carbonitride.
  • the structure of the hot-rolled annealed sheet after being subjected to hot-rolled sheet annealing in an appropriate composition range as described later under an appropriate annealing condition has a ferrite phase structure of almost 100% in volume ratio, and the workability Very good.
  • the method for producing the stainless steel sheet of the present invention is not particularly limited as long as it is carried out according to a conventional method, but as a method that can be produced with high efficiency, a steel slab melted in the above composition is slabd by continuous casting or the like. Then, a hot-rolled coil is formed, and after annealing as necessary, descaling (shot blasting, pickling, etc.) is performed to obtain the stainless steel plate according to the present invention. The method is recommended.
  • the molten steel adjusted to the component composition of the present invention is melted in a commonly used melting furnace such as a converter (electric converter) or an electric furnace (vacuum degassing (RH method)).
  • a known refining method such as VOD (Vacuum Oxygen Decarburization) method, AOD (Argon Oxygen Decarburization) method, etc.
  • steel slab steel material
  • continuous casting method continuous casting
  • the slab thickness is preferably set to 100 mm or more in order to secure a reduction ratio in hot rough rolling described later. A more preferable range is 200 mm or more.
  • the steel slab is heated to a temperature of 1100 to 1300 ° C. and then hot rolled to obtain a hot rolled steel sheet.
  • the slab heating temperature is desirable to prevent the rough surface of the hot-rolled sheet (surface roughness resistance) and to improve the ridging properties after cold-rolling annealing (anti-riding property or ridding property).
  • (Slab sag) becomes remarkable, and the crystal grains become coarse and the toughness of the hot-rolled sheet decreases.
  • the heating temperature is lower than 1100 ° C., the load in hot rolling becomes high, the rough surface in hot rolling becomes remarkable, and recrystallization during hot rolling becomes insufficient, and the toughness of hot rolled sheet is also necessary. Decreases.
  • hot rough rolling step it is preferable to perform rolling at a rolling rate of 30% or more in a temperature range exceeding 1000 ° C. for at least one pass.
  • hot finish rolling is performed according to a conventional method (conditions of normal hot finish rolling).
  • a hot-rolled sheet having a thickness of about 2.0 to 8.0 mm manufactured by hot rolling can be used as a structural material as it is or after pickling without annealing.
  • the hot-rolled sheet may be subjected to pickling after annealing the hot-rolled sheet at a temperature of 600 to 1000 ° C. If the annealing temperature of the hot-rolled sheet is less than 600 ° C., the martensite phase and the residual ⁇ phase that may exist in the hot-rolled state may remain, and the ferrite structure may be 50% by volume. Therefore, sufficient workability cannot be obtained. On the other hand, when the temperature exceeds 1000 ° C., the coarsening of crystal grains becomes remarkable and the toughness is lowered.
  • the hot-rolled sheet is preferably annealed at a predetermined temperature of 600 to 1000 ° C. for 1 hour or longer by so-called box annealing. Also, if the annealing temperature is too high, it may not enter the temperature at which ⁇ transformation occurs. For this reason, it is necessary to adjust the composition to an appropriate range and to select an appropriate temperature range according to the composition. In the composition range of the steel of the present invention, when the annealing temperature is mainly 600 to 900 ° C., almost 100% of the volume ratio becomes a ferrite phase, and this temperature range is preferable.
  • the welding of the stainless steel plate according to the present invention includes resistance welding such as TIG welding, MIG welding, arc welding, seam welding, spot welding, laser welding (laser welding). Etc.) All the usual welding methods are applicable.
  • Stainless steel having the composition shown in Table 1 was made into a 200 mm thick slab by a converter-VOD-continuous casting method. These slabs were heated to a temperature of 1180 ° C., and then hot rolled to form a coiled hot rolled plate having a thickness of 5.0 mm. The hot rolling end temperature was 900 ° C., and the coiling temperature after hot rolling was 700 ° C. The obtained hot-rolled steel sheet was annealed at 690 ° C. for 10 hours, and then subjected to shot blasting and pickling to remove the scale.
  • a flat plate sample is cut out from the steel plate after the scale is removed, a T-shaped test body composed of a lower plate and a standing plate is assembled, and both side one pass fill welding (gas metal arc welding) is performed. (Gas metal arc welding), shielding gas (98% by volume Ar-2% by volume O 2 , flow rate: 20 liters / minute) were performed to prepare three fillet welded test pieces.
  • MGS-309LS manufactured by Kobe Steel, Ltd. was used as the welding rod, and the heat input was in the range of 0.4 to 0.8 kJ / mm.
  • Corrosion test specimens were collected from the fillet welds of these fillet weld test specimens and subjected to a sulfuric acid-copper sulfate corrosion test (Modified Strauss test in accordance with ASTM A262 practice E and ASTM A763 practice Z.
  • the test solution was Cu / 6. % CuSO 4 /0.5% H 2 SO 4, and a test piece whose end face was polished in this boiling liquid was immersed for 20 hours), and the corrosion state in the vicinity of the weld heat affected zone was observed.
  • FIG. 2 is an optical micrograph showing an example of observation of a cross section of a test piece after a sulfuric acid-copper sulfate corrosion test.
  • C when grain boundary corrosion is observed in the weld heat-affected zone or when severe deep pit-like corrosion is observed
  • B when observed with an optical microscope
  • the case where corrosion was not recognized was evaluated as A.
  • the surface state after the pickling of the hot-rolled annealed plate was observed over the entire length.
  • the ratio of the length at which surface defects due to slab cracks or inclusions were observed relative to the total length was used as an index, and the ratio of defect occurrence was 3% or less a, 3% to 30% b, 30% or more.
  • c These results are shown in Table 2.
  • No. 1 which is an example of the present invention within the scope of the present invention.
  • F. No. which is a comparative example that deviates from the scope of the present invention.
  • Nos. 9 and 14 since the amount of martensite produced in the weld heat affected zone was small, the intergranular corrosion resistance was clearly inferior.
  • No. 1 which is a comparative example in which Si is higher than the range of the present invention and Al is lower than the range of the present invention.
  • No. 6 and FFV values which are comparative examples deviating from the scope of the present invention.
  • 7, 8, 9 and 14 in the surface observation after hot rolling annealing, many cracks due to slabs and lashes due to inclusions were observed.
  • the steel of the present invention is used in the state of a hot-rolled sheet or a hot-rolled annealed sheet, the occurrence of lashes greatly reduces the yield. This is because the shaved portion not only has a bad appearance but can also be a starting point of rust generation, and therefore, when shipped as a product, the target portion must be cut off.

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  • Mechanical Engineering (AREA)
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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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Abstract

L'invention concerne une tôle d'acier inoxydable de construction qui peut être produite avec une grande efficacité et à bas coût et qui possède une excellente résistance à la corrosion dans la partie soudée, ainsi qu'un procédé de production de ladite tôle. L'invention concerne spécifiquement une tôle d'acier inoxydable de construction qui contient, en pourcentage massique, 0,01-0,03 % de C, 0,01-0,03 % de N, 0,01-0,40 % de Si, 1,5-2,5 % de Mn, 0,04 % ou moins de P, 0,02 % ou moins de S, 0,05-0,15 % d'Al, 10-13 % de Cr, 0,5-1,0 % de Ni, et 4×(C+N) ou plus mais 0,3 % ou moins de Ti, tout en contrôlant V à 0,05 % ou moins, Ca à 0,0030 % ou moins et O à 0,0080 % ou moins. La tôle d'acier inoxydable de construction se caractérise en outre en ce que la valeur F obtenue par Cr + 2×Si + 4×Ti - 2×Ni - Mn - 30×(C+N) est de 11 ou moins, la valeur FFV obtenue par Cr + 3×Si + 16×Ti + Mo + 2×Al - 2×Mn - 4×(Ni+Cu) - 40×(C+N) + 20×V] est de 9,0 ou moins, et le solde de la composition de la tôle est constitué de fer et des inévitables impuretés.
PCT/JP2011/062640 2010-05-31 2011-05-26 Tôle d'acier inoxydable de construction ayant une excellente résistance à la corrosion dans la partie soudée, et son procédé de production Ceased WO2011152475A1 (fr)

Priority Applications (9)

Application Number Priority Date Filing Date Title
BR112012030684-7A BR112012030684B1 (pt) 2010-05-31 2011-05-26 chapa de aço inoxidável estrutural tendo excelente resistência à corrosão na soldagem e método para produção da mesma
RU2012157554/02A RU2522065C1 (ru) 2010-05-31 2011-05-26 Листовая конструкционная нержавеющая сталь, обладающая превосходной коррозионной устойчивостью в сварном шве, и способ ее производства
CN201180026476.7A CN102933732B (zh) 2010-05-31 2011-05-26 焊接部耐腐蚀性优异的结构用不锈钢板及其制造方法
KR1020127032216A KR101409291B1 (ko) 2010-05-31 2011-05-26 용접부 내식성이 우수한 구조용 스테인레스 강판 및 그의 제조 방법
CA2799696A CA2799696C (fr) 2010-05-31 2011-05-26 Tole d'acier inoxydable de construction ayant une excellente resistance a la corrosion dans la partie soudee, et son procede de production
EP11789877.5A EP2578715B1 (fr) 2010-05-31 2011-05-26 Tôle d'acier inoxydable de construction ayant une excellente résistance à la corrosion dans la partie soudée, et son procédé de production
ES11789877.5T ES2643150T3 (es) 2010-05-31 2011-05-26 Lámina estructural de acero inoxidable que tiene excelente resistencia a la corrosión en la parte soldada, y método para producir la misma
AU2011259992A AU2011259992B2 (en) 2010-05-31 2011-05-26 Structural stainless steel sheet having excellent corrosion resistance at weld and method for manufacturing same
US13/698,483 US20130126052A1 (en) 2010-05-31 2011-05-26 Structural stainless steel sheet having excellent corrosion resistance at weld and method for manufacturing same

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JP2010124059 2010-05-31
JP2010-124059 2010-05-31

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EP (1) EP2578715B1 (fr)
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AU (1) AU2011259992B2 (fr)
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CA (1) CA2799696C (fr)
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TW201418549A (zh) * 2012-11-12 2014-05-16 Shehkai Prec Co Ltd 複合式混凝土之螺絲錨栓
WO2015064077A1 (fr) 2013-10-31 2015-05-07 Ｊｆｅスチール株式会社 Acier inoxydable diphasique ferrite-martensite, et son procédé de fabrication
WO2015064128A1 (fr) 2013-10-31 2015-05-07 Ｊｆｅスチール株式会社 Acier inoxydable à deux phases ferrite-martensite présentant une résilience aux basses températures, et son procédé de production
CN108690936B (zh) * 2018-06-13 2020-12-01 燕山大学 用于焊接高锰钢辙叉与钢轨的不锈钢钢轨材料及制备方法
KR102173277B1 (ko) * 2018-11-06 2020-11-03 주식회사 포스코 저온 충격인성이 우수한 열연 강판 및 그 제조방법

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CA2799696A1 (fr) 2011-12-08
EP2578715B1 (fr) 2017-07-12
TW201207128A (en) 2012-02-16
BR112012030684A2 (pt) 2017-12-05
KR101409291B1 (ko) 2014-06-18
CN102933732A (zh) 2013-02-13
BR112012030684B1 (pt) 2018-08-14
ES2643150T3 (es) 2017-11-21
RU2012157554A (ru) 2014-07-20
US20130126052A1 (en) 2013-05-23
EP2578715A4 (fr) 2015-08-19
TWI439555B (zh) 2014-06-01
CA2799696C (fr) 2015-11-17
EP2578715A1 (fr) 2013-04-10
JP4893866B2 (ja) 2012-03-07
AU2011259992B2 (en) 2013-12-19
RU2522065C1 (ru) 2014-07-10
JP2012012702A (ja) 2012-01-19
AU2011259992A1 (en) 2012-12-20
CN102933732B (zh) 2016-06-29
KR20130034025A (ko) 2013-04-04

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