EP2182085B1 - Platte aus ferritischem nichtrostendem stahl mit hervorragender stanzbarkeit und herstellungsverfahren dafür - Google Patents

Platte aus ferritischem nichtrostendem stahl mit hervorragender stanzbarkeit und herstellungsverfahren dafür Download PDF

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EP2182085B1
EP2182085B1 EP08777563.1A EP08777563A EP2182085B1 EP 2182085 B1 EP2182085 B1 EP 2182085B1 EP 08777563 A EP08777563 A EP 08777563A EP 2182085 B1 EP2182085 B1 EP 2182085B1
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content
steel sheet
stainless steel
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French (fr)
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EP2182085A4 (de
EP2182085A1 (de
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Tomohiro Ishii
Yoshimasa Funakawa
Shuji Okada
Masayuki Ohta
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JFE Steel Corp
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JFE Steel Corp
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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
    • C22C38/02—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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—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
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—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
    • C22C38/18—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • 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
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the present invention relates to a ferritic stainless steel sheet having a superior punching workability and a method for manufacturing the same.
  • a ferritic stainless steel sheet Since having a superior corrosion resistance and being easily worked, a ferritic stainless steel sheet has been used in various applications, such as architectural materials, transport machines, electric home appliances, and kitchen instruments. In order to manufacture these structures, after a ferritic stainless steel sheet is cut into a predetermined shape, a work, such as forming or welding, is further performed. For cutting of a ferritic stainless steel sheet, a shearing work, which has a high productivity, has been widely used.
  • burrs are generated at a cross section of a ferritic stainless steel sheet.
  • a forming machine such as a press forming machine
  • a trouble may arise due to the presence of the burrs
  • (b) when welding is performed since a space may be generated at a burr position of a ferritic stainless steel sheet which is to be welded, for example, burn through may disadvantageously occur.
  • Burrs are not only generated by a shearing work but are also generated by a punching work as shown in Fig, 1B . Hence, development of a punching technique and/or a shearing technique that generates no burrs has been desired.
  • the punching work since a cutting plane is also formed by shearing, the punching work and the shearing work are essentially the same. That is, a generation mechanism of burrs by the punching work is the same as that by the shearing work.
  • US 5,492,575 discloses a process for producing a thin strip of Cr-stainless steel having high toughness.
  • a process includes the steps of: casting a thin cast strip of a Cr-stainless steel having a thickness of 10 mm or less, the steel containing 13-25 wt % of Cr, 0.05-1 wt % of one or more of Nb, Ti, Al and V in terms of a total amount, 0.03 wt % or less of C, 0.03 wt % or less of N, and 0.3-3.0 wt % of Mo in accordance with need, and having a ⁇ p value of 0% or less; hot-rolling the thin cast strip in a temperature range of from 1150 °C to 950 °C at a reduction in thickness of 5 to 50% to form a thin strip; either
  • the ⁇ p in % is given by the following formular: 420C+470N+23Ni+9Cu+7Mn-11.5Cr-11.5Si-12 Mo-23V-47Nb-49 Ti-52Al+189 (respective elements in wt %).
  • An object of the present invention is to provide a ferritic stainless steel sheet which can be processed by a punching work and/or a shearing work without generating burrs and a method for manufacturing the above ferritic stainless steel sheet.
  • the punching work and the shearing work are collectively called a punching work.
  • the inventors of the present invention carried out an intensive research on causes of burrs generated when a punching work is performed on a ferritic stainless steel sheet. As a result, the following are found.
  • the present invention provides a ferritic stainless steel sheet having a superior punching workability, which comprises: a composition consisting of 0.0030 to 0.012 mass percent of C, 0.13 mass percent or less of Si, 0.25 mass percent or less of Mn, 0.04 mass percent or less of P, 0.005 mass percent or less of S, 0.06 mass percent or less of Al, 0.0030 to 0.012 mass percent of N, 20.5 to 23.5 mass percent of Cr, 0.3 to 0.6 mass percent of Cu, 0.5 mass percent or less of Ni, 0.3 to 0.5 mass percent of Nb, 0.05 to 0.15 mass percent of Ti, and optionally 0.001 mass percent or less of B, 0.1 mass percent or less of Mo, 0.05 mass percent or less of V, 0.01 mass percent or less of Ca; wherein the balance being Fe and inevitable impurities; and a structure in which an average ferrite crystal grain size is 20 ⁇ m or less, and a ratio [Nb]/[Ti] of a Nb content to a Ti content contained in
  • the Nb content is 0.3 to 0.45 mass percent
  • the Ti content is 0.05 to 0.12 mass percent.
  • the present invention provides a method for manufacturing a ferritic stainless steel sheet having a superior punching workability, which comprises: performing hot-rolling of a slab having a composition which consits of 0.0030 to 0.012 mass percent of C, 0.13 mass percent or less of Si, 0.25 mass percent or less of Mn, 0.04 mass percent or less of P, 0.005 mass percent or less of S, 0.06 mass percent or less of Al, 0.0030 to 0.012 mass percent of N, 20.5 to 23.5 mass percent of Cr, 0.3 to 0.6 mass percent of Cu, 0.5 mass percent or less of Ni, 0.3 to 0.5 mass percent of Nb, 0.05 to 0.15 mass percent of Ti, and optionally 0.001 mass percent or less of B, 0.1 mass percent or less of Mo, 0.05 mass percent or less of V, 0.01 mass percent or less of Ca; wherein the balance being Fe and inevitable impurities at a hot-rolling finishing temperature of 900°C or more and at a coiling temperature of 400 to 550°C; performing soften
  • the Nb content is 0.3 to 0.45 mass percent
  • the Ti content is 0.05 to 0.12 mass percent.
  • a slab heating temperature is 1,000°C or less.
  • a ferritic stainless steel sheet can be manufactured which can be processed by a punching work without generating large burrs which cause an industrial problem.
  • a punching work and a shearing work are collectively called a punching work.
  • C is an element that binds to Cr, which will be described later, to form a Cr carbide which makes stainless steel sensitive to corrosion.
  • C is fixed in the form of a NbTi complex carbonitride, and the NbTi complex carbonitride is dispersed and precipitated, so that the generation of burrs caused by a punching work is prevented.
  • the C content is less than 0.0030 mass percent, the above effect cannot be obtained.
  • the content is more than 0.012 mass percent, the generation of a Cr carbide cannot be suppressed, and the corrosion resistance is degraded.
  • the C content is set in the range of 0.0030 to 0.012 mass percent. More preferably, the content is 0.004 to 0.010 mass percent.
  • Si is an element that hardens a ferritic stainless steel sheet by solid-solution hardening to degrade the ductility.
  • the Si content is set to 0.13 mass percent or less. More preferably, the content is 0.10 mass percent or less.
  • Mn is an element that degrades the corrosion resistance of a ferritic stainless steel sheet.
  • Mn content is more than 0.25 mass percent, in addition to the degradation in corrosion resistance, Mn binds to S which will be described later, and as a result, fine MnS is liable to be generated.
  • MnS is precipitated in grain boundaries of ferrite crystal grains and expands the ferrite crystal grains by hot rolling and/or cold rolling, and as a result, burrs having a large height are generated in a punching work.
  • the Mn content is set to 0.25 mass percent or less. More preferably, the content is 0.20 mass percent or less.
  • P is an element that hardens a ferritic stainless steel sheet by solid-solution hardening to degrade the toughness.
  • the P content is set to 0.04 mass percent or less. More preferably, the content is 0.03 mass percent or less.
  • S is an element that binds to Mn or Ti, which will be described later, to form MnS or TiS and disturb equiaxial crystallization of ferrite crystal grains.
  • S content is set to 0.005 mass percent or less. More preferably, the content is 0.003 mass percent or less.
  • Al is used as a deoxidizing agent in a steelmaking process for forming ferritic stainless steel.
  • the content is preferably 0.01 mass percent or more.
  • Al content is more than 0.06 mass percent, Al binds to N, and AlN is liable to be generated. AlN expands ferrite crystal grains by hot rolling and/or cold rolling, so that burrs having a large height are generated in a punching work.
  • the Al content is set to 0.06 mass percent or less.
  • the Al content is preferably in the range of 0.02 to 0.06 mass percent. More preferably, the content is 0.02 to 0.045 mass percent.
  • N generates a NbTi complex carbonitride.
  • a NbTi complex carbonitride is uniformly dispersed in a ferritic stainless steel sheet, cracks generated by a punching work are likely to be propagated, so that the generation of burrs can be prevented.
  • the N content is less than 0.0030 mass percent, a sufficient NbTi complex carbonitride amount is not generated.
  • the content is more than 0.012 mass percent, a Cr nitride is precipitated, so that the corrosion resistance is degraded.
  • the N content is set in the range of 0.0030 to 0.012 mass percent. More preferably, the content is 0.0040 to 0.010 mass percent.
  • Cr is an element for forming a passivation film on a surface of a ferritic stainless steel sheet to improve the corrosion resistance.
  • the Cr content is less than 20.5 mass percent, a superior corrosion resistance to that of a stainless steel containing 18% of Cr, which is an object of the present invention, cannot be obtained.
  • the Cr content is set in the range of 20.5 to 23.5 mass percent. More preferably, the content is 20.5 to 22.5 mass percent.
  • Cu has a function to further improve the corrosion resistance of a ferritic stainless steel sheet containing 20.5 mass percent or more of Cr.
  • the Cu content is less than 0.3 mass percent, the above effect cannot be obtained.
  • the content is more than 0.6 mass percent, Cu binds to S, and hence CuS is liable to be generated.
  • CuS expands ferrite crystal grains by hot rolling and/or cold rolling and generates burrs having a large height in a punching work.
  • the Cu content is set in the range of 0.3 to 0.6 mass percent. More preferably, the content is 0.3 to 0.5 mass percent. Even more preferably, the content is 0.3 to 0.45 mass percent.
  • Ni 0.5 mass percent or less
  • Ni has a function to further improve the corrosion resistance of a ferritic stainless steel sheet.
  • the content is preferably 0.1 mass percent or more.
  • the Ni content is set to 0.5 mass percent or less. More preferably, the content is 0.4 mass percent or less.
  • Nb has a function to generate a NbTi complex carbonitride in a ferritic stainless steel sheet and to facilitate propagation of cracks generated in a punching work, so that the generation of burrs can be prevented.
  • the Nb content is less than 0.3 mass percent, a large amount of Cr carbonitride is precipitated, and as a result, the corrosion resistance of a ferritic stainless steel sheet is degraded.
  • the content is more than 0.5 mass percent, a hard phase containing Cr and Nb is generated, the workability is degraded, and in addition, since the NbTi complex carbonitride is not likely to be generated, burrs having a large height are generated in a punching work.
  • the Nb content is set in the range of 0.3 to 0.5 mass percent. More preferably, the content is 0.3 to 0.45 mass percent.
  • Ti has a function to generate a NbTi complex carbonitride in a ferritic stainless steel sheet and to facilitate propagation of cracks generated in a punching work, so that the generation of burrs can be prevented.
  • the Ti content is less than 0.05 mass percent, the NbTi complex carbonitride is not generated, and a Ti carbonitride and/or a Nb carbonitride is precipitated in ferrite crystal grains. As a result, burrs having a large height are generated in a punching work.
  • the Ti content is set in the range of 0.05 to 0.15 mass percent. More preferably, the content is 0.05 to 0.12 mass percent.
  • the balance other than the components described above contains Fe and inevitable impurities.
  • the amount of the inevitable impurities is preferably decreased as small as possible.
  • At least one selected from the group consisting of B, Mo, V, and Ca is preferably contained.
  • 0.001 mass percent or less of B, 0.1 mass percent or less of Mo, 0.05 mass percent or less of V, and 0.01 mass percent or less of Ca may be contained.
  • the content is preferably 0.0001 mass percent or more.
  • the B content is set to 0.001 mass percent or less.
  • Mo is an element to strengthen a passivation film, facilitate re-passivation after corrosion generation, and improve the corrosion resistance of stainless steel.
  • the content is preferably 0.01 mass percent or more.
  • the workability such as press workability, is degraded by solid solution strengthening.
  • the Mo content is set to 0.1 mass percent or less.
  • V 0.05 mass percent or less
  • V is an element to improve the corrosion resistance of stainless steel.
  • the content is preferably 0.01 mass percent or more.
  • the V content is set to 0.05 mass percent or less.
  • Ca is an element to prevent molten steel from adhering to steelmaking devices, such as a nozzle. This effect can be obtained at a content of 0.001 mass percent or more. However, when more than 0.01 mass percent is added, Ca is precipitated in the form, for example, of CaO and CaS in steel. Since these inclusions are easily dissolved in water and increase a local pH, corrosion starts therefrom. Hence, the Ca content is set to 0.01 mass percent or less.
  • Average grains size of ferrite crystal grains 20 ⁇ m or less
  • the size of ferrite crystal grains of a ferritic stainless steel sheet has a significant influence on the height of burrs generated by a punching work.
  • the grain size of ferrite crystal grains is set to 20 ⁇ m or less.
  • the ferrite crystal grain size is an ASTM nominal grain diameter obtained in accordance with ASTM E 112.
  • Ratio [Nb]/[Ti] between Nb content and Ti content contained in NbTi complex carbonitride 1 to 10
  • the ratio [Nb]/[Ti] between the Nb content and the Ti content contained in the NbTi complex carbonitride is set in the range of 1 to 10.
  • the Nb content [Nb] and the Ti content [Ti] of the NbTi complex carbonitride inclusions in which a Nb carbonitride and a Ti carbonitride are mixed together on an atomic level, or precipitated inclusions in which one carbonitride functions as precipitation sites and the other carbonitride adheres thereto
  • the [Nb]/[Ti] value is calculated.
  • the ferritic stainless steel sheet of the present invention has a yield ratio of 0.65 or more.
  • hot rolling finishing temperature: 900°C or more, coiling temperature: 400 to 550°C
  • heating temperature: 1,000°C or more so that a hot-rolled steel sheet is formed.
  • Heating temperature of slab 1,000°C or more
  • the heating temperature of the slab is preferably set to 1,000°C or more.
  • the upper limit of the slab heating temperature is 1,250°C.
  • a more preferable range is 1,050 to 1,200°C.
  • Finishing temperature 900°C or more
  • the finishing temperature is set to 900°C or more.
  • the upper limit of the finishing temperature is 1,050°C. More preferably, the finishing temperature is in the range of 920 to 1,000°C.
  • Coiling temperature 400 to 550°C
  • the coiling temperature of a hot-rolled steel sheet has an important function to precipitate a NbTi complex carbonitride in grain boundaries of ferrite crystal grains.
  • the coiling temperature is less than 400°C, the NbTi complex carbonitride is not precipitated. More preferably, the coiling temperature is in the range of 450 to 530°C.
  • the coiling temperature of a hot-rolled steel sheet is set in the range of 400 to 550°C.
  • the NbTi complex carbonitride is precipitated in grain boundaries of ferrite crystal grains.
  • the hot-rolled steel sheet thus obtained is processed by softening annealing and is further processed by pickling.
  • Conditions of the softening annealing and those of the pickling are not particularly limited, and these processes are performed in accordance with known methods.
  • the temperature is 900 to 1,100°C, and the time is 30 to 180 seconds.
  • cold rolling is performed, so that a cold-rolled steel sheet is obtained.
  • the cold-rolled steel sheet thus obtained is processed by recrystallization annealing, so that a ferritic stainless steel sheet is obtained.
  • Conditions of the cold rolling and those of the recrystallization annealing are not particularly limited, and these processes are performed in accordance with known methods.
  • the temperature is 900 to 1,100°C, and the time is 30 to 180 seconds.
  • the cold-rolled steel sheet may be processed by temper rolling.
  • the draft of the temper rolling is preferably in the range of 0.5% to 1.5%.
  • the cold-rolled steel sheet thus obtained was processed by recrystallization annealing (temperature: 900 to 1,100°C, time: 100 to 500 seconds) and was further processed by pickling.
  • the ASTM nominal grain diameter was obtained in such a way that the total length of the line segments was divided by the number of intersections, and the value obtained thereby was multiplied by 1.13.
  • the results are shown in Table 2.
  • the measurement of the grain size was performed using one arbitrary viewing field.
  • JIS-No. 13B tensile test piece was formed from the ferritic stainless steel sheet, and a tensile test was performed. The results are shown in Table 2. The tensile test piece was obtained so that a tensile direction was parallel to the rolling direction.
  • a punching test piece (100 mm by 100 mm) was obtained by cutting the ferritic stainless steel sheet, and a punching test was performed using a punching device shown in Figs. 1A and 1B . After a round hole having a diameter of 10 mm was formed by a punching work at a central portion of the punching test piece, the height of burrs was measured. The results are shown in Table 2.
  • Fig. 2 a schematic view of a burr of a punched-out hole formed by punching out a disc having a diameter of 10 mm is shown. The height of the burr of one round hole was measured at 4 points at 90° regular intervals, and the average of the height was obtained therefrom.
  • Nos. 1 to 5 of Table 2 are examples in each of which the C content was changed.
  • the height of the burr of Nos. 2 to 4 which were within the range of the present invention was 50 ⁇ m or less, in Nos. 1 and 5 which were out of the range of the present invention, a burr having a height of more than 100 ⁇ m was generated.
  • Nos. 6 to 10 are examples in each of which the Nb content was changed.
  • the height of the burr of Nos. 7 to 9 which were within the range of the present invention was 50 ⁇ m or less.
  • the grain size of the ferrite crystal grains was large, and the yield ratio was small. Hence, a burr having a height of more than 100 ⁇ m was generated.
  • the ferrite crystal grains were expanded, and a burr having a height of more than 100 ⁇ m was generated.
  • Nos. 11 to 15 are examples in each of which the Ti content was changed.
  • the height of the burr of Nos. 12 to 14 which were within the range of the present invention was 50 ⁇ m or less.
  • No. 11 in which the Ti content was lower than the range of the present invention the grain size of the ferrite crystal grains was large, and the yield ratio was small. Since the amount of precipitation of the NbTi complex carbonitride was small, a burr having a height of more than 100 ⁇ m was generated.
  • No. 15 in which the Ti content was higher than the range of the present invention in addition to a low [Nb]/[Ti] value, the grain size of the ferrite crystal grains was large, and the yield ratio was small. Hence, a burr having a height of more than 100 ⁇ m was generated.
  • Nos. 16 to 20 are examples in each of which the N content was changed.
  • the height of the burr of Nos. 17 to 19 which were within the range of the present invention was 50 ⁇ m or less.
  • No. 16 in which the N content was lower than the range of the present invention since the amount of the NbTi complex carbonitride was small, and the [Nb]/[Ti] value was small, a burr having a height of more than 100 ⁇ m was generated.
  • No. 20 in which the N content was higher than the range of the present invention in addition to a high [Nb]/[Ti] value, the grain size of the ferrite crystal grains was large, and the yield ratio was small. Hence, a burr having a height of more than 100 ⁇ m was generated.
  • Nos. 21 to 25 are examples in which the conditions of the hot rolling were changed.
  • the height of the burr of Nos. 23 and 24 which were within the range of the present invention was 50 ⁇ m or less.
  • the finishing temperature and the coiling temperature were out of the range of the present invention, in addition to a low [Nb]/[Ti] value, the grain size of the ferrite crystal grains was large, and the yield ratio was small.
  • a burr having a height of more than 100 ⁇ m was generated.
  • No. 22 in which the coiling temperature was lower than the range of the present invention, in addition to a low [Nb]/[Ti] value, the grain size of the ferrite crystal grains was large, and the yield ratio was small.

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

Claims (5)

  1. Ferritisches Edelstahlblech, umfassend:
    eine Zusammensetzung bestehend aus
    0,0030 bis 0,012 Massenprozent C,
    0,13 Massenprozent oder weniger Si,
    0,25 Massenprozent oder weniger Mn,
    0,04 Massenprozent oder weniger P,
    0,005 Massenprozent oder weniger S,
    0,06 Massenprozent oder weniger Al,
    0,0030 bis 0,012 Massenprozent N,
    20,5 bis 23,5 Massenprozent Cr,
    0,3 bis 0,6 Massenprozent Cu,
    0,5 Massenprozent oder weniger Ni,
    0,3 bis 0,5 Massenprozent Nb,
    0,05 bis 0,15 Masseprozent Ti;
    und optional
    0,001 Massenprozent oder weniger B,
    0,1 Massenprozent oder weniger Mo,
    0,05 Massenprozent oder weniger V,
    0,01 Massenprozent oder weniger Ca;
    wobei
    der Rest Fe und unvermeidliche Verunreinigungen ist;
    und eine Struktur, bei der eine Ferritkristallkorngröße 20 µm oder weniger beträgt und ein Verhältnis [Nb] / [Ti] eines Nb-Gehalts zu einem Ti-Gehalt, welcher in einem komplexen NbTi-Carbonitrid enthalten ist, welches in Ferritkristallkorngrenzen vorhanden ist, im Bereich von 1 bis 10 liegt.
  2. Ferritisches Edelstahlblech nach Anspruch 1, wobei der Nb-Gehalt 0,3 bis 0,45 Masseprozent beträgt und der Ti-Gehalt 0,05 bis 0,12 Massenprozent beträgt.
  3. Verfahren zur Herstellung eines ferritischen Edelstahlblechs, umfassend:
    Warmwalzen einer Bramme mit einer Zusammensetzung bestehend aus
    0,0030 bis 0,012 Massenprozent C,
    0,13 Massenprozent oder weniger Si,
    0,25 Massenprozent oder weniger Mn,
    0,04 Massenprozent oder weniger P,
    0,005 Massenprozent oder weniger S,
    0,06 Massenprozent oder weniger Al,
    0,0030 bis 0,012 Massenprozent N,
    20,5 bis 23,5 Massenprozent Cr,
    0,3 bis 0,6 Massenprozent Cu,
    0,5 Massenprozent oder weniger Ni,
    0,3 bis 0,5 Massenprozent Nb,
    0,05 bis 0,15 Massenprozent Ti;
    und optional
    0,001 Massenprozent oder weniger B,
    0,1 Massenprozent oder weniger Mo,
    0,05 Massenprozent oder weniger V,
    0,01 Massenprozent oder weniger Ca;
    wobei der Rest Fe und unvermeidliche Verunreinigungen ist,
    bei einer Warmwalzfinishingtemperatur von 900 ° C oder mehr und bei einer Aufwickeltemperatur von 400 bis 550 ° C;
    Durchführen eines Erweichungsglühens eines erhaltenen warmgewalzten Stahlblechs; dann Durchführen eines Beizens;
    dann Durchführen eines Kaltwalzens; und
    Durchführen eines Rekristallisationsglühens eines erhaltenen kaltgewalzten Stahlblechs.
  4. Verfahren zur Herstellung eines ferritischen Edelstahlblechs nach Anspruch 3, wobei der Nb-Gehalt 0,3 bis 0,45 Masseprozent beträgt und der Ti-Gehalt 0,05 bis 0,12 Massenprozent beträgt.
  5. Verfahren zur Herstellung eines ferritischen Edelstahlblechs nach einem der Ansprüche 3 oder 4, wobei eine Brammenheiztemperatur 1000 °C oder weniger beträgt.
EP08777563.1A 2007-08-20 2008-06-18 Platte aus ferritischem nichtrostendem stahl mit hervorragender stanzbarkeit und herstellungsverfahren dafür Active EP2182085B1 (de)

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US20110061777A1 (en) 2011-03-17
JP2009068104A (ja) 2009-04-02
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EP2182085A4 (de) 2016-03-16
CN101784686B (zh) 2011-09-21
TW200918676A (en) 2009-05-01
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