EP3121304B1 - Acier inoxydable à base de ferrite et procédé de production s'y rapportant - Google Patents

Acier inoxydable à base de ferrite et procédé de production s'y rapportant Download PDF

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Publication number
EP3121304B1
EP3121304B1 EP15764119.2A EP15764119A EP3121304B1 EP 3121304 B1 EP3121304 B1 EP 3121304B1 EP 15764119 A EP15764119 A EP 15764119A EP 3121304 B1 EP3121304 B1 EP 3121304B1
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Prior art keywords
steel
nitrogen
brazing
content
nitrogen concentration
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German (de)
English (en)
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EP3121304A1 (fr
EP3121304A4 (fr
Inventor
Kunio Fukuda
Mitsuyuki Fujisawa
Akito Mizutani
Tomohiro Ishii
Chikara Kami
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JFE Steel Corp
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JFE Steel Corp
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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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • 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
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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/02—Pretreatment of the material to be coated
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    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
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    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
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    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
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    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
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    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
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    • C21D6/00—Heat treatment of ferrous alloys
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Definitions

  • the present disclosure relates to a ferritic stainless steel having excellent corrosion resistance and displaying good brazing properties when brazing is carried out at high temperature using a Ni-containing brazing metal, and to a production method for the ferritic stainless steel.
  • An exhaust heat recovery unit is an apparatus that improves fuel efficiency by, for example, using heat from engine coolant for automobile heating and using heat from exhaust gas to warm up engine coolant in order to shorten warming-up time when the engine is started up.
  • the exhaust heat recovery unit is normally located between a catalytic converter and a muffler, and includes a heat exchanger part formed by a combination of pipes, plates, fins, side plates, and so forth, and entry and exit pipe parts. Exhaust gas enters the heat exchanger part through the entry pipe, transfers its heat to a coolant via a heat-transfer surface such as a fin, and is discharged from the exit pipe. Bonding and assembly of plates, fins, and so forth forming the heat exchanger part of an exhaust heat recovery unit such as explained above is mainly carried out by brazing using a Ni-containing brazing metal.
  • An EGR cooler includes a pipe for intake of exhaust gas from an exhaust manifold or the like, a pipe for returning the exhaust gas to a gas intake-side of an engine, and a heat exchanger for cooling the exhaust gas.
  • the EGR cooler more specifically has a structure in which a heat exchanger including both a water flow passage and an exhaust gas flow passage is located on a path along which exhaust gas is returned to the gas intake-side of the engine from the exhaust manifold.
  • the heat exchanger part of the EGR cooler is formed by overlapping thin plates in a fin shape for reasons such as improving compactness, and reducing weight and cost. Bonding and assembly of these thin plates is mainly carried out by brazing using a Ni-containing brazing metal.
  • a heat exchanger part in an exhaust heat recovery unit or an EGR cooler such as described above are carried out by brazing using a Ni-containing brazing metal
  • materials used in the heat exchanger part are expected to have good brazing properties with respect to the Ni-containing brazing metal.
  • a heat exchanger part such as described above is expected to be highly resistant to oxidation caused by high-temperature exhaust gas passing through the heat exchanger part.
  • the exhaust gas includes small amounts of nitrogen oxides (NO x ), sulfur oxides (SO x ), and hydrocarbons (HC) that may condense in the heat exchanger to form a strongly acidic and corrosive condensate.
  • materials used in a heat exchanger part such as described above are expected to have corrosion resistance at normal temperatures.
  • brazing heat treatment is carried out at high temperature, it is necessary to prevent formation of a Cr depletion layer due to preferential reaction of Cr at grain boundaries with C and N, which is referred to as sensitization, in order to ensure that corrosion resistance is obtained.
  • austenite-based stainless steel such as SUS316L or SUS304L that has a reduced carbon content and is resistant to sensitization.
  • austenite-based stainless steels suffer from problems such as high cost due to having high Ni content, and also poor heat fatigue properties at high temperatures and poor fatigue properties when used in an environment in which constraining force is received at high temperature and with violent vibration, such as when used as a component located peripherally to an exhaust manifold.
  • steels other than austenite-based stainless steels are being considered for use in heat exchanger parts of exhaust heat recovery units and EGR coolers.
  • PTL 1 discloses, as a heat exchanger component of an exhaust heat recovery unit, a ferritic stainless steel that has added Mo, Ti, or Nb and that has reduced Si and Al content. PTL 1 discloses that addition of Ti or Nb prevents sensitization by stabilizing C and N in the steel as carbonitrides of Ti and Nb and that reduction of Si and Al content improves brazing properties.
  • PTL 2 discloses, as a component for a heat exchanger of an exhaust heat recovery unit, a ferritic stainless steel having excellent condensate corrosion resistance in which Mo content is defined by Cr content, and Ti and Nb content is defined by C and N content.
  • PTL 3 discloses, as a material for an EGR cooler, a ferritic stainless steel in which added amounts of components such as Cr, Cu, Al, and Ti satisfy a certain relationship.
  • PTL 4 and 5 disclose, as a component of an EGR cooler and a material for a heat exchanger part of an EGR cooler, a ferritic stainless steel containing 0.3 mass% to 0.8 mass% of Nb and a ferritic stainless steel containing 0.2 mass% to 0.8 mass% of Nb.
  • PTL 7 describes a ferritic stainless steel for automotive muffler applications, and its production method.
  • the steel has a stable oxide film to raise the corrosion resistance in a muffler environment.
  • PTL 7 further discloses the method to produce this oxide film and the atmosphere annealing is executed under an atmosphere of 80-100% H2, remainder N2, dew point: -45 to -70°C, annealing temperature: 850-970°C, holding time: 20-200s.
  • the pre- or post- processing consists of etching chemically or electrolytically. In both cases a stable oxide film is formed during the etching.
  • brazing of the steel disclosed in PTL 1 is carried out using a copper brazing metal having a low brazing temperature and inadequate brazing may, therefore, occur in a situation in which a Ni-containing brazing metal (for example, BNi-2 or BNi-5 stipulated by Japanese Industrial Standards (JIS Z 3265)) having a high brazing temperature is used.
  • a Ni-containing brazing metal for example, BNi-2 or BNi-5 stipulated by Japanese Industrial Standards (JIS Z 3265) having a high brazing temperature
  • a problem of reduced brazing properties may occur as a result of a thick Ti oxide film being formed such that spreading of the brazing metal is decreased when brazing is carried out at a temperature that is high, even among brazing metals in which a Ni-containing brazing metal is used.
  • steel disclosed in PTL 4 and 5 has a high Nb content in order to inhibit coarsening of crystal grains during brazing using a Ni-containing brazing metal and prevent reduction in toughness, and a certain degree of improvement of brazing properties is obtained in a situation in which Ti and Al are not contained in the steel.
  • Nb is also expensive, which is problematic in terms of production costs.
  • the present disclosure is the result of development conducted in order to solve the problems described above and an objective thereof is to provide a ferritic stainless steel that has excellent corrosion resistance, displays good brazing properties when brazing is carried out at high temperature using a Ni-containing brazing metal, and can be produced by a highly efficient production process, and also to provide a production method for this ferritic stainless steel.
  • the inventors decided to use Ti as a stabilizing element for C and N due to the fact that, unlike Nb addition, Ti addition does not lead to a higher recrystallization temperature.
  • the inventors conducted diligent investigation in which they produced Ti-containing ferritic stainless steel using various different chemical compositions and production conditions, and investigated various properties thereof, particularly brazing properties when brazing is carried out at high temperature using a Ni-containing brazing metal.
  • the inventors conducted further investigation with an objective of effectively inhibiting formation of an oxide film of Ti, Al, or the like when brazing is carried out at high temperature using a Ni-containing brazing metal.
  • the inventors also realized that steel having a nitrogen-enriched layer formed therein as described above is also extremely advantageous in terms of production efficiency because an efficient production process is applicable thereto.
  • a ferritic stainless steel can be obtained that has excellent corrosion resistance and that displays good brazing properties when brazing is carried out at high temperature using a Ni-containing brazing metal.
  • ferritic stainless steel can be produced by a highly efficient production process and is, therefore, extremely advantageous in terms of productions costs.
  • C is an element contained incidentally in the steel. Strength of the steel improves with increasing C content whereas workability of the steel improves with decreasing C content.
  • the C content is required to be 0.003% or greater in order to obtain sufficient strength.
  • the C content is in a range of 0.003% to 0.020%.
  • the C content is preferably in a range of 0.010% to 0.020%.
  • Si is a useful element as a deoxidizer. This effect is obtained through Si content of 0.05% or greater. However, if Si content is greater than 1.00%, workability noticeably decreases and forming becomes difficult. Furthermore, application of a high-speed pickling process using a normal carbon steel production line as described in PTL 6 becomes difficult if the Si content is greater than 1.00%. Accordingly, the Si content is in a range of 0.05% to 1.00%. The Si content is preferably in a range of 0.10% to 0.50%. Moreover, an upper limit for the Si content is more preferably 0.40%, and particularly preferably 0.30%.
  • Mn has a deoxidizing effect that is obtained through Mn content of 0.10% or greater.
  • excessive Mn addition leads to loss of workability due to solid solution strengthening.
  • excessive Mn decreases corrosion resistance by promoting precipitation of MnS, which acts as a starting point for corrosion. Therefore, Mn content of 0.50% or less is appropriate. Accordingly, the Mn content is in a range of 0.10% to 0.50%.
  • the Mn content is preferably in a range of 0.15% to 0.50%.
  • an upper limit for the Mn content is more preferably 0.35%, and particularly preferably 0.25%.
  • P is an element that is incidentally included in the steel.
  • excessive P content reduces weldability and facilitates grain boundary corrosion. This trend is noticeable if the P content is greater than 0.05%. Accordingly, the P content is 0.05% or less.
  • the P content is preferably 0.03% or less.
  • the P content is preferably 0.02% or greater.
  • S is an element that is incidentally contained in the steel, and that promotes MnS precipitation and decreases corrosion resistance if S content is greater than 0.01%. Accordingly, the S content is 0.01% or less. The S content is preferably 0.007% or less.
  • Cr is an important element for ensuring corrosion resistance of the stainless steel. Adequate corrosion resistance after brazing is not obtained if Cr content is less than 16.0%. However, excessive addition of Cr causes deterioration of workability. Accordingly, the Cr content is in a range of 16.0% to 25.0%. The Cr content is preferably in a range of 18.0% to 23.0%.
  • Ti is an element that prevents the precipitation of Cr carbonitride, which decreases corrosion resistance (sensitization), since Ti combines with C and N preferentially. This effect is obtained through Ti content of 0.05% or greater.
  • Ti is not a particularly preferable element from a viewpoint of brazing properties. The reason for this is that Ti is an active element with respect to oxygen and thus brazing properties are decreased as a result of a dense and continuous Ti oxide film being formed during brazing.
  • Ti oxide film formation is prevented in the present disclosure through creation of a nitrogen-enriched layer in a surface layer of the steel, but it is not possible to adequately prevent Ti oxide film formation if Ti content is greater than 0.35%. Accordingly, the Ti content is in a range of 0.05% to 0.35%.
  • the Ti content is preferably in a range of 0.10% to 0.25%, and is more preferably in a range of 0.10% to 0.20%.
  • Al is a useful element for deoxidization, which is obtained as an effect through Al content of 0.005% or greater.
  • Al is not a particularly preferable element from a viewpoint of brazing properties.
  • Al oxide film formation is prevented in the present disclosure through creation of the nitrogen-enriched layer in the surface layer of the steel, but it is not possible to adequately prevent Al oxide film formation if Al content is greater than 0.05%. Accordingly, the Al content is in a range of 0.005% to 0.05%.
  • the Al content is preferably in a range of 0.01% to 0.03%.
  • N is an important element for preventing Ti or Al oxide film formation and improving brazing properties through creation of the nitrogen-enriched layer.
  • N content is required to be 0.005% or greater in order to create the nitrogen-enriched layer.
  • N content of greater than 0.025% facilitates sensitization and reduces workability. Accordingly, the N content is in a range of 0.005% to 0.025%.
  • the N content is preferably in a range of 0.007% to 0.020%.
  • the chemical composition in the present disclosure may appropriately further contain the following elements as required.
  • Ni is an element that effectively contributes to improving toughness and to improving crevice corrosion resistance when contained in an amount of 0.05% or greater.
  • Ni content of greater than 0.50% increases stress corrosion crack sensitivity.
  • Ni is an expensive element that leads to increased costs. Accordingly, in a situation in which Ni is contained in the steel, the Ni content is in a range of 0.05% to 0.50%.
  • the Ni content is preferably in a range of 0.10% to 0.30%.
  • Mo improves corrosion resistance by stabilizing a passivation film of the stainless steel.
  • Mo has an effect of preventing inner surface corrosion by a condensate and outer surface corrosion by a snow-melting agent or the like.
  • Mo has an effect of improving high-temperature heat fatigue properties and is a particularly preferable element in a situation in which the steel is used in an EGR cooler attached directly below an exhaust manifold. These effects are obtained through Mo content of 0.10% or greater.
  • Mo is an expensive element that leads to increased costs.
  • Mo content of greater than 3.00% reduces workability. Accordingly, in a situation in which Mo is contained in the steel, the Mo content is in a range of 0.10% to 3.00%.
  • the Mo content is preferably in a range of 0.50% to 2.50%.
  • Cu is an element that enhances corrosion resistance. This effect is obtained through Cu content of 0.10% or greater. However, Cu content of greater than 0.60% reduces hot workability. Accordingly, in a situation in which Cu is contained in the steel, the Cu content is in a range of 0.10% to 0.60%. The Cu content is preferably in a range of 0.20% to 0.50%.
  • V 0.01% to 0.50%
  • V combines with C and N contained in the steel and prevents sensitization in the same way as Ti. V also has an effect of creating the nitrogen-enriched layer by combining with nitrogen. These effects are obtained through V content of 0.01% or greater. On the other hand, V content of greater than 0.50% reduces workability. Accordingly, in a situation in which V is contained in the steel, the V content is in a range of 0.01% to 0.50%. The V content is preferably in a range of 0.05% to 0.40%.
  • Nb combines with C and N contained in the steel and prevents sensitization in the same way as Ti. Nb also has an effect of creating the nitrogen-enriched layer by combining with nitrogen. These effects are obtained through Nb content of 0.01% or greater.
  • Nb content of greater than 0.15% raises the recrystallization temperature such that an efficient high-speed pickling process such as described in PTL 6 cannot be adopted. Accordingly, in a situation in which Nb is contained in the steel, the Nb content is in a range of 0.01% to 0.15%.
  • the Nb content is preferably in a range of 0.01% to 0.10%.
  • Ca improves weldability by improving penetration of a welded part. This effect is obtained through Ca content of 0.0003% or greater. However, Ca content of greater than 0.0040% decreases corrosion resistance by combining with S to form CaS. Accordingly, in a situation in which Ca is contained in the steel, the Ca content is in a range of 0.0003% to 0.0040%. The Ca content is preferably in a range of 0.0005% to 0.0030%.
  • B is an element that improves resistance to secondary working brittleness. This effect is exhibited when B content is 0.0003% or greater. However, B content of greater than 0.0100% reduces ductility due to solid solution strengthening. Accordingly, in a situation in which B is contained in the steel, the B content is in a range of 0.0003% to 0.0100%. The B content is preferably in a range of 0.0005% to 0.0030%.
  • components other than those listed above are Fe and incidental impurities.
  • the chemical composition of the steel is appropriately controlled such as to be in the range described above and that a nitrogen-enriched layer such as described below is created in the surface layer part of the steel by performing heat treatment in a controlled atmosphere prior to brazing.
  • Nitrogen concentration peak value at depth of within 0.05 ⁇ m of surface 0.05 mass% to 0.30 mass%
  • a nitrogen-enriched layer is created that has a nitrogen concentration peak value of 0.05 mass% to 0.30 mass% at a depth of within 0.05 ⁇ m of the surface of the steel in a depth direction.
  • This nitrogen-enriched layer can prevent formation of a continuous and dense oxide film of Ti, Al, or the like at the surface and, as a result, can improve brazing properties when a Ni-containing brazing metal is used.
  • N in the nitrogen-enriched layer described above combines with Ti, Al, V, Nb, Cr, and the like in the steel.
  • the following describes a mechanism which the inventors consider to be responsible for the nitrogen-enriched layer inhibiting formation of a Ti or Al oxide film.
  • formation of the nitrogen-enriched layer causes Ti and Al present in the surface layer part of the steel to combine with N such that the Ti and Al cannot diffuse to the surface of the steel. Furthermore, Ti and Al present inward of the nitrogen-enriched layer cannot diffuse to the surface of the steel because the nitrogen-enriched layer acts as a barrier. According, formation of a Ti or Al oxide film is inhibited as a result of Ti and Al in the steel not diffusing to the surface.
  • the nitrogen concentration peak value is less than 0.05 mass%.
  • the surface layer part hardens if the nitrogen concentration peak value is greater than 0.30 mass%, making defects more likely to occur, such as fin plate cracking due to hot vibration of an engine or the like.
  • the nitrogen concentration peak value at a depth of within 0.05 ⁇ m of the surface has a value in a range of 0.05 mass% to 0.30 mass%.
  • the nitrogen concentration peak value is preferably in a range of 0.07 mass% to 0.20 mass%.
  • the nitrogen concentration peak value at a depth of within 0.05 ⁇ m of the surface referred to herein can for example be calculated by measuring nitrogen concentration in the steel in a depth direction by glow discharge optical emission spectroscopy, dividing a maximum value for nitrogen concentration at a depth of within 0.05 ⁇ m of the steel surface by a measured value for nitrogen concentration at a depth of 0.50 ⁇ m, and multiplying the resultant value by the nitrogen concentration of the steel obtained though chemical analysis.
  • the nitrogen-enriched layer described herein refers to a region in which nitrogen is enriched due to permeation of nitrogen from the surface of the steel.
  • the nitrogen-enriched layer is created in the surface layer part of the steel and more specifically in a region spanning for a depth of approximately 0.005 ⁇ m to 0.05 ⁇ m in the depth direction from the surface of the steel.
  • Molten steel having the chemical composition described above is prepared by steelmaking through a commonly known method such as using a converter, an electric heating furnace, or a vacuum melting furnace, and is subjected to continuous casting or ingot casting and blooming to obtain a semi-finished casting product (slab).
  • the semi-finished casting product is hot rolled to obtain a hot-rolled sheet either directly without prior heating or after heating at 1100°C to 1250°C for 1 hour to 24 hours.
  • the hot-rolled sheet is normally subjected to hot band annealing at 800°C to 1100°C for 1 minute to 10 minutes, but depending on the intended use, this hot band annealing may be omitted.
  • the sheet is subjected to a combination of cold rolling and annealing to obtain a product steel sheet.
  • the cold rolling is preferably performed with a rolling reduction rate of 50% or greater in order to improve shape correction, extensibility, bendability, and press formability. Furthermore, the cold rolling and annealing process may be repeated two or more times.
  • Treatment for creating the nitrogen-enriched layer is preferably performed during final annealing (finish annealing) carried out after the cold rolling.
  • treatment for creating the nitrogen-enriched layer can be performed in a separate step to annealing, such as, for example, after a component has been cut from the steel sheet.
  • annealing such as, for example, after a component has been cut from the steel sheet.
  • the following describes conditions in treatment for creating the nitrogen-enriched layer.
  • the dew point is -20°C or lower.
  • the dew point is preferably -30°C or lower.
  • the nitrogen concentration of the treatment atmosphere is less than 5 vol%, a nitrogen-enriched layer is not created because an insufficient amount of nitrogen permeates into the steel. Accordingly, the nitrogen concentration of the treatment atmosphere is 5 vol% or greater.
  • the nitrogen concentration of the treatment atmosphere is preferably 10 vol% or greater.
  • the remainder of the treatment atmosphere, besides nitrogen, is hydrogen.
  • Treatment temperature 800°C or higher
  • the treatment temperature is 800°C or higher.
  • the treatment temperature is preferably 850°C or higher.
  • the treatment temperature is preferably 1050°C or lower because a treatment temperature of higher than 1050°C (particularly 1100°C or higher) leads to deformation of the steel.
  • the treatment temperature is more preferably 1000°C or lower, and is particularly preferably 950°C or lower.
  • the treatment time is preferably in the range of 5 seconds to 3600 seconds.
  • the reason for this is that nitrogen in the treatment atmosphere does not sufficiently permeate into the steel if the treatment time is shorter than 5 seconds, whereas the effects of treatment reach saturation if the treatment time is longer than 3600 seconds.
  • the treatment time is preferably in a range of 30 seconds to 300 seconds.
  • descaling may be performed after final annealing (finish annealing) by normal pickling or polishing, from a viewpoint of production efficiency, it is preferable to perform descaling by adopting the high-speed pickling process described in PTL 6 in which mechanical grinding is performed using a brush roller, a polishing powder, shot blasting, or the like, and pickling is subsequently performed in a nitrohydrochloric acid solution.
  • descaling was performed by carrying out pickling in which the sheet was immersed in a 200 g/l sulfuric acid solution at a temperature of 80°C for 120 seconds and was subsequently immersed in a mixed acid of 150 g/l of nitric acid and 30 g/l of hydrofluoric acid at a temperature of 55°C for 60 seconds.
  • brazing was carried out for each cold-rolled and annealed sheet using a Ni-containing brazing metal and the cold-rolled and annealed sheet was evaluated after brazing in terms of (3) corrosion resistance and (4) brazing properties.
  • the evaluation of (4) brazing properties was performed as described below for (a) joint gap infiltration of the brazing metal and (b) joint strength of a brazed part.
  • GDS glow discharge optical emission spectroscopy
  • Nitrogen concentration was measured while performing sputtering from the surface of the steel to a depth of 0.50 ⁇ m.
  • the measured values of Cr and Fe are fixed at the depth of 0.50 ⁇ m and thus a measured value for nitrogen concentration at the depth of 0.50 ⁇ m was taken to be the nitrogen concentration of the base material (steel substrate).
  • a highest peak value (greatest value) among measured nitrogen concentration values within 0.05 ⁇ m of the steel surface was divided by the measured nitrogen concentration value at the depth of 0.50 ⁇ m and the resultant value was multiplied by a nitrogen concentration of the steel obtained by chemical analysis to give a value that was taken to be a nitrogen concentration peak value at a depth of within 0.05 ⁇ m of the surface.
  • Nitrogen concentration peak values that were obtained are shown in Table 2.
  • V c'100 of 150 mV vs SCE
  • a 30 mm square sheet and a 25 mm ⁇ 30 mm sheet were cut out from each of the cold-rolled and annealed sheets and these two sheets were overlapped and clamped in place using a clamp jig with a fixed torque force (170 kgf).
  • a brazing metal was applied onto an end surface of one of the sheets and brazing was carried out. After the brazing, the degree to which the brazing metal had infiltrated between the sheets was visually confirmed from a side surface part of the overlapped sheets and was evaluated using the following standard. The evaluation results are shown in Table 2. Note that in the drawings, the reference sign 1 indicates the cold-rolled and annealed sheet and the reference sign 2 indicates the brazing metal.
  • portions of a JIS No. 13B tensile test piece that had been split at the center thereof were overlapped by 5 mm and were clamped in place using a clamp jig.
  • brazing was carried out by applying 0.1 g of a brazing metal to an overlapping part of one of the portions. After the brazing, a tensile test was conducted at normal temperature and joint strength of the brazed part was evaluated using the following standard. The evaluation results are shown in Table 2. Note that in the drawings, reference sign 3 indicates the tensile test piece.
  • the brazing metal was a representative Ni-containing brazing metal BNi-5 (19% Cr and 10% Si in a Ni matrix) stipulated by Japanese Industrial Standards.
  • the brazing was carried out in a sealed furnace. Furthermore, brazing was carried out in a high vacuum atmosphere of 10 -2 Pa and was also carried out in an Ar carrier gas atmosphere by enclosing Ar with a pressure of 100 Pa after forming a high vacuum.
  • Table 2 shows that for each of Examples 1-12, infiltration of the brazing metal into the joint gap was good and joint strength of the brazed part was good. Accordingly, it was demonstrated that Examples 1-12 display good brazing properties even when a Ni-containing brazing metal is used. Furthermore, Examples 1-12 had good corrosion resistance and ductility.
  • the present disclosure enables a ferritic stainless steel to be obtained that can be suitably used for heat exchanger components and the like of exhaust heat recovery units and EGR coolers that are assembled by brazing, and is therefore extremely useful in industry.

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Claims (2)

  1. Un acier inoxydable ferritique comprenant une composition chimique composée en % en masse de :
    0,003 % à 0,020 % de C;
    0,05 % à 1,00 % de Si ;
    0,10 % à 0,50 % de Mn ;
    0,05 % ou moins de P ;
    0,01 % ou moins de S ;
    16,0 % à 25,0% de Cr;
    0,05 % à 0,35 % de Ti ;
    0,005 % à 0,05 % d'Al ; et
    0,005 % à 0,025 % de N, éventuellement, un ou plusieurs de
    0,05 % à 0,50 % de Ni ;
    0,10 % à 3,00 % de Mo;
    0,10 % à 0,60 % de Cu ;
    0,01 % à 0,50 % de V;
    0,01 % à 0,15 % de Nb;
    0,0003 % à 0,0040 % de Ca ; et
    0,0003 % à 0,0100 % de B,
    le reste étant le Fe et des impuretés accidentelles, dans lequel une couche enrichie en azote dans la partie de la couche de surface de l'acier est présente et comporte une valeur de crête de concentration d'azote de 0,05 % en masse à 0,30 % en masse à une profondeur de 0,05 µm d'une surface de l'acier, dans lequel la valeur de crête de la concentration d'azote est calculée en mesurant la concentration d'azote dans l'acier dans une direction de profondeur par spectroscopie d'émission optique de décharge luminescente, en divisant une valeur maximale pour la concentration d'azote à une profondeur de 0,05 µm à l'intérieur de la surface de l'acier par une valeur mesurée pour la concentration d'azote à une profondeur de 0,50 µm et en multipliant la valeur résultante par la concentration d'azote de l'acier obtenue par analyse chimique.
  2. Un procédé de production destiné à l'acier inoxydable ferritique selon la revendication 1, comprenant
    la soumission d'une brame présentant la composition chimique selon la revendication 1 à un laminage à chaud, à un recuit à bande chaude ultérieur au besoin, à une combinaison de laminage à froid et de recuit ultérieurs et au décapage ou au polissage ultérieurs au besoin, pour produire l'acier inoxydable ferritique, dans lequel le recuit final du traitement de recuit destiné à la création d'une couche enrichie en azote est effectué à une température de 800 °C ou plus et 950 °C ou moins dans une atmosphère présentant une température de point de rosée de -20 °C ou moins, une concentration d'azote de 5 % en volume ou plus et la partie restante d'une atmosphère de traitement étant l'hydrogène pendant au moins 5 secondes et
    en décapant ou en polissant, la quantité de décapage ou de polissage est ajustée afin que la couche enrichie en azote ne soit pas supprimée.
EP15764119.2A 2014-03-20 2015-02-25 Acier inoxydable à base de ferrite et procédé de production s'y rapportant Active EP3121304B1 (fr)

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US20170088912A1 (en) 2017-03-30
EP3121304A1 (fr) 2017-01-25
WO2015141145A8 (fr) 2016-07-07
EP3121304A4 (fr) 2017-04-26
CN106103773B (zh) 2018-02-27
JP5846339B1 (ja) 2016-01-20
KR20160122824A (ko) 2016-10-24
CN106103773A (zh) 2016-11-09
WO2015141145A1 (fr) 2015-09-24
KR101830561B1 (ko) 2018-02-20
JPWO2015141145A1 (ja) 2017-04-06

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