CN108495944B - Hot-rolled Nb-containing ferritic stainless steel sheet and method for producing same, and cold-rolled Nb-containing ferritic stainless steel sheet and method for producing same - Google Patents
Hot-rolled Nb-containing ferritic stainless steel sheet and method for producing same, and cold-rolled Nb-containing ferritic stainless steel sheet and method for producing same Download PDFInfo
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- CN108495944B CN108495944B CN201780007794.6A CN201780007794A CN108495944B CN 108495944 B CN108495944 B CN 108495944B CN 201780007794 A CN201780007794 A CN 201780007794A CN 108495944 B CN108495944 B CN 108495944B
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 81
- 238000004519 manufacturing process Methods 0.000 title claims description 32
- 229910001068 laves phase Inorganic materials 0.000 claims abstract description 29
- 239000000203 mixture Substances 0.000 claims abstract description 17
- 238000001556 precipitation Methods 0.000 claims abstract description 16
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 8
- 229910000831 Steel Inorganic materials 0.000 claims description 54
- 239000010959 steel Substances 0.000 claims description 54
- 238000005098 hot rolling Methods 0.000 claims description 35
- 239000010960 cold rolled steel Substances 0.000 claims description 34
- 239000010935 stainless steel Substances 0.000 claims description 25
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 8
- 238000012360 testing method Methods 0.000 claims description 6
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 238000009863 impact test Methods 0.000 claims description 3
- 230000007704 transition Effects 0.000 claims description 2
- 238000000137 annealing Methods 0.000 description 15
- 238000000034 method Methods 0.000 description 14
- 238000005097 cold rolling Methods 0.000 description 10
- 238000005260 corrosion Methods 0.000 description 9
- 230000007797 corrosion Effects 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 7
- 230000003647 oxidation Effects 0.000 description 6
- 238000007254 oxidation reaction Methods 0.000 description 6
- 239000002245 particle Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 229910052710 silicon Inorganic materials 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 4
- OKKJLVBELUTLKV-UHFFFAOYSA-N Methanol Chemical compound OC OKKJLVBELUTLKV-UHFFFAOYSA-N 0.000 description 3
- 230000002411 adverse Effects 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910052726 zirconium Inorganic materials 0.000 description 3
- YRKCREAYFQTBPV-UHFFFAOYSA-N acetylacetone Chemical compound CC(=O)CC(C)=O YRKCREAYFQTBPV-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000003197 catalytic effect Effects 0.000 description 2
- 238000010273 cold forging Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000008021 deposition Effects 0.000 description 2
- 238000005553 drilling Methods 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- OKIZCWYLBDKLSU-UHFFFAOYSA-M N,N,N-Trimethylmethanaminium chloride Chemical compound [Cl-].C[N+](C)(C)C OKIZCWYLBDKLSU-UHFFFAOYSA-M 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- ZOMNIUBKTOKEHS-UHFFFAOYSA-L dimercury dichloride Chemical class Cl[Hg][Hg]Cl ZOMNIUBKTOKEHS-UHFFFAOYSA-L 0.000 description 1
- 238000005868 electrolysis reaction Methods 0.000 description 1
- 230000014509 gene expression Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000011259 mixed solution Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- 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
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- C21D6/00—Heat treatment of ferrous alloys
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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
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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
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- 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
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- 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
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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
- C21D8/0447—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
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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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- 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
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
The hot rolled Nb-containing ferritic stainless steel sheet according to the present invention has the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, and the balance of Fe and inevitable impurities. In the hot rolled Nb-containing ferritic stainless steel sheet, the amount of precipitation of Nb carbonitride is 0.2 mass% or more, and the Laves phase having a grain size of 0.1 μm or less is 10 μm per phase2The area of (A) is 10 or less.
Description
Technical Field
The present invention relates to a hot-rolled Nb-containing ferritic stainless steel sheet and a method for producing the same, and a cold-rolled Nb-containing ferritic stainless steel sheet and a method for producing the same. In particular, the present invention relates to a hot-rolled Nb-containing ferritic stainless steel sheet for manufacturing exhaust pipe flange parts and exhaust pipe parts, a method for manufacturing the same, and a cold-rolled Nb-containing ferritic stainless steel sheet and a method for manufacturing the same.
Background
Since exhaust pipe flange parts and exhaust pipe parts are required to have properties such as corrosion resistance, heat resistance, and strength, stainless steel sheets having such excellent properties are used as blanks. Here, the exhaust pipe component means a component through which exhaust gas can flow, and particularly means a component such as an exhaust manifold, a front pipe, a center pipe, and a catalytic converter outer cylinder in an automobile. The exhaust pipe flange component is a component constituting a flange portion welded to an end portion of the exhaust pipe component and serving to fasten the exhaust pipe component to another component.
Conventionally, austenitic stainless steel sheets having good manufacturability have been generally used as stainless steel sheets, but substitution for ferritic stainless steel sheets, which are advantageous in terms of thermal expansion coefficient and cost, has been advanced. As such a ferritic stainless steel sheet, a Nb-containing ferritic stainless steel sheet is exemplified.
The exhaust pipe flange part is manufactured by cold forging a hot-rolled steel sheet. The exhaust pipe flange component has a hole corresponding to an end of the exhaust pipe component and a hole for fastening a bolt, and is usually subjected to cutting. Therefore, workability is required for hot-rolled steel sheets used for manufacturing exhaust pipe flange parts.
In addition, the exhaust pipe part is generally manufactured by press working a cold-rolled steel sheet or performing various kinds of working after pipe working (pipe processing) the cold-rolled steel sheet. Therefore, cold-rolled steel sheets used for manufacturing exhaust pipe parts are also required to have workability. In particular, with the recent miniaturization of exhaust pipe components (particularly exhaust manifolds), further improvements in workability of cold-rolled steel sheets are desired. The workability of a cold-rolled steel sheet can be expressed by a Lankford (Lankford) value (hereinafter, referred to as "r value") as an index, and it is effective to increase the cold rolling reduction in order to increase the r value.
However, the Nb-containing ferritic stainless steel sheet generates a Laves phase (as Fe) during hot rolling2An intermetallic compound mainly composed of Nb) and easily causes a decrease in toughness. In addition, originally ferritic stainless steel sheets are susceptible to embrittlement at 475 ℃. Therefore, when a hot-rolled Nb-containing ferritic stainless steel sheet having a thickness of 5mm to 10mm is produced and cold-rolled, cracks are likely to occur, and it is difficult to increase the cold rolling reduction.
As a method for improving the toughness of a hot-rolled Nb-containing ferritic stainless steel sheet, for example, patent document 1 proposes a method for suppressing the formation of a Laves phase by controlling the total amount of C and N in a specific range.
As a method for improving the workability of Nb-containing ferritic stainless cold-rolled steel sheets, for example, patent document 2 proposes a method for controlling the finish hot-rolling start temperature, finish hot-rolling end temperature, hot-rolled sheet annealing temperature, and the like.
Documents of the prior art
Patent document
Patent document 1: japanese laid-open patent publication No. 10-237602
Patent document 2: japanese patent laid-open publication No. 2002-30346
Disclosure of Invention
Problems to be solved by the invention
However, in the method of patent document 1, the Nb-containing ferritic stainless steel hot-rolled sheet having a sheet thickness of about 4.5mm is targeted, and the formation of Laves phase cannot be sufficiently suppressed in the thick Nb-containing ferritic stainless steel hot-rolled sheet.
Further, even when the method of patent document 2 is used, there is a problem that the workability of the Nb-containing ferritic stainless steel cold-rolled steel sheet cannot be sufficiently ensured.
The present invention has been made to solve the above problems, and an object thereof is to provide a hot-rolled Nb-containing ferritic stainless steel sheet having excellent toughness and workability, and a method for producing the same.
Further, an object of the present invention is to provide a Nb-containing ferritic stainless cold-rolled steel sheet having excellent workability and a method for producing the same.
Means for solving the problems
The present inventors have continued intensive studies to solve the above problems, and as a result, have found the following facts, thereby completing the present invention: when a stainless steel slab having a specific composition is hot-rolled, the temperature is maintained at 1000 to 1100 ℃ for 60 seconds or more, the finish hot-rolling temperature is 850 ℃ or more, and the steel slab is coiled at a coiling temperature of 550 ℃ or less after hot-rolling, whereby the amounts of Nb carbonitride and Laves phases can be controlled within appropriate ranges, and as a result, the toughness of the Nb-containing ferritic stainless steel hot-rolled sheet is improved.
Further, the present inventors have found the following fact, thereby completing the present invention: after annealing the Nb-containing ferritic stainless steel hot-rolled sheet, the r value can be increased to 1.2 or more by annealing the sheet by cold rolling at a reduction ratio of 70% or more, and as a result, the workability of the Nb-containing ferritic stainless steel cold-rolled sheet is improved.
That is, the present invention is a hot-rolled Nb-containing ferritic stainless steel sheet having the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, the balance being Fe and unavoidable impurities, the amount of precipitation of Nb carbonitride in the Nb-containing ferritic stainless steel hot-rolled sheet being 0.2% by mass or more, and the Laves phase having a particle size of 0.1 μm or less being per 10 μm2The area of (A) is 10 or less.
The present invention also provides a method for producing a hot-rolled Nb-containing ferritic stainless steel sheet, characterized in that, when a stainless steel slab is hot-rolled, the stainless steel slab is held at a temperature of 1000 to 1100 ℃ for 60 seconds or more and a finish hot-rolling temperature of 850 ℃ or more, and after the hot-rolling, the stainless steel slab is coiled at a coiling temperature of 550 ℃ or less, wherein the stainless steel slab has the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, and the balance of Fe and inevitable impurities.
Further, the present invention provides a Nb-containing ferritic stainless steel cold-rolled steel sheet having the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, the balance being Fe and inevitable impurities, the amount of Nb carbonitride precipitated in the Nb-containing ferritic stainless steel cold-rolled steel sheet being 0.2% by mass or more, and the Laves phase having a grain size of 0.1 μm or less being present at 10 μm intervals2Has an area of 10 or less and an r value of 1.2 or more.
The present invention is a method for producing a Nb-containing ferritic stainless cold-rolled steel sheet, characterized in that the Nb-containing ferritic stainless cold-rolled steel sheet is annealed, then cold-rolled at a reduction ratio of 70% or more, and then annealed.
Effects of the invention
According to the present invention, a hot-rolled Nb-containing ferritic stainless steel sheet having excellent toughness and workability and a method for producing the same can be provided.
Further, according to the present invention, it is possible to provide a Nb-containing ferritic stainless cold-rolled steel sheet having excellent workability and a method for manufacturing the same.
Detailed Description
< ferrite stainless steel hot-rolled steel sheet containing Nb >
The Nb-containing ferritic stainless steel hot-rolled steel sheet (hereinafter, sometimes simply referred to as "hot-rolled steel sheet") of the present invention has the following composition: contains C, Si, Mn, P, S, Cr, N and Nb, and the balance is Fe and unavoidable impurities. Further, the hot rolled steel sheet of the invention may also have the following composition: and also contains more than one of Ni, Mo, Cu, Co, Al, W, V, Ti, Zr, B, rare earth elements and Ca.
Hereinafter, the hot-rolled steel sheet according to the present invention will be described in detail.
< C: 0.030% by mass or less
C becomes a factor that hardens the steel to lower the toughness of the hot-rolled steel sheet. Therefore, the content of C is limited to 0.030 mass% or less. However, the content of C does not need to be extremely reduced, and the content of C may be usually 0.001 to 0.030 mass%, preferably 0.003 to 0.025 mass%, and more preferably 0.005 to 0.020 mass%.
< Si: 2.00 mass% or less, Mn: 2.00% by mass or less
Si and Mn are effective as a deoxidizer and have an effect of improving high-temperature oxidation resistance. In particular, when importance is attached to high-temperature oxidation resistance, it is effective to ensure a content of 0.05 mass% or more of Si and a content of 0.05 mass% or more of Mn. However, when these elements are contained in a large amount, they cause embrittlement of the steel. As a result of various studies, both Si and Mn were limited to contents of 2.00 mass% or less. The contents of both Si and Mn may be controlled to 1.00 mass% or less or 0.50 mass% or less. The lower limit of the content of Si and Mn is not particularly limited, but is usually 0.05 mass%, preferably 0.1 mass%, and more preferably 0.15 mass%.
< P: 0.050% by mass or less, S: 0.040 mass% or less
When P and S are contained in a large amount, they may cause a decrease in corrosion resistance. Therefore, the content of P is limited to 0.050% by mass or less, and the content of S is limited to 0.040% by mass or less. In general, the content of P may be set to 0.010 mass% to 0.050 mass%, and the content of S may be set to 0.0005 mass% to 0.040 mass%. The preferable content of P is 0.020 to 0.040 mass%, and the preferable content of S is 0.001 to 0.010 mass%. In particular, when corrosion resistance is regarded as important, it is effective to limit the S content to 0.005 mass% or less.
< Cr: 10.00-25.00 mass%
Cr is an important element for ensuring corrosion resistance of stainless steel, and is also effective for improving high-temperature oxidation resistance. In order to exhibit these effects, the Cr content of 10.00 mass% or more is required. The content of Cr is preferably 13.50 mass% or more, more preferably 17.00 mass% or more, which is effective in exerting the above-described effects. On the other hand, when Cr is contained in a large amount, it becomes difficult to manufacture a thick hot-rolled steel sheet due to hardening of the steel and reduction in toughness. As a result of various studies, the content of Cr is limited to 25.00 mass% or less, preferably 22.00 mass% or less, and more preferably 20.00 mass% or less.
< N: 0.030% by mass or less
N is a factor of reducing toughness. Therefore, the content of N is limited to 0.030 mass% or less. However, the content of N does not need to be extremely reduced, and the content of N may be usually 0.001 to 0.030 mass%, preferably 0.005 to 0.025 mass%.
< Nb: 0.01-0.80 mass%
Nb is an element that suppresses grain boundary segregation of Cr carbonitride (carbide/nitride) by fixing C and N, and is extremely effective in maintaining high corrosion resistance and high-temperature oxidation resistance of steel. Therefore, the content of Nb needs to be 0.01 mass% or more. The content of Nb is effectively 0.05 mass% or more, and more effectively 0.20 mass% or more. However, if the content of Nb is too high, the toughness of the hot-rolled steel sheet is promoted to be lowered, which is not preferable. As a result of various studies, the content of Nb is limited to 0.80 mass% or less, preferably 0.60 mass% or less.
< Ni: 2.00% by mass or less
Ni has an effect of suppressing the progress of corrosion and may be added as needed. In this case, it is effective to secure an Ni content of 0.01 mass% or more. However, since a large amount of Ni may adversely affect workability, it is necessary to add Ni in a range of 2.00 mass% or less, preferably 1.00 mass% or less.
< Mo: 2.50% by mass or less
Mo is an element effective for improving corrosion resistance, and may be added as needed. In this case, it is effective to secure a Mo content of 0.02 mass% or more, and it is more effective to set the Mo content to 0.50 mass% or more. However, when a large amount of Mo is contained, the toughness is adversely affected, and therefore, when Mo is added, the addition needs to be performed in a range of 2.50 mass% or less, preferably 1.50 mass% or less.
< Cu: 1.80% by mass or less
Cu is an element effective for improving low-temperature toughness and also effective for improving high-temperature strength. Therefore, Cu may be added as necessary. In this case, it is effective to secure a Cu content of 0.02 mass% or more. However, when Cu is added in a large amount, workability is rather lowered. When Cu is added, the amount of Cu needs to be 1.80% by mass or less, preferably 0.80% by mass or less.
< Co: 0.50% by mass or less
Co is an element contributing to low-temperature toughness, and may be added as needed. In this case, it is effective to secure a Co content of 0.010 mass% or more. However, since excessive addition of Co causes reduction in ductility (ductility), it is necessary to add Co in a range of 0.50 mass% or less.
< Al: 0.50% by mass or less
Al is an element effective as a deoxidizer, and may be added as necessary. In this case, it is effective to set the Al content to 0.005 mass% or more. However, when Al is contained in a large amount, it becomes a factor of lowering toughness. Therefore, when Al is contained, the Al content is limited to 0.50 mass% or less, preferably 0.20 mass% or less.
< W: 1.80% by mass or less, V: 0.30% by mass or less
W and V are elements effective for improving the high-temperature strength, and one or more of them may be added as necessary. In this case, it is effective to secure a content of W of 0.10 mass% or more and a content of V of 0.10 mass% or more. However, when these elements are added in large amounts, the steel becomes hard and becomes a factor causing cracks in cold rolling. When W is added, it is necessary to be in the range of 1.80 mass% or less, preferably 0.50 mass% or less. When V is added, it is necessary to be in the range of 0.30% by mass or less, preferably 0.15% by mass or less.
< Ti: 0.50% by mass or less, Zr: 0.20% by mass or less
Ti and Zr are effective elements for fixing C and N and maintaining high corrosion resistance and high temperature oxidation resistance of steel. Therefore, one or more of Ti and Zr may be added as necessary. 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. However, when an excessive amount of Ti is contained, the toughness of the hot-rolled coil (hot-rolled coil) is promoted to be lowered, and therefore, when Ti is added, it is necessary to be in a range of 0.50 mass% or less. Further, when Zr is contained in a large amount, it is a factor that inhibits workability, and therefore, when Zr is added, it is necessary to be in the range of 0.20 mass% or less.
< B: 0.0050 wt.% or less
B is an element which improves corrosion resistance and workability by adding a small amount, and may be added as needed. In this case, it is effective to secure a B content of 0.0001 mass% or more. However, when B is contained excessively, it adversely affects hot workability, and therefore, when B is added, it is necessary to be in the range of 0.0050 mass% or less.
< rare earth elements: 0.100 mass% or less, Ca: 0.0050 wt.% or less
The rare earth element and Ca are effective elements for improving high-temperature oxidation resistance, and one or more of them may be added as needed. In this case, it is effective to secure a content of the rare earth element of 0.001 mass% or more and a content of Ca of 0.0005 mass% or more. However, since the toughness is lowered by adding a large amount of these elements, it is necessary to add the rare earth element in a content range of 0.100 mass% or less, and to add Ca in a content range of 0.0050 mass% or less.
< remainder: fe and inevitable impurities
The balance of the components other than the above components is composed of Fe and inevitable impurities. The inevitable impurities are impurity elements inevitably mixed into the material in the production process. The inevitable impurities are not particularly limited.
The amount of precipitated Nb carbonitride is 0.2 mass% or more, and the particle size of the Laves phase is 0.1 μm or less per 10 μm2Has an area of 10 or less
Nb carbonitride (carbide/nitride) and Laves phases are precipitates generated by hot rolling. When C and N are present in a state of being solid-dissolved in steel, the toughness of the hot-rolled steel sheet is lowered, and therefore, C and N are effective to precipitate as Nb carbonitrides. Further, precipitation of Nb carbonitride reduces Nb dissolved in the steel, and reduces the amount of precipitated Laves phase which reduces the toughness of the hot-rolled steel sheet. In order to reduce C and N dissolved in steel and improve the toughness of the hot-rolled steel sheet, the amount of precipitation of Nb carbonitride needs to be 0.2 mass% or more. Furthermore, the Laves phase with a particle size of 0.1 μm or less needs to be set to 10 μm per phase2The area of (A) is 10 or less.
Here, a mixed solution of 10 mass% of acetylacetone, 1 mass% of tetramethylammonium chloride, and 89 mass% of methanol was used, and after a precipitate residue was extracted by electrolysis at an SCE potential of-100 mV to 400mV with respect to a saturated calomel reference electrode, the extracted residue was filtered through a 0.2 μm microporous filter, and the amount (mass%) of Nb carbonitride precipitated was calculated from the ratio of the weight thereof to the total dissolved weight.
Further, for the Laves phase, a photograph of the surface was taken using a Scanning Electron Microscope (SEM), the size of the Laves phase was measured, and the size was measured for each 10 μm2The number of Laves phases having an area particle diameter of 0.1 μm or less was measured. The number of Laves phases was measured at least at 5 points, and the average value was taken.
< thickness >
The thickness of the hot-rolled steel sheet of the present invention may be appropriately set according to the application, and is not particularly limited. For example, when the hot-rolled steel sheet of the present invention is used for manufacturing an exhaust pipe flange part for an automobile, the thickness of the hot-rolled steel sheet is usually 5.0mm to 11.0mm, preferably 5.5mm to 9.0 mm. When the hot-rolled steel sheet of the present invention is used for manufacturing exhaust pipe parts for automobiles, it is necessary to increase the reduction ratio when cold-rolling the hot-rolled steel sheet of the present invention in order to increase the r value which is an index of the workability of an Nb-containing ferritic stainless cold-rolled steel sheet (hereinafter, may be simply referred to as "cold-rolled steel sheet"). Therefore, when the thickness and cold rolling reduction of a cold-rolled steel sheet used for manufacturing exhaust pipe parts of automobiles are taken into consideration, the thickness of a hot-rolled steel sheet is generally more than 4.5mm and 10.00mm or less. The thickness of the hot-rolled steel sheet is preferably 5.0 to 9.0mm, more preferably 5.5 to 8.0 mm.
Method for producing < Nb-containing ferritic stainless steel hot-rolled steel sheet
The Nb-containing ferritic stainless steel hot-rolled steel sheet of the present invention having the above-described characteristics can be produced by: when a stainless steel slab having the same composition as that of the hot rolled steel sheet of Nb-containing ferritic stainless steel is hot-rolled, the hot-rolled steel sheet is retained at a temperature of 1000 to 1100 ℃ for 60 seconds or more and a finish hot-rolling temperature of 850 ℃ or more, and then coiled at a coiling temperature of 550 ℃ or less after hot-rolling.
Prior to hot rolling, the stainless steel slab is typically heated. The heating temperature of the stainless steel slab is not particularly limited, but is preferably 1200 to 1300 ℃. When the heating temperature of the stainless steel slab is less than 1200 ℃, strain (strain) due to hot rolling may be excessively introduced, and the subsequent structure control becomes difficult, and in addition, surface scratches (surface scratches) may become a problem. On the other hand, when the heating temperature of the stainless steel slab exceeds 1300 ℃, the structure may be coarsened, and a hot rolled steel sheet having desired properties may not be obtained.
After the stainless steel slab was heated in the above manner, hot rolling was performed. Hot rolling typically includes multiple passes of rough hot rolling and multiple passes of finish hot rolling. In order to efficiently promote the precipitation of Nb carbonitride and reduce the precipitation of Laves phase during hot rolling, it is necessary to maintain the temperature of 1000 to 1100 ℃ for 60 seconds or more and set the finish hot rolling temperature to 850 ℃ or more. The reason why the holding temperature is set to 1000 to 1100 ℃ is that: the precipitation temperature of Nb carbonitride is 1100 ℃ or lower, and particularly by setting this holding temperature, precipitation of Nb carbonitride can be promoted efficiently. When the holding temperature and holding time are outside the above ranges, Nb carbonitride is not sufficiently precipitated. Further, when the finish hot rolling temperature is less than 850 ℃, the deposition temperature of the Laves phase is around 800 ℃, and therefore, the deposition of the Laves phase cannot be sufficiently reduced.
The method of holding at 1000 to 1100 ℃ for 60 seconds or more is not particularly limited, and the strip passing speed may be reduced or a delay (delay) may be introduced before the finish rolling.
The timing of holding at a temperature of 1000 to 1100 ℃ for 60 seconds or more is not particularly limited if it is during the hot rolling step, but it is preferably performed from the final stage of rough hot rolling to the initial stage of finish hot rolling.
The finish hot rolling time is not particularly limited, and may be set according to a hot rolling method known in the art. The finish hot rolling time is usually determined in consideration of the balance with the total time of the hot rolling process, but the precipitation amount of Nb carbonitride increases as the finish hot rolling time becomes longer.
After hot rolling, the steel sheet is coiled at a coiling temperature of 550 ℃ or lower to form a coil. When the coiling temperature is higher than 550 ℃, the Laves phase may precipitate and the toughness may be lowered.
In addition, in the hot-rolled steel sheet obtained as described above, since the precipitation amount of Nb carbonitride is sufficiently increased in the hot-rolling step, the Laves phase is less likely to precipitate even at a precipitation temperature of the Laves phase (around 800 ℃. Therefore, there is less necessity to use a method of shortening the transit time of the precipitation temperature of the Laves phase by quenching with water cooling or the like before coiling the hot-rolled steel sheet.
< Nb containing ferritic stainless steel cold-rolled steel sheet and method for producing same
The cold-rolled steel sheet of the present invention has a characteristic that the r value is 1.2 or more in addition to the characteristics of the hot-rolled steel sheet described above. Therefore, the cold-rolled steel sheet of the present invention has excellent workability, and can be processed into various types of automobile exhaust pipe components such as an exhaust manifold, a front pipe, a center pipe, and a catalytic converter outer cylinder.
The cold-rolled steel sheet of the present invention having the above-described characteristics can be produced by: after annealing the hot-rolled steel sheet, cold rolling is performed at a reduction ratio of 70% or more, and annealing is performed.
Before cold rolling, annealing of the hot rolled steel sheet is performed. Annealing is performed at a temperature at which a recrystallized structure is obtained. The annealing temperature may be appropriately set according to the composition of the hot-rolled steel sheet, and is not particularly limited, but is usually 950 to 1150 ℃. When the annealing temperature is lower than 950 ℃, a recrystallized structure may not be obtained. On the other hand, when the annealing temperature is higher than 1150 ℃, the crystal grains are sometimes coarsened.
In order to increase the r-value of a cold-rolled steel sheet to 1.2 or more, cold rolling is performed at a reduction of 70% or more. When the reduction is less than 70%, the r-value of the cold-rolled steel sheet is less than 1.2.
After the cold rolling, annealing of the cold rolled steel sheet is performed. Annealing is performed at a temperature at which a recrystallized structure is obtained. The annealing temperature may be appropriately set according to the composition of the cold-rolled steel sheet, and is not particularly limited, but is usually 1000 to 1100 ℃. When the annealing temperature is less than 1000 ℃, a recrystallized structure may not be obtained. When the annealing temperature is higher than 1100 ℃, crystal grains are coarsened, and surface roughness occurs during processing, which may cause cracks.
[ examples ]
The present invention will be further described with reference to the following examples, but the present invention is not limited to these examples.
Steels having the composition shown in table 1 were melted to prepare stainless steel slabs, and hot-pressed under the conditions shown in table 1 to obtain Nb-containing ferritic stainless hot-rolled steel sheets having a predetermined thickness.
[ Table 1]
Then, from the obtained Nb-containing ferritic stainless steel hot-rolled sheetTest pieces were sampled and tested for the amount of Nb carbonitride precipitated, the size of the Laves phase, and the thickness of each 10 μm2The number of Laves phases having a particle size of 0.1 μm or less in area and toughness were evaluated.
The amount of Nb carbonitride precipitated and the size and number of Laves phases were measured by the methods described above. In the measurement of the amount of precipitated Nb carbonitride, the SCE potential was set to 400 mV. The toughness was evaluated by Charpy impact test (Charpy impact test) using U-notch test pieces. With respect to the acceptance or rejection of toughness, a ductile-brittle transition temperature (DBTT) of 20 ℃ or lower is evaluated as being good (good).
The evaluation results are shown in table 2.
[ Table 2]
As shown in table 2, it was confirmed that: in the Nb-containing ferritic stainless steel rolled sheet of No.1 to 8 produced by holding the stainless steel slab at a temperature of 1000 to 1100 ℃ for 60 seconds or more and a finish hot rolling temperature of 850 ℃ or more and then coiling the stainless steel slab at a coiling temperature of 550 ℃ or less after hot rolling, the amount of precipitation of Nb carbonitride is 0.2 mass% or more and the Laves phase having a particle size of 0.1 μm or less is per 10 μm2Has an area of 10 or less and is excellent in toughness.
In contrast, it is known that: in the hot rolled steel sheets of No.9 to 12 containing Nb ferrite stainless steel, which have too short holding time at 1000 to 1100 ℃ in hot rolling of stainless steel slabs, the amount of Nb carbonitride precipitation is small, the amount of Laves phase is also large, and the toughness is insufficient.
Further, using the Nb-containing ferritic stainless steel hot-rolled steel sheet obtained as described above, a cold forging test, a pressure drilling test (press drilling test), and a cutting test were performed for simulating the processing of a flange part of an exhaust pipe. As a result, the Nb-containing ferritic stainless steel hot-rolled steel sheets of Nos. 1 to 8 were excellent in workability to a desired shape, and no cracks or the like were generated due to insufficient toughness or the like. On the other hand, in the hot-rolled steel sheets of Nb-containing ferritic stainless steels of Nos. 9 to 12, cracks were generated due to insufficient toughness.
Next, the obtained Nb-containing ferritic stainless steel-rolled sheets of Nos. 1 to 7 were annealed, then cold-rolled and annealed to obtain Nb-containing ferritic stainless steel-cold-rolled sheets. The production conditions at this time are shown in table 3. The hot-rolled steel sheets of Nb-containing ferritic stainless steels of Nos. 9 to 12 had low toughness and could not be cold-rolled.
Next, the r value was determined for the obtained Nb-containing ferritic stainless steel cold-rolled steel sheet. For the r value, JIS 13B tensile test pieces were taken from Nb-containing ferritic stainless steel cold-rolled steel sheets, and after 14.4% strain was applied, the average r value was calculated using the following expressions (1) and (2).
r＝ln(W0/W)/ln(t0/t) (1)
Here, W0The width of the sheet before stretching, the width of the sheet after stretching, and t0The thickness before drawing and t the thickness after drawing.
Average r value ═ r0+2r45+r90)/4 (2)
Herein, r is0R is the value of r in the rolling direction45R is a value of r in a direction of 45 DEG to the rolling direction90The r value is taken as the value in the direction perpendicular to the rolling direction.
In exhaust pipe parts of automobiles requiring complicated shapes, the average r value is 1.2 or more, which is a characteristic that can be sufficiently processed, and therefore, the average r value is 1.2 or more, which can be judged to be excellent in workability.
The evaluation results are shown in table 3.
[ Table 3]
As shown in table 3, it was confirmed that: the Nb-containing ferritic stainless steel cold-rolled steel sheets of Nos. 1 to 5 and 7 cold-rolled at a reduction ratio of 70% or more have r values of 1.2 or more and excellent workability.
In contrast, it is known that: no.6 Nb-containing ferritic stainless cold-rolled steel sheet cold-rolled at a reduction of less than 70% has an r value of less than 1.2 and is insufficient in workability.
From the above results, it is understood that the present invention can provide a hot-rolled Nb-containing ferritic stainless steel sheet having excellent toughness and workability, and a method for producing the same. Further, according to the present invention, it is possible to provide a Nb-containing ferritic stainless cold-rolled steel sheet having excellent workability and a method for manufacturing the same.
It is to be noted that the present application claims priority based on Japanese patent application No. 2016-.
Claims (9)
1. A hot-rolled Nb-containing ferritic stainless steel sheet characterized by,
the Nb-containing ferritic stainless steel hot-rolled sheet is obtained by holding a stainless steel slab at a temperature of 1000 to 1100 ℃ for 60 to 71 seconds inclusive and a finish hot-rolling temperature of 850 ℃ inclusive, and then coiling the slab at a coiling temperature of 550 ℃ inclusive after hot-rolling, wherein the stainless steel slab has the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, the balance being Fe and unavoidable impurities,
the amount of precipitation of Nb carbonitride in the hot-rolled Nb-containing ferritic stainless steel sheet is 0.2 mass% or more, and the amount of Laves phase having a grain size of 0.1 μm or less is 10 μm per unit2The area of (a) is 10 or less,
the Charpy impact test using the U-notch test piece has a ductile-brittle transition temperature of 20 ℃ or lower.
2. The Nb-containing ferritic stainless steel hot-rolled steel sheet according to claim 1, characterized in that,
has the following composition: also contains Ni: 2.00 mass% or less, Mo: 2.50% by mass or less of Cu: 1.80% by mass or less, Co: 0.50 mass% or less, Al: 0.50 mass% or less, W: 1.80% by mass or less, V: 0.30% by mass or less, Ti: 0.50% by mass or less, Zr: 0.20% by mass or less, B: 0.0050% by mass or less of rare earth elements: 0.100 mass% or less, Ca: 0.0050 wt% or less.
3. The Nb-containing ferritic stainless steel hot-rolled steel sheet according to claim 1 or 2, characterized by being used for manufacturing a flange part for an exhaust pipe.
4. A method for producing a hot-rolled Nb-containing ferritic stainless steel sheet according to any one of claims 1 to 3, characterized in that,
a stainless steel slab having a composition comprising, when hot-rolled, a stainless steel slab having a temperature of 1000-1100 ℃ for 60-71 seconds inclusive and a finish hot-rolling temperature of 850-850 ℃ inclusive, and thereafter coiled at a coiling temperature of 550 ℃ or lower: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, and the balance of Fe and inevitable impurities.
5. The method of manufacturing the Nb-containing ferritic stainless steel hot-rolled steel sheet according to claim 4, characterized in that,
the stainless steel slab has the following composition: also contains Ni: 2.00 mass% or less, Mo: 2.50% by mass or less of Cu: 1.80% by mass or less, Co: 0.50 mass% or less, Al: 0.50 mass% or less, W: 1.80% by mass or less, V: 0.30% by mass or less, Ti: 0.50% by mass or less, Zr: 0.20% by mass or less, B: 0.0050% by mass or less of rare earth elements: 0.100 mass% or less, Ca: 0.0050 wt% or less.
6. A Nb-containing ferritic stainless cold-rolled steel sheet produced by using the Nb-containing ferritic stainless hot-rolled steel sheet according to any one of claims 1 to 3, characterized in that,
has the following composition: contains C: 0.030% by mass or less, Si: 2.00 mass% or less, Mn: 2.00% by mass or less, P: 0.050% by mass or less, S: 0.040 mass% or less, Cr: 10.00-25.00 mass%, N: 0.030% by mass or less, Nb: 0.01 to 0.80% by mass, the balance being Fe and unavoidable impurities,
the precipitation amount of Nb carbonitride of the Nb-containing ferritic stainless steel cold-rolled steel sheet is 0.2 mass% or more, and the amount of Laves phase having a grain size of 0.1 μm or less is 10 μm per unit2Has an area of 10 or less and an r value of 1.2 or more.
7. The Nb-containing ferritic stainless steel cold-rolled steel sheet according to claim 6,
has the following composition: also contains Ni: 2.00 mass% or less, Mo: 2.50% by mass or less of Cu: 1.80% by mass or less, Co: 0.50 mass% or less, Al: 0.50 mass% or less, W: 1.80% by mass or less, V: 0.30% by mass or less, Ti: 0.50% by mass or less, Zr: 0.20% by mass or less, B: 0.0050% by mass or less of rare earth elements: 0.100 mass% or less, Ca: 0.0050 wt% or less.
8. The Nb-containing ferritic stainless cold-rolled steel sheet according to claim 6 or 7, characterized by being used for production of exhaust pipe parts.
9. A method for producing a ferritic stainless steel cold-rolled steel sheet containing Nb, characterized in that,
a hot-rolled steel sheet of Nb-containing ferritic stainless steel according to claim 1 or 2, which is then annealed, cold-rolled at a reduction of 70% or more, and then annealed.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2016-017883 | 2016-02-02 | ||
| JP2016017883 | 2016-02-02 | ||
| PCT/JP2017/003379 WO2017135240A1 (en) | 2016-02-02 | 2017-01-31 | HOT ROLLED Nb-CONTAINING FERRITIC STAINLESS STEEL SHEET AND METHOD FOR PRODUCING SAME, AND COLD ROLLED Nb-CONTAINING FERRITIC STAINLESS STEEL SHEET AND METHOD FOR PRODUCING SAME |
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| Publication Number | Publication Date |
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| CN108495944A CN108495944A (en) | 2018-09-04 |
| CN108495944B true CN108495944B (en) | 2020-12-25 |
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| CN201780007794.6A Active CN108495944B (en) | 2016-02-02 | 2017-01-31 | Hot-rolled Nb-containing ferritic stainless steel sheet and method for producing same, and cold-rolled Nb-containing ferritic stainless steel sheet and method for producing same |
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| Country | Link |
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| US (2) | US20180363089A1 (en) |
| EP (2) | EP3708690A1 (en) |
| JP (1) | JP6383503B2 (en) |
| KR (1) | KR102267129B1 (en) |
| CN (1) | CN108495944B (en) |
| CA (1) | CA3009133A1 (en) |
| MX (1) | MX2018009402A (en) |
| RU (1) | RU2712668C1 (en) |
| TW (1) | TWI707049B (en) |
| WO (1) | WO2017135240A1 (en) |
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| CA3018162C (en) * | 2016-03-30 | 2022-07-05 | Nisshin Steel Co., Ltd. | Nb-containing ferritic stainless steel sheet and manufacturing method therefor |
| KR102020511B1 (en) * | 2017-12-14 | 2019-09-10 | 주식회사 포스코 | Ferritic stainless steel with excellent impact toughness and manufacturing method thereof |
| JP7009278B2 (en) * | 2018-03-26 | 2022-02-10 | 日鉄ステンレス株式会社 | Ferritic stainless steel sheets with excellent heat resistance and exhaust parts and their manufacturing methods |
| KR102135158B1 (en) * | 2018-09-19 | 2020-07-17 | 주식회사 포스코 | Ferritic stainless steel excellent in workability and high temperature strength and manufacturing method thereof |
| KR102123663B1 (en) * | 2018-09-27 | 2020-06-17 | 주식회사 포스코 | Ferritic stainless steel and ferritic stainless steel pipe with improved mechanical properties of weld |
| KR101943591B1 (en) | 2018-11-13 | 2019-01-30 | 한국과학기술원 | Austenitic stainless steel having niobium and manufacturing method of the same |
| CN109355478B (en) * | 2018-12-24 | 2021-02-05 | 东北大学 | B444M2 type ferritic stainless steel with improved high-temperature oxidation resistance and preparation method thereof |
| US20220170129A1 (en) * | 2019-03-26 | 2022-06-02 | Jfe Steel Corporation | Ferritic stainless steel sheet and method for manufacturing the same |
| CN109913758B (en) * | 2019-03-29 | 2020-08-11 | 东北大学 | Ferritic stainless steel plate with good high-temperature strength and forming performance and preparation method thereof |
| JP7047813B2 (en) * | 2019-05-29 | 2022-04-05 | Ｊｆｅスチール株式会社 | Ferritic stainless steel sheet and its manufacturing method |
| CN113767181B (en) * | 2019-05-29 | 2023-05-09 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet and method for producing same |
| KR102280643B1 (en) | 2019-10-22 | 2021-07-22 | 주식회사 포스코 | Chromium steel having excellent high-temperature oxidation resistance, high-temperature strength and method of manufacturing the same |
| TWI750077B (en) * | 2020-04-15 | 2021-12-11 | 日商日鐵不鏽鋼股份有限公司 | Fertilizer-based stainless steel material and manufacturing method thereof |
| EP4151755A4 (en) * | 2020-07-08 | 2023-09-20 | JFE Steel Corporation | Method for manufacturing ultra-low carbon steel product |
| KR20220088157A (en) * | 2020-12-18 | 2022-06-27 | 주식회사 포스코 | Ferritic stainless steel excellent in heat resistance and method for manufacturing thereof |
| CN113322417B (en) * | 2021-06-04 | 2022-06-28 | 西安建筑科技大学 | Laves phase reinforced stainless steel and preparation method thereof |
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- 2017-01-31 EP EP17747396.4A patent/EP3388542A4/en not_active Withdrawn
- 2017-01-31 RU RU2018119752A patent/RU2712668C1/en active
- 2017-01-31 MX MX2018009402A patent/MX2018009402A/en unknown
- 2017-01-31 JP JP2017549433A patent/JP6383503B2/en active Active
- 2017-01-31 CA CA3009133A patent/CA3009133A1/en not_active Abandoned
- 2017-01-31 KR KR1020187018664A patent/KR102267129B1/en active IP Right Grant
- 2017-01-31 US US16/061,159 patent/US20180363089A1/en not_active Abandoned
- 2017-01-31 WO PCT/JP2017/003379 patent/WO2017135240A1/en active Application Filing
- 2017-02-02 TW TW106103476A patent/TWI707049B/en active
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2020
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Also Published As
| Publication number | Publication date |
|---|---|
| KR102267129B1 (en) | 2021-06-18 |
| KR20180109865A (en) | 2018-10-08 |
| US20200255919A1 (en) | 2020-08-13 |
| EP3708690A1 (en) | 2020-09-16 |
| TW201732055A (en) | 2017-09-16 |
| CN108495944A (en) | 2018-09-04 |
| EP3388542A1 (en) | 2018-10-17 |
| EP3388542A4 (en) | 2019-11-06 |
| RU2712668C1 (en) | 2020-01-30 |
| MX2018009402A (en) | 2018-12-19 |
| JP6383503B2 (en) | 2018-08-29 |
| TWI707049B (en) | 2020-10-11 |
| JPWO2017135240A1 (en) | 2018-02-08 |
| WO2017135240A1 (en) | 2017-08-10 |
| US20180363089A1 (en) | 2018-12-20 |
| CA3009133A1 (en) | 2017-08-10 |
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