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EP3683324A1 - Austenitischer edelstahl und verfahren zur herstellung davon - Google Patents

Austenitischer edelstahl und verfahren zur herstellung davon Download PDF

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Publication number
EP3683324A1
EP3683324A1 EP18856267.2A EP18856267A EP3683324A1 EP 3683324 A1 EP3683324 A1 EP 3683324A1 EP 18856267 A EP18856267 A EP 18856267A EP 3683324 A1 EP3683324 A1 EP 3683324A1
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EP
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Prior art keywords
mass
equal
less
stainless steel
austenitic stainless
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EP18856267.2A
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English (en)
French (fr)
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EP3683324A4 (de
Inventor
Yosuke YONENAGA
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Maruichi Stainless Tube Co Ltd
Original Assignee
Kobelco Steel Tube Co Ltd
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Application filed by Kobelco Steel Tube Co Ltd filed Critical Kobelco Steel Tube Co Ltd
Publication of EP3683324A1 publication Critical patent/EP3683324A1/de
Publication of EP3683324A4 publication Critical patent/EP3683324A4/de
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • C21D6/02—Hardening by precipitation
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite

Definitions

  • the present invention relates to an austenitic stainless steel and a production method thereof.
  • Austenitic stainless steels are extensively used in various applications as steel materials superior in strength, workability, corrosion resistance, and the like. Further, various kinds of austenitic stainless steels having controlled component compositions, crystal structures, and the like have been developed in attempts to further improve performance in accordance with applications and the like (see Patent Documents 1 to 5).
  • high-strength stainless steels such as duplex stainless steels are used for automobile fuel injection tubes in light of reduction in weight, prevention of fatigue fractures, corrosion resistance against salt water, and the like.
  • materials used for automobile fuel injection tubes as well, development of materials having strength (proof stress, tensile strength) and the like higher than those of conventional materials has been desired to support an extension of useful life, higher performance, and the like.
  • a brazing heat treatment may be performed on steel tubes. When such a heat treatment is performed, strength of the steel tube may be reduced, and there is also a problem of the duplex stainless steel being unable to retain a straight tube shape.
  • the present invention was made on the basis of the foregoing circumstances and an object of the present invention is to provide: an austenitic stainless steel having high strength and favorable shape retention properties after a heat treatment; and a production method thereof.
  • One aspect of the present invention made for solving the aforementioned problems is an austenitic stainless steel wherein a component composition satisfies C: less than or equal to 0.12% by mass; Si: greater than or equal to 0.1% by mass and less than or equal to 1.0% by mass; Mn: greater than or equal to 0.1% by mass and less than or equal to 3.0% by mass; P: less than or equal to 0.05% by mass; S: less than or equal to 0.01% by mass; Cr: greater than or equal to 13.0% by mass and less than or equal to 22.0% by mass; Ni: greater than or equal to 4.0% by mass and less than or equal to 12.0% by mass; Cu: greater than or equal to 0.01% by mass and less than or equal to 0.50% by mass; Mo: less than or equal to 5.0% by mass; Al: less than or equal to 0.03% by mass; Nb: greater than or equal to 0.05% by mass and less than or equal to 0.30% by mass; N: greater than or equal to 0.10% by mass and less than or equal to
  • the austenitic stainless steel by virtue of having the above component composition and crystal grain size, has high strength (proof stress and tensile strength) due to solid-solution strengthening and/or crystal grain miniaturization.
  • the austenitic stainless steel being the austenitic stainless steel having the component composition and crystal grain size described above, has favorable shape retention properties after a heat treatment.
  • the above component composition further satisfies the following inequality (1).
  • coarsening of crystal grains may be inhibited even when a heat treatment such as brazing or the like is performed.
  • reduction in strength of the steel after the heat treatment may be suppressed.
  • [%C], [%Cr], [%N], and [%Nb] represent the content (% by mass) of each component.
  • a maximum crystal grain diameter of the austenitic stainless steel is preferably less than or equal to 60 ⁇ m. In such a case, the coarsening of crystal grains may be inhibited even if a heat treatment such as brazing is performed. Thus, reduction in strength of the steel after the heat treatment may be suppressed.
  • the component composition described above further satisfies the following inequality (2). Controlling the content of carbon and nitrogen in this way can, for example, further enhance the strength. 0.20 ⁇ % C + % N ⁇ 0.40
  • [%C] and [%N] represent the content (% by mass) of each component.
  • the austenitic stainless steel preferably has a maximum height Ry of less than or equal to 10 ⁇ m. Increasing a smoothness of a surface of the austenitic stainless steel in this way can improve corrosion resistance and the like.
  • the austenitic stainless steel is preferably a seamless steel tube.
  • austenitic stainless steel is a seamless tube, breakage originating in a welding portion can be avoided.
  • the austenitic stainless steel is a seamless steel tube, it can be more suitably used for automobile fuel injection tubes and the like, to which repeated stress from internal pressure is applied.
  • the austenitic stainless steel due to its superior strength, can also sufficiently support an increase in direct-injection pressure in automobile engines, and therefore can be suitably used for automobile fuel injection tubes.
  • the austenitic stainless steel due also to its favorable shape retention properties after the heat treatment, can be suitably used for automobile fuel injection tubes to be subjected to a brazing heat treatment.
  • a production method A of the austenitic stainless steel comprising: performing cold working on a steel material with a working rate per pass of greater than or equal to 20%; and performing a heat treatment on the steel material before and after performing the cold working, wherein a heat treatment temperature T (°C) in the heat treatment satisfies the following inequality (3): 1,000 ⁇ T ⁇ ⁇ 2090 % C + 12.8 % Cr + 320 % N + 42.3 % Nb + 900 wherein, in the inequality (3), [%C], [%Cr], [%N], and [%Nb] represent the content (% by mass) of each component in the steel material.
  • an austenitic stainless steel having high strength and favorable shape retention properties after a heat treatment can be obtained by performing solid-solution strengthening and/or crystal grain miniaturization strengthening.
  • a still other aspect of the present invention made for solving the aforementioned problems is a production method B of the austenitic stainless steel comprising: performing cold working on a steel material with a working rate per pass of greater than or equal to 20%; and performing a heat treatment on the steel material before and after performing the cold working, wherein a heat treatment temperature T (°C) in the heat treatment is greater than or equal to 1,000°C and less than or equal to 1,200°C.
  • an austenitic stainless steel having high strength and favorable shape retention properties after a heat treatment can be obtained by performing solid-solution strengthening and/or crystal grain miniaturization strengthening.
  • a final heat treatment after the cold working is preferably bright annealing.
  • the final heat treatment is open air annealing
  • subsequent pickling is required, which causes surface roughening due to scale peeling and/or dissolution by acid.
  • performing the bright annealing as the final heat treatment in this way makes pickling unnecessary; accordingly, the surface roughness does not occur.
  • the austenitic stainless steel which is obtained has high smoothness, and as a result, is superior in corrosion resistance and the like.
  • the present invention can provide an austenitic stainless steel having high strength and favorable shape retention properties after a heat treatment, and a production method thereof.
  • An austenitic stainless steel according to one embodiment of the present invention has a specific component composition and crystal grain size, thereby exhibiting high strength. It is to be noted that the austenitic stainless steel is substantially composed of an austenitic single phase, and its shape retention properties after a heat treatment are better than those of ferritic-austenitic duplex stainless steels. In the austenitic stainless steel of this embodiment, typically, greater than or equal to 99% of the structure is in the austenite phase.
  • the component composition of the austenitic stainless steel comprises a predetermined amount of C, Si, Mn, P, S, Cr, Ni, Cu, Mo, Al, Nb, and N, and the balance comprises Fe and inevitable impurities.
  • a numerical range of the content of each component and a reason for the limitation will be described below.
  • C is an element effective for solid-solution strengthening and austenite phase stabilization.
  • C is an element that forms non-intermetallic compounds by being added together with Cr, Nb, and N, thereby effectively serving to inhibit crystal grain coarsening due to a heat treatment.
  • a content of C is set to less than or equal to 0.12% by mass for forming the non-intermetallic compounds as aimed.
  • the upper limit of the content of C is preferably 0.10% by mass, more preferably 0.08% by mass, and still more preferably 0.06% by mass.
  • the lower limit of the content of C may be more than 0% by mass, and because of the solid-solution strengthening and the like due to adding C, is preferably 0.01% by mass, and more preferably 0.02% by mass.
  • Si Greater than or equal to 0.1% by mass and less than or equal to 1.0% by mass
  • Si is an element effective for solid-solution strengthening of stainless steels.
  • Si becomes a factor that may impair brazing properties.
  • an amount of Si added must be less than or equal to 1.0% by mass.
  • the upper limit of a content of Si is preferably 0.8% by mass.
  • Si is also an element used for preliminary deoxidation in melting and casting.
  • a lower limit of the content is preferably 0.2% by mass, more preferably 0.3% by mass, still more preferably 0.35% by mass, sometimes even more preferably 0.4% by mass, and sometimes even more preferably 0.5% by mass.
  • Mn Greater than or equal to 0.1% by mass and less than or equal to 3.0% by mass
  • Mn manganese
  • MnS non-intermetallic compounds
  • a content of Mn is set to greater than or equal to 0.1% by mass and less than or equal to 3.0% by mass.
  • the lower limit of the content of Mn is preferably 0.3% by mass, more preferably 0.5% by mass, and still more preferably 0.7% by mass.
  • the upper limit of the content is preferably 2.7% by mass, and more preferably 2.4% by mass.
  • P phosphorus
  • P is an element which may be contained as an impurity. Since P may reduce hot workability, weldability, strength, and the like, a content of P is set to less than or equal to 0.05% by mass.
  • the upper limit of the content of P is preferably 0.04% by mass, more preferably 0.03% by mass, and still more preferably 0.02% by mass.
  • the lower limit of the content of P may be more than 0% by mass, and may be 0.001 % by mass or 0.005% by mass.
  • S sulfur
  • S is an element which may be contained as an impurity, and is an element that bonds with Mn and/or Ca to form non-intermetallic compounds that may harm corrosion resistance and/or mechanical properties. S forms sulfides and reduces corrosion resistance, and thus, an amount of S added should be limited to be as low as possible. Accordingly, the upper limit of a content of S must be 0.01% by mass, and is preferably 0.005% by mass, and more preferably 0.003% by mass. On the other hand, the lower limit of the content of S may be more than 0% by mass, and may be 0.0001 % by mass or 0.0003% by mass.
  • Cr chromium
  • Cr is an element effective for corrosion resistance improvement and solid-solution strengthening.
  • Cr forms non-intermetallic compounds when added in combination with C, Nb and N, thereby inhibiting the coarsening of crystal grains due to the heat treatment.
  • Increasing the amount of added Cr elevates the temperatures at which the non-intermetallic compounds are stable, and therefore, a microstructure can be maintained even when the heat treatment is performed at a higher temperature.
  • Cr acts as a ferrite-forming element, excessive addition must be avoided in such cases as when added amounts of C, Mn, Ni, and N are small, and the like.
  • a content of Cr is set to greater than or equal to 13.0% by mass and less than or equal to 22.0% by mass.
  • the upper limit of the content of Cr is preferably 21.0% by mass, and more preferably 20.0% by mass.
  • the lower limit of the content of Cr is preferably 15.0% by mass, more preferably 16.0% by mass, and even more preferably 18.0% by mass.
  • Ni Greater than or equal to 4.0% by mass and less than or equal to 12.0% by mass
  • Ni nickel
  • a content of Ni is set to greater than or equal to 4.0% by mass and less than or equal to 12.0% by mass.
  • the lower limit of the content of Ni is preferably 5.0% by mass, more preferably 7.0% by mass, and still more preferably 7.8% by mass. Further, by comparatively increasing the content of Ni, a single-phase austenitic stainless steel can be obtained.
  • the upper limit of the content of Ni is preferably 11.0% by mass, and more preferably 10.0% by mass.
  • Cu Greater than or equal to 0.01% by mass and less than or equal to 0.50% by mass
  • Cu copper is an austenite-forming element. Since Cu is an element that becomes mixed in from stainless steel scraps and the like, excessive reduction leads to an increase in raw material costs. Thus, a content of Cu is set to greater than or equal to 0.01% by mass and less than or equal to 0.50% by mass.
  • the lower limit of the content of Cu is sometimes preferably 0.05% by mass, and sometimes preferably 0.1 % by mass.
  • the upper limit of the content of Cu is preferably 0.40% by mass.
  • Mo molybdenum
  • Mo molybdenum
  • the upper limit of the content of Mo is sometimes preferably 1.0% by mass, sometimes more preferably 0.50% by mass, sometimes even more preferably 0.45% by mass, and sometimes yet even more preferably 0.40% by mass.
  • the lower limit of the content of Mo may be greater than 0% by mass, and is preferably 0.01% by mass, more preferably 0.05% by mass, and still more preferably 0.1% by mass.
  • Al is an element that has a deoxidation action, but stabilizes ferrite, and therefore, excessive addition of Al may lower the stability of austenite, thereby lowering its hot workability and/or ductility. Further, Al-based inclusions may be a cause of decreased workability and/or scratches on mirror surfaces.
  • the upper limit of a content of Al is 0.03% by mass, and is preferably 0.02% by mass.
  • the lower limit of the content of Al content may be greater than 0% by mass, and is sometimes preferably 0.001% by mass, and sometimes more preferably 0.005% by mass.
  • Nb Greater than or equal to 0.05% by mass and less than or equal to 0.30% by mass
  • Nb (niobium) forms non-intermetallic compounds when added in combination with C, Cr, and N, thereby inhibiting the coarsening of crystal grains due to the heat treatment.
  • Increasing an amount of added Nb elevates the temperatures at which the non-intermetallic compounds are stable, and therefore, the microstructure can be maintained even when the heat treatment is performed at a higher temperature.
  • Nb is an expensive element. Thus, excessive addition of Nb needs to be avoided in light of cost. Accordingly, a range of a content of Nb is set to greater than or equal to 0.05% by mass to less than or equal to 0.30% by mass.
  • the lower limit of the content of Nb is preferably 0.07% by mass, and more preferably 0.09% by mass.
  • the upper limit of the content of Nb is preferably 0.20% by mass, and more preferably 0.15% by mass.
  • N Greater than or equal to 0.10% by mass and less than or equal to 0.50% by mass
  • N nitrogen
  • N is an element effective for austenite stabilization, corrosion resistance improvement, and solid-solution strengthening.
  • N forms non-intermetallic compounds when added in combination with C, Cr, and Nb, thereby inhibiting the coarsening of crystal grains due to the heat treatment.
  • Increasing an amount of added N elevates the temperatures at which the non-intermetallic compounds are stable, which thereby inhibits the coarsening of crystal grains even when the heat treatment is performed at a higher temperature.
  • increasing the amount of added N decreases workability and the like.
  • a range of a content of N is set to greater than or equal to 0.10% by mass to less than or equal to 0.50% by mass.
  • the lower limit of the content of N is preferably 0.15% by mass, and more preferably 0.20% by mass.
  • the upper limit of the content of N is preferably 0.35% by mass, and more preferably 0.30% by mass.
  • Basic components of the component composition constituting the austenitic stainless steel are as described above, and remaining components comprise Fe and inevitable impurities.
  • the inevitable impurities are impurities inevitably mixed in during melt forming, and are contained within a range not impairing various properties of the steel tubes.
  • the component composition of the austenitic stainless steel may further comprise other elements in addition to the aforementioned components to an extent not adversely affecting effects of the present invention.
  • the component composition of the austenitic stainless steel preferably further satisfies the following inequality (1): 200 ⁇ ⁇ 2090 % C + 12.8 % Cr + 320 % N + 42.3 % Nb ⁇ 300
  • [%C], [%Cr], [%N], and [%Nb] represent the content (% by mass) of each component.
  • the present inventors have found that, by controlling the content of C, Cr, N, and Nb, the compounds (z-phase) of C, Cr, N, and Nb are stably present before and after the heat treatment, and crystal grain diameters and/or precipitate amounts are maintained before and after the heat treatment; therefore, crystal grain miniaturization strengthening and/or precipitation strengthening can be utilized even after the heat treatment. More specifically, it was found that, by having a component composition in which a value of -2090 [%C] + 12.8 [%Cr] + 320 [%N] + 42.3 [%Nb] is greater than or equal to 200 and less than or equal to 300, a temperature of a z-phase solid solution becomes greater than or equal to 1,100°C.
  • steel tubes used for automobile fuel injection tubes are typically processed into parts through a brazing heat treatment using a Cu-based brazing filler or the like. Since the Cu-based brazing filler has a melting point of 1,082°C, the heat treatment is often performed at approximately 1,080°C to 1,150°C. Thus, in a case in which the component composition of the austenitic stainless steel satisfies the above inequality (1), a grain boundary pinning effect or the like by the precipitates can be obtained even when the brazing heat treatment is performed in the above temperature range.
  • the component composition of the austenitic stainless steel preferably further satisfies the following inequality (2): 0.20 ⁇ % C + % N ⁇ 0.40
  • [%C] and [%N] represent the content (% by mass) of each component.
  • C and N effectively act as solid-solution strengthening elements.
  • Setting the value of [%C] + [%N] to greater than or equal to 0.20 provides sufficient solid-solution strengthening, which enables enhancement of the proof stress, the tensile strength, and the like.
  • the lower limit of [%C] + [%N] is preferably 0.25.
  • by setting the value of [%C] + [%N] to less than or equal to 0.40 sufficient workability can be attained, thereby reducing the frequency of crack occurrences when cold working is performed.
  • the upper limit of [%C] + [%N] is preferably 0.35.
  • the lower limit of a crystal grain size number of the austenite crystals is 7.0, and is preferably 8.0, more preferably 9.0, and still more preferably 9.5.
  • setting the crystal grain size number to greater than or equal to the lower limit in addition to having the specific component composition can facilitate crystal grain miniaturization strengthening, enabling expression of great strength. It is to be noted that generally, adding nitrogen and/or carbon as a solid-solution element is effective to strengthen a stainless steel, but excessive addition of these elements decreases workability due to strain aging. For this reason, in the austenitic stainless steel, the strengthening by crystal grain miniaturization is utilized to enhance the strength of the stainless steel while limiting the content of nitrogen and/or carbon.
  • the upper limit of the crystal grain size number of the austenite crystals is not particularly limited, but it may, for example, be 16.0, and may be 14.0, 13.0, 12.0, 11.5, or 11.0.
  • the crystal grain size number is a value measured in accordance with JIS G0551 (2013), and is specifically a value determined by a method described in the Examples.
  • the crystal grain size of the austenitic stainless steel can be adjusted by, for example, a heat treatment temperature before and after cold working, or the like, as will be described later.
  • the upper limit of a maximum crystal grain diameter of the austenitic crystals may, for example, be 200 ⁇ m, 150 ⁇ m, or 100 ⁇ m, but is preferably 60 ⁇ m, more preferably 50 ⁇ m, still more preferably 40 ⁇ m, and even more preferably 30 ⁇ m.
  • reducing the maximum crystal grain diameter in addition to having a greater crystal grain size number, or in other words, having a smaller average crystal grain diameter, as described above inhibits the mixed grain sizes and/or crystal grain coarsening after the heat treatment. As a result, reduction in strength of the steel after the heat treatment is suppressed.
  • the lower limit of the maximum crystal grain diameter is, for example, 1 ⁇ m, may be 5 ⁇ m, and may also be 10 ⁇ m.
  • the maximum crystal grain diameter is a value measured by a method described in the Examples described later.
  • the maximum crystal grain diameter of the austenitic stainless steel can be set to less than or equal to 60 ⁇ m.
  • the upper limit of a maximum height Ry is preferably 10 ⁇ m, more preferably 8 ⁇ m, and still more preferably 6 ⁇ m. Setting the maximum height of the austenitic stainless steel to less than or equal to the upper limit so as to increase the smoothness of a surface can enhance the corrosion resistance, fatigue strength, and the like of the austenitic stainless steel. That is, setting the maximum height of the austenitic stainless steel to less than or equal to the upper limit can, for example, extend the useful life of the austenitic stainless steel when it is used for automobile fuel injection tubes and the like.
  • the lower limit of the maximum height Ry is not particularly limited, but it, for example, is 0.5 ⁇ m, or may be 1 ⁇ m or 2 ⁇ m.
  • the maximum height Ry as referred to herein means a value measured in accordance with JIS B0601 (1994). It is to be noted that in a case in which the austenitic stainless steel is a steel tube, the maximum height Ry may be a measurement value on an external surface.
  • a surface roughness (maximum height Ry) of the austenitic stainless steel can be reduced by performing bright annealing as a final step as will be described later, subjecting the austenitic stainless steel to mirror finishing aside from the bright annealing, or the like.
  • the shape of the austenitic stainless steel is not particularly limited, and may be a plate shape, a rod shape, a tubular shape, or the like, but a tubular shape is preferred. That is, the austenitic stainless steel is suitably used as a steel tube.
  • the steel tube include a seamless steel tube, an electric resistance welded steel tube, an arc-welded steel tube such as a UOE steel tube or a spiral steel tube, a forged steel tube, and the like.
  • the seamless steel tube is preferred.
  • the austenitic stainless steel has high strength and can be applied to various applications.
  • the austenitic stainless steel can be suitably used for automobile fuel injection tubes.
  • the austenitic stainless steel can inhibit deformation after the brazing heat treatment, and can be made to maintain a crystal structure having high strength even after the heat treatment by adjusting the composition and the like.
  • the austenitic stainless steel is suitable as a material for automobile fuel injection tubes to be subjected to a brazing heat treatment.
  • a production method of an austenitic stainless steel according to one embodiment of the present invention comprises: performing cold working (1) on a steel material with a working rate per pass of greater than or equal to 20%; and performing a heat treatment (2) on the steel material before and after performing the cold working (1).
  • the steel material having the aforementioned component composition is cold-worked with a working rate per pass of greater than or equal to 20%.
  • the cold working include cold rolling, cold drawing, and the like, and a procedure is selected from these, depending on the shape and the like of the final product.
  • the cold drawing is suitably employed.
  • the working rate of cold working is greater than or equal to 20%, and is preferably greater than or equal to 25%.
  • the upper limit of the working rate per pass is preferably 50%, and more preferably 40%.
  • a heat treatment (2) is performed on the steel material.
  • the heat treatment temperature T (°C) in the heat treatment (2) preferably satisfies the following inequality (3) in both the heat treatment before and the heat treatment after the cold working (1). This can inhibit the coarsening of crystal grains due to the heat treatment and enhance the strength of the austenitic stainless steel to be obtained.
  • [%C], [%Cr], [%N], and [%Nb] represent the content (% by mass) of each component.
  • the value of -2090 [%C] + 12.8 [%Cr] + 320 [%N] + 42.3 [%Nb] in the component composition of the austenitic stainless steel is greater than or equal to 100.
  • the heat treatment temperature T (°C) in the heat treatment (2) is preferably greater than or equal to 1,000°C and less than or equal to 1,200°C for both the heat treatment before and the heat treatment after the cold working (1). This can inhibit the coarsening of crystal grains due to the heat treatment and enhance the strength of the austenitic stainless steel to be obtained.
  • the upper limit of the heat treatment temperature T is preferably 1,150°C, and more preferably 1,130°C.
  • the heat treatment procedure in the heat treatment (2) is not particularly limited, and a known procedure may be used for the heat treatment.
  • the heat treatment performed after the cold working (1) is preferably bright annealing.
  • the heat treatment performed after the cold working (1) is preferably a final heat treatment.
  • the bright annealing is a heat treatment performed in a reducing atmosphere, and can heat-treat the stainless steel without oxidizing the surface thereof. This enables omission of pickling after the heat treatment, and a stainless steel having great smoothness, which is to say superior corrosion resistance and the like, can be obtained.
  • the present invention is not limited to the embodiments described above. Various modifications and improvements can be made in addition to the aspects of the invention described above.
  • the final heat treatment may be performed with open-air annealing, followed by pickling, and then mirror-finishing the surface to increase the smoothness.
  • an ingot weighing 20 kg and being cylindrical, and having the component composition described in Table 1 (the balance being Fe and inevitable impurities) was prepared.
  • the ingot was heat-treated at greater than or equal to 1,250°C for 24 hours, and hot-forged at a temperature in a range of greater than or equal to 1,200°C to less than or equal to 1,000°C to prepare a plate material of W60 mm x L250 mm x t17 mm.
  • the plate material was heat-treated at a pre-cold working heat treatment temperature (Tc) as described in Table 1. Then, the plate material was cold-rolled at a working rate of 30%.
  • Tc pre-cold working heat treatment temperature
  • the plate material was heat-treated in a bright annealing furnace at a post-cold working heat treatment temperature (Tf) described in Table 1 to give test samples for Examples 1 to 7 and Comparative Examples 1 to 3.
  • Tf post-cold working heat treatment temperature
  • Examples 1 to 7 and Comparative Examples 1 to 2 are austenitic stainless steels
  • Comparative Example 3 is a duplex stainless steel.
  • an ingot weighing 150 kg and being cylindrical, and having the component composition (the balance being Fe and inevitable impurities) described in Table 1 was prepared.
  • the ingot was heat-treated for 24 hours at greater than or equal to 1,250°C, and hot-forged at a temperature in a range of greater than or equal to 1,200°C to less than or equal to 1,000°C to prepare a bloom of ⁇ 150 mm.
  • a billet of ⁇ 146 mm x 330 mm was prepared from the bloom, and a steel tube was obtained by the Ugine-Sejournet hot extrusion method.
  • the steel tube After being subjected to the heat treatment and the cold working multiple times, the steel tube was heat-treated at the pre-cold working heat treatment temperature (Tc) described in Table 1. Then, the steel tube was shaped by cold working with a working rate of 35%. Subsequently, as the final heat treatment, the steel was heat-treated in a bright annealing furnace at the post-cold working heat treatment temperature (Tf) described in Table 1 to give the test sample (austenitic stainless steel) of Example 8.
  • Tc pre-cold working heat treatment temperature
  • Tf post-cold working heat treatment temperature
  • a sample of 1 cm x 1 cm x 1.2 cm was cut out from each test sample (plate material) obtained in Examples 1 to 7 and Comparative Examples 1 to 3. Each sample was filled with a resin so that a width-thickness cross-section was visible, and a surface thereof was polished to a mirror finish; subsequently, each sample was subjected to a 65% nitric acid electrolytic etch to reveal a structure. Further, a sample was cut out from a test sample (steel tube) obtained in Example 8 so that a vertical surface in a lengthwise direction was visible.
  • the sample was filled with a resin so that a width-thickness cross-section was visible, and a surface thereof was polished to a mirror finish; subsequently, the sample was subjected to a 65% nitric acid electrolytic etch to reveal a structure.
  • the structure was observed with an optical microscope at a magnification of 400x to measure crystal grain size numbers in five fields of view, and a median value was determined to be the crystal grain size number.
  • Table 1 It is to be noted that "-" in the table indicates that a measurement was not performed.
  • the maximum height Ry was obtained in accordance with JIS B0601 (1994). A roughness meter was used to perform the measurement for 3 mm in an axial direction. It is to be noted that for the test sample (steel tube) in Example 8, the external surface was measured for 3 mm in a length direction. The measurement results are shown in Table 1.
  • a tensile test specimen having a parallel section of ⁇ 4 x L15 was prepared from each test sample (plate material) of Examples 1 to 7 and Comparative Examples 1 to 3, to be used for a tensile test. Further, for Example 8 (steel tube), a No. 11 test specimen in compliance with JIS Z 2241 was prepared for use in the tensile test. In the tensile test, the test specimen was pulled at a constant speed at an initial strain rate of 2.0 x 10 -3 s -1 . The 0.2% proof stress and the tensile strength were measured.
  • test samples were wire-cut into plate materials having a length of 200 mm and a thickness of 2.0 mm.
  • Each of the plate materials was heat-treated at 1,100°C for 5 minutes under an air-cooling condition while being supported at two points being 50 mm away from both ends of the plate material.
  • image data was used to draw a perpendicular line from a line connecting both ends of the plate material, and a length at a time at which the perpendicular line was the longest was determined to be the amount of warp caused by the heat treatment.
  • the amount of warp being less than or equal to 0.1 mm was evaluated as A, greater than 0.1 mm and less than or equal to 1 mm was evaluated as B, and greater than 1 mm was evaluated as C.
  • the measurement results are shown in Table 2.
  • test sample was heat-treated at 1,100°C for 5 minutes under a water-cooling condition. Subsequently, each test sample (plate material) of Examples 1 to 7 and Comparative Examples 1 to 3 was cut so that a width-thickness cross-section was visible and filled with a resin, and a surface thereof was polished to a mirror finish; subsequently, each test sample was subjected to a 65% nitric acid electrolytic etch to reveal a structure.
  • Example 8 The test sample (steel tube) of Example 8 was cut so that a surface perpendicular to a length direction was visible, then filled with a resin, and a surface thereof was polished to a mirror finish; subsequently, the test sample was subjected to a 65% nitric acid electrolytic etch to reveal a structure. Each structure was observed with an optical microscope at a magnification of 400x to measure crystal grain size numbers in 5 fields of view. Each median value was determined to be the crystal grain size number. The crystal grain size number being greater than or equal to 9.0 was evaluated as A, as the coarsening of crystal grains had been inhibited even after the heat treatment, and the crystal grain size number being less than 9.0 was evaluated as B. The results are shown in Table 2. It is to be noted that "-" in the table indicates that a measurement was not performed.
  • the austenitic stainless steel according to the present invention can be suitably used for automobile fuel injection tubes and the like.

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