WO2021182525A1 - Tôle d'acier plaquée, son procédé de fabrication et structure soudée - Google Patents

Tôle d'acier plaquée, son procédé de fabrication et structure soudée Download PDF

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WO2021182525A1
WO2021182525A1 PCT/JP2021/009610 JP2021009610W WO2021182525A1 WO 2021182525 A1 WO2021182525 A1 WO 2021182525A1 JP 2021009610 W JP2021009610 W JP 2021009610W WO 2021182525 A1 WO2021182525 A1 WO 2021182525A1
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steel sheet
clad
clad steel
base material
less
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PCT/JP2021/009610
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English (en)
Japanese (ja)
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真知 川
雄介 及川
柘植　信二
潤平 安藤
剛志 橋本
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日鉄ステンレス株式会社
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Priority to JP2022507251A priority Critical patent/JP7357761B2/ja
Priority to CN202180018681.2A priority patent/CN115210399B/zh
Publication of WO2021182525A1 publication Critical patent/WO2021182525A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 clad steel sheet having excellent hydrogen embrittlement resistance on the joint surface, a method for manufacturing the clad steel sheet, and a welded structure manufactured by a manufacturing process including welding or gouging using the clad steel sheet using a gas containing hydrogen.
  • Stainless steel and Ni-based alloys are suitable materials in severe corrosive environments because they have excellent corrosion resistance.
  • Examples of the above-mentioned corrosive environment include an oil well environment, a high chloride environment exposed to seawater and brackish water, plant equipment exposed to various acid solutions, a chemical tanker, and the like.
  • stainless steel and Ni-based alloys are used in seawater desalination plants, flue gas desalination equipment, chemical storage tanks, structural members such as oil pipes, pumps and valves, heat exchangers, etc. There is.
  • stainless steel and Ni-based alloys contain a large amount of alloying elements such as Cr, Ni, and Mo to ensure corrosion resistance, and compared to carbon steel and low alloy steel, not only material costs but also processing and welding costs. Is also expensive. It is also possible that the price will fluctuate significantly due to the soaring price of alloying elements. Therefore, its use may be restricted mainly in terms of cost.
  • a clad steel sheet is a material obtained by laminating two or more different types of metals. Further, a steel sheet that is not bonded is hereinafter referred to as a "solid steel sheet". Compared with solid steel sheets made only of high alloy steel, clad steel sheets can reduce the amount of high alloy steel used, reduce material costs, and reduce welding of dissimilar materials, so molten materials during welding can be reduced. Costs can also be reduced.
  • base material one metal is described as “base material” and the other metal (material) bonded to the base material is described as “laminated material”.
  • laminated material By laminating a material (laminated material) having excellent properties to the base material, both the excellent properties of the laminated material and the base material can be obtained.
  • a high alloy steel having the characteristics required in the usage environment is used for the laminated material, and a carbon steel or a low alloy steel having the toughness and strength required in the usage environment is used as the base material. ..
  • a carbon steel or a low alloy steel having the toughness and strength required in the usage environment is used as the base material. ..
  • the cost can be reduced as described above, but also the same characteristics as the solid steel sheet and the same strength and toughness as the carbon steel and the low alloy steel can be secured. Therefore, both economy and functionality can be achieved at the same time.
  • a diffusion layer of elements is formed at the interface of the laminated lumber (hereinafter simply referred to as "interface").
  • the concentration of each element gradually changes in the diffusion layer, but depending on the element concentration, the temperature at which martensitic transformation starts is high, and the critical cooling rate at which martensitic transformation occurs is slow. Transformation may occur.
  • Patent Document 1 discloses a technique for suppressing sensitization near the interface by controlling the thickness of the carbon diffusion layer at the interface of a duplex stainless clad steel sheet. However, there is no mention of the martensite phase at the interface.
  • Patent Document 2 discloses a technique for preventing delayed fracture of martensite at the interface by specifying the temperature and time of tempering after rolling for an austenitic stainless clad steel sheet. However, this technique is to prevent delayed fracture during manufacturing, and there is no disclosure of preventive techniques for welded structures.
  • Non-Patent Document 1 evaluates the hydrogen embrittlement susceptibility of martensite at the interface for the cladding of SUS316L and Inconel 625.
  • Patent Document 2 discloses a technique for preventing delayed fracture of martensite at an interface.
  • Patent Document 1 describes a method for evaluating the hydrogen embrittlement susceptibility of martensite at an interface.
  • the width of the diffusion layer differs depending on the heating temperature and the reduction ratio, but there is no description or suggestion about the relationship between the width of the diffusion layer and the hydrogen embrittlement sensitivity.
  • the present inventor controls the hardness and width of martensite at the interface, the hydrogen concentration in steel, and the stress applied to martensite in order to suppress the interfacial peeling of the clad due to hydrogen embrittlement during welding. was found to be a problem to be solved.
  • an object of the present invention is to provide a clad steel sheet having good hydrogen embrittlement resistance of the joint surface and excellent hydrogen embrittlement resistance, a method for producing the same, and a welded structure.
  • a clad steel sheet including a base material and a laminated material joined to the base material.
  • the base material is made of carbon steel or low alloy steel.
  • the laminated material is made of a corrosion-resistant alloy and is made of a corrosion-resistant alloy.
  • the chemical composition of the base material is C: 0.020 to 0.200%, Si: 1.00% or less, Mn: 0.10 to 3.00% in mass%. , P: 0.050% or less, S: 0.050%, Ceq is 0.20 to 0.40, and the balance has a component composition of Fe and impurities, according to [1].
  • Ceq is defined by the following equation (1).
  • Ceq C + Mn / 6 + (Cu + Ni) / 15+ (Cr + Mo + V) / 5 ...
  • C, Mn, Cu, Ni, Cr, Mo and V are elements of each element in the composition of the base steel sheet. The content (% by mass).
  • the component composition of the base material is, instead of a part of the Fe, in mass%, Ni: 0.01 to 1.00%, Cr: 0.01 to 1.00%, Mo: 0. 0.01 to 0.50%, Cu: 0.01 to 1.00%, Co: 0.01 to 0.50%, Se + Te: 0.01 to 0.10%, V: 0.001 to 0.100 %, Ti: 0.001 to 0.200%, Nb: 0.001 to 0.200%, Al: 0.005 to 0.300%, Ca: 0.0003 to 0.0050%, B: 0.
  • the base material and the laminated material are laminated so that the crimping surface becomes vacuum, and the four circumferences of the crimping surface are sealed by welding and clad.
  • T maximum heating temperature
  • T-20 ° C. in the heating furnace From the time when the maximum heating temperature T (° C.) in the heating furnace and the maximum heating temperature T-20 ° C. in the heating furnace are reached for the clad rolled material obtained by assembling one or more of the above clad materials as the material.
  • the time t (minutes) until extraction into the heating furnace, and the reduction ratio r calculated by the material thickness / product thickness, d calculated by the formula (2) is 1 or more and 9 or less. Heating and hot rolling are performed, and after rolling.
  • the average cooling rate in the TA3 (° C.) to 650 ° C. section calculated by the formula (3) is 2 ° C./s or more and the nanohardness at the interface between the base material and the laminated material is 7 GPa or more.
  • the present inventors conducted the following studies on the above problems. Specifically, in clad steel sheets made of various stainless steels and Ni-based alloys, the element diffusion and metallographic structure at the interface were investigated by changing the heating temperature, heating time, rolling ratio and cooling rate after rolling. , The relationship with the hydrogen embrittlement resistance of the interface was evaluated. As a result, the following findings (a) to (c) were obtained.
  • the carbon steel or low alloy steel as the base material is in contact with the stainless steel or Ni-based alloy as the laminated material.
  • the profile of the alloying elements at the interface could be organized by the temperature / time of material heating and the reduction ratio. Further, it was confirmed that the diffusion width of Cr and the width of the martensite phase correspond to each other when a laminated material containing 10% or more by mass% of Cr was used. Since Cr is the element that diffuses the fastest among the main alloy elements and further enhances hardenability, martensitic transformation occurs in the region where only the content of Cr is high and the content of austenite stabilizing elements such as Ni is low. Because.
  • the clad steel sheet according to the present invention includes a base material and a laminated material joined to the base material.
  • the base material consists of carbon steel or low alloy steel, which will be described later.
  • the laminated material is made of a corrosion-resistant alloy, and examples of the corrosion-resistant alloy include stainless steel and Ni-based alloys containing 10% or more of Cr. Further, the width of the region where the nanohardness is 7 GPa or more at the interface between the base material and the laminated material is 5 ⁇ m or less.
  • Nano-hardness of the clad interface The width of the region where the nano-hardness is 7 GPa or more at the clad interface shall be 5 ⁇ m or less. When the width of the region with nano-hardness of 7 GPa or more in the plate thickness direction exceeds 5 ⁇ m, the region of martensite, which is hard and highly sensitive to hydrogen embrittlement, is large, so the interface peels off when welding containing hydrogen in the welding gas is performed. In some cases. It is preferably 3 ⁇ m or less, and more preferably 1 ⁇ m or less. The smaller the region where the nanohardness is 7 GPa or more, the lower the hydrogen embrittlement sensitivity, so no lower limit is set.
  • the nano-hardness means the hardness of a material evaluated in accordance with an instrumentation indentation hardness test (also referred to as a nano-indentation test) specified in ISO 14577.
  • the base material consists of carbon steel or low alloy steel.
  • the preferable chemical composition of the base material is C: 0.020 to 0.200%, Si: 1.00% or less, Mn: 0.10 to 3.00%, P: 0.050% or less in mass%.
  • Ceq is defined by the following equation (1).
  • Ceq C + Mn / 6 + (Cu + Ni) / 15+ (Cr + Mo + V) / 5 ... Equation (1)
  • C, Mn, Cu, Ni, Cr, Mo and V are the contents (mass%) of each element in the component composition of the base material.
  • C is an element that improves the strength of steel, and when it is contained in an amount of 0.020% or more, sufficient strength is exhibited. However, if it exceeds 0.200%, the weldability and toughness are deteriorated. Therefore, the amount of C is set to 0.020 to 0.200%. It is preferably 0.040% or more, and more preferably 0.050% or more. On the other hand, the upper limit is preferably 0.100% or less, more preferably 0.080% or less. A more preferable range is 0.040% to 0.100%, and a more preferable range is 0.050% to 0.080%.
  • Si is an element that is effective in deoxidizing and improves the strength of steel. However, if it exceeds 1.00%, the surface properties and toughness of the steel deteriorate. Therefore, the amount of Si is set to 1.00% or less. It is preferably 0.50% or less. Si may not be contained. The preferable lower limit of the content of Si is 0.01%.
  • Mn is an element that increases the strength of steel, and its effect is exhibited when it is contained in an amount of 0.10% or more. However, if it exceeds 3.00%, the weldability is impaired and the alloy cost also increases. Therefore, the amount of Mn is set to 0.10 to 3.00%.
  • the lower limit is 0.50% and the upper limit is 2.00%. More preferably, the lower limit is 0.90% and the upper limit is 1.60%.
  • the amount of P is set to 0.050% or less. It is preferably 0.020% or less.
  • the amount of S is set to 0.050% or less. It is preferably 0.010% or less.
  • Ni 0.01 to 1.00%, Cr: 0.01 to 1.00%, Mo: 0.01 to 0 in mass% instead of a part of the Fe. .50%
  • Cu 0.01 to 1.00%
  • Co 0.01 to 0.50%
  • Se + Te 0.01 to 0.10%
  • V 0.001 to 0.100%
  • Ti 0.001 to 0.200%
  • Nb 0.001 to 0.200%
  • Al 0.005 to 0.300%
  • Ca 0.0003 to 0.0050%
  • B 0.0003 to 0. It can contain one or more selected from 0030% and REM: 0.0003-0.0100%.
  • Ni is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 1.00%, it causes deterioration of weldability and toughness. Therefore, when Ni is contained, the amount of Ni is set to 1.00% or less. It is preferably 0.50% or less, and more preferably 0.30% or less. The preferred lower limit of Ni content is 0.01%.
  • Cr is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 1.00%, it causes deterioration of weldability and toughness. Therefore, when Cr is contained, the amount of Cr is set to 1.00% or less. It is preferably 0.50% or less, and more preferably 0.30% or less. The preferred lower limit of Cr content is 0.01%.
  • Mo is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 0.50%, it causes deterioration of weldability and toughness. Therefore, when Mo is contained, the amount of Mo is 0.50% or less. It is preferably 0.30% or less, and more preferably 0.1% or less. The preferred lower limit of Mo content is 0.01%.
  • Cu is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 1.00%, it causes deterioration of weldability and toughness. Therefore, when Cu is contained, the amount of Cu is set to 1.00% or less. It is preferably 0.50% or less, and more preferably 0.30% or less. The preferred lower limit of Cu content is 0.01%.
  • Co is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 0.50%, the workability in hot water is impaired and the productivity is lowered. Therefore, when Co is contained, the amount of Co is set to 0.50% or less. It is preferably 0.30% or less, and more preferably 0.1% or less. The preferred lower limit of Co content is 0.01%.
  • Se and Te suppress the formation of oxides by diffusing easily oxidizable elements such as Mn, Si, and Al in the steel sheet onto the surface of the steel sheet, and improve the surface properties and plating properties of the steel sheet.
  • the total amount of Se and Te is 0.10% or less. More preferably, it is 0.05% or less.
  • the preferred Se + Te content lower limit is 0.01%.
  • Al is an element that is effective in deoxidizing steel. However, if it exceeds 0.300%, the toughness of the welded portion deteriorates. Therefore, when Al is contained, the amount of Al is set to 0.300% or less. It is preferably 0.100% or less. The preferable lower limit of Al content is 0.005%.
  • V increases the strength of steel by forming a carbonitride. However, if it exceeds 0.100%, it causes deterioration of weldability and toughness. Therefore, when V is contained, the amount of V is set to 0.100% or less. It is preferably 0.050% or less. The preferred lower limit of V content is 0.001%.
  • Ti is an element that refines crystal grains and increases strength, and its effect is exhibited by adding 0.001% or more. However, if it exceeds 0.200%, the weldability is impaired and the alloy cost also increases. Therefore, the amount of Ti is set to 0.001 to 0.200%.
  • the lower limit is 0.005% and the upper limit is 0.100%. More preferably, the lower limit is 0.010% and the upper limit is 0.050%.
  • Nb is an element that raises the recrystallization temperature, and its effect is exhibited by adding 0.001% or more. However, if it exceeds 0.200%, the weldability is impaired and the alloy cost also increases. Therefore, the amount of Nb is set to 0.001 to 0.200%.
  • the lower limit is 0.005% and the upper limit is 0.100%. More preferably, the lower limit is 0.010% and the upper limit is 0.050%.
  • Ca refines the structure of the weld heat affected zone and improves toughness. However, if it exceeds 0.0050%, coarse inclusions are formed and the toughness is deteriorated. Therefore, when Ca is contained, the amount of Ca is set to 0.0050% or less. It is preferably 0.0030% or less. The preferable lower limit of Ca content is 0.0003%.
  • B is an element that improves the hardenability of steel and improves the strength and toughness of rolled steel. However, if it exceeds 0.0030%, it causes deterioration of weldability and toughness. Therefore, when B is contained, the amount of B is set to 0.0030% or less. It is preferably 0.0020% or less. The preferable lower limit of the B content is 0.0003%.
  • REM refines the structure of the weld heat affected zone and improves toughness. However, if it exceeds 0.0100%, coarse inclusions are formed and the toughness is deteriorated. Therefore, when REM is contained, the amount of REM is 0.0100% or less. It is preferably 0.005% or less. The preferred lower limit of REM content is 0.0003%.
  • REM is a general term for 17 elements in which Y and Sc are combined with 15 elements of lanthanoids.
  • One or more of these 17 elements can be contained in the steel material, and the REM content means the total content of these elements.
  • the balance is Fe and impurities.
  • impurity is a component mixed by various factors of raw materials such as ore and scrap, and various factors in the manufacturing process when steel materials are industrially manufactured, and is allowed as long as it does not adversely affect the present invention. Means something.
  • the corrosion-resistant alloy is a stainless steel or nickel-based alloy containing 10% or more of Cr.
  • the laminated material of the present invention is made of a corrosion-resistant alloy. As described above, the corrosion-resistant alloy contains a large amount of Cr, and the diffusion of Cr increases the hardenability of the clad interface and facilitates the transformation to martensite, and the carbon on the base metal side diffuses to the mating material side to diffuse the base metal. A hard martensite phase is formed at the side interface, which causes a decrease in hydrogen embrittlement resistance of the joint surface. That is, the effect of the present invention is exhibited when a corrosion-resistant alloy containing a large amount of Cr is used. When the Cr content of the laminated material is 10% or more, the effect of applying the present invention is remarkable. If the Cr content is 15% or more, the effect can be more remarkable.
  • the present invention is a technique for a clad steel sheet having excellent hydrogen embrittlement resistance of a joint surface and a method for manufacturing the same by controlling the joint interface structure.
  • the steel type of the laminated material is not particularly specified, but stainless steel is an example of the laminated material.
  • a nickel-based alloy can be exemplified.
  • Stainless steels include austenite-based stainless steels, ferrite-based stainless steels, and two-phase stainless steels, and nickel-based alloys have various alloy components under trade names such as Inconel, Incoloy, and Hastelloy.
  • the maximum heating temperature T (° C.) in the heating furnace the time t (minutes) from the time when the heating temperature in the heating furnace reaches the maximum heating temperature T-20 ° C. to the extraction into the heating furnace, T A3 by the reduction ratio r which is calculated by the material thickness / product thickness d is calculated by the equation (2) performs a heating and hot rolling is 1 to 9, which is calculated by the equation (3) after rolling ( A clad steel plate is manufactured by cooling at an average cooling rate of 2 ° C./s or more in the section from (° C.) to 650 ° C.
  • the clad material is produced by the method described below. Specifically, after melting carbon steel and low alloy steel as a base material and corrosion resistant alloy as a binder by a known method such as a converter, an electric furnace, a vacuum melting furnace, etc., a continuous casting method or ingot formation- Create a slab by the slab method. The obtained slab is hot-rolled under commonly used conditions to obtain a laminated lumber and a base material which are hot-rolled plates. The obtained hot-rolled plate may be annealed, pickled, polished or the like, if necessary.
  • the above-mentioned laminated material and base material are laminated so that the crimping surface becomes a vacuum, and the four circumferences of the crimping surface are sealed by welding to assemble the clad material.
  • An insert material such as Ni foil may be inserted between the laminated material and the base material in order to improve the adhesion and the interfacial corrosion resistance.
  • the method of evacuating the crimping surface is not particularly specified, but a method of electron beam welding in vacuum or a vacuum pump after making holes for vacuuming in advance and welding 4 laps by arc welding or laser welding in the atmosphere. An example is a method of evacuating with.
  • the degree of vacuum (absolute pressure) is 0.1 Torr or less, a good bonding interface with less oxides at the interface can be obtained, more preferably 0.05 Torr or less, and the higher the degree of vacuum (the lower the absolute pressure). ) Since the bonding interface tends to be good, no lower limit is set.
  • the obtained clad material may be used as it is for hot rolling as a clad rolling material, or a material assembled by applying a release agent between two clad materials so as to be overlapped is used for hot rolling as a clad rolling material. You may. When two are stacked, it is desirable that the base materials and the laminated materials have the same thickness in order to reduce the plate warpage during cooling. Of course, it is not necessary to limit the assembly method described above.
  • the obtained clad-rolled material is subjected to the maximum heating temperature T (° C.) in the heating furnace and the maximum heating temperature T-20 ° C. in the heating furnace from the time when the heating furnace extraction occurs.
  • Heating and hot rolling are performed in which d calculated by the formula (3) is 1 or more and 9 or less based on the reduction ratio r calculated by the time t (minutes) and the material thickness / product thickness.
  • d exceeds 9, the element diffusion distance becomes long at the product interface, so that the width of the region where martensitic transformation can occur becomes large, and the hydrogen embrittlement resistance of the interface decreases.
  • d is 7 or less.
  • the maximum heating temperature T in the heating furnace is preferably 1050 to 1250 ° C. If the maximum heating temperature T is less than 1050 ° C., the hot workability deteriorates and the bonding strength also deteriorates. Therefore, the maximum heating temperature T is preferably 1050 ° C.
  • the maximum heating temperature T is more than 1250 ° C., the steel pieces are easily deformed in the heating furnace and flaws are likely to occur during hot rolling, and the diffusion at the interface becomes faster. Therefore, the maximum heating temperature T is preferably 1250 ° C. or lower, and more preferably 1220 ° C. or lower. The shorter the time t (minutes) from the time when the heating temperature in the heating furnace reaches the maximum heating temperature T-20 ° C. to the extraction in the heating furnace, the shorter the element diffusion distance at the interface, so no lower limit is set. Heating for 30 minutes or more is desirable to make the temperature uniform up to the center of the plate thickness.
  • the reduction ratio r calculated by the material thickness / product thickness is preferably 3 or more and 15 or less. If the reduction ratio r is less than 3, the interfacial bonding by rolling may be insufficient and the shear strength of the interface may be low. More preferably, it is 5 or more. If the rolling ratio is more than 15, the rolling time becomes long and the rolling cost increases. More preferably, it is 10 or less.
  • the size of the martensite phase region at the interface is mainly affected by the diffusion of Cr.
  • Cr diffusion occurs at a temperature of several hundred degrees Celsius or higher, the diffusion distance increases exponentially as the temperature rises, so that the actual diffusion is maintained near the maximum temperature during the material heating time. Occurs in.
  • the diffusion is negligibly small because the plate temperature drops rapidly during rolling and cooling. Therefore, it can be considered that the Cr diffusion distance of the product is such that the diffusion distance generated during heating is reduced by the ratio of the reduction ratio.
  • the authors measured the size of the martensite phase region by TEM observation of the thin film at the interface for clad products with various heating temperatures, times, and reduction ratios, and measured the maximum temperature T (° C.) in the heating furnace and the heating furnace.
  • the time t minutes (minutes) from the time when the heating temperature in the room reaches the maximum heating temperature T-20 ° C. to the extraction into the heating furnace and the value d calculated by the equation (2) from the reduction ratio r are the sizes of the martensite phase region. We have confirmed that it corresponds accurately with.
  • the average cooling rate in the TA3 (° C) to 650 ° C section calculated from equation (3) after rolling is 2 ° C / s or more.
  • the average cooling rate in the TA3 (° C) to 650 ° C section calculated from equation (3) after rolling is 2 ° C / s or more.
  • the width of the area is increased. It is preferably 4 ° C./s or higher.
  • T A3 (°C) 937.2-436.5C + 56Si-19.7Mn-26.6Ni + 136.3Ti-19.1Nb + 198.4Al ⁇ formula (3)
  • C, Si, Mn, Ni, Ti, Nb and Al are the contents (mass%) of each element in the component composition of the base steel sheet.
  • the present invention it is possible to obtain a clad steel sheet having excellent hydrogen embrittlement resistance on the joint surface.
  • the clad steel plate according to the present invention and the welded structure using the clad steel plate of the present invention do not require peeling measures at the time of welding or additional heat treatment.
  • the present invention frees us from controlling the hydrogen concentration in steel or the stress applied to martensite, if the hardness and width of the martensite at the interface are defined in the present invention.
  • the clad steel sheet has no limitation on the intended use, and can be applied to a structural member in which a solid steel sheet has been conventionally used. Therefore, the clad steel sheet greatly contributes to cost reduction.
  • the welded structure made of the clad steel sheet of the present invention can be a welded structure manufactured by a manufacturing process including welding using a gas containing hydrogen or gouging.
  • the clad steel sheet of the present invention has excellent hydrogen embrittlement resistance, hydrogen embrittlement does not occur even when it is used for welding using hydrogen as a welding gas.
  • the combined material with the chemical composition shown in Table 1 and the base material with the chemical composition shown in Table 2 are melted into steel pieces, and after undergoing the steps of hot rolling, annealing, and pickling, the combined material has a thickness of 30 mm, and the base material has a thickness of 30 mm.
  • a steel plate having a thickness of 130 mm was manufactured.
  • the base material and the combined material were laminated so that the crimping surface became a vacuum, and four circumferences of the crimping surface were sealed by welding to prepare a clad material.
  • the two clad materials were laminated by applying a release agent between the laminated materials so as to form a base material-laminated material-stripping agent-laminated material-base material, and assembled as a clad rolled material.
  • the obtained clad-rolled material was hot-rolled under the hot-rolling conditions shown in Table 3 and then peeled off at the release agent portion to obtain a clad steel sheet having a thickness of 53 mm (compression ratio 3) to 12 mm (compression ratio 13).
  • T indicates the maximum heating temperature (° C.) in the heating furnace before rolling
  • t is the time from the time when the heating temperature in the heating furnace reaches the maximum heating temperature T-20 ° C. to the extraction into the heating furnace.
  • (Minute) is shown.
  • r indicates the reduction ratio calculated by the material thickness / product thickness.
  • d represents a value calculated by the equation (2) from the above T
  • t represents the maximum heating temperature
  • CR indicates the average cooling rate (° C./s) from TA3 (° C.) to 650 ° C.
  • L indicates the width ( ⁇ m) of the region where the nanohardness is 7 GPa or more in the vicinity of the interface.
  • Hydrogen resistance is the result of the hydrogen embrittlement resistance evaluation test. A indicates good hydrogen embrittlement resistance, and X indicates poor hydrogen embrittlement resistance.
  • the measurement of nano-hardness is based on the instrumentation indentation hardness test specified in ISO 14577, and the nano-hardness is measured at a pitch of 0.5 ⁇ m in the range of 10 ⁇ m from the interface on the mating material side and the base material side in the plate thickness direction. bottom.
  • the conditions for nano-hardness measurement may be appropriately selected. For example, measurements with a load of 1000 ⁇ N, a push-in specified load of 5 sec, a hold of 0 sec, and a return of 5 sec are performed three times at each position, and the average value is taken as the nano-hardness. Can be exemplified. The range of the region where the nanohardness was 7 GPa or more was read and designated as L.
  • the cross section of the test piece was observed to confirm that the weld metal was separated from the interface by 2 mm or more.
  • the prepared test piece was charged with a cathode having a current density of 10 (A / m 2 ) ⁇ 72 (hr) in a 3 mass% NaCl + 3 g / L ⁇ NH 4 SCN aqueous solution before tensioning, and then 3% NaCl + 3 g / L ⁇ NH. 4 While charging the cathode at 10 (A / m 2 ) in the SCN aqueous solution, the strain was pulled to break at the strain rate of the parallel portion: 1 ⁇ 10 -3 (1 / s).
  • Sample numbers 1 to 41 are examples of the present invention, satisfying preferable production conditions, having a region length L of 5 ⁇ m or less having a nanohardness of 7 GPa or more, and having good hydrogen embrittlement resistance of the joint surface.
  • Sample numbers 42 to 47 are comparative examples, do not satisfy preferable production conditions, have a length L of a region having a nanohardness of 7 GPa or more of more than 5 ⁇ m, and have poor hydrogen embrittlement resistance of the joint surface. ..
  • the clad steel sheet of the present invention can be used in a high chloride environment such as that exposed to seawater, or in plant equipment exposed to an acid solution such as phosphoric acid or sulfuric acid as a corrosive environment. It may be applied to corrosive environments. Specific examples include seawater desalination plants, flue gas desulfurization equipment, chemical storage tanks, structural members such as oil country tubular goods, pumps and valves, and heat exchangers.

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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)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)

Abstract

L'invention concerne une tôle d'acier plaquée inoxydable ayant une excellente résistance à la fragilisation par l'hydrogène sur une surface de jonction, un acier inoxydable ou un alliage à base de Ni étant utilisé comme matériau de placage, un acier au carbone ou un acier faiblement allié étant utilisé comme matériau de base, et la largeur d'une région ayant une nanodureté d'au moins 7 GPa étant d'au maximum 5 µm à l'interface entre le matériau de base et le matériau de placage. Comme la surface de jonction de la tôle d'acier plaquée possède une petite aire de martensite qui est hautement sensible à la fragilisation par l'hydrogène, une désolidarisation interfaciale peut être empêchée même lorsqu'un soudage est réalisé à l'aide d'un gaz de soudage contenant de l'hydrogène.
PCT/JP2021/009610 2020-03-13 2021-03-10 Tôle d'acier plaquée, son procédé de fabrication et structure soudée WO2021182525A1 (fr)

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CN202180018681.2A CN115210399B (zh) 2020-03-13 2021-03-10 包层钢板及其制造方法以及焊接结构物

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Citations (4)

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JPS52102848A (en) * 1976-02-26 1977-08-29 Nippon Steel Corp Method of gas shield arc welding
JPH0657377A (ja) * 1992-08-12 1994-03-01 Nippon Steel Corp 加工時の耐界面破壊性に著しく優れた高耐食性クラッド鋼板
WO2019189871A1 (fr) * 2018-03-30 2019-10-03 日鉄ステンレス株式会社 Tôle d'acier inoxydable revêtu biphasé et son procédé de production
WO2020071343A1 (fr) * 2018-10-01 2020-04-09 日鉄ステンレス株式会社 Tôle d'acier inoxydable austénitique plaquée, tôle d'acier de base et procédé de production de tôle d'acier plaquée

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JP5223360B2 (ja) * 2007-03-22 2013-06-26 Ｊｆｅスチール株式会社 成形性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法
KR101402503B1 (ko) * 2009-08-31 2014-06-03 신닛테츠스미킨 카부시키카이샤 고강도 용융 아연 도금 강판 및 그 제조 방법
EP2987581B1 (fr) * 2013-04-17 2017-11-22 Nippon Steel & Sumitomo Metal Corporation Procédé de soudage par points
CN105658831B (zh) * 2013-10-21 2017-08-04 杰富意钢铁株式会社 奥氏体类不锈钢包层钢板及其制造方法
CN107075645B (zh) * 2014-11-11 2020-06-16 杰富意钢铁株式会社 Ni合金包层钢板及其制造方法
KR102115278B1 (ko) * 2016-02-25 2020-05-26 닛폰세이테츠 가부시키가이샤 내충격 박리성 및 가공부 내식성이 우수한 고강도 용융 아연 도금 강판
WO2018179169A1 (fr) * 2017-03-29 2018-10-04 新日鐵住金株式会社 Tuyau en acier soudé par résistance électrique de type brut de laminage pour tuyaux de canalisation
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JPS52102848A (en) * 1976-02-26 1977-08-29 Nippon Steel Corp Method of gas shield arc welding
JPH0657377A (ja) * 1992-08-12 1994-03-01 Nippon Steel Corp 加工時の耐界面破壊性に著しく優れた高耐食性クラッド鋼板
WO2019189871A1 (fr) * 2018-03-30 2019-10-03 日鉄ステンレス株式会社 Tôle d'acier inoxydable revêtu biphasé et son procédé de production
WO2020071343A1 (fr) * 2018-10-01 2020-04-09 日鉄ステンレス株式会社 Tôle d'acier inoxydable austénitique plaquée, tôle d'acier de base et procédé de production de tôle d'acier plaquée

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CN115210399A (zh) 2022-10-18
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