WO2008013305A1 - Feuille en acier inoxydable pour pièces et procédé de fabrication de celle-ci - Google Patents

Feuille en acier inoxydable pour pièces et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2008013305A1
WO2008013305A1 PCT/JP2007/064910 JP2007064910W WO2008013305A1 WO 2008013305 A1 WO2008013305 A1 WO 2008013305A1 JP 2007064910 W JP2007064910 W JP 2007064910W WO 2008013305 A1 WO2008013305 A1 WO 2008013305A1
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Prior art keywords
mass
stainless steel
less
cold rolling
parts
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PCT/JP2007/064910
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English (en)
Japanese (ja)
Inventor
Kazuhiko Adachi
Masaru Abe
Kazuyoshi Fujisawa
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Sumitomo Metal Industries, Ltd.
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Application filed by Sumitomo Metal Industries, Ltd. filed Critical Sumitomo Metal Industries, Ltd.
Priority to JP2008526850A priority Critical patent/JP4475352B2/ja
Priority to CN2007800276522A priority patent/CN101490298B/zh
Priority to EP07791595.7A priority patent/EP2048256B1/fr
Publication of WO2008013305A1 publication Critical patent/WO2008013305A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0452—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 with application of tension
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0252—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with application of tension

Definitions

  • the present invention relates to a stainless steel plate processed as an industrial product and a method for producing the same, and in particular, has high strength, high fatigue characteristics and excellent workability, and further has high flatness and low residual stress.
  • the present invention relates to a stainless steel plate for parts and a manufacturing method thereof. That is, the present invention relates to a stainless steel plate that exhibits excellent performance in many products and parts manufactured from a stainless steel plate or a steel strip (hereinafter sometimes collectively referred to as “stainless steel plate”), and its It relates to a manufacturing method.
  • the present invention relates to a stainless steel plate suitable for a wide variety of parts used in industrial products, which is highly accurate and complicated as products become smaller, lighter, and more complicated.
  • a wide variety of parts are used inside and outside various industrial products such as automobiles, home appliances, IT equipment, and mobile phones.
  • materials for each part there are a wide variety of materials for each part, but many metal materials are used, and stainless steel is often used.
  • Many of these parts made of stainless steel are manufactured from stainless steel plates by methods such as pressing and etching.
  • the stainless steel plate is formed into a predetermined shape using a die after being made into a predetermined size by cutting I ", blanking or the like.
  • a typical example is the ability to list panel parts.
  • Panel parts are used in many industrial products and may be used in many parts of a product.
  • there are many types of panel parts which are roughly divided into dish panels and plate panels. Specific examples include washers inserted between bolts and nuts, small dish panels used under mobile phone buttons, gaskets used in automobiles and motorcycles, and methanol packing.
  • etching a pattern is formed on the surface of the plate by a photoresist method, and a part of the material is corroded and removed (etched) by chemical means such as dipping in acid or spraying to cope with the pattern. It is to obtain a shape. Etching is difficult to press There are many applications to the processing of precision parts that are difficult, for example. This includes, for example, small parts such as the paper used for fixing magnetic heads, printer paper feed gears, shadow masks for conventional TVs that have an extremely large number of small holes, and meshes for printed circuit board printing. The power of S
  • Formability Complicating parts ⁇ With higher precision, it is necessary to process more complex shapes with high precision, so excellent formability is required. In general, the formability is proportional to the elongation (ductility) of the material, and the strength and elongation are in conflict (incompatible), and both high strength and excellent formability are required.
  • Etching performance Similarly, as parts become more complex and highly accurate, excellent etching performance is required to obtain a smooth machined surface free from defects such as locally generated holes (etching pits).
  • Residual stress When taken from a relatively large material (relative to the part), the part is released from surrounding constraints and changes shape due to the release of residual stress. In other words, the parts do not show the prescribed shape, and the defect rate when assembled into a product (which is smaller and lighter) increases (yield decreases). For this reason, the force S is required that the residual stress is low and stable.
  • the above-mentioned parts and the like are metastable like SUS301 and SUS304.
  • Stenai K ⁇ stainless steel has been used.
  • the transformation from the ⁇ parent phase to the hard martensite phase (processing-induced martensite ( ⁇ ′) transformation) can be caused by processing at room temperature.
  • This processing is usually performed by cold rolling, and the strength can be adjusted by adjusting the rolling reduction of the cold rolling.
  • Patent Document 1 discloses the fatigue characteristics due to the limitation of the dimensions of the compounds that are the starting points of fracture.
  • Patent Document 2 discloses an improvement in etching properties by limiting the distribution of compounds that serve as starting points of etching pits (holes).
  • Patent Document 3 discloses improvement of formability and fatigue characteristics by refining crystal grains!
  • Patent Document 4 and Patent Document 5 disclose a TA (Tension-Annealing) process as an improvement of the series of manufacturing steps. In this method, heating is performed at a relatively low temperature while applying tension within a range in which the performance after temper rolling is not significantly changed, and flatness improvement and residual stress reduction can be performed simultaneously.
  • Patent Document 6 and Patent Document 7 describe a stainless steel manufacturing method having a temper annealing method and a high-performance metastable ⁇ obtained by the temper annealing method. A stainless steel sheet is disclosed. The outline of the process is shown in Fig. 6.
  • a stainless steel material having a predetermined composition is softened by temper annealing of a material that has been work-hardened by cold rolling to a product sheet thickness, and the performance is adjusted.
  • the material becomes a mixed structure of the recrystallized grains and the unrecrystallized portion that remains affected by the pre-processing, and it is possible to achieve both high strength and high ductility by optimizing the ratio.
  • transformation from work-induced martensite ( ⁇ ') phase to austenite ( ⁇ ) parent phase this is referred to as "reverse transformation"
  • recovery and recrystallization occur, resulting in residual stress. Reduced.
  • Patent Documents 8 to 10 the rolling conditions and heat treatment conditions of the stainless steel plate as the material are specified, and transition and martensite are introduced into the crystal grains to increase the etching rate in the crystal grains.
  • An increasing stainless steel sheet for photoetching is disclosed. This means that the smoothness of the etched surface is improved by making the etching rate in the crystal grains equal to that of the crystal grain boundaries.
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2005-290449
  • Patent Document 2 Japanese Patent Laid-Open No. 2000-273586
  • Patent Document 3 Japanese Patent Laid-Open No. 5-279802
  • Patent Document 4 Japanese Patent Laid-Open No. 10-34237
  • Patent Document 5 JP 2001-226718
  • Patent Document 6 Japanese Patent No. 3603726
  • Patent Document 7 Japanese Patent Application Laid-Open No. 2002-194506
  • Patent Document 8 Japanese Patent Laid-Open No. 2005-314772
  • Patent Document 9 JP-A-2005-320586
  • Patent Document 10 Japanese Unexamined Patent Application Publication No. 2005-320587 Disclosure of the invention
  • the manufacturing method has the same problem, and it has been an object to adopt a method for manufacturing a stainless steel plate that can solve the above-described problem.
  • the conventional manufacturing method and the manufacturing methods of Patent Document 4 and Patent Document 5 have a limit in achieving both high strength and high ductility of the material.
  • shape correction becomes difficult and the plate shape tends to deteriorate.
  • strain relief annealing took a long time and became a factor that hindered productivity.
  • the plate thickness and hardness are different, and the amount used may be relatively small, these problems become prominent, resulting in a significant increase in product cost.
  • Patent Document 6 and Patent Document 7 have problems for coping with further improvement in workability by promoting the tendency to reduce the size and weight of products and parts, and expanding the variety of products. It was.
  • the present invention provides a stainless steel plate capable of improving workability (formability, etching property) and fatigue characteristics while having good strength and ductility, and a method for producing the stainless steel plate. Let it be an issue. Furthermore, another object is to stably supply the stainless steel plate of the present invention at low cost and industrially by the method for producing the stainless steel plate. Means for solving the problem
  • the performance is improved by the structure having the ⁇ mixed structure.
  • the recrystallization part in the mixed structure has the effect of strengthening by grain refinement and the suppression of non-uniform deformation at the grain boundary due to the increase in density, while the non-recrystallized part in the mixed structure has work hardening and reverse transformation.
  • the deformation progresses uniformly and the formability (ductility) is improved.
  • the etching property can be considered, and it is considered that the etched surface becomes uniform due to the refinement of crystal grains and the increase in the single structure of the ⁇ parent phase. As a result, the non-uniform portion that becomes the starting point of fatigue fracture disappears, and the fatigue characteristics after molding and after etching are improved.
  • the final cold rolling can pulverize and refine the compound by increasing the reduction ratio. This is one of the advantages of performance adjustment as a separate process (temper annealing), and temper rolling is inevitably performed at a predetermined processing rate for performance adjustment.
  • the invention as described in claim 1 is the entire stainless steel is taken as 100 mass%, 0.1 to C 01-0. 08 mass 0/0, Si and 0. 1 2. 0 weight 0/0, Mn and 3.0 mass 0/0 or less, the Cr 10. 0-20. 0 wt 0/0, Ni 3. 0-12. 0 wt 0/0, N and 0.02 -0. containing each ingredient 24 mass 0/0, and the formula wherein is contained the values of the mass% of each component is substituted
  • the invention described in claim 2 is the whole stainless steel is taken as 100 mass%, 0.1 to C 01-0. 08 mass 0/0, Si and 0. 1 2. 0 weight 0/0, Mn and 3.0 mass 0/0 or less, the Cr 10. 0 to 20. 0 wt 0/0, Ni of 3.0 to 12.0 mass 0/0, N and 0.02 to 0. 24 wt 0/0, and Nb, Ti, and containing each component at least one of 0.5 mass% or less selected from V, and the hydrated Formula that substitutes the mass% value of each component
  • Md 500-458 (C + N) -9 (Si + Mn)-14Cr-20Ni- 65Nb- 27Ti- 61V Md value of 0 ⁇ 80 is satisfied, the balance is unavoidable chemical composition
  • the internal diameter of the compound having a maximum diameter of 20 m or more among the compounds formed by each component is 30 or less per 5 g of the stainless steel mass, and the metal structure of the entire stainless steel is The problem is solved by providing a stainless steel sheet for parts, which is a mixed structure of recrystallized grains and non-recrystallized parts.
  • the invention described in claim 3 is characterized in that the average grain size of recrystallized grains of the stainless steel sheet for parts described in claim 1 or 2 is 10 m or less. To do.
  • the invention described in claim 4 is characterized in that the mixed structure of the stainless steel sheet for parts described in claim 3 is an austenitic phase of 70 mass% or more.
  • the invention described in claim 5 is the entire stainless steel is taken as 100 mass%, 0.1 to C 01-0. 08 mass 0/0, Si and 0. 1 2. 0 weight 0/0, Mn and 3.0 mass 0/0 or less, the Cr 10. 0-20. 0 wt 0/0, Ni 3. 0-12. 0 wt 0/0, N and 0.02 -0. containing each ingredient 24 mass 0/0, and the formula wherein is contained the values of the mass% of each component is substituted
  • a first cold rolling step (S1) in which a material having a chemical composition with an Md value of 0 to 80 and a balance of inevitable impurities is cold-rolled at least once (S1)
  • the first annealing step (S2) arranged after the first cold rolling step in combination with the hot rolling step, and the final rolling provided on the subsequent step side of the first annealing step, with a reduction rate of 20%
  • the second cold rolling step (S3) in which the total rolling reduction with the first cold rolling is 60% or more, and the material after the second cold rolling step is 650 to 1000 ° C.
  • a second annealing step (S4) in which the material is held at 300 seconds or less and tempered by applying a tensile strength of 0.2% or less of the material at the held temperature. Solve the problem.
  • the invention described in claim 6 is the entire stainless steel is taken as 100 mass%, 0.1 to C 01-0. 08 mass 0/0, Si and 0. 1 2. 0 weight 0/0, Mn and 3.0 mass 0/0 or less, the Cr 10. 0 to 20. 0 wt 0/0, Ni of 3.0 to 12.0 mass 0/0, N and 0.02 to 0. 24 wt 0/0, and Nb, Ti, and containing each component at least one of 0.5 mass% or less selected from V, and the hydrated Formula that substitutes the mass% value of each component
  • the invention described in claim 7 is the material at a temperature where the tension in the second annealing step of the method for manufacturing a stainless steel sheet for parts according to claim 5 or 6 is maintained. 0. 40% or less of 2% yield strength.
  • the invention described in claim 8 is further adjusted after the second annealing step (S4) in the method for manufacturing a stainless steel plate for parts according to any one of claims 5 to 7. It is characterized by applying quality rolling.
  • the present invention it is possible to provide a stainless steel plate and a method for manufacturing the same that can manufacture a wide variety of parts with high accuracy and high reliability.
  • FIG. 1 is a diagram for explaining one embodiment of the flow of the production method of the present invention.
  • FIG. 2 is a graph showing an example of the relationship between the temperature of a material and the 0 ⁇ 2% proof stress.
  • FIG. 4 The surface of the bent portion in the case of No. 4 and No. 28 of this example is shown enlarged. It is a photograph.
  • FIG. 5 is a diagram for explaining one example of a conventional method for producing a stainless steel plate.
  • FIG. 6 is a view for explaining another example of a conventional method for producing a stainless steel plate.
  • the stainless steel plate of the present invention will be described.
  • the stainless steel sheet of the present invention is characterized by its composition and structure, Md value, and the mode of the underlying compound. Each will be described below.
  • the component contained in this invention and its content are demonstrated.
  • the main component of the stainless steel plate of the present invention is Fe, and the contents shown below show the ratio when the entire stainless steel plate is 100 mass%.
  • C The content of C is set to 0.01 to 0.08 mass%.
  • C is one of the cheap and effective interstitial solid solution strengthening elements. The effect of strengthening the solid solution by adding 0.1% by mass or more is exhibited. On the other hand, the upper limit is 0.08% by mass. This is because C is a strong ⁇ -stabilizing element, and excessive addition suppresses the processing-induced martensite ( ⁇ ') transformation that is necessary.
  • ⁇ ' processing-induced martensite
  • a more preferable range of the C content is 0.02-0.07% by mass.
  • Si content should be 0 .;!-2.0 mass%.
  • Si is an effective solid solution strengthening element.
  • the reason why the lower limit is set to 0.1% by mass or more is that this increases the high-temperature strength and facilitates acquisition of the above-mentioned mixed structure, which is a feature of the present invention.
  • the upper limit was set to 2.0% by mass because Si is also a ferri ( ⁇ ) stabilizing element, and excessive addition increases the ⁇ and phase remaining during temper annealing.
  • a more preferable range of the Si content is 0.2 to 1.8% by mass.
  • Mn The Mn content is 3.0 mass% or less.
  • Mn is a ⁇ -stabilizing element and is added in consideration of the balance with other elements. The reason why the content is 3.0% by mass or less is that when it is added excessively, ⁇ and compatibility S cannot be obtained. In addition, inclusions and the like may be formed, which may deteriorate workability and corrosion resistance.
  • a more preferable range of the Mn content is 2.6% by mass or less.
  • the content of Cr is 10.0 to 20.0 mass%.
  • Cr is one of the basic alloy elements of stainless steel. The reason why the content is 10.0% by mass or more is to obtain the necessary corrosion resistance.
  • the upper limit was set to 20.0% by mass because Cr is an ⁇ -stabilizing element, and excessive addition increases the ⁇ ′ phase remaining after temper annealing.
  • a more preferred range of Cr content is 13. 0-19. 0 wt 0/0.
  • Ni The Ni content is 3.0 to 12.0% by mass.
  • Ni is one of the basic alloy elements of stainless steel and is the most effective gamma stabilizing element.
  • the reason why the lower limit is set to 3.0% by mass is that it is indispensable for obtaining a stable ⁇ phase at room temperature.
  • the upper limit is set to 12.0% by mass because it is necessary to cause the ⁇ ′ transformation within a predetermined range.
  • a more preferable range of the Ni content is 3.5-11. 5% by mass.
  • N is 0.02 to 0.25% by mass.
  • N is one of the effective interstitial solid-solution strengthening elements like C, and it has the ability to form a solid solution without forming a compound up to a higher temperature than C. That is, it is the main reinforcing element of the present invention. From this point of view, the lower limit was set to 0.02 mass%. The upper limit is set to 0.25% by mass because when it is added excessively, the hot workability is deteriorated and the production of the plate may be hindered.
  • N like C, is one of the powerful ⁇ -stabilizing elements, and it also depends on suppressing ⁇ ′ transformation.
  • Nb The content of Nb is 0.50 mass% or less. Nb precipitates Nb compounds that are relatively stable and finely dispersed even at high temperatures, making it easy to obtain a mixed structure, and recrystallized grains can be refined by suppressing grain growth.
  • the upper limit is set to 0.50% by mass because excessive addition forms a coarse compound and lowers the ductility of the material. Moreover, since it is an expensive substance, an upper limit is set from the viewpoint of cost.
  • a more preferable range of Nb is 0.45% by mass or less.
  • Ti content is 0.50 mass% or less. Ti is considered to have the same effect as Nb. In other words, the precipitation of Ti compound facilitates the acquisition of the mixed structure, and the recrystallized grains can be refined. In addition, it is thought to form compounds more easily than Nb.
  • the upper limit is set to 0.50% by mass because excessive addition forms a coarse compound and lowers the ductility of the material.
  • the Ti content is more preferably 0.45% by mass or less
  • V The content of V is 0.50 mass% or less. V has the same effect as Nb and Ti.
  • the precipitation of the V compound facilitates the acquisition of the mixed structure and refines the recrystallized grains.
  • the upper limit is set to 0.50% by mass because excessive addition forms a coarse compound and lowers the ductility of the material.
  • a more preferable range of the V content is 0.001% by mass or more and 0.45% by mass or less.
  • elements added from an industrial aspect such as Ca, A1 or REM (rare earth metal) used as a deoxidizer during melting, and B, which is expected to improve hot workability, are required.
  • the total amount may be 0.3% by mass or less.
  • each of Cu and Mo, which are inevitable may be contained in an amount of 0.4% by mass or less.
  • Cu and Mo act as elements for adjusting the ⁇ stability in the present invention.
  • inevitable impurities in a normal composition may be included.
  • the Md value is calculated according to the formula (1) or formula (2) in the present invention, and the value is 0 to 80 ° C.
  • formula (2) is used. If neither is added, it is calculated using equation (1).
  • the symbols C, N, Si, M in the formula For n, Cr, Ni, Nb, Ti, and V, the content (% by mass) of the corresponding component is substituted.
  • Md 500-458 (C + N) — 9 (Si + Mn) — 14Cr— 20Ni ⁇ ⁇ ⁇ (1)
  • Md value It is expressed in units of C and indicates the ease with which processing-induced martensite ( ⁇ ') transformation occurs.
  • the present invention targets metastable ⁇ stainless steel and utilizes the ⁇ ′ transformation, so it is necessary to control the ⁇ ′ transformation. Therefore, the optimum Md value for this purpose was set to 0 to 80 ° C. More preferably, it is 10-70 degreeC.
  • the stainless steel plate of the present invention in the compounds contained in the stainless steel plate, those having a maximum diameter of 20 m or more are inherent in 30 or less per 5 g of the mass of the stainless steel plate. As a result, the occurrence of defects due to the compound can be reduced. That is, it is considered that the material has excellent moldability, and the probability that a coarse compound exists in the vicinity of the surface becomes extremely small. In the case of pressing, unevenness and minute cracks due to a large difference in deformability between the two (material and coarse compound) are improved. In the case of the etching process, the occurrence of local defects such as compound exposure due to the difference in corrosion resistance, and further, holes (etch pits) due to dropping off is eradicated. As a result, the surface of the machined part becomes smooth and the fatigue characteristics are improved. This local defect is considered to be detected by measuring the maximum roughness of the surface of the processed part.
  • the material structure of the stainless steel sheet of the present invention is a “mixed structure” defined by a mixed structure of recrystallized grains and unrecrystallized parts that remain affected by pre-processing. As a result, it is possible to achieve both high strength and high ductility, as well as high flatness and low residual stress.
  • the mixed structure may have a ⁇ phase force of 70 area% or more. By forming the ⁇ phase as the main structure, formability and fatigue characteristics are further improved. More preferably, it is 80 area% or more.
  • the various properties are excellent. Further, it is possible to provide a stainless steel sheet that can improve workability (formability, etching property) and fatigue characteristics.
  • the grain size of recrystallization may be 10 m or less. This further improves the formability and fatigue characteristics resulting from the refinement of crystal grains. More preferably, it is 6 m or less.
  • the method for producing a stainless steel plate of the present invention comprises a first cold rolling step (S 1) that is at least one cold rolling step, and a first cold rolling step (S1 ) And at least one first annealing step (S2), a second cold rolling step (S3), and a second annealing step (S4) that is annealing for tempering. is there.
  • S 1 first cold rolling step
  • S1 first cold rolling step
  • S2 at least one first annealing step
  • S3 a second cold rolling step
  • S4 second annealing step
  • the first cold rolling step (S1) a material that has been hot-worked by adding the above-described components is supplied. This process is performed mainly for the purpose of bringing the dimensions of the material closer to the steel sheet that is finally obtained. Therefore, the rolling may be performed several times, not necessarily once. Specifically, if the total rolling reduction with the second cold rolling performed later is 60% or more, preferably 70% or more, more preferably 80% or more, most preferably 90%. That's it.
  • This is a process that is combined with the first cold rolling process (S1), and is a process mainly intended to impart softening and ductility of the material. Therefore, the conditions are not particularly limited as long as the annealing process is performed normally. The conditions are determined by the material to be supplied and the form of the steel sheet finally obtained.
  • the second cold rolling step (S3) is a step that is arranged after the first cold rolling step (S1) and the first annealing step (S2) and performs the final cold rolling.
  • the thickness is reduced to the final thickness of the stainless steel plate.
  • the thickness reduction is 20% or more in terms of rolling reduction, and the total rolling reduction with the first cold rolling is 60% or more. This reduces the rolling reduction by 20 This is because a sufficient work-induced martensite ( ⁇ ′) phase can be obtained by setting the content to at least%. Furthermore, this makes it possible to refine crystal grains. Preferably it is 30% or more.
  • the total reduction ratio of the first cold rolling and the second cold rolling was set to 60% or more.
  • the compound was finely pulverized to obtain a coarse compound of 20 inches or more.
  • the number of can be reduced. This makes it possible to reduce the maximum diameter of the compound and reduce the number of coarse compounds of 20 m or more. At this time, cold rolling using a small-diameter work roll is preferable because the effect of crushing coarse compounds is high.
  • the second annealing step (S4) is the final annealing step, and this determines the material aspect of the stainless steel plate that can be finally obtained. Specifically, in this step, the annealing temperature was set to 650 to 1000 ° C, and the holding time was set to 300 seconds or less. This is specified from the viewpoints of adjusting the mechanical properties of the material and also affecting the metal structure of the material, such as crystal grain growth, and the production efficiency. This makes it possible to obtain a stainless steel plate that is efficient and has high flatness and low residual stress.
  • the annealing temperature is set and tension is applied to the material.
  • the magnitude of the tension is less than 0.2% resistance of the material at the annealing temperature. More preferably, it is 40% or less of the 0.2% proof stress.
  • the reverse transformation is adjusted by applying tension to the material at such a size. Accordingly, fine recrystallized grains are included in the material, and the material can have a mixed structure with a high proportion of ⁇ phase. As a result, the obtained stainless steel sheet is given a well-balanced strength and ductility, and both high flatness and low residual stress can be achieved.
  • Figure 2 shows a graph showing an example of the relationship between the temperature of the material and the 0.2% proof stress value of the material. For example, the tension is determined and applied according to FIG.
  • temper rolling can be performed after the second annealing for the purpose of increasing the strength, etc., as long as the effect of the inclusion distribution and the mixed structure exhibiting high performance can be maintained. It is.
  • the stainless steel plate for parts of the present invention can be produced. That is, it is possible to produce and provide a stainless steel plate that can improve the caloric properties (formability, etching property) and fatigue properties while making the above various properties excellent. According to the production method, the stainless steel sheet of the present invention can be supplied inexpensively and industrially stably.
  • the present invention is not limited to the examples.
  • a stainless steel plate corresponding to the present invention and a stainless steel plate not corresponding to the present invention were manufactured and subjected to various evaluations.
  • Table 1 shows the composition of the specimens. Among each component, those outside the scope of the present invention are marked with “*” for the content number.
  • a stainless steel plate was manufactured according to each manufacturing condition for each of the materials having the compositions shown in Tables 1 to 1.
  • Table 2 shows the main conditions in the manufacturing process.
  • Test steel Manufacturing process Inclusion miniaturization measures 1st and 2nd cold 2nd cold rolling 2nd annealing process
  • temper rolling was performed to a thickness of 0.2 mm, and each hardness specification defined in JI S G 4313 was used. Then, straightening with a tension leveler, 500 ° C heating, and strain relief annealing for 300 seconds were performed.
  • the work rolls used in the cold rolling were those with a diameter of 200 mm.
  • Test pieces were collected from the 0.2 mm-thick thin plate obtained as described above, and various characteristics were investigated and compared.
  • Crystal grain size Regarding the cross section of the sample parallel to the rolling direction (R. D.), the structure after embedding, polishing and etching was observed using an optical microscope and SEM. In addition, a thin film was formed and the structure was observed using a transmission electron microscope (TEM). Then, a photograph of an average structure was taken in each, and the crystal grain size was measured from the photograph. This also determined whether the tissue was a mixed tissue.
  • the crystal grain size is No .;! To No. 26 is the value of recrystallized grains after temper annealing,
  • ⁇ phase ratio A diffraction pattern was measured on the surface of the plate using an X-ray diffractometer, and the ratio of the negative phase and the ⁇ 'phase was calculated from the integrated intensity ratio of each phase peak.
  • Hardness The surface of the plate was measured at a load of 9.8 mm using a Micro'Vickers hardness tester.
  • Elongation Samples taken in parallel with the rolling direction (R. D.) and measured for an IS-3 ⁇ test piece were measured using an Instron type tester.
  • Rate of increase (%) 100 X (Ry after bending, Ry before processing) / (Ry before processing).
  • Fatigue properties Using a swing-type plane bending tester, the fatigue limit (the upper limit of the stress that can withstand 107 repeated bendings) in a material that has not been bent was clarified. Next, the test specimens whose surface roughness was used for the measurement bending were repeatedly bent at a stress of 90% of the fatigue limit of the material, and the presence or absence of cracks after 107 repeated bendings was investigated. The case of cracking was evaluated as X, and the case of cracking force was evaluated as ⁇ .
  • Plate warpage In this example, flatness was evaluated by plate warpage. The method is to measure the height of the rising warp by hanging the test piece of 500mm in length taken parallel to R.D. before and after temper annealing or shape correction + strain relief annealing.
  • Decrease rate (%) 100 X (warp after treatment warp before treatment) / warp before treatment
  • Wood yield fi ⁇ ⁇ * (26) 30 Comparative example As can be seen from Table 3, No. satisfying the conditions of the production method of the present invention; With respect to 17, all compounds having a maximum diameter of 20 m or more were 30 or less, and a mixed tissue could be obtained. On the other hand, in each of No. 18 to No. 32, there was a problem that the number of compounds having a maximum diameter of 3 ⁇ 40 m or more was 30 or more, or the structure was not a mixed structure. It appears prominently.
  • FIG. 3 shows the relationship between hardness and elongation based on the results of the examples.
  • Table 4 and Figure 3 As can be seen, No. 1 to No. 17 which is an example of the present invention has higher strength and higher ductility than any of No. 18 to No. 32 which are comparative examples.
  • the increase rate of the maximum value of the surface roughness after bending is all 60% or less, and the improvement of formability is exhibited by the progress of uniform deformation.
  • Figure 4 shows a photograph of the surface before and after bending and the surface roughness (Ry) at that time.
  • the invention example (No. 4) and the comparative example (No. 28) are shown for a flat plate, a bending radius of 2 mm, and a bending radius of 0.5 mm.
  • These photos and the value of Ry can also see the effect of the present invention.
  • in the case of flat plates when stainless steel plates are subjected to force bending, which has almost the same surface roughness, a large difference appears in the surface roughness.
  • the bending fatigue characteristics of the present invention are also good. As a result, excellent fatigue characteristics can be maintained even after bending. In other words, by optimizing the distribution of the compound in addition to the mixed structure, uniform deformation progresses and defects that occur during bending are reduced. As a result, it is considered that the excellent formability and high fatigue strength were maintained.
  • the processed surface has a tendency that the maximum value of the surface roughness is reduced and defects such as etching pits are reduced, and the processed surface is smoothed compared to before processing. That is, according to the present invention, the workability including the etching property can be improved, and the high V and fatigue strength can be maintained even in the processed parts.
  • the plate warpage and the residual stress also decreased by 70% or more with respect to the residual stress whose increase rate was small. Therefore, the present invention has a significant effect on such characteristics!
  • No. 2, No. 11, and No. 12 have a relatively high temper annealing temperature, so that the recrystallized grain size exceeds 10 ⁇ m.
  • the applied tension exceeds 40% of the 0.2% proof stress, so the ratio of the ⁇ phase of the mixed structure is less than 70%.
  • the grain growth is suppressed by adding Nb, Ti, and V. Can be further improved, and No. 7, For No. 8, it can be improved by reducing the applied tension as in No. 10.
  • No. l to No. 18, No. 20 to No. 22, and No. 26 to No. 32, in which the measures for inclusion miniaturization were implemented, included in the present invention the number of inclusions having a maximum diameter of 20 or more
  • No. 10 using the floating of inclusions and a small-diameter work roll shows the best balance between strength and ductility and workability among the examples of the present invention.
  • the comparative example is inferior in balance between strength and ductility as compared with the inventive example as described above.
  • No. 18 to No. 21 fall within the scope of the present invention in terms of component content and Md value, but No. 18 and No. 19 have a maximum diameter of 20 due to insufficient rolling reduction. More than 30 compounds over m were generated. As a result, good characteristics cannot be obtained due to the absence of a mixed structure.
  • the temper annealing temperature was outside the range of the production method of the present invention, so a mixed structure was not formed, and the workability and fatigue characteristics were both equal to or lower than those of conventional materials. In other comparative examples, the material does not satisfy the required composition, and the performance is not improved.
  • Table 5 shows the characteristic adjustment results of the material obtained by subjecting the No. 2 material to temper rolling at a reduction rate of 10% and 20%.
  • No. 2-a is when the temper rolling is applied to the No. 2 material at a reduction rate of 10%
  • No. 2-b is the same when the reduction rate is 20%. As a result, it is confirmed that the same material retains excellent properties even after temper rolling.

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

L'invention concerne une feuille en acier inoxydable qui possède une excellente résistance et une excellente ductilité et qui présente une aptitude au traitement (aptitude au formage et à l'étirement) ainsi que des caractéristiques de fatigue améliorées, et un procédé de fabrication de la feuille en acier inoxydable. En outre, l'invention assure l'approvisionnement industriel et stable de la feuille en acier inoxydable à un faible coût. Cette feuille en acier inoxydable contient, en poids, C : de 0,01 à 0,08 %, Si : de 0,1 à 2,0 %, Mn : 3,0 % ou moins, Cr : de 10,0 à 20,0 %, Ni : de 3,0 à 12,0 % et N : de 0,02 à 0,24 % lorsque la quantité totale de la feuille en acier inoxydable est prise comme étant 100 % en poids et a une valeur de Md de 0 à 80 telle que définie par la formule : Md = 500-458(C+N) - 9(Si+Mn) - 14Cr - 20Ni et dans laquelle les composés formés à partir des composants ci-dessus et ayant des diamètres maximaux moyens de 20 µm ou plus sont présents en une quantité d'au plus 30 pièces par 5 g en poids de l'acier inoxydable et la structure métallique de la totalité de la feuille en acier inoxydable est une structure mixte composée de grains recristallisés et de parties non recristallisées.
PCT/JP2007/064910 2006-07-28 2007-07-30 Feuille en acier inoxydable pour pièces et procédé de fabrication de celle-ci WO2008013305A1 (fr)

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CN2007800276522A CN101490298B (zh) 2006-07-28 2007-07-30 部件用不锈钢钢板及其制造方法
EP07791595.7A EP2048256B1 (fr) 2006-07-28 2007-07-30 Feuille en acier inoxydable pour pièces et procédé de fabrication de celle-ci

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JP2009219306A (ja) * 2008-03-12 2009-09-24 Jfe Steel Corp 高速モータ用ロータおよびその製造方法
WO2014030607A1 (fr) * 2012-08-20 2014-02-27 新日鐵住金株式会社 Plaque en acier inoxydable, et procédé de fabrication de celle-ci
JP2018149587A (ja) * 2017-03-15 2018-09-27 日立金属株式会社 鋼帯の製造方法
JP2019502816A (ja) * 2015-12-23 2019-01-31 ポスコＰｏｓｃｏ 親水性および接触抵抗が向上した高分子燃料電池の分離板用ステンレス鋼およびその製造方法
JP2020041204A (ja) * 2018-09-13 2020-03-19 日鉄日新製鋼株式会社 ステンレス鋼およびその製造方法
WO2020071534A1 (fr) * 2018-10-04 2020-04-09 日本製鉄株式会社 Tôle d'acier inoxydable austénitique et procédé de production de ladite tôle

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WO2014038510A1 (fr) * 2012-09-04 2014-03-13 新日鐵住金株式会社 Tôle d'acier inoxydable et procédé de production
CN106148849A (zh) * 2015-03-23 2016-11-23 江苏锦明不锈钢新材料有限公司 一种高强度不锈钢
WO2017203311A1 (fr) * 2016-05-24 2017-11-30 Arcelormittal Tôle d'acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
WO2017203315A1 (fr) 2016-05-24 2017-11-30 Arcelormittal Tôle mince en acier laminée à froid et recuite, son procédé de production et utilisation d'un tel acier pour produire des pièces de véhicule
KR102448735B1 (ko) * 2020-09-03 2022-09-30 주식회사 포스코 오스테나이트계 스테인리스강 및 그 제조 방법

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JP2009219306A (ja) * 2008-03-12 2009-09-24 Jfe Steel Corp 高速モータ用ロータおよびその製造方法
WO2014030607A1 (fr) * 2012-08-20 2014-02-27 新日鐵住金株式会社 Plaque en acier inoxydable, et procédé de fabrication de celle-ci
JP5843019B2 (ja) * 2012-08-20 2016-01-13 新日鐵住金株式会社 ステンレス鋼板とその製造方法
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JP2019502816A (ja) * 2015-12-23 2019-01-31 ポスコＰｏｓｃｏ 親水性および接触抵抗が向上した高分子燃料電池の分離板用ステンレス鋼およびその製造方法
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JP2018149587A (ja) * 2017-03-15 2018-09-27 日立金属株式会社 鋼帯の製造方法
JP2020041204A (ja) * 2018-09-13 2020-03-19 日鉄日新製鋼株式会社 ステンレス鋼およびその製造方法
JP7116648B2 (ja) 2018-09-13 2022-08-10 日鉄ステンレス株式会社 ステンレス鋼板およびその製造方法
WO2020071534A1 (fr) * 2018-10-04 2020-04-09 日本製鉄株式会社 Tôle d'acier inoxydable austénitique et procédé de production de ladite tôle
JPWO2020071534A1 (ja) * 2018-10-04 2021-09-02 日本製鉄株式会社 オーステナイト系ステンレス鋼板及びその製造方法
JP7165202B2 (ja) 2018-10-04 2022-11-02 日本製鉄株式会社 オーステナイト系ステンレス鋼板及びその製造方法

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JPWO2008013305A1 (ja) 2009-12-17
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