WO2012133573A1 - 耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法 - Google Patents

耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法 Download PDF

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WO2012133573A1
WO2012133573A1 PCT/JP2012/058218 JP2012058218W WO2012133573A1 WO 2012133573 A1 WO2012133573 A1 WO 2012133573A1 JP 2012058218 W JP2012058218 W JP 2012058218W WO 2012133573 A1 WO2012133573 A1 WO 2012133573A1
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stainless steel
ferritic stainless
temperature
steel sheet
heat resistance
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PCT/JP2012/058218
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English (en)
French (fr)
Japanese (ja)
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濱田　純一
憲博 神野
井上　宜治
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新日鐵住金ステンレス株式会社
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Priority to US14/008,406 priority Critical patent/US20140023550A1/en
Priority to EP12765258.4A priority patent/EP2692889B1/en
Priority to CN2012800158527A priority patent/CN103459639A/zh
Priority to KR1020137022243A priority patent/KR101557463B1/ko
Publication of WO2012133573A1 publication Critical patent/WO2012133573A1/ja

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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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C21D8/0273—Final recrystallisation annealing
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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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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • 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
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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
    • C22C38/18—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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/16—Selection of particular materials
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N13/00—Exhaust or silencing apparatus characterised by constructional features ; Exhaust or silencing apparatus, or parts thereof, having pertinent characteristics not provided for in, or of interest apart from, groups F01N1/00 - F01N5/00, F01N9/00, F01N11/00
    • F01N13/08—Other arrangements or adaptations of exhaust conduits
    • F01N13/10—Other arrangements or adaptations of exhaust conduits of exhaust manifolds
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F01—MACHINES OR ENGINES IN GENERAL; ENGINE PLANTS IN GENERAL; STEAM ENGINES
    • F01N—GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR MACHINES OR ENGINES IN GENERAL; GAS-FLOW SILENCERS OR EXHAUST APPARATUS FOR INTERNAL COMBUSTION ENGINES
    • F01N2530/00—Selection of materials for tubes, chambers or housings
    • F01N2530/02—Corrosion resistive metals
    • F01N2530/04—Steel alloys, e.g. stainless steel

Definitions

  • the present invention relates to a ferritic stainless steel sheet excellent in heat resistance and particularly suitable for use in exhaust system members that particularly require high-temperature strength and oxidation resistance, and a method for producing the same.
  • Exhaust system members such as exhaust manifolds, front pipes, and center pipes for automobiles pass high-temperature exhaust gas exhausted from the engine, so there are various materials such as oxidation resistance, high-temperature strength, and thermal fatigue characteristics. Characteristics are required.
  • cast iron is generally used for automobile exhaust members, but an exhaust manifold made of stainless steel is used from the viewpoints of strengthening exhaust gas regulations, improving engine performance, and reducing the weight of the vehicle body. It became so.
  • the exhaust gas temperature varies depending on the vehicle type and engine structure, but in general gasoline vehicles are often around 700-900 ° C, and materials that have high high-temperature strength and oxidation resistance in an environment that is used for a long time in such a temperature range are desired. ing.
  • austenitic stainless steel has excellent heat resistance and workability, but due to its large thermal expansion coefficient, thermal fatigue failure occurs when applied to a member that repeatedly receives heating and cooling, such as an exhaust manifold. It is easy to produce.
  • ferritic stainless steel has a smaller coefficient of thermal expansion than austenitic stainless steel, and is excellent in thermal fatigue characteristics and scale peel resistance. Further, compared with austenitic stainless steel, it does not contain Ni, so the material cost is low and it is used for general purposes.
  • ferritic stainless steel has lower high-temperature strength than austenitic stainless steel, a technique for improving high-temperature strength has been developed. For example, there are SUS430J1 (Nb-added steel), Nb-Si-added steel, and SUS444 (Nb-Mo-added steel) of Japan Industrial Standard (JIS), all of which are premised on the addition of Nb. This increased the high-temperature strength by solid solution strengthening or precipitation strengthening with Nb.
  • Patent Documents 1 to 4 disclose techniques for adding Cu or Cu-V composites as alloys that contribute to improving high-temperature strength.
  • Cu addition in Patent Document 1 has been studied for addition of 0.5% or less in order to improve low-temperature toughness, and is not an addition from the viewpoint of heat resistance.
  • Patent Documents 2 to 4 disclose techniques for improving high-temperature strength in a temperature range of 600 ° C. or 700 to 800 ° C. by utilizing precipitation strengthening by Cu precipitates.
  • Patent Documents 1 and 2 and Patent Documents 5 to 7 disclose steel containing B as a ferritic stainless steel having excellent high temperature characteristics.
  • Patent Documents 8 to 13 Measures relating to ferritic stainless steel added with W are disclosed in Patent Documents 8 to 13 as countermeasures for increasing the temperature of exhaust gas.
  • W is known as an element for improving the high-temperature strength.
  • the addition of W has a problem in terms of the problem that the workability (elongation) is deteriorated and the part processing becomes difficult and the cost is low.
  • bonds with Fe and precipitates as the Laves phase mentioned later at high temperature when the Laves phase coarsened, there existed a subject which cannot improve heat resistance effectively.
  • Patent Documents 14 and 15 disclose that the high temperature strength of ferritic stainless steel is ensured by defining the sum of Mo and W to be added, and Mo + W. However, the Laves phase is also coarsened.
  • Patent Document 16 describes that the inclusion of P has an adverse effect due to the precipitation of FeTiP, so the P content needs to be kept low.
  • Patent Document 17 stipulates that P in ferritic stainless steel is useful for increasing the strength at high temperatures (solid solution strengthening), and that P is contained up to 0.1% by weight. Including embodiments are not disclosed.
  • JP 2006-37176 A International Publication WO2003 / 004714 Japanese Patent No. 3468156 Japanese Patent No. 3397167 JP-A-9-279312 JP 2000-169943 A Japanese Patent Laid-Open No. 10-204590 JP 2009-215648 A JP 2009-235555 A Japanese Patent Laid-Open No. 2005-206944 JP 2008-189974 A Japanese Unexamined Patent Publication No. 2009-120893 JP 2009-120894 A JP 2009-197306 A JP 2009-197307 A JP 2000-336462 A Japanese Patent No. 30216656
  • the present invention provides a ferritic stainless steel that is used in a thermal environment where the maximum temperature of exhaust gas is 950 ° C. and is excellent in heat resistance and workability.
  • the present invention balances various solid solution elements including P and disperses various precipitates, thereby improving high temperature characteristics and excellent ferritic stainless steel for exhaust manifolds having excellent room temperature workability.
  • An object is to provide a steel sheet. That is, the present invention is a new ferritic stainless steel sheet that balances refinement of precipitates and solid solution strengthening, and a method for manufacturing the same.
  • the present inventors investigated in detail about the expression property of the high temperature strength at 950 ° C., the improvement of the thermal fatigue life, the suppression of abnormal oxidation, and the ductility at normal temperature. As a result, the following knowledge was obtained. That is, the present invention secures the amount of precipitates generated at 950 ° C. and controls the precipitation form when adding a predetermined amount of Cu as a precipitation strengthening element while controlling Mo and W to appropriate amounts. By doing so, precipitation strengthening is effectively expressed. Moreover, this invention ensures heat resistance, suppressing a ductility fall as much as possible by combining with the solid solution strengthening by Nb, Mo, and W.
  • an intermetallic compound called a Laves phase generated by adding Nb, Mo, and W in combination, and ⁇ -Cu generated by adding Cu are utilized as high-temperature precipitation strengthening.
  • the precipitates become coarse, so that the precipitation strengthening ability acts only for a very short time.
  • the thermal fatigue life of the steel material is not improved and the steel material is destroyed in a short time. Therefore, the present inventors use the compound of Fe and P as the precipitation sites, so that the aforementioned Laves phase and ⁇ -Cu are finely and uniformly precipitated in the grains, and as a result, the precipitation strengthening is stable for a long time.
  • the thermal fatigue life is improved. Furthermore, the present inventors have found that the high temperature characteristics are further improved by utilizing the solid solution strengthening by solid solution Nb, Mo, and W. In addition, the present inventors have found that both the thermal fatigue life and the room temperature ductility can be achieved by defining the addition amounts of Mo + W and Cu within a predetermined range. As a result, it is possible to provide a highly reliable ferritic stainless steel sheet having high heat resistance and freedom of parts processing in a temperature range where the maximum temperature of exhaust gas is 950 ° C. In addition, Mo + W is mass% and is the sum of Mo addition amount and W addition amount.
  • the gist of the present invention is as follows. (1) In mass%, C: 0.02% or less, N: 0.02% or less, Si: more than 0.1 to 1.0%, Mn: 0.5% or less, P: 0.02 to 0.10%, Cr: 13.0 to 20.0%, Nb: 0.5 to 1.0%, Cu: 1.0 to 3.0%, Mo: 1.5 to 3.5%, W : 2.0% or less, B: 0.0001 to 0.0010%, and Al: 0.01 to 1.0%, the balance is made of Fe and inevitable impurities, and Mo + W is 2.0 to 3 A ferritic stainless steel sheet excellent in heat resistance and workability, characterized by being 5%.
  • the C content is set to 0.02% or less.
  • excessive reduction leads to an increase in refining costs, so 0.001 to 0.009% is desirable.
  • N like C, deteriorates moldability and corrosion resistance and causes a decrease in high-temperature strength, so the smaller the content, the better. Therefore, the N content is set to 0.02% or less. However, excessive reduction leads to an increase in refining costs, so 0.003 to 0.015% is desirable.
  • Si is an element useful as a deoxidizer and an element that improves high-temperature strength and oxidation resistance.
  • High-temperature strength and oxidation resistance increase with increasing Si content, and the effect is manifested at over 0.1%.
  • Mo and W when combined with Mo and W, the effect is remarkable.
  • excessive addition reduces the room temperature ductility, so the upper limit is made 1.0%. In consideration of manufacturability, 0.2 to 0.5% is desirable.
  • Mn is an element added as a deoxidizer and contributes to an increase in high-temperature strength in a temperature range of about 600 to 800 ° C. (medium temperature range).
  • addition of more than 0.5% tends to cause scale adhesion and abnormal oxidation due to formation on the Mn-based oxide surface layer at high temperatures.
  • the upper limit was made 0.5% or less. Further, considering the pickling property and the room temperature ductility in the production of the steel sheet, 0.05 to 0.2% is desirable.
  • P is an important element for controlling the precipitation of the Laves phase and ⁇ -Cu. Usually, it is desirable to reduce P as much as possible from the viewpoint of workability.
  • the Laves phase and ⁇ -Cu are finely dispersed and precipitated at 950 ° C. using this compound as a nucleus, and these can be maintained for a long time at a high temperature. Prevents coarsening of precipitates. If the Laves phase or ⁇ -Cu precipitates alone in the ferrite grains and grain boundaries of the parent phase, it coarsens early and the precipitation strengthening ability decreases, and the origin of cracks and crack propagation are accelerated during the thermal fatigue process. End up.
  • Cr is an essential element for securing oxidation resistance and corrosion resistance in the present invention. If it is less than 13%, oxidation resistance cannot be particularly secured. If it exceeds 20%, workability and toughness are deteriorated. Further, considering the manufacturability and high temperature ductility, 16 to 18% is desirable.
  • Nb is an element necessary for improving high-temperature strength by strengthening solid solution and strengthening precipitates.
  • C and N are fixed as carbonitrides, and there is also a role that contributes to the development of the recrystallization texture that affects the corrosion resistance and r value of the product plate.
  • the strength at 950 ° C. is mainly solid solution strengthening, but when added in combination with Mo and W, it contributes to the fine precipitation of the Laves phase and promotes the formation of Fe and P compounds that become the precipitation sites of the Laves phase. Also have.
  • Cu contributes to precipitation strengthening due to ⁇ -Cu precipitation, but in order to secure a precipitation amount contributing to high temperature strength at 950 ° C., addition of 1.0% or more is necessary, so the lower limit is 1.0%. It was. Furthermore, as described above, the ⁇ -Cu precipitates interact with the Fe—P-based precipitates and finely disperse with each other. This is a significant difference from Patent Document 16. On the other hand, Cu is an element that significantly lowers the room temperature ductility. If more than 3.0% is added, the total elongation of the steel sheet does not reach 30% required for normal press forming, so the upper limit was made 3.0%. . Furthermore, considering the manufacturability and oxidation resistance, 1.2 to 2.0% is desirable.
  • Mo is an element effective as a solid solution strengthening at 950 ° C., and also generates a Laves phase (Fe 2 Mo) to bring about an effect of precipitation strengthening. These effects are manifested at 1.5% or more. However, excessive addition increases the alloy cost, and addition of more than 3.5% significantly deteriorates room temperature ductility and oxidation resistance. 0.5%. Furthermore, considering the manufacturability, 1.5 to 2.7% is desirable.
  • W like Mo
  • the Laves phase of Fe 2 (Nb, Mo, W) is precipitated.
  • W is added, the coarsening of the Laves phase is suppressed and the precipitation strengthening ability is improved.
  • the cause of this is thought to be due to the interaction between W and the FeP compound that forms the precipitation site of Fe 2 (Nb, Mo, W).
  • these Laves phases tend to become fine due to the coexistence with the Fe—P-based precipitates.
  • the Cu precipitates, the Laves phase, and the three types of Fe—P-based precipitates affect each other, finely disperse and precipitate, prevent coarsening, and contribute to the improvement of high temperature fatigue properties. That is, adding Mo, W, and P in combination is a significant difference from Patent Document 16.
  • FIG. 2 shows the effect of addition of Mo and W on the total elongation of the same component system at room temperature.
  • the elongation at break needs to be 30% or more. Accordingly, the case where the elongation at break of 30% or more is obtained is shown as ⁇ , and the case where it is less than 30% is shown as x.
  • FIG. 3 shows the effect of addition of Mo and W on the oxidation resistance of the same component system at 950 ° C. The case where no abnormal oxidation and scale peeling occurred is shown as ⁇ , and the case where it occurred is shown as x.
  • the range of Mo + W should be 2.0 to 3.5%, and Mo should be 1.5% or more. Is effective. Moreover, excessive addition of W increases the cost and lowers the room temperature ductility, so the upper limit of W was set to 2.0%. Further, in consideration of manufacturability, low temperature toughness, and oxidation resistance, it is desirable that the W addition amount is 1.5% or less and the Mo + W amount is 2.1 to 2.9%.
  • B is an element that improves the secondary workability during product press working.
  • addition of B suppresses the coarsening of Cu precipitates, the Laves phase, and the FeP compound, and increases the strength stability during use in a high-temperature environment. This is because B is segregated at the grain boundaries during the recrystallization process in the cold-rolled sheet annealing step, and the precipitates that precipitate when exposed to a subsequent high temperature environment are less likely to precipitate at the grain boundaries. This is thought to promote fine precipitation inside. Thereby, long-term stability of precipitation strengthening is expressed, strength reduction is suppressed, and thermal fatigue life is improved.
  • Al is an element that improves oxidation resistance in addition to being added as a deoxidizing element. Further, it is useful as a solid solution strengthening element for improving the strength at 600 to 700 ° C. Although its action is stably manifested from 0.01%, excessive addition hardens it to significantly reduce uniform elongation and toughness to remarkably decrease, so the upper limit was made 1.0%. Furthermore, if considering the occurrence of surface defects, weldability, and manufacturability, 0.01 to 0.2% is desirable.
  • Ti is an element that combines with C, N, and S to improve corrosion resistance, intergranular corrosion resistance, room temperature ductility, and deep drawability, and is added as necessary. These effects are manifested from 0.05% or more, but addition of more than 0.4% increases the amount of dissolved Ti and lowers the room temperature ductility, forms coarse Ti-based precipitates, It becomes the starting point of cracks during expansion processing, and press workability deteriorates. Moreover, since oxidation resistance also deteriorates, Ti addition amount was made 0.4% or less. Furthermore, considering the occurrence of surface flaws and toughness, 0.05 to 0.2% is desirable.
  • V is an element that improves the corrosion resistance, and is added as necessary. This effect is stably manifested with addition of 0.05% or more, but if added over 1%, the precipitates become coarse and the high-temperature strength decreases, and the oxidation resistance deteriorates, so the upper limit was made 1%. . Further, considering the manufacturing cost and manufacturability, 0.08 to 0.5% is desirable.
  • Zr is a carbonitride-forming element like Ti and Nb, and is an element that improves the corrosion resistance and deep drawability. Therefore, it is added as necessary. These effects are manifested at 0.05% or more. However, since the manufacturability is remarkably deteriorated by addition of more than 1.0%, it was set to 0.05 to 1.0%. Furthermore, if considering the cost and surface quality, 0.1 to 0.6% is desirable.
  • Sn is an element that improves the corrosion resistance, and is added as necessary to improve the high temperature strength in the middle temperature range. These effects are manifested at 0.05% or more, but if added over 0.5%, manufacturability is remarkably reduced, so 0.05 to 0.5% was set. Furthermore, if considering oxidation resistance and manufacturing cost, 0.1 to 0.5% is desirable.
  • Ni is an element that improves acid resistance and toughness, and is added as necessary. These effects are manifested at 0.05% or more, but adding more than 1.0% increases the cost, so 0.05 to 1.0% was set. Furthermore, if manufacturability is taken into consideration, 0.1 to 0.5% is desirable.
  • the method for producing a steel sheet of the present invention includes steelmaking, hot rolling, pickling, cold rolling, annealing and pickling processes.
  • steelmaking a method in which a steel containing the essential components and optional components added as necessary is subjected to melting in a converter, followed by secondary refining is preferable.
  • the molten steel is made into a slab according to a known casting method (continuous casting).
  • the slab is heated to a predetermined temperature by a conventional method, and hot-rolled to a predetermined plate thickness by continuous rolling. Hot rolling is rolled up after being rolled by a hot rolling mill comprising a plurality of stands.
  • coil water cooling is performed after winding in order to improve hot rolled sheet toughness. Since various alloys are added to the steel of the present invention, the hot-rolled sheet toughness tends to decrease, and troubles such as the steel sheet breaking in the next process may occur.
  • the causes include crystal grain coarsening, Cu cluster formation, and Cr two-phase separation. Therefore, in order to surely solve these causes, the coil is immersed in the pool as it is and cooled with water. However, if the time from winding to water cooling exceeds 1 hour, there is no effect of improving toughness, so the time from winding to water cooling is set to within 1 hour. This time is preferably within 20 minutes.
  • the coiling temperature is not particularly defined, but is preferably 400 to 750 ° C. from the viewpoint of structure refinement.
  • hot-rolled sheet annealing is heated to the recrystallization temperature from the viewpoint of homogenization and softening of the structure.
  • the recrystallized structure has coarse crystal grains, the toughness of the hot-rolled annealed plate may be a problem. Therefore, in the present invention, preferably, hot-rolled sheet annealing is omitted, or heat treatment is performed at a temperature at which non-recrystallization occurs, and toughness is ensured by refining the structure.
  • the recrystallization temperature of the steel of the present invention is 1000 ° C. or higher. However, when a recrystallized structure is obtained, the crystal grains become coarse, the toughness is lowered, and the steel sheet may be broken during coil passage.
  • hot-rolled sheet annealing When hot-rolled sheet annealing is omitted, it is subjected to cold rolling with the structure non-uniformity. Even in such a case, a sized structure is obtained after cold-rolled sheet annealing. Further, even if the cold-rolled material is hard, cold-rolling is possible, and finely processed grains can be obtained at the hot-rolling stage, so there is no problem with toughness. Further, in the present invention, because of the formation of subgrains, it is possible to remove processing strain and obtain a subgrain structure, and to prevent toughness deterioration due to the generation of deformation twins.
  • the hot-rolled sheet annealing temperature is preferably 700 to 950 ° C. Further, it is desirable to perform heat treatment at 750 to 900 ° C. from the viewpoint of pickling properties.
  • the holding time and the cooling rate are not particularly defined, but from the viewpoint of productivity, the holding time is preferably within 20 seconds and the cooling rate is preferably 10 ° C./sec or more.
  • the recrystallization temperature of the steel having the composition of the present invention is 1000 to 1100 ° C., it is cooled after being heated to this temperature range.
  • Cu, Nb, Mo, and W produce ⁇ -Cu and Laves phases in the cooling process, but if the cooling rate is slow, ⁇ -Cu and Laves phases are excessively precipitated, resulting in a decrease in high temperature strength and cold ductility. Therefore, it is preferable to maintain a solid solution state as much as possible. Therefore, it is preferable that the cooling rate to 400 ° C. at which salt treatment or neutral salt electrolysis treatment is performed is 10 ° C./sec or more. Considering productivity and pickling properties, the cooling rate is preferably 20 to 100 ° C./sec. Moreover, what is necessary is just to select a cooling method suitably, such as air-water cooling and water cooling.
  • the hot-rolled sheet thickness, cold-rolled sheet annealing atmosphere, etc. may be selected as appropriate. Further, after cold rolling and annealing, at least one of temper rolling and tension leveler may be applied. Further, the product plate thickness may be selected according to the required member thickness.
  • the slab heating temperature was 1250 ° C.
  • the finishing temperature was 850 to 950 ° C.
  • the winding temperature was 450 to 750 ° C.
  • the coil was water-cooled, and hot-rolled sheet annealing was omitted or heat treatment was performed at 700 to 900 ° C. Thereafter, the coil was pickled, cold-rolled to a thickness of 2 mm, annealed and pickled to obtain a product plate.
  • the annealing temperature of the cold-rolled sheet was set to 1000 to 1100 ° C.
  • the crystal grain size number is an austenite crystal grain size defined by JIS G 0551.
  • the steel having the component composition defined in the present invention is produced by the above-described ordinary method, it is excellent in thermal fatigue characteristics, room temperature elongation, and oxidation resistance characteristics as compared with the comparative example.
  • 11 and 12 are inferior in thermal fatigue, elongation, and oxidation resistance because C and N are outside the upper limit.
  • No. No. 13 is inferior in thermal fatigue, elongation, and oxidation resistance because Si is outside the lower limit.
  • No. No. 14 is inferior in thermal fatigue, elongation, and oxidation resistance because Mn is outside the upper limit.
  • No. No. 15 is inferior in thermal fatigue characteristics because P is outside the lower limit.
  • No. No. 16 is inferior in thermal fatigue characteristics and room temperature workability because P is outside the upper limit.
  • No. 17 since Cr is off the lower limit, the oxidation resistance is inferior, and thermal fatigue failure occurs at an early stage starting from the abnormal oxidation portion. No. In No. In No.
  • No. No. 25 is inferior in all characteristics because B is outside the upper limit.
  • No. Nos. 26 and 27 are inferior in workability because Al and Ti are outside the upper limit.
  • No. 28 and 30 are inferior in workability and oxidation resistance because V and Sn are outside the upper limit.
  • No. 29 and 31 are inferior in workability because Zr and Ni are outside the upper limit.
  • the present invention it is possible to provide a ferritic stainless steel sheet excellent in heat resistance and workability suitable for an exhaust gas path component exposed to an atmosphere of 950 ° C. Therefore, the present invention is useful for environmental measures and cost reduction of exhaust gas path components, and is industrially useful.
PCT/JP2012/058218 2011-03-29 2012-03-28 耐熱性と加工性に優れたフェライト系ステンレス鋼板及びその製造方法 WO2012133573A1 (ja)

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US14/008,406 US20140023550A1 (en) 2011-03-29 2012-03-28 Ferritic stainless steel sheet excellent in heat resistance and workability and method of production of same
EP12765258.4A EP2692889B1 (en) 2011-03-29 2012-03-28 Ferritic stainless steel sheet having excellent heat resistance and processability, and method for producing same
CN2012800158527A CN103459639A (zh) 2011-03-29 2012-03-28 耐热性和加工性优良的铁素体系不锈钢板及其制造方法
KR1020137022243A KR101557463B1 (ko) 2011-03-29 2012-03-28 내열성과 가공성이 우수한 페라이트계 스테인리스 강판 및 그 제조 방법

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US10358689B2 (en) 2013-02-04 2019-07-23 Nippon Steel & Sumikin Stainless Steel Corporation Method of producing ferritic stainless steel sheet
CN104968818A (zh) * 2013-03-06 2015-10-07 新日铁住金不锈钢株式会社 耐热性优良的铁素体系不锈钢板
CN104968818B (zh) * 2013-03-06 2017-09-08 新日铁住金不锈钢株式会社 耐热性优良的铁素体系不锈钢板
US10450623B2 (en) 2013-03-06 2019-10-22 Nippon Steel & Sumikin Stainless Steel Corporation Ferritic stainless steel sheet having excellent heat resistance
US10385429B2 (en) 2013-03-27 2019-08-20 Nippon Steel & Sumikin Stainless Steel Corporation Hot-rolled ferritic stainless-steel plate, process for producing same, and steel strip

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EP2692889A1 (en) 2014-02-05
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KR20130107371A (ko) 2013-10-01
US20140023550A1 (en) 2014-01-23
KR101557463B1 (ko) 2015-10-06
EP2692889B1 (en) 2017-06-21
JP2012207252A (ja) 2012-10-25
EP2692889A4 (en) 2014-11-26

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