EP2220260A1 - Low chrome ferritic stainless steel with high corrosion resistance and stretchability and method of manufacturing the same - Google Patents

Low chrome ferritic stainless steel with high corrosion resistance and stretchability and method of manufacturing the same

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Publication number
EP2220260A1
EP2220260A1 EP08852156A EP08852156A EP2220260A1 EP 2220260 A1 EP2220260 A1 EP 2220260A1 EP 08852156 A EP08852156 A EP 08852156A EP 08852156 A EP08852156 A EP 08852156A EP 2220260 A1 EP2220260 A1 EP 2220260A1
Authority
EP
European Patent Office
Prior art keywords
less
corrosion resistance
stainless steel
ferritic stainless
stretchability
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP08852156A
Other languages
German (de)
French (fr)
Other versions
EP2220260A4 (en
Inventor
Do Ieal Yoo
Soo Chan Lee
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.)
Posco Holdings Inc
Original Assignee
Posco Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Posco Co Ltd filed Critical Posco Co Ltd
Publication of EP2220260A1 publication Critical patent/EP2220260A1/en
Publication of EP2220260A4 publication Critical patent/EP2220260A4/en
Withdrawn legal-status Critical Current

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Classifications

    • 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
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same, and more specifically to a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same used in various pipes and a muffler of a cold zone of an automobile exhaust system requiring a high corrosion resistance and a high formability.
  • Background Art
  • DBTT Ductile-Brittle Transition Temperature
  • a low chrome ferritic stainless steel with a high corrosion resistance and stretchability is composed of C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.2wt% or less, C+N of 0.040wt% or less, Ti of 0.5wt% or less, remaining Fe, and inevitably added impurities, being controlled in EL value defined by Equation 1 below to be 33 or more and a P.I. value defined by Equation 2 below to be in a range of 14 to 16.
  • the low chrome ferritic stainless steel with the high corrosion resistance and stretchability can contain at lease any one component selected from a group consisting of Ca of 0.005 wt% or less, Mg of 0.005 wt% or less, and Zr of 0.01wt% or less.
  • the ratio of Ti/(C+N) preferably is in a range of 15 to
  • a method of manufacturing a low chrome ferritic stainless steel with a high corrosion resistance and stretchability comprises: hot rolling a slab of the ferritic stainless steel composed as described above at a heating temperature of 1230 to 1280°C and a finishing rolling temperature of 740 to 850°C; hot annealing the slab at 900 to 1000°C; cold annealing the slab at 900 to 1000°C to have a cold reduction ratio 50% or more; and adjusting the slab to have a particle size of a range of 6.0 to 7.0 in ASTM crystal particle size number.
  • Ductile-Brittle Transition Temperature by adjusting the addition amounts of Ca, Mg, and Zr, and to reduce fabrication cost by reducing the addition amounts of Cr and Mo, which are expensive materials, using the EL equation (Equation 1) and the P.I. equation (Equation 2), which are equations calculating an elongation and a fitting index, in order to control the heating temperature, the finishing rolling temperature, and the hot and cold annealing conditions of the slab.
  • FIG. 1 is a view showing a change of elongation according to a change of ASTM crystal particle size number after cold annealing in a 15Cr-Ti steel (specimen No. 1).
  • FIG. 2 is a view showing a change of elongation according to the ratio of Ti/(C+N) in the 15Cr-Ti steel.
  • FIG. 3 is a view showing a change of Ductile-Brittle Transition Temperature (DBTT) according to a change of addition amounts of Ca, Mg, and Zr in the 15Cr-Ti steel.
  • DBTT Ductile-Brittle Transition Temperature
  • a low chrome ferritic stainless steel having reduced Cr and Mo contents and at the same time, having a high corrosion resistance, stretchability, and pipe expanding properties at a low temperature is composed of C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.4wt% or less, C+N of 0.040wt% or less, Ti of 0.05 wt% or less, remaining Fe and inevitably added impurities, on condition that an EL value defined by Equation 1 below is controlled to be 33 or more and a P.I. value defined by Equation2 below is controlled to be in a range of 14 to 16.
  • a cheap low chrome ferritic stainless steel containing component composition as described above and at least any one component selected from a group consisting of Ca of 0.005 wt% or less, Mg of 0.005 wt% or less, and Zr of 0.01wt% or less as other alloy composition and satisfying that the ratio of Ti/(C+N) is in a range of 15 to 20 is prepared.
  • a slab of such a steel is hot rolled at a heating temperature of 1230 to 1280°C and a finishing rolling temperature of 740 to 850°C, it is hot-annealed at 900 to 1000°C.
  • the particle size of a material is adjusted to be a range of 6.0 to 7.0 in ASTM crystal particle size number.
  • C and N which are Ti(C, N) carbonitride forming elements, exist in an interstitial form.
  • contents of C and N become high, solid C and N not formed into a Ti(C, N) carbonitride deteriorate the elongation and the stretchability of a material. Accordingly, the content of C is limited to be 0.03% or less, and the content of N also is limited to be 0.03% or less.
  • the content of C+N becomes high, a high content of Ti is added so that steelmaking inclusions increase, thereby causing many surface defects such as scab.
  • the content of C+N is limited to be 0.04% or less.
  • Si is a ferritic phase forming element.
  • content of Si increases, stability of a ferritic phase becomes high and oxidation resistance is improved.
  • Si of 0.5% or more is added, steelmaking Si inclusions increase so that the surface defect is easy to occur.
  • Si raises hardness, yield strength, and tensile strength but deteriorates the elongation, it is disadvantageous in formability. Therefore, the content of Si is limited to be 0.5% or less.
  • Ni is a gamma phase forming element.
  • a gamma phase increases.
  • the addition amount of Ni is limited to be 0.2% or less.
  • P and S form inclusions such as MnS, etc., to deteriorate the corrosion resistance and hot rolling formability. Therefore, contents of them are preferably managed as low as possible: the content of P is limited to be 0.035% or less and the content of S is limited to be 0.01% or less.
  • Al is an element added as a deoxidizer. When a large amount of Al is added, the surface defect occurs. Therefore, content of Al is limited to be 0.05% or less.
  • Cu is a gamma phase forming element like Ni.
  • the gamma phase increases.
  • content of Cu is limited to be 0.5% or less.
  • the ratio of Ti/(C+N) when the ratio of Ti/(C+N) becomes too low, the in- tergranular corrosion occurs at a welded portion after welding. On the contrary, when it becomes too high, the content of the solid Ti is raised so that the formability such as the elongation, etc., is deteriorated. Therefore, the ratio of Ti/(C+N) is limited to be in a range of 15 to 20.
  • the heating temperature of the slab is limited to be in a range of 1230 to 1280°C.
  • finishing rolling temperature at the time of hot rolling becomes low, variation accumulation energy during the hot rolling becomes high to help the recrystallization at the time of annealing. Accordingly, a low finishing rolling temperature is ad- vantageous for elongation improvement. However, when the finishing rolling temperature becomes too low, sticking surface defect occur due to adhesion of a rolling roll and a material. Therefore, the finishing rolling temperature is limited to be in a range of 740 to 850°C.
  • the cold reduction ratio of the material becomes too low, it is difficult to remove the surface defect and to secure the surface properties. On the contrary, when it becomes high, it is advantageous for improvement of formability. Therefore, the cold reduction ratio is limited to be 50% or more at the time of material manufacturing.
  • An ingot with a thickness of 120mm was manufactured by melting the ferritic stainless steel composed as in Table 1 below in a vacuum melting equipment of 50Kg.
  • the ingot manufactured as described above was heated at 1250°C, and hot rolled at a finishing rolling temperature of 800°C to manufacture a hot rolled steel with a thickness of 3.0mm. Then, it was hot annealed at 960°C and then acid-cleaned, to be cool rolled into a thickness of 1.5mmt and 0.6mmt. Thereafter, it was cool annealed at 960°C and then acid cleaned. A tension test and an Erichsen test were performed and crystal particle size of the cool annealed steel was measured using an image analyzer.
  • the Ductile-Brittle Transition Temperature was measured by processing the cool annealed steel (a steel to which Cr, Zr, Mg are added and a steel to which they are not added) with a thickness of 1.5mm to V notch impact specimen with server size and measuring impact test temperature in intervals of 10°C in a range of +20 to -70°C.
  • Table 1 and Table 2 indicate the chemical component by specimen, the EL and P.I. calculation values, the corrosion resistance (nominal potential), and the stretchability (Erichsen value), etc.
  • the contents of Cr and Mo were adjusted so that the P.I. value is in a range of 14 to 16 using Equation 2, which is an equation calculating the P.I. value, and product properties of the middle degree of the conventional steel (409: No.13, 439 steel: Mo.14) have been indicated.
  • the contents of C, N, Cr, Mo, and Ti/(C+N) were adjusted so that the EL value is 33 or more using Equation 1, which is an equation calculating the EL value.
  • the corrosion resistance is excellent, measured elongation is high as much as 34% or more, and Erichson value indicating the stretchability also is high as much as 9.3mm or more. Also, it is appreciated that in the inventive steel having the ratio of Ti(C+N) adjusted in the range of 15 to 20, the intergranular corrosion at the welded portion does not occur as compared to the comparative example out of this range.
  • FIG. 1 is a view showing a change in the elongation according to a change in ASTM crystal particle size of the annealed steel after cold annealing in 15Cr-Ti (specimen No. 1) steel. It is appreciated from FIG. 1 that the elongation is the most excellent in the ASTM crystal particle size number within the range of 6.0 to 7.0 at the time of the cool annealing.
  • FIG. 2 is a view showing a change of the elongation after the cool annealing according to the ratio of Ti/(C+N) in the 15Cr-Ti added steel, wherein as the ratio of Ti(C+N) is low, the elongation is excellent.
  • the ratio of Ti/(C+N) become less than 15, the intergranular corrosion at the welded portion occurs as in a result of Table 1, and when the ratio of Ti/(C+N) exceeds 20, the elongation is deteriorated. Therefore, it is required to add Ti while adjusting the ratio of Ti/(C+N) in the range of 15 to 20 in consideration of the intergranular corrosion at the welded portion and the elongation.
  • FIG. 3 is a view showing a change of the Ductile-Brittle Transition Temperature
  • DBTT Ductile-Brittle Transition Temperature

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The present invention relates to a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same, wherein the low chrome ferritic stainless steel with the high corrosion resistance and stretchability is composed of C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.2wt% or less, C+N of 0.040wt% or less, Ti of 0.5wt% or less, remaining Fe and, inevitably added impurities, being controlled in EL value defined by Equation 1 below to be 33 or more and in P.I. value defined by Equation 2 below to be in a range of 14 to 16. EL= -162.1x(C+N)-0.2xCr-l.lxMo-0.2xTi/(C+N)+42.2 (1) P.I.=Cr+3.3Mo (2)

Description

Description
LOW CHROME FERRITIC STAINLESS STEEL WITH HIGH
CORROSION RESISTANCE AND STRETCHABILITY AND
METHOD OF MANUFACTURING THE SAME
Technical Field
[1] The present invention relates to a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same, and more specifically to a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same used in various pipes and a muffler of a cold zone of an automobile exhaust system requiring a high corrosion resistance and a high formability. Background Art
[2] Generally, in a ferritic stainless steel, Cr and Mo are added in order to improve corrosion resistance. However, when expensive Cr and Mo are added, fabrication cost is raised, and elongation reduces so that stretchability is deteriorated at forming a muffler of a stamping type, etc, thereby causing fracture of the stainless steel. Also, when temperature is low as in winter, fracture frequently occurs in a case of expanding a pipe after TIG welding like an exhaust system end pipe, etc.
[3] In order to solve these problems, several conventional techniques have been known.
In Europe Patent No. 0930375, a manufacturing method improving dip drawability and ridging properties by combining a component composition and a hot rolling condition has been disclosed. In Japan Patent Laid-Open Publication No. 2000-328197, a method improving surface gloss and formability by adding a proper amount of Al has been disclosed. Also, in Europe Patent No. 0765741, a method improving ridging resistance and plane anisotropy by optimizing composition, a rolling condition, and an annealing condition has been disclosed. In Japan Patent Laid-Open Publication No. 1995-032997, component composition reference and a manufacturing condition of a cheap ferritic stainless steel with a high corrosion resistance in atmospheric environment have been suggested; however, the content of Cr was defined in a range of 17 to 32% higher than that of the present patent.
[4] However, the above patents do not define component and manufacturing conditions for satisfying both the corrosion resistance and the formability and at the same time, satisfying requirements of a client desiring a low cost. Accordingly, in the case where the ferritic stainless steel is used in the muffler and for expansion of the pipe requiring a high corrosion resistance and a high formability, it is impossible to satisfy quality of a cold rolled product. [5]
Disclosure of Invention
Technical Problem
[6] It is an object of the present invention to provide a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same capable of improving Ductile-Brittle Transition Temperature (DBTT) by controlling the addition amounts of Ca, Mg, and Zr, and reducing fabrication cost by reducing the addition amounts of Cr and Mo, which are expensive materials, using an EL equation (Equation 1) and a P.I. equation (Equation 2), which are equations calculating an elongation and a fitting index, in order to control heating temperature, finishing rolling temperature, and hot and cold annealing conditions of a slab. Further, it is another object of the present invention to provide a low chrome ferritic stainless steel with a high corrosion resistance and stretchability and a method of manufacturing the same capable of raising pipe expanding properties of a welded portion of a TIG pipe by optimally controlling the contents of addition alloy elements C, N, Si, Mn, Cr, Mo, and Ti and a content ratio of Ti%/(C% + N%) using an EL equation and a P.I. equation.
[7]
Technical Solution
[8] A low chrome ferritic stainless steel with a high corrosion resistance and stretchability according to the present invention is composed of C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.2wt% or less, C+N of 0.040wt% or less, Ti of 0.5wt% or less, remaining Fe, and inevitably added impurities, being controlled in EL value defined by Equation 1 below to be 33 or more and a P.I. value defined by Equation 2 below to be in a range of 14 to 16.
[9] EL= -162.1x(C+N)-0.2xCr-l.lxMo-0.2xTi/(C+N)+42.2 (1)
[10] P.I.=Cr+3.3Mo (2)
[11] Also, in the present invention, the low chrome ferritic stainless steel with the high corrosion resistance and stretchability can contain at lease any one component selected from a group consisting of Ca of 0.005 wt% or less, Mg of 0.005 wt% or less, and Zr of 0.01wt% or less.
[12] Also, in the present invention, the ratio of Ti/(C+N) preferably is in a range of 15 to
20.
[13] Also, a method of manufacturing a low chrome ferritic stainless steel with a high corrosion resistance and stretchability according to the present invention comprises: hot rolling a slab of the ferritic stainless steel composed as described above at a heating temperature of 1230 to 1280°C and a finishing rolling temperature of 740 to 850°C; hot annealing the slab at 900 to 1000°C; cold annealing the slab at 900 to 1000°C to have a cold reduction ratio 50% or more; and adjusting the slab to have a particle size of a range of 6.0 to 7.0 in ASTM crystal particle size number. [14]
Advantageous Effects
[15] As described above, according to the present invention, it is possible to improve the
Ductile-Brittle Transition Temperature (DBTT) by adjusting the addition amounts of Ca, Mg, and Zr, and to reduce fabrication cost by reducing the addition amounts of Cr and Mo, which are expensive materials, using the EL equation (Equation 1) and the P.I. equation (Equation 2), which are equations calculating an elongation and a fitting index, in order to control the heating temperature, the finishing rolling temperature, and the hot and cold annealing conditions of the slab. Further, it is also possible to raise the pipe expanding properties of the welded portion of the TIG pipe by optimally adjusting the contents of the addition alloy elements C, N, Si, Mn, Cr, Mo, and Ti and a content ratio of Ti%/(C% + N%) using the EL equation and the P.I. equation. Accordingly, it is possible to manufacture a cheap low chrome ferritic stainless cold rolled steel with a high corrosion resistance, elongation, stretchability, and pipe expanding properties at a low temperature. Therefore, it is possible to secure a material capable of being used for a muffler and an end part of an automobile exhaust system.
[16]
Brief Description of the Drawings
[17] FIG. 1 is a view showing a change of elongation according to a change of ASTM crystal particle size number after cold annealing in a 15Cr-Ti steel (specimen No. 1).
[18] FIG. 2 is a view showing a change of elongation according to the ratio of Ti/(C+N) in the 15Cr-Ti steel.
[19] FIG. 3 is a view showing a change of Ductile-Brittle Transition Temperature (DBTT) according to a change of addition amounts of Ca, Mg, and Zr in the 15Cr-Ti steel.
[20]
Best Mode for Carrying Out the Invention
[21] Hereinafter, the present invention will be described with reference to the accompanying drawings.
[22] According to the present invention, it is possible to solve a problem that 409L steel, which is 11% Cr steel used for various pipes for an end part of an automobile exhaust system and for a muffler of the automobile exhaust system has a bad corrosion resistance so that when it is used for the muffler of the automobile exhaust system, corrosion due to condensing water frequently occurs. Also, according to the present invention, it is possible to solve a problem that 430 steel, which is 17.5%Cr steel, has a good corrosion resistance, but fabrication cost is raised due to an increase in Cr content, as well as, formability and pipe expanding properties are poor so that it may not be widely used.
[23] To this end, a low chrome ferritic stainless steel having reduced Cr and Mo contents and at the same time, having a high corrosion resistance, stretchability, and pipe expanding properties at a low temperature is composed of C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.4wt% or less, C+N of 0.040wt% or less, Ti of 0.05 wt% or less, remaining Fe and inevitably added impurities, on condition that an EL value defined by Equation 1 below is controlled to be 33 or more and a P.I. value defined by Equation2 below is controlled to be in a range of 14 to 16.
[24] EL= -162.1x(C+N)-0.2xCr-l.lxMo-0.2xTi/(C+N)+42.2 (1)
[25] P.I.=Cr+3.3Mo (2)
[26] In a method of manufacturing such a ferritic stainless steel, a cheap low chrome ferritic stainless steel containing component composition as described above and at least any one component selected from a group consisting of Ca of 0.005 wt% or less, Mg of 0.005 wt% or less, and Zr of 0.01wt% or less as other alloy composition and satisfying that the ratio of Ti/(C+N) is in a range of 15 to 20 is prepared. After a slab of such a steel is hot rolled at a heating temperature of 1230 to 1280°C and a finishing rolling temperature of 740 to 850°C, it is hot-annealed at 900 to 1000°C. After it is cold-annealed to make a cold reduction ratio of 50% or more, the particle size of a material is adjusted to be a range of 6.0 to 7.0 in ASTM crystal particle size number.
[27] Hereinafter, a composition range of the present invention and a limitation reason thereof will be described in detail.
[28] C and N, which are Ti(C, N) carbonitride forming elements, exist in an interstitial form. When contents of C and N become high, solid C and N not formed into a Ti(C, N) carbonitride deteriorate the elongation and the stretchability of a material. Accordingly, the content of C is limited to be 0.03% or less, and the content of N also is limited to be 0.03% or less. At the same time, when the content of C+N becomes high, a high content of Ti is added so that steelmaking inclusions increase, thereby causing many surface defects such as scab. Also, a nozzle clogging phenomenon occurs at the time of continuous casting, and the elongation of the material is deteriorated due to the increase in the contents of the solid C and N. Therefore, the content of C+N is limited to be 0.04% or less.
[29] Si is a ferritic phase forming element. When content of Si increases, stability of a ferritic phase becomes high and oxidation resistance is improved. However, when Si of 0.5% or more is added, steelmaking Si inclusions increase so that the surface defect is easy to occur. Also, Si raises hardness, yield strength, and tensile strength but deteriorates the elongation, it is disadvantageous in formability. Therefore, the content of Si is limited to be 0.5% or less.
[30] When content of Mn becomes high, MnS is eluted to deteriorate fitting corrosion resistance. Therefore, the content of Mn is limited to be 0.5% or less.
[31] Ni is a gamma phase forming element. When content of Ni increases, a gamma phase increases. Thus, when air-cooling a coil after hot rolling it, martensite phase generation is promoted to increase strength and hardness so that the elongation is deteriorated. Therefore, the addition amount of Ni is limited to be 0.2% or less.
[32] P and S form inclusions such as MnS, etc., to deteriorate the corrosion resistance and hot rolling formability. Therefore, contents of them are preferably managed as low as possible: the content of P is limited to be 0.035% or less and the content of S is limited to be 0.01% or less.
[33] When content of Cr becomes low, the corrosion resistance is deteriorated. When it becomes too high, the corrosion resistance is improved, whereas the elongation is low to deteriorate formability. Therefore, the content of Cr is limited to a range of 14 to 16%.
[34] When content of expensive Mo increases, the corrosion resistance is remarkably improved, whereas fabrication cost of the material is raised, and the hardness is raised to decrease the elongation, thereby deteriorating the formability. Therefore, the content of Mo is limited to be 0.2% or less in consideration of the corrosion resistance and the formability.
[35] Al is an element added as a deoxidizer. When a large amount of Al is added, the surface defect occurs. Therefore, content of Al is limited to be 0.05% or less.
[36] Cu is a gamma phase forming element like Ni. When a large amount of Cu is added, the gamma phase increases. Thus, when air-cooling the coil after hot rolling it, the martensite phase generation is promoted to increase strength and hardness so that the elongation is deteriorated. Therefore, content of Cu is limited to be 0.5% or less.
[37] When too much Ti is added, the steelmaking inclusions increase to cause many surface defects such as the scab. Also, a nozzle clogging phenomenon occurs at the time of the continuous casting, the elongation is deteriorated due to the increase in content of solid Ti, and addition amount of Ti becomes very low in comparison to the content of C+N. When the ratio of Ti/(C+N) becomes low, intergranular corrosion occurs so that the corrosion resistance is deteriorated. Therefore, addition amount of Ti is limited to be 0.5% or less, and the ratio of Ti/(C+N) is limited to be in a range of 15 to 20 in consideration of the corrosion resistance and the formability. [38] When Ca, Mg, and Zr are added singly or in combination of two thereof, a crystal particle size in heat affected zone at the time of TIG welding becomes fine, to lower Ductile-Brittle Transition Temperature (DBTT), thereby raising the pipe expanding properties of a welded portion of a TIG pipe at a low temperature like winter. However, when addition amounts of them become too much, generation amount of oxidative inclusions of Ca, Mg, and Zr increases so that the corrosion resistance is deteriorated. Therefore, the addition amount of Ca is limited to be 0.005% or less, the addition amount of Mg is limited to be 0.005% or less, and the addition amount of Zr is limited to be 0.01% or less.
[39] When an EL value in EL calculation equation found in order to improve the elongation in the present invention becomes less than 33, it is lacking in the elongation and the stretchability as a muffler material of a stamping type. Accordingly, fracture occurs at the time of forming. Therefore, the EL value is limited to be 33 or more.
[40] EL= -162.1x(C+N)-0.2xCr-l.lxMo-0.2xTi/(C+N)+42.2 (1)
[41] Also, when a pitting index (P.I.) value in Equation 2 becomes high, the corrosion resistance is improved. Therefore, in order to raise the P.I. value, it is necessary to raise the content of Cr or the content of Mo which is an expensive element. However, when the contents of them become excessively high, the elongation and the stretchability are deteriorated while the fabrication cost is raised. Also, when they are too low, the corrosion resistance is deteriorated. Therefore, in order to have the corrosion resistance and the fabrication cost which is a middle degree between a previously used STS409L steel and 439 steel, the P.I. value in the P.I. calculation equation (2) is limited to be in a range of 14 to 16.
[42] P.I.=Cr+3.3Mo (2)
[43] For the ratio of Ti/(C+N), when the ratio of Ti/(C+N) becomes too low, the in- tergranular corrosion occurs at a welded portion after welding. On the contrary, when it becomes too high, the content of the solid Ti is raised so that the formability such as the elongation, etc., is deteriorated. Therefore, the ratio of Ti/(C+N) is limited to be in a range of 15 to 20.
[44] Next, a fabrication condition of the present invention and a limitation reason thereof will be described.
[45] In a hot rolling condition, as heating temperature of the slab becomes high, it is advantageous for recrystallization during hot rolling operation. However, when the heating temperature is too high, the surface defect occurs. Therefore, the heating temperature of the slab is limited to be in a range of 1230 to 1280°C.
[46] As finishing rolling temperature at the time of hot rolling becomes low, variation accumulation energy during the hot rolling becomes high to help the recrystallization at the time of annealing. Accordingly, a low finishing rolling temperature is ad- vantageous for elongation improvement. However, when the finishing rolling temperature becomes too low, sticking surface defect occur due to adhesion of a rolling roll and a material. Therefore, the finishing rolling temperature is limited to be in a range of 740 to 850°C.
[47] Also, when the cold reduction ratio of the material becomes too low, it is difficult to remove the surface defect and to secure the surface properties. On the contrary, when it becomes high, it is advantageous for improvement of formability. Therefore, the cold reduction ratio is limited to be 50% or more at the time of material manufacturing.
[48] Since elongation is the most excellent when ASTM crystal particle size number within annealed steel after cold annealing is in a range of 6.0 to 7.0, it is limited within this range.
[49] Hereinafter, the present invention will be described in detail through an embodiment.
[50] (Embodiment)
[51] In Table 1, chemical component by specimen, an EL calculation value, and a P.I. calculation value have been indicated. In Table 2, measured elongations by specimen, nominal potential, intergranular corrosion generation existence or non-existence, Ductile-Brittle Transition Temperature (DBTT) at a welded portion of a TIG pipe, and an Erichsen value have been indicated.
[52] An ingot with a thickness of 120mm was manufactured by melting the ferritic stainless steel composed as in Table 1 below in a vacuum melting equipment of 50Kg. The ingot manufactured as described above was heated at 1250°C, and hot rolled at a finishing rolling temperature of 800°C to manufacture a hot rolled steel with a thickness of 3.0mm. Then, it was hot annealed at 960°C and then acid-cleaned, to be cool rolled into a thickness of 1.5mmt and 0.6mmt. Thereafter, it was cool annealed at 960°C and then acid cleaned. A tension test and an Erichsen test were performed and crystal particle size of the cool annealed steel was measured using an image analyzer.
[53] The nominal potential of the cool annealed steel was tested by a KS D 0238 method and measured five times at V C 10 to indicate it as a mean value.
[54] The Ductile-Brittle Transition Temperature was measured by processing the cool annealed steel (a steel to which Cr, Zr, Mg are added and a steel to which they are not added) with a thickness of 1.5mm to V notch impact specimen with server size and measuring impact test temperature in intervals of 10°C in a range of +20 to -70°C.
[55] Table 1
[56]
[57]
[Table 2]
[58] Hereinafter, a test result will be described. Table 1 and Table 2 indicate the chemical component by specimen, the EL and P.I. calculation values, the corrosion resistance (nominal potential), and the stretchability (Erichsen value), etc. In the inventive steel, the contents of Cr and Mo were adjusted so that the P.I. value is in a range of 14 to 16 using Equation 2, which is an equation calculating the P.I. value, and product properties of the middle degree of the conventional steel (409: No.13, 439 steel: Mo.14) have been indicated. Also, in the inventive steel, the contents of C, N, Cr, Mo, and Ti/(C+N) were adjusted so that the EL value is 33 or more using Equation 1, which is an equation calculating the EL value. Accordingly, it is appreciated that in the inventive steel, the corrosion resistance is excellent, measured elongation is high as much as 34% or more, and Erichson value indicating the stretchability also is high as much as 9.3mm or more. Also, it is appreciated that in the inventive steel having the ratio of Ti(C+N) adjusted in the range of 15 to 20, the intergranular corrosion at the welded portion does not occur as compared to the comparative example out of this range.
[59] FIG. 1 is a view showing a change in the elongation according to a change in ASTM crystal particle size of the annealed steel after cold annealing in 15Cr-Ti (specimen No. 1) steel. It is appreciated from FIG. 1 that the elongation is the most excellent in the ASTM crystal particle size number within the range of 6.0 to 7.0 at the time of the cool annealing.
[60] FIG. 2 is a view showing a change of the elongation after the cool annealing according to the ratio of Ti/(C+N) in the 15Cr-Ti added steel, wherein as the ratio of Ti(C+N) is low, the elongation is excellent. However, when the ratio of Ti/(C+N) become less than 15, the intergranular corrosion at the welded portion occurs as in a result of Table 1, and when the ratio of Ti/(C+N) exceeds 20, the elongation is deteriorated. Therefore, it is required to add Ti while adjusting the ratio of Ti/(C+N) in the range of 15 to 20 in consideration of the intergranular corrosion at the welded portion and the elongation.
[61] FIG. 3 is a view showing a change of the Ductile-Brittle Transition Temperature
(DBTT) according to addition or non-addition of Ca, Mg, and Zr in the 15Cr-Ti added steel, wherein when Ca is added, Ca and Mg are added together, or Ca and Zr are added together, the Ductile-Brittle Transition Temperature (DBTT) is low as much as - 50°C, so that in the case where working temperature is low like winter, TIG pipe expanding properties becomes excellent.
[62] An optimal embodiment of the present invention has been disclosed through the specific description and the drawings as above. Terms were used in order to describe the present invention, rather than limitation of meaning or limitation of the scope of the present invention described in claims. Therefore, it would be appreciated by those skilled in the art that various modifications and equivalent other embodiments are possible herein. Accordingly, the scope of the present should be defined by technical idea of accompanying claims.
[63]

Claims

Claims
[1] A low chrome ferritic stainless steel with a high corrosion resistance and stretchability comprising C of 0.03wt% or less, Si of 0.5wt% or less, Mn of 0.5wt% or less, P of 0.035wt% or less, S of 0.01wt% or less, Cr of 14 to 16wt%, Mo of 0.2wt% or less, N of 0.030wt% or less, Cu of 0.5wt% or less, Al of 0.05 wt% or less, Ni of 0.2wt% or less, C+N of 0.040wt% or less, Ti of 0.5wt% or less, remaining Fe, and inevitably added impurities, being controlled in EL value defined by Equation 1 below to be 33 or more and in P.I. value defined by Equation 2 below to be in a range of 14 to 16: EL= -162.1x(C+N)-0.2xCr-l.lxMo-0.2xTi/(C+N)+42.2 (1) P.I.=Cr+3.3Mo (2).
[2] The low chrome ferritic stainless steel with the high corrosion resistance and stretchability according to claim 1, comprising one or two or more selected from a group consisting of Ca of 0.005 wt% or less, Mg of 0.005 wt% or less, and Zr of 0.01wt% or less.
[3] The low chrome ferritic stainless steel with the high corrosion resistance and stretchability according to claim 1 or claim 2, wherein the ratio of Ti/(C+N) is in a range of 15 to 20.
[4] A method of manufacturing a low chrome ferritic stainless steel with a high corrosion resistance and stretchability comprising: hot rolling a slab of the ferritic stainless steel according to any one of claims 1 to 3 at a heating temperature of 1230 to 1280°C and a finishing rolling temperature of 740 to 850°C; hot annealing the slab at 900 to 1000°C; cold annealing the slab at 900 to 1000°Cto have a cold reduction ratio 50% or more; and adjusting the slab to have a particle size of a range of 6.0 to 7.0 in ASTM crystal particle size number.
EP08852156A 2007-11-22 2008-09-30 Low chrome ferritic stainless steel with high corrosion resistance and stretchability and method of manufacturing the same Withdrawn EP2220260A4 (en)

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