Classifications

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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
  • 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
• • 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
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  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/002—Heat treatment of ferrous alloys containing Cr
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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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  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/005—Heat treatment of ferrous alloys containing Mn
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  • C21D6/00—Heat treatment of ferrous alloys
  • C21D6/008—Heat treatment of ferrous alloys containing Si
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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
  • 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
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  • C21—METALLURGY OF IRON
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  • 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
  • C21D8/0226—Hot rolling
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  • 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
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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
  • 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
  • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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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
  • 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
  • C21D8/0273—Final recrystallisation annealing
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  • 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
  • C21D8/0426—Hot rolling
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  • 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
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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
  • 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
  • C21D8/0463—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 following hot 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
  • 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
  • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
• • 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
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  • C22C—ALLOYS
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  • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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  • 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
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  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
• • C—CHEMISTRY; METALLURGY
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  • 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
  • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
• • C—CHEMISTRY; METALLURGY
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  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
  • C22C38/18—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
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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
  • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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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  • C22C38/18—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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  • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
  • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
  • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B15/00—Arrangements for performing additional metal-working operations specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
  • B21B2015/0057—Coiling the rolled product
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
  • B21B—ROLLING OF METAL
  • B21B2261/00—Product parameters
  • B21B2261/20—Temperature
  • B21B2261/21—Temperature profile
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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
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/004—Dispersions; Precipitations
• • C—CHEMISTRY; METALLURGY
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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
  • C21D2211/00—Microstructure comprising significant phases
  • C21D2211/005—Ferrite

Definitions

• the present invention relates to a hot-rolled Nb-containing ferritic stainless steel sheet and a method for producing same, and to a cold-rolled Nb-containing ferritic stainless steel sheet and a method for producing same. More particularly, the present invention relates to a hot-rolled Nb-containing ferritic stainless steel sheet and a method for producing same, and to a cold-rolled Nb-containing ferritic stainless steel sheet and a method for producing same, the stainless steel sheets being used in order to produce exhaust pipe flange parts and exhaust pipe parts.
• exhaust pipe part denotes parts through which exhaust gas can flow, in particular exhaust manifolds, front pipes, center pipes, catalytic converter barrels and the like used in automobiles.
• exhaust pipe flange part denotes a part that is welded to an end of the exhaust pipe part, and that constitutes a flange portion having the function of fastening the exhaust pipe part to other parts.
• Stainless steel sheets generally used in conventional art are austenitic stainless steel sheets having good manufacturability, but these are being replaced by ferritic stainless steel sheets, which are advantageous from the viewpoint of coefficient of thermal expansion and cost.
• ferritic stainless steel sheets include Nb-containing ferritic stainless steel sheets.
• Exhaust pipe flange parts are produced through cold forging of a hot-rolled steel sheet.
• Exhaust pipe flange parts have a hole corresponding to an end of the exhaust pipe part, and a hole for bolt fastening, and ordinarily also undergo cutting work. Workability is accordingly required for a hot-rolled steel sheet that is used to produce exhaust pipe flange parts.
• Exhaust pipe parts are generally produced through pressing of cold-rolled steel sheets and pipe processing of cold-rolled steel sheets, followed by various work processes. Workability is accordingly required for a cold-rolled steel sheet that is used to produce exhaust pipe parts. Better workability of cold-rolled steel sheets has come to be demanded in recent years as exhaust pipe parts (in particular, exhaust manifolds) have become smaller.
• the workability of cold-rolled steel sheets can be expressed using the Lankford value (hereafter "r-value”) as an index. Increasing the cold rolling reduction ratio is effective herein in order to increase the r-value.
• Nb-containing ferritic stainless steel sheets are prone to suffer from drops in toughness due to the generation of Laves phases (intermetallic compounds being mainly Fe 2 Nb).
• Laves phases intermetallic compounds being mainly Fe 2 Nb.
• ferritic stainless steel sheets are prone to exhibit 475°C embrittlement.
• cracks occur readily and it is difficult to increase the cold rolling reduction ratio upon cold rolling of a produced hot-rolled Nb-containing ferritic stainless steel sheet of thick gauge (5 mm to 10 mm).
• Patent Document 1 proposes a method of suppressing generation of Laves phases, through control of the total amount of C and N so as to lie within a specific range.
• Patent Document 2 proposes a method that involves controlling, among others, the starting temperature and end temperature of hot rolling finishing, as well as the annealing temperature of a hot-rolled sheet.
• Patent Document 1 is aimed at hot-rolled Nb-containing ferritic stainless steel sheets having a sheet thickness of about 4.5 mm, and cannot sufficiently suppress generation of Laves phases in hot-rolled Nb-containing ferritic stainless steel sheets of thick gauge.
• a further problem is that sufficient workability of a cold-rolled Nb-containing ferritic stainless steel sheet cannot be secured even when resorting to the method of Patent Document 2.
• the inventors found that the amount of Nb carbonitrides and quantity of Laves phases can be controlled, so as to lie within proper ranges, by holding at a temperature of 1100°C to 1000°C for 60 seconds or longer and setting a finish hot rolling temperature to 850°C or higher, during hot rolling of a stainless steel slab having a specific composition, and, after hot rolling, performing coiling at a coiling temperature of 550°C or lower, as a result of which there is enhanced toughness of the resulting hot-rolled Nb-containing ferritic stainless steel sheet, and perfected the present invention on the basis of that finding.
• the present invention is a hot-rolled Nb-containing ferritic stainless steel sheet having a composition containing C: 0.030 mass% or less, Si: 2.00 mass% or less, Mn: 2.00 mass% or less, P: 0.050 mass% or less, S: 0.040 mass% or less, Cr: 10.00 mass% to 25.00 mass%, N: 0.030 mass% or less and Nb: 0.01 mass% to 0.80 mass%, with the balance being made up of Fe and unavoidable impurities, wherein the precipitation amount of Nb carbonitrides is 0.2 mass% or more, and the number of Laves phases having a grain size of 0.1 ⁇ m or less is 10 or fewer per 10 ⁇ m 2 of surface area.
• the present invention is also a method for producing a hot-rolled Nb-containing ferritic stainless steel sheet, the method including: holding at a temperature of 1000°C to 1100°C for 60 seconds or longer, and setting a finish hot rolling temperature to 850°C or higher, during hot rolling of a stainless steel slab having a composition containing C: 0.030 mass% or less, Si: 2.00 mass% or less, Mn: 2.00 mass% or less, P: 0.050 mass% or less, S: 0.040 mass% or less, Cr: 10.00 mass% to 25.00 mass%, N: 0.030 mass% or less and Nb: 0.01 mass% to 0.80 mass%, with the balance being made up of Fe and unavoidable impurities, and, after hot rolling, performing coiling at a coiling temperature of 550°C or lower.
• the present invention is also a cold-rolled Nb-containing ferritic stainless steel sheet having a composition containing C: 0.030 mass% or less, Si: 2.00 mass% or less, Mn: 2.00 mass% or less, P: 0.050 mass% or less, S: 0.040 mass% or less, Cr: 10.00 mass% to 25.00 mass%, N: 0.030 mass% or less and Nb: 0.01 mass% to 0.80 mass%, with the balance being made up of Fe and unavoidable impurities, wherein the precipitation amount of Nb carbonitrides is 0.2 mass% or more, the number of Laves phases having a grain size of 0.1 ⁇ m or less is 10 or fewer per 10 ⁇ m 2 of surface area, and the r-value is 1.2 or greater.
• the present invention is also a method for producing a cold-rolled Nb-containing ferritic stainless steel sheet, the method including annealing the above hot-rolled Nb-containing ferritic stainless steel sheet, and performing thereafter cold rolling at a reduction ratio of 70% or higher, and annealing the cold-rolled steel sheet.
• the present invention allows the provision of a hot-rolled Nb-containing ferritic stainless steel sheet having excellent toughness and workability, and a production method thereof.
• the present invention allows the provision of a cold-rolled Nb-containing ferritic stainless steel sheet having excellent workability, and a production method thereof.
• the hot-rolled Nb-containing ferritic stainless steel sheet of the present invention (hereafter also referred to as "hot-rolled steel sheet” for short) has a composition containing C, Si, Mn, P, S, Cr, N and Nb, with the balance being made up of Fe and unavoidable impurities.
• the hot-rolled steel sheet of the present invention may have a composition further containing one or more from among Ni, Mo, Cu, Co, Al, W, V, Ti, Zr, B, rare earth elements and Ca.
• C causes steel hardening and drops in the toughness of the hot-rolled steel sheet. Accordingly, the content of C is limited to 0.030 mass% or less. However, there is no need to lower the content of C to the extreme, and generally it suffices to set a C content of 0.001 mass% to 0.030 mass%, preferably 0.003 mass% to 0.025 mass% and more preferably 0.005 mass% to 0.020 mass%.
• Si and Mn are effective as deoxidizers, and moreover elicit the effect of increasing resistance to oxidation at high temperature.
• it is effective to secure a content of 0.05 mass% or more of Si, and 0.05 mass% or more of Mn.
• an excessively high content of these elements gives rise to steel embrittlement.
• the content of both Si and Mn is limited to 2.00 mass% or less.
• the content of both Si and Mn may be managed to be 1.00 mass% or less, or 0.50 mass% or less.
• the lower limit of the content of Si and Mn is not particularly restricted, and is generally 0.05 mass%, preferably 0.1 mass% and more preferably 0.15 mass%.
• P and S give rise to, for example, drops in corrosion resistance when present in large amounts. Accordingly, the content of P is limited to 0.050 mass% or less, and the content of S is limited to 0.040 mass% or less. Ordinarily it suffices to set the content of P to lie in the range of 0.010 mass% to 0.050 mass%, and the content of S to lie in the range of 0.0005 mass% to 0.040 mass%.
• the preferred content of P is 0.020 mass% to 0.040 mass% while the preferred content of S is 0.001 mass% to 0.010 mass%. In particular where corrosion resistance is emphasized, it is effective to limit the content of S to 0.005 mass% or less.
• Cr is an important element in order to secure corrosion resistance in stainless steel, and is also effective in terms of enhancing resistance to oxidation at high temperature.
• the content of Cr must be 10.00 mass% or more.
• the content of Cr is preferably 13.50 mass% or more, more preferably 17.00 mass% or more. This is effective in terms of eliciting the above effect.
• the content of Cr is high, on the other hand, manufacturability of thick-gauge hot-rolled steel sheet is impaired on account of the resulting steel hardening and drop in toughness.
• the content of Cr is limited to 25.00 mass% or less, preferably to 22.00 mass% or less and more preferably to 20.00 mass% or less.
• N causes a decrease in toughness. Accordingly, the content of N is limited to 0.030 mass% or less. However, there is no need to lower the content of N to the extreme, and generally it suffices to set the content of N to 0.001 mass% to 0.030 mass%, preferably to 0.005 mass% to 0.025 mass%.
• Nb is an element effective for suppressing boundary segregation of Cr carbonitrides (carbides / nitrides), through fixing of C and N, and for preserving high corrosion resistance, and high resistance to oxidation at high temperature, in steel. Accordingly, the content of Nb must be set to 0.01 mass% or more. It is effective to set the content of Nb to 0.05 mass% or more, and more effective to set the content of Nb to 0.20 mass% or more. An excessively high content of Nb, however, promotes drops in the toughness of the hot-rolled steel sheet, and is therefore undesirable. As a result of various studies, the content of Nb is limited to 0.80 mass% or less, preferably to 0.60 mass% or less.
• Ni has the effect of inhibiting the progress of corrosion, and can be added as needed. In this case it is effective to secure a Ni content of 0.01 mass% or more.
• a high Ni content has an adverse impact on workability, and hence the content of Ni that is added, if any, must be 2.00 mass% or less, preferably 1.00 mass% or less.
• Mo is an effective element in terms of enhancing corrosion resistance, and can be added as needed. In this case it is effective to set the content of Mo to 0.02 mass% or more, and more effective to set the content of Mo to 0.50 mass% or more.
• a high content of Mo affects toughness adversely, and hence the content of Mo that is added, if any, must be 2.50 mass% or less, preferably 1.50 mass% or less.
• Cu is an element effective in terms of enhancing low-temperature toughness, and in terms of enhancing also high-temperature strength. Accordingly, Cu can be added as needed. In this case it is effective to secure a Cu content of 0.02 mass% or more. However, workability rather decreases when Cu is added in large amounts.
• the content of Cu that is added, if any, must be 1.80 mass% or less, preferably 0.80 mass% or less.
• Co is an element that contributes to low-temperature toughness, and can be added as needed. In this case it is effective to secure a Co content of 0.010 mass% or more. However, excessive addition of Co results in a loss of ductility, and hence the content of Co that is added, if any, must be 0.50 mass% or less.
• Al is an effective element as a deoxidizer, and can be added as needed. In this case, it is effective to set an Al content of 0.005 mass% or more. However, a high Al content is one factor underlying drops in toughness. Therefore, if Al is contained, the content thereof is limited to 0.50 mass% or less, and is preferably limited to 0.20 mass% or less.
• W and V are effective elements in terms of increasing high-temperature strength, and one or more of the foregoing can be added as needed. In this case it is effective to secure a content of 0.10 mass% or more of W and a content of 0.10 mass% or more of V. However, steel becomes hard, which may give rise to cracks, when the foregoing elements are added in large amounts.
• the content of W that is added, if any, must be 1.80 mass% or less, preferably 0.50 mass% or less.
• the content of V that is added, if any, must be 0.30 mass% or less, preferably 0.15 mass% or less.
• Ti and Zr have the effect of fixing C and N, and are effective elements in terms of preserving high corrosion resistance, and high resistance to oxidation at high temperature, in steel. Accordingly, one or both of Ti and Zr can be added as needed. In this case it is effective to secure a content of 0.01 mass% or more of Ti, and a content of 0.02 mass% or more of Zr.
• an excessive content of Ti promotes loss of toughness in hot-rolled coils, and accordingly the content of Ti that is added, if any, must be 0.50 mass% or less.
• a high content of Zr constitutes a hindrance to workability, and hence the content of Zr that is added, if any, must be 0.20 mass% or less.
• B is an element that improves corrosion resistance and workability by being added in small amounts, and can be added as needed in the form of one or more types. In this case it is effective to secure a B content of 0.0001 mass% or more. However, an excessive B content affects hot workability adversely, and accordingly the content of B that is added, if any, must be 0.0050 mass% or less.
• Rare earth elements and Ca are effective elements in terms of enhancing resistance to oxidation at high temperature, and one or more of the foregoing can be added as needed. In this case it is effective to secure a content of 0.001 mass% or more of rare earth elements and a content of 0.0005 mass% or more of Ca.
• toughness decreases when these elements are added in large amounts, and hence the content of the rare earth elements that are added, if any, must be 0.100 mass% or less, and that of Ca that is added, if any, must be 0.0050 mass% or less.
• the balance, being components other than those above, is made up of Fe and unavoidable impurities.
• the term "unavoidable impurities" denotes herein impurity elements that cannot be prevented from being mixed into the materials during the production process.
• the unavoidable impurities are not particularly limited.
• Precipitation amount of Nb carbonitrides 0.2 mass% or more; Number of Laves phases having a grain size of 0.1 ⁇ m or less, per 10 ⁇ m 2 of surface area: 10 or fewer>
• Nb carbonitrides (carbides / nitrides) and Laves phases are precipitates generated as a result of a hot rolling process.
• the toughness of the hot-rolled steel sheet decreases when C and N are present in the form of a solid solution in steel, and thus the presence of such a solid solution is accordingly effective in allowing C and N to precipitate in the form of Nb carbonitrides.
• the amount of Nb in solid solution within the steel decreases, and it becomes possible to reduce the precipitation quantity of Laves phases that reduce the toughness of the hot-rolled steel sheet.
• the precipitation amount of Nb carbonitrides must be set to 0.2 mass% or more in order to increase the toughness of the hot-rolled steel sheet through a reduction in the amount of C and N in solid solution within the steel. Further, the number of Laves phases having a grain size of 0.1 ⁇ m or less must be 10 or fewer per 10 ⁇ m 2 of surface area.
• the precipitation amount (mass%) of Nb carbonitrides there was used a mixed solution of 10 mass% acetylacetone + 1 mass% tetramethylammonium chloride + 89 mass% methyl alcohol, with electrolytic extraction of a precipitate residue at a SCE potential of -100 mV to 400 mV with respect to a saturated calomel electrode, followed by filtration of the extracted residue, using a 0.2 ⁇ m micropore filter.
• the precipitation amount was calculated on the basis of the ratio between the weight of the filtered residue and total dissolution weight.
• a scanning electron microscope (SEM) was used to capture surface micrographs and measure the size of Laves phases, and also measure the number of Laves phases having a grain size of 0.1 ⁇ m or less, per 10 ⁇ m 2 of surface area. The average value of the number of Laves phases, measured at least in five points, was taken herein as the number of Laves phases.
• the thickness of the hot-rolled steel sheet of the present invention is not particularly limited and may be set as appropriate depending on the intended application. In a case for instance where the hot-rolled steel sheet of the present invention is used to produce exhaust pipe flange parts for automobiles, the thickness of the hot-rolled steel sheet is ordinarily 5.0 mm to 11.0 mm preferably 5.5 mm to 9.0 mm.
• the reduction ratio must be increased at the time of cold rolling of the hot-rolled steel sheet of the present invention, in order to increase the r-value, which is an index of the workability of a cold-rolled Nb-containing ferritic stainless steel sheet (hereafter also referred to as "cold-rolled steel sheet" for short). Therefore, the thickness of the hot-rolled steel sheet is ordinarily set to be larger than 4.5 mm, but no larger than 10.00 mm, taking into consideration the thickness and cold rolling reduction ratio of the cold-rolled steel sheet that is used in order to produce automotive exhaust pipe parts.
• the thickness of the hot-rolled steel sheet is preferably 5.0 mm to 9.0 mm, more preferably 5.5 mm to 8.0 mm.
• the hot-rolled Nb-containing ferritic stainless steel sheet of the present invention having the above features can be produced through hot rolling of a stainless steel slab having a composition identical to that of the above hot-rolled Nb-containing ferritic stainless steel sheet, such that during hot rolling the slab is held at a temperature of 1000°C to 1100°C for 60 seconds or longer and a finish hot rolling temperature is set to 850°C or higher, and after hot rolling, coiling is performed at a coiling temperature of 550°C or lower.
• the stainless steel slab is ordinarily heated prior to hot rolling.
• the heating temperature of the stainless steel slab is not particularly limited, but is preferably 1200°C to 1300°C.
• the heating temperature of the stainless steel slab is lower than 1200°C, excessive strain derived from hot rolling is introduced, and it is difficult to control thereafter the structure of the steel, and moreover surface scratches become problematic.
• a heating temperature of the stainless steel slab in excess of 1300°C results in structure coarsening, and there may be a failure to obtain a hot-rolled steel sheet having the desired characteristics.
• Hot rolling is carried out after heating of the stainless steel slab.
• Hot rolling ordinarily includes a plurality of rough rolling passes and a plurality of finish hot rolling passes. Holding at a temperature of 1000°C to 1100°C for 60 seconds or longer is necessary, and the finish hot rolling temperature must be set to 850°C or higher, in order to reduce precipitation of Laves phases during hot rolling while efficiently promoting precipitation of Nb carbonitrides.
• the reason for setting the holding temperature to be 1000°C to 1100°C is that precipitation of Nb carbonitrides can be promoted with good efficiency by a precipitation temperature of Nb carbonitrides of 1100°C or lower, and in particular by setting such a holding temperature.
• Precipitation of Nb carbonitrides is insufficient when the holding temperature and the hold time lie outside the above ranges.
• the finish hot rolling temperature is lower than 850°C, moreover, the precipitation temperature of the Laves phases is about 800°C, and accordingly precipitation of Laves phases cannot be reduced sufficiently.
• the method for holding at a temperature of 1000°C to 1100°C for 60 seconds or longer is not particularly limited, and may involve lowering a passing speed, and/or introducing a delay before finish rolling.
• the timing for the holding at a temperature of 1000°C to 1100°C for 60 seconds or longer is not particularly limited, so long as it lies within the hot rolling process, but preferably lasts from the end of rough rolling up to the beginning of finish hot rolling.
• the finish hot rolling time is not particularly limited, and can be set in accordance with known hot rolling methods in the relevant technical field.
• the finish hot rolling time is generally established taking into consideration a balance with respect to the total duration of the hot rolling process, but the longer the finish hot rolling time, the greater the precipitation amount of Nb carbonitrides is.
• Hot rolling is followed by coiling into coils at a coiling temperature of 550°C or lower.
• a coiling temperature in excess of 550°C may result in precipitation of Laves phases and in reduced toughness.
• the precipitation amount of Nb carbonitrides in the hot-rolled steel sheet obtained as described above is sufficiently increased during the hot rolling process, and accordingly Laves phases do not precipitate readily even at the precipitation temperature of the Laves phases (around 800°C). Accordingly, there is little need for a method of quenching the hot-rolled steel sheet by water cooling or the like before coiling, to shorten the transit time of the Laves phases at the precipitation temperature.
• a further characterizing feature of the cold-rolled steel sheet of the present invention is that the r-value of the sheet is 1.2 or greater.
• the cold-rolled steel sheet of the present invention boasts excellent workability, and, by being worked in various ways, allows the production of automotive exhaust pipe parts such as exhaust manifolds, front pipes, center pipes and catalyst converter barrels.
• the cold-rolled steel sheet of the present invention having the above characterizing features can be produced through annealing of the above hot-rolled steel sheet, followed by cold rolling at a reduction ratio of 70% or higher, and annealing the cold-rolled steel sheet.
• the hot-rolled steel sheet is annealed prior to cold rolling. Annealing is carried out at a temperature such that a recrystallized structure is obtained.
• the annealing temperature is not particularly limited and may be set as appropriate depending on the composition of the hot-rolled steel sheet, but is ordinarily 950°C to 1150°C. There may be a failure to obtain a recrystallized structure in some instances when the annealing temperature is lower than 950°C. On the other hand, crystal grains become coarser when the annealing temperature exceeds 1150°C.
• Cold rolling is carried out at a reduction ratio of 70% or more, in order to increase the r-value of the cold-rolled steel sheet to 1.2 or more.
• the r-value of the cold-rolled steel sheet is smaller than 1.2 when the reduction ratio is lower than 70%.
• the cold-rolled steel sheet is annealed after cold rolling. Annealing is carried out at a temperature such that a recrystallized structure is obtained.
• the annealing temperature is not particularly limited and may be set as appropriate depending on the composition of the cold-rolled steel sheet, but is ordinarily 1000°C to 1100°C. There may be a failure to obtain a recrystallized structure in some instances when the annealing temperature is lower than 1000°C. Crystal grains become coarser and rough skin arises during working, which may give rise to cracks, when the annealing temperature exceeds 1100°C.
• Stainless steel slabs were produced through smelting of steels having the component compositions given in Table 1, and the slabs were hot rolled in accordance with the conditions given in Table 1, to yield respective hot-rolled Nb-containing ferritic stainless steel sheets having a predetermined thickness.
• specimens were sampled from the obtained hot-rolled Nb-containing ferritic stainless steel sheets, and were evaluated for precipitation amount of Nb carbonitrides, size of Laves phases, quantity of Laves phases having a grain size of 0.1 ⁇ m or less, per 10 ⁇ m 2 of surface area, and toughness.
• the precipitation amount of Nb carbonitrides and the size and quantity of Laves phases were measured in accordance with the methods described above.
• the SCE potential in the measurement of the precipitation amount of Nb carbonitrides was set to 400 mV.
• Toughness was evaluated on the basis of a Charpy impact test of U-notch specimens.
• the admissibility of toughness was evaluated on the basis of observable toughness (good: O) at a ductile-brittle transition temperature (DBTT) of 20°C or lower.
• Table 2 reveals that hot-rolled Nb-containing ferritic stainless steel sheets Nos. 1 to 8, produced by holding at a temperature of 1000°C to 1100°C for 60 seconds or longer, with the finish hot rolling temperature set to 850°C or higher, during hot rolling of the stainless steel slab, and, after hot rolling, by coiling at a coiling temperature of 550°C or lower, exhibited a precipitation amount of Nb carbonitrides of 0.2 mass% or more, 10 or fewer Laves phases having a grain size of 0.1 ⁇ m or less, per 10 ⁇ m 2 of surface area, and excellent toughness.
• hot-rolled Nb-containing ferritic stainless steel sheets Nos. 1 to 8 exhibited good workability to a desired shape, without occurrence of cracks or the like caused by lack of toughness.
• hot-rolled Nb-containing ferritic stainless steel sheets Nos. 9 to 12 exhibited cracks caused by lack of toughness.
• Hot-rolled Nb-containing ferritic stainless steel sheets Nos. 1 to 7 were annealed and were thereafter cold rolled, with further annealing to yield respective cold-rolled Nb-containing ferritic stainless steel sheets.
• the production conditions involved are given in Table 3.
• Hot-rolled Nb-containing ferritic stainless steel sheets Nos. 9 to 12 had low toughness and could not be cold rolled.
• the r-value of the obtained cold-rolled Nb-containing ferritic stainless steel sheets was worked out next.
• the r-value was calculated in the form of an average r-value, in accordance with Expression (1) and Expression (2) below, after application of 14.4% strain to a JIS 13B tensile specimen of each cold-rolled Nb-containing ferritic stainless steel sheet.
• r ln W 0 / W / ln t 0 / t
• W 0 denotes sheet width before tension
• W denotes sheet width after tension
• t 0 denotes sheet thickness before tension
• t denotes sheet thickness after tension.
• Average r ⁇ value r 0 + 2 r 45 + r 90 / 4
• r 0 denotes the r-value in the rolling direction
• r 45 denotes the r-value in a 45° direction with respect to the rolling direction
• r 90 denotes the r-value in a direction perpendicular to the rolling direction.
• An average r-value of 1.2 or greater translates into a characteristic of enabling sufficient working of automotive exhaust pipe parts, for which complex shapes are required. Accordingly, it can be concluded that workability is excellent if the average r-value is 1.2 or greater.
• the present invention allows the provision of a hot-rolled Nb-containing ferritic stainless steel sheet having excellent toughness and workability, and a production method thereof. Further, the present invention allows the provision of a cold-rolled Nb-containing ferritic stainless steel sheet having excellent workability, and a production method thereof.
• the following properties are suitable for the hot-rolled Nb-containing ferritic stainless steel sheet, the cold-rolled Nb-containing ferritic stainless steel sheet or the method:

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