WO2018180643A1 - Acier inoxydable ferritique ayant une résistance à l'usure supérieure à haute température, procédé de production de tôle d'acier inoxydable ferritique, de composants d'échappement, de composants coulissants à haute température, et de composants de turbocompresseur - Google Patents

Acier inoxydable ferritique ayant une résistance à l'usure supérieure à haute température, procédé de production de tôle d'acier inoxydable ferritique, de composants d'échappement, de composants coulissants à haute température, et de composants de turbocompresseur Download PDF

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WO2018180643A1
WO2018180643A1 PCT/JP2018/010619 JP2018010619W WO2018180643A1 WO 2018180643 A1 WO2018180643 A1 WO 2018180643A1 JP 2018010619 W JP2018010619 W JP 2018010619W WO 2018180643 A1 WO2018180643 A1 WO 2018180643A1
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Prior art keywords
stainless steel
ferritic stainless
temperature
high temperature
wear resistance
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PCT/JP2018/010619
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English (en)
Japanese (ja)
Inventor
濱田　純一
睦子 吉井
俊希 吉澤
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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Priority to MX2019011210A priority Critical patent/MX2019011210A/es
Priority to JP2019509311A priority patent/JP6768929B2/ja
Priority to CN201880019902.6A priority patent/CN110462081B/zh
Publication of WO2018180643A1 publication Critical patent/WO2018180643A1/fr
Anticipated expiration legal-status Critical
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    • 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
    • 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
    • C22C38/32—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention relates to a ferritic stainless steel excellent in high-temperature wear resistance, a method for producing a ferritic stainless steel sheet, an exhaust part, a high-temperature sliding part, and a turbocharger, which are materials for heat-resistant parts that require heat resistance and workability. It relates to parts.
  • the present invention is particularly applicable to automobile exhaust manifolds, converters, and turbocharger parts.
  • the present invention relates to materials suitable for internal precision parts such as nozzle mounts, nozzle plates, vanes, and back plates of turbochargers mounted on gasoline vehicles and diesel vehicles, and outer cylinders such as turbine housings.
  • Environment-friendly parts for automobile exhaust manifold, front pipe, center pipe, muffler and exhaust gas purification have high heat resistance such as oxidation resistance, high temperature strength, thermal fatigue characteristics, etc. in order to allow high temperature exhaust gas to flow stably. Excellent material is used. Moreover, since it is also a condensed water corrosive environment, it is also required to have excellent corrosion resistance. Stainless steel is often used for these parts from the viewpoints of stricter exhaust gas regulations, improved engine performance, and lighter body weight. Further, in recent years, exhaust gas regulations have been further strengthened, and the exhaust gas temperature flowing through the exhaust manifold directly under the engine has been on the rise due to improvements in fuel efficiency and downsizing.
  • turbochargers and other turbochargers are often installed, and stainless steel used in exhaust manifolds and turbochargers is required to have further improved heat resistance.
  • the rise in the exhaust gas temperature it is expected that the exhaust gas temperature, which was conventionally about 900 ° C., will rise to about 1000 ° C.
  • Patent Documents 1 and 2 disclose high Cr and Mo-added steels.
  • Patent Document 3 discloses an exhaust guide part of a nozzle vane type turbocharger using austenitic stainless steel to which 2 to 4% of Si is added.
  • Patent Document 3 discloses an austenitic stainless steel component in consideration of hot workability. However, since both of them contain expensive Ni and increase in cost, the development of ferritic stainless steel not containing Ni has been expected.
  • the parts to which stainless steel is mainly applied are precision parts and housings inside the nozzle vane turbocharger.
  • parts called back plates and oil deflectors are located between the turbine part and compressor part and the center core, and are parts that stably rotate the turbine and compressor wheel while maintaining the sealing performance of each part. Therefore, surface smoothness is important in addition to oxidation resistance and high temperature strength.
  • a nozzle component composed of precision components such as a nozzle mount, a nozzle plate, a nozzle vane, a drive ring, and a drive lever.
  • high-temperature strength, creep characteristics, and oxidation resistance are important, and high-temperature wear resistance is important because the exhaust gas flow rate and flow rate are adjusted by opening and closing the vanes.
  • high-temperature strength, creep, and thermal fatigue characteristics are regarded as important for turbine housings, but because they are in contact with the housing, back plate, clamps, and subsequent exhaust components in a high-temperature environment, wear resistance at high temperatures is required.
  • Ferritic stainless steel is mainly used for exhaust manifolds, and Patent Documents 4 to 16 disclose technologies related to ferritic stainless steel to which Nb, Si, Cu, W, etc. are added as countermeasures for increasing the exhaust gas temperature. Has been.
  • JP 2002-332862 A International Publication No. 2014/157655 Japanese Patent No. 4937277 JP 2006-37176 A International Publication No. 2003/004714 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 JP 2005-206944 A JP 2008-189974 A JP 2009-120893 A JP 2009-120894 A
  • An object of the present invention is to solve the problems of the known art and to provide a ferritic stainless steel excellent in high temperature wear resistance suitable for use as a turbocharger component in a high temperature sliding component, particularly an automobile exhaust component, and a method for producing the same. Is to provide.
  • the present inventors have intensively studied and found that not only the steel components but also precipitates and hardness in the vicinity of the surface layer are particularly important for high temperature wear resistance. When subjected to friction at high temperatures, it undergoes strong processing locally in the vicinity of the surface layer, so that the structural change and hardness change of the part are important. Regarding the change in structure, precipitation of various precipitates occurs, so that high-temperature strengthening is a point.
  • the present inventors have examined in detail the precipitation behavior and wear resistance during high-temperature sliding, and in particular, have examined whether or not ferritic stainless steel can be applied to turbocharger parts.
  • the present inventors conducted detailed studies on the high-temperature wear resistance of ferritic stainless steel sheets from the viewpoints of steel composition, metal structure, and high-temperature characteristics.
  • components that are exposed to extremely harsh thermal environments, such as turbochargers ensure heat resistance with steel components and control the metal structure near the surface layer.
  • a ferritic stainless steel sheet having excellent high-temperature wear resistance and a component composed thereof can be obtained.
  • the surface layer has good oxidation characteristics and is hard, but in the present invention, the hardness when exposed to fine precipitates on the surface layer for a long time at high temperatures. It was found that the amount of wear can be significantly reduced. As a result, it is possible to provide a component with improved high-temperature wear resistance using a ferritic stainless steel plate without using an expensive austenitic stainless steel plate.
  • the gist of the present invention for solving the above problems is as follows. (1) By mass%, C: 0.003-0.02%, Si: 0.05-1.0%, Mn: 0.05-1.0%, P: 0.01-0.05% , S: 0.0001 to 0.01%, Cr: 15 to 18%, N: 0.002 to 0.02%, Al: 0.01 to 0.20%, Cu: 1 to 3%, Mo: 1.7 to 3%, Nb: 0.4 to 0.7%, B: 0.0002 to 0.0030%, the balance is made of Fe and inevitable impurities, and Nb is contained at a depth of 20 ⁇ m from the surface layer A ferritic stainless steel excellent in high temperature wear resistance characterized by the presence of 0.06 precipitates / ⁇ m 2 or more.
  • the manufacturing method of the ferritic stainless steel plate excellent in high temperature abrasion resistance characterized by making it less than 10 degrees C / sec. (6)
  • An exhaust part comprising the ferritic stainless steel according to any one of (1) to (4).
  • a high-temperature sliding component comprising the ferritic stainless steel according to any one of (1) to (4).
  • a turbocharger part comprising the ferritic stainless steel according to any one of (1) to (4).
  • the present invention it is possible to provide a ferritic stainless steel having high-temperature wear resistance that is suitable for turbocharger parts. At the same time, it contributes to cost reduction and reduction of parts manufacturing load.
  • FIG. 1 The figure which shows the relationship between the hardness after aging heat processing, and the wear depth in a high temperature abrasion test of this invention steel and a comparison steel.
  • FIG. 1 The figure which shows the relationship between the hardness after aging heat processing, and the wear depth in a high temperature abrasion test of this invention steel and a comparison steel.
  • C is an austenite-forming element.
  • an austenite phase is generated during high temperature use, abnormal oxidation occurs and the high temperature wear resistance is remarkably reduced. Further, when carbide is generated in the ferrite phase, the high temperature strength is lowered, so 0.02% is made the upper limit. On the other hand, excessive reduction leads to cost increase, so 0.003% is made the lower limit.
  • the lower limit is preferably 0.005%.
  • the upper limit is preferably 0.010%.
  • Si may be added as a deoxidizing element, and 0.05% or more is added in order to improve scale peelability and high-temperature wear resistance by internal oxidation of Si.
  • the upper limit is made 1.0%.
  • the upper limit of the Si content is preferably 0.5%.
  • the lower limit is preferably 0.1%.
  • the upper limit is preferably 0.2%.
  • Mn is used as a deoxidizing element and is added in an amount of 0.05% or more in order to improve scale peelability.
  • it is an austenite-forming element.
  • the upper limit is made 1.0%.
  • the lower limit of the Mn content is 0.2%, and the upper limit of Mn is preferably 0.3% from the viewpoint of softening.
  • P is an element that promotes hot workability and solidification cracking at the time of manufacture, and its content is preferably as low as possible because it hardens.
  • the upper limit is 0.05% and the lower limit is 0. .01%.
  • the lower limit of the P content is preferably 0.02%.
  • the upper limit is preferably 0.04%.
  • S is an element that degrades hot workability during production and deteriorates corrosion resistance. Further, when coarse sulfide (MnS) is formed, the cleanliness is remarkably deteriorated and the hole expandability is deteriorated, so the upper limit is made 0.01%. On the other hand, excessive reduction leads to an increase in refining costs, so the lower limit is made 0.0001%. Furthermore, considering the manufacturing cost and oxidation resistance, the lower limit of the S content is preferably 0.0005%. The upper limit is preferably 0.0050%.
  • Cr is an element that improves corrosion resistance and oxidation resistance and improves high-temperature wear resistance.
  • 15% or more is necessary from the viewpoint of suppressing abnormal oxidation.
  • the upper limit was made 18%.
  • the lower limit of the Cr content is desirably 16%.
  • the upper limit is desirably 17.5%.
  • N is an austenite-forming element like C, and when an austenite phase is generated during high-temperature use, abnormal oxidation occurs and the high-temperature wear resistance is significantly reduced.
  • the upper limit when a large amount of nitride is generated in the ferrite phase, the high temperature strength decreases, so 0.02% is made the upper limit.
  • the lower limit is preferably 0.003%.
  • the upper limit is desirably 0.010%.
  • Al is added as a deoxidizing element to improve inclusion cleanliness, and to improve high temperature wear resistance by forming an internal oxide at a high temperature, it is added in an amount of 0.01% or more.
  • addition of more than 0.20% makes it harder and also lowers the pickling property, so the upper limit is made 0.20%.
  • the lower limit of the Al content is preferably 0.02%.
  • the upper limit is desirably 0.10%.
  • Cu is added at 1% or more because precipitation strengthening acts in a high temperature environment and improves high temperature strength, thermal fatigue characteristics, high temperature high cycle fatigue characteristics and high temperature wear resistance. On the other hand, addition of more than 3% generates an austenite phase, and the oxidation resistance and high-temperature wear resistance are remarkably deteriorated. Furthermore, considering the creep characteristics, the lower limit is desirably 1.1% and more desirably 1.2%. Furthermore, considering the manufacturability, the upper limit is desirably 2.0%.
  • Mo contributes to the improvement of high temperature strength by solid solution strengthening and reacts with Nb and Fe to promote the precipitation of the Laves phase.
  • this Laves phase is dissolved in the product plate stage, it precipitates when the part is used in a high temperature environment, and contributes to improvement of high temperature strength and high temperature wear resistance. Since these effects are manifested at 1.7% or more, the lower limit is set to 1.7%.
  • the upper limit is made 3%.
  • the upper limit is desirably 2.8%.
  • the lower limit of the Mo content is preferably 2.3%.
  • Nb is an element that combines with C and N to improve corrosion resistance and intergranular corrosion resistance, as well as high temperature strength.
  • the mechanism for improving the high-temperature strength includes a solid phase strengthening Laves phase precipitation strengthening.
  • the present inventor has found that although it is precipitated as a carbonitride or a small amount of a Laves phase at the stage of the product plate, these Nb-containing precipitates are extremely effective for enhancing the high-temperature wear resistance. This is because the Nb-containing precipitate is hard and contributes to a reduction in the wear amount of the base material by increasing the hardness in the vicinity of the sliding surface.
  • Oxidation scale greatly affects high-temperature wear resistance, but if other elements specified in the present invention (for example, oxide-forming elements such as Cr, Si, Mn, etc.) are properly added, abnormal oxidation or excessive oxidation Increase in quantity does not occur. Therefore, the wear rate of the base material is rate-determined, and the high-temperature wear resistance is better when the hard Nb-containing precipitates are dispersed. Since these effects are manifested by addition of 0.4% or more, the lower limit was made 0.4%. On the other hand, since the workability is remarkably deteriorated by adding over 0.7%, the upper limit is made 0.7%. Furthermore, considering the high temperature strength, intergranular corrosion of the weld and the alloy cost, it is desirable that the lower limit of the Nb content is 0.5% and the upper limit is 0.6%.
  • oxide-forming elements such as Cr, Si, Mn, etc.
  • B is an element that generally segregates at grain boundaries and improves secondary workability.
  • the grain boundary segregation of B improves the high temperature wear resistance, so 0.0002% or more is added. This is presumably because B segregates at the grain boundary in the vicinity of the surface layer to increase the grain boundary strength and improve the wearability at high temperatures.
  • the grain boundary strength is weak, the grain boundary is likely to wear during friction and wear, but it is considered that the grain boundary strengthening by addition of B suppresses this.
  • the addition of B also has the effect of finely dispersing and precipitating Nb-containing precipitates within the crystal grains, and is effective in improving wear.
  • Nb-containing precipitates are prevented from precipitating at the grain boundaries due to B grain boundary segregation, and fine precipitates are precipitated within the grains, thereby improving the high-temperature wear resistance.
  • 0.0002% or more is added in the present invention.
  • addition of over 0.0030% causes deterioration of intergranular corrosion, toughness, and fatigue properties due to boride precipitation, so the upper limit is made 0.0030%.
  • the lower limit of the B content is preferably 0.0002% and the upper limit is preferably 0.0020%.
  • the ferritic stainless steel sheet of the present invention may further contain one or two of Ti, W, V, Zr, Sn, Ni, Co, Mg, Sb, REM, Ga, Ta, and Ca.
  • 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.
  • this invention when improving normal temperature workability by precipitation of FeTiP, since the effect expresses from 0.005% or more, the minimum was made into 0.005%.
  • the amount of dissolved Ti and lowers room temperature ductility increases the amount of dissolved Ti and lowers room temperature ductility, forms coarse Ti-based precipitates, degrades high-temperature wear resistance, and at the time of hole expansion processing It becomes the starting point of cracking and deteriorates press workability.
  • the Laves phase is excessively precipitated, so that the solid solution Nb and the solid solution Mo are insufficient, and the high temperature strength is lowered.
  • the amount of Ti added is set to 0.3% or less.
  • the lower limit is preferably 0.05%.
  • the upper limit is preferably 0.2%.
  • 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.
  • these Laves phases tend to become fine due to the coexistence with Fe-P-based precipitates. Since this works with addition of 0.1% or more, the lower limit is made 0.1%.
  • the addition of more than 3.0% increases the cost and forms a coarse Laves phase to deteriorate the high temperature wear resistance. Moreover, since normal temperature ductility falls, an upper limit was made into 3.0%. Furthermore, when manufacturability, low temperature toughness and oxidation resistance are taken into consideration, the lower limit of the W addition amount is desirably 0.2%, and the upper limit is desirably 1.5%.
  • V is an element that improves the corrosion resistance, and is added as necessary. Moreover, VC is formed and high temperature abrasion resistance is improved. 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%. . Furthermore, considering the manufacturing cost and manufacturability, the lower limit is preferably 0.08%. The upper limit is preferably 0.5%.
  • Zr is a carbonitride-forming element like Ti and Nb, is an element that improves corrosion resistance and deep drawability, and is added as necessary. Although these effects are manifested at 0.05% or more, the productivity was markedly deteriorated by adding over 0.3%. Furthermore, considering the cost and surface quality, the lower limit is preferably 0.05%. The upper limit is preferably 0.2%.
  • 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 0.01% or more, but if added over 0.5%, manufacturability is remarkably reduced, so 0.01 to 0.5% was set. Furthermore, considering the oxidation resistance and manufacturing cost, the lower limit is preferably 0.03%. The upper limit is preferably 0.3%.
  • Ni is an element that improves acid resistance and toughness, and is added as necessary. These effects are manifested at 0.1% or more, but if added over 0.5%, the cost increases, and when accompanied by the formation of austenite, the high temperature wear resistance deteriorates. %. Further, considering the manufacturability, the lower limit is preferably 0.15%. The upper limit is preferably 0.3%.
  • Co contributes to improving high-temperature strength, so 0.03% or more is added as necessary. Addition of over 0.3% leads to toughness deterioration, so the upper limit is made 0.3%. Furthermore, considering refining costs and manufacturability, the upper limit is preferably 0.1%.
  • Mg is an element that may be added as a deoxidizing element and that contributes to improving the formability by refining the slab structure. Further, the Mg oxide becomes a precipitation site for carbonitrides such as Ti (C, N) and Nb (C, N), and has an effect of finely dispersing and depositing them. This effect appears at 0.0002% or more, and contributes to toughness improvement, so the lower limit was made 0.0002%. However, excessive addition leads to deterioration of weldability and corrosion resistance, so the upper limit was made 0.01%. In consideration of refining costs, the lower limit is preferably 0.0003%. The upper limit is preferably 0.0010%.
  • Sb contributes to improvement of corrosion resistance and high-temperature strength, so 0.005% or more is added as necessary. Since addition of more than 0.5% may excessively cause slab cracking or ductility reduction during steel sheet production, the upper limit is made 0.5%. Furthermore, considering refining costs and manufacturability, the lower limit is preferably 0.005%. The upper limit is preferably 0.15%.
  • REM may be added as necessary from the viewpoint of improving toughness and oxidation resistance by refining various precipitates, and this effect is manifested at 0.001% or more, so the lower limit is 0. 0.001%. However, addition of more than 0.2% significantly deteriorates castability and lowers ductility, so the upper limit was made 0.2%. Furthermore, considering refining costs and manufacturability, 0.001 to 0.05% is desirable.
  • REM rare earth element refers to a generic name of two elements of scandium (Sc) and yttrium (Y) and 15 elements (lanthanoid) from lanthanum (La) to lutetium (Lu) according to a general definition. It may be added alone or as a mixture.
  • Ga may be added at 0.3% or less for improving corrosion resistance and suppressing hydrogen embrittlement.
  • the lower limit is made 0.0002% from the viewpoint of sulfide and hydride formation.
  • 0.0020% or less is desirable from the viewpoints of manufacturability and cost and from the viewpoints of ductility and toughness.
  • Ta is combined with C and N to contribute to the improvement of toughness, so 0.001% or more is added as necessary.
  • the addition of more than 1.0% increases the cost and remarkably deteriorates manufacturability, so the upper limit is made 1.0%.
  • the lower limit is preferably 0.005%.
  • the upper limit is preferably 0.08%.
  • the lower limit was made 0.0002%.
  • the upper limit was made 0.01%.
  • the lower limit is preferably 0.0003%.
  • the upper limit is preferably 0.0020%.
  • the balance is Fe and inevitable impurities and is not particularly specified in the present invention.
  • Bi or the like is added in an amount of 0.001% or more and 0.1% or less as required. May be. Note that it is desirable to reduce general harmful elements and impurity elements such as As and Pb as much as possible.
  • the cross-sectional hardness at room temperature at a depth of 20 ⁇ m from the surface layer after aging at 850 ° C. for 1 hour is HV180 or more in terms of Vickers hardness with a load of 1 kg.
  • HV180 or higher high temperature wear resistance higher than that of general-purpose austenitic stainless steels SUS310S and SUSXM15J11 can be obtained. it can.
  • the hardness after aging heat treatment is preferably HV210 or more.
  • the hardness after aging heat treatment is preferably HV250 or less from the viewpoint of workability of the turbo parts.
  • the ferritic stainless steel of the present invention uses the amount of wear after a high temperature friction test as an index of high temperature wear resistance. This is because it is assumed that the ferritic stainless steel of the present invention is used under the condition of sliding at a high speed in a high temperature environment like a turbocharger part. Specifically, in an air atmosphere at 850 ° C., a pin with a diameter of 4 mm is pressed with a vertical load of 0.5 N, and a rotary radius of 10 mm and a speed of 3.3 mm / sec are rotated and slid until the test length reaches 20 m. The amount of wear after the wear test is desirably 7 ⁇ m or less.
  • the ferritic stainless steel of the present invention is limited to the presence of 0.06 / ⁇ m 2 or more of Nb-containing precipitates at a depth of 20 ⁇ m from the surface layer.
  • the reason is as follows.
  • As a characteristic of a ferritic stainless steel sheet used for heat-resistant applications what is important is high-temperature strength, but particularly in the case of turbocharger parts, high-temperature wear resistance with other parts is also extremely important.
  • a part called a nozzle vane for controlling the flow rate and flow rate of exhaust gas a part called a nozzle plate or nozzle mount and a part called a vane slide at high speed in a high-temperature exhaust gas environment.
  • the Nb-containing precipitate has high hardness and is stable even at a relatively high temperature range, it is considered that the wear during high-temperature sliding can be reduced by the hard Nb-containing precipitate. Therefore, in the present invention, the number density of Nb-containing precipitates is defined. The reason why the depth from the surface layer is limited to 20 ⁇ m is that the amount of wear is taken into consideration, but considering a closer relationship with the amount of wear, the Nb-containing precipitates are 0 even at a depth of 10 ⁇ m from the surface layer. .06 / ⁇ m 2 or more is desirable.
  • the method for producing a steel sheet of the present invention comprises a steelmaking-hot rolling-annealing / pickling process or a steelmaking-hot rolling-annealing / pickling-cold rolling-annealing / pickling process.
  • steelmaking a method in which steel containing the essential components and components added as necessary is subjected to electric furnace melting or converter melting, followed by secondary refining is preferable.
  • the molten steel is made into a slab according to a known casting method (such as continuous casting).
  • the slab is heated to a predetermined temperature and hot-rolled to a predetermined plate thickness by continuous rolling.
  • the hot rolling may be tandem continuous hot rolling or Steckel reverse rolling, and the manufacturing conditions may be determined according to the steel composition.
  • the steel sheet after hot rolling is generally subjected to hot-rolled sheet annealing and pickling treatment, but hot-rolled sheet annealing may be omitted. Then, it cold-rolls to predetermined plate
  • the annealing temperature is 1000 ° C. or higher and 1120 ° C. or lower to obtain a recrystallized structure.
  • the cold-rolled sheet annealing temperature is increased to over 1050 ° C., and Nb is dissolved as much as possible in the heating stage, and then precipitated in the subsequent cooling process.
  • the cooling rate to 900 degreeC in the cooling process after a heating is prescribed
  • the cooling rate is excessively slow, the Nb-containing precipitate is excessively precipitated and coarsened, resulting in insufficient high-temperature strength.
  • productivity since productivity also deteriorates remarkably, it is set to 1 ° C./sec or more. Furthermore, when considering the shape, productivity, toughness, and corrosion resistance of the steel sheet, it is preferably 3 ° C./sec or more and 9 ° C./sec or less. By carrying out a process that satisfies such conditions, it can be controlled so that 0.06 pieces / ⁇ m 2 or more of Nb-containing precipitates are present at a depth of 20 ⁇ m from the surface layer. Note that other conditions in the manufacturing process may be appropriately selected. For example, what is necessary is just to design slab thickness, hot rolling board thickness, etc. suitably. In cold rolling, roll roughness, roll diameter, rolling oil, number of rolling passes, rolling speed, rolling temperature, etc.
  • a lubricating film can be applied to the product plate.
  • a special surface treatment such as nitriding or carburizing may be performed to further improve the heat resistance.
  • Nb-containing precipitates are deposited during annealing after hot rolling.
  • the present invention by ensuring the number density of Nb-containing precipitates in the vicinity of the surface layer of the stainless steel sheet product, high hardening after aging heat treatment is achieved, and excellent high-temperature wear resistance is obtained.
  • the number density of the Nb-containing precipitates may be secured by performing a heat treatment after processing into a turbocharger part or during the processing.
  • Steel A is the steel of the present invention.
  • Steels B and C are typical heat-resistant ferritic stainless steels.
  • Steel B is SUS444, and steel C is SUS430LX.
  • Steels D and E are typical austenitic stainless steels SUS310S and SUSXM15J1.
  • FIG. 1 shows the test results of the wear depth of three types of ferritic stainless steels (A, B, C) and the wear depth of typical general-purpose austenitic stainless steels (D, E).
  • FIG. 1 is a graph showing the relationship with the normal temperature hardness of each steel after aging heat treatment at 850 ° C. for 1 hour.
  • For the normal temperature hardness an average value obtained by measuring the Vickers hardness of a cross section at a depth of 20 ⁇ m from the surface layer at a load of 1 kg at five points was used.
  • the present invention steel A not only has higher wear resistance than other typical ferritic stainless steels, but also has less wear than austenitic stainless steels and exhibits excellent high temperature wear resistance. It was. This indicates that austenitic stainless steel, which was conventionally expensive from the viewpoint of high temperature wear resistance, can be replaced with the ferritic stainless steel of the present invention, which is extremely effective economically. It can be said to be a characteristic.
  • the reason for having excellent high temperature wear resistance is considered to be due to the high hardness after aging heat treatment.
  • the relationship between the hardness and the wear amount of the ferritic stainless steel and the austenitic stainless steel tends to be different, which may be influenced by the crystal structure and oxide scale.
  • the ferritic stainless steel of the present invention has high-temperature wear resistance (wear amount of 7 ⁇ m or less) of general-purpose austenitic stainless steels SUS310S and SUSXM15J11 if the hardness after aging heat treatment is HV180 or more. I found out that Therefore, it was found that the hardness after aging heat treatment of the ferritic stainless steel of the present invention is desirably HV180 or more, and the amount of wear after the high temperature wear test is desirably 7 ⁇ m or less. This range is the range indicated by hatching in FIG.
  • Nb precipitation state in the range from the surface layer before the test of Steel A and Steel B used in the high temperature sliding test shown in FIG. 1 to a depth of 20 ⁇ m was observed.
  • a cross section parallel to the rolling direction of the steel sheet was embedded and polished, etched with aqua regia, Nb-containing precipitates were observed with a scanning electron microscope, and the number density was calculated.
  • Judgment of Nb-containing precipitates was performed by elemental analysis of the precipitates with an analyzer attached to the scanning electron microscope, and judged by the presence or absence of Nb concentration.
  • the Nb-containing precipitates include Nb-containing carbonitrides, Laves phases, phosphides, and those that are segregated and complex-precipitated at the interfaces such as Cu precipitates and Ti-based precipitates.
  • the granular white portions are Nb-containing precipitates.
  • the number density of the Nb-containing precipitates in the comparative steel B was 0.03 / ⁇ m 2
  • the steel A excellent in high temperature wear resistance has a number density of 0.06. / ⁇ m 2 and higher than that of Comparative Steel B. Therefore, it can be seen that the hardness after aging heat treatment can be secured and the high-temperature wear resistance can be improved by setting the number density of Nb-containing precipitates with a depth of 20 ⁇ m to 0.06 pieces / ⁇ m 2 or more. It was. This is presumably because Nb-containing precipitates have high hardness and are stable even in a relatively high temperature range, and thus wear is reduced by the Nb-containing precipitates.
  • the prepared steel is melted and cast into a slab, and hot rolled, hot-rolled sheet annealing / pickling, cold-rolling, final annealing / pickling are performed to obtain 4.3 mm and 2.0 mm thick product plates. Obtained.
  • the component composition of the product plate obtained was as shown in Tables 2 and 3.
  • the final annealing conditions are shown in Tables 4 and 5 described later.
  • the hardness measurement after the aging heat treatment at 850 ° C. for 1 hour, the high temperature sliding test, and the number density measurement of the Nb-containing precipitates were performed on the 4.3 mm thick product plate.
  • the high temperature tensile test was done with respect to the 2.0 mm thick product board.
  • tensile test pieces are prepared so that the rolling direction and the tensile direction are parallel, heated to 850 ° C. at a heating rate of 100 ° C./min, holding time of 10 min, and constant speed at a crosshead speed of 1 mm / min.
  • a tensile test was performed to obtain a 0.2% yield strength in the rolling direction.
  • the high temperature sliding test was performed under the same conditions as the preliminary test, and the amount of wear was measured under the same conditions as the preliminary test after the test. A wear amount of 7 ⁇ m or less was accepted and over 7 ⁇ m was rejected. Moreover, cross-sectional hardness was measured on the same conditions as a preliminary test, and the hardness after aging passed 180 or more, and made less than 180 disqualified. Furthermore, the number density of the Nb-containing precipitates was measured under the same conditions as in the preliminary test, and 0.06 / ⁇ m 2 or more was accepted and less than 0.06 / ⁇ m 2 was rejected. About 0.2% yield strength of the high temperature tensile test, 40 MPa or more was passed at 850 ° C., and less than 40 MPa was rejected.
  • the sample material is processed into nozzle mount, nozzle plate and housing parts, mounted on a known nozzle vane turbocharger, and high temperature (850 ° C) exhaust gas is allowed to flow while repeatedly opening and closing the nozzle to improve gas flowability. Examined. At this time, the steel in which there was no problem in the gas flow was accepted, and the steel in which the gas flow failure (pressure loss 10% or more) and the nozzle opening / closing were defective was rejected.
  • the steel of the present invention example was excellent in workability, heat resistance, and surface properties and satisfied the performance as a turbocharger part.
  • the steel composition, Nb-containing precipitate density, and cross-sectional hardness were outside the scope of the present invention, the processing accuracy and turbocharger performance were poor, resulting in problems. Further, even when the high-temperature strength was poor, the turbocharger performance was poor due to creep deformation.
  • the present invention it is possible to provide a ferritic stainless steel sheet that is superior in cost to austenitic stainless steel for exhaust parts that require high temperature wear resistance.
  • a ferritic stainless steel sheet that is superior in cost to austenitic stainless steel for exhaust parts that require high temperature wear resistance.
  • the present invention can be applied not only to automobiles and motorcycle exhaust parts, but also to exhaust parts used in high-temperature environments such as various boilers and fuel cell systems, and high-temperature sliding parts. It is.

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  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Supercharger (AREA)
  • Exhaust Silencers (AREA)

Abstract

Cette invention concerne un acier inoxydable ferritique ayant une résistance à l'usure supérieure à haute température, caractérisé en ce qu'il contient, en % en masse, 0,003 à 0,02 % de C, 0,05 à 1,0 % de Si, 0,05 à 1,0 % de Mn, 0,01 à 0,05 % de P, 0,0001 à 0,01 % de S, de 15 à 18 % de Cr, 0,002 à 0,02 % de N, 0,01 à 0,20 % d'Al, 1 à 3 % de Cu, de 1,7 à 3 % de Mo, 0,4 à 0,7 % de Nb, et 0,0002 à 0,0030 % de B, le reste étant du Fe et les inévitables impuretés. Un dépôt contenant du Nb présente une densité de 0,06 particules/µm2ou plus à une profondeur de 20 µm à partir de la couche de surface.
PCT/JP2018/010619 2017-03-29 2018-03-16 Acier inoxydable ferritique ayant une résistance à l'usure supérieure à haute température, procédé de production de tôle d'acier inoxydable ferritique, de composants d'échappement, de composants coulissants à haute température, et de composants de turbocompresseur Ceased WO2018180643A1 (fr)

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MX2019011210A MX2019011210A (es) 2017-03-29 2018-03-16 Acero inoxidable ferritico que tiene resistencia al desgaste superior a alta temperatura, metodo de produccion para lamina de acero inoxidable ferritico, componentes de escape, componentes de deslizamiento de alta temperatura y componentes de turbocompresor.
JP2019509311A JP6768929B2 (ja) 2017-03-29 2018-03-16 高温耐摩耗性に優れたフェライト系ステンレス鋼、フェライト系ステンレス鋼板の製造方法、排気部品、高温摺動部品、およびターボチャージャー部品
CN201880019902.6A CN110462081B (zh) 2017-03-29 2018-03-16 高温耐磨性优良的铁素体系不锈钢、铁素体系不锈钢板的制造方法、排气部件、高温滑动部件以及涡轮增压器部件

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JPWO2021100687A1 (fr) * 2019-11-19 2021-05-27
CN114317898A (zh) * 2021-12-24 2022-04-12 哈尔滨工程大学 一种提高铁素体不锈钢表面耐磨和耐蚀性的方法
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CN114317898B (zh) * 2021-12-24 2024-01-26 哈尔滨工程大学 一种提高铁素体不锈钢表面耐磨和耐蚀性的方法
WO2024070493A1 (fr) * 2022-09-26 2024-04-04 日鉄ステンレス株式会社 Matériau d'acier inoxydable ferritique pour composants de batterie, son procédé de production et composant de batterie
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