US20170253945A1 - Martensitic stainless steel for brake disk and method for producing said steel - Google Patents

Martensitic stainless steel for brake disk and method for producing said steel Download PDF

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US20170253945A1
US20170253945A1 US15/511,905 US201515511905A US2017253945A1 US 20170253945 A1 US20170253945 A1 US 20170253945A1 US 201515511905 A US201515511905 A US 201515511905A US 2017253945 A1 US2017253945 A1 US 2017253945A1
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stainless steel
hot
martensitic stainless
rolling
rolled
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Shinichi Teraoka
Yoshiharu Inoue
Yuji Koyama
Junichi Hamada
Toshio Tanoue
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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 claimed from PCT/JP2015/074912 external-priority patent/WO2016043050A1/ja
Assigned to NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION reassignment NIPPON STEEL & SUMIKIN STAINLESS STEEL CORPORATION ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: HAMADA, JUNICHI, TANOUE, TOSHIO, INOUE, YOSHIHARU, KOYAMA, YUJI, TERAOKA, SHINICHI
Publication of US20170253945A1 publication Critical patent/US20170253945A1/en
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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
    • 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
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a stainless steel plate used for a brake disk of a two-wheeled vehicle and a producing method of the stainless steel plate, more specifically, to a martensitic stainless steel plate used for a brake disk of a two-wheeled vehicle, the martensitic stainless steel plate having excellent properties of a surface and an end surface.
  • the brake disk of a two-wheeled vehicle is required to have properties such as wear resistance, corrosion resistance, and toughness.
  • wear resistance is increased as hardness is increased.
  • the hardness of the brake is required to range from 32 to 38 HRC (Rockwell hardness C-scale). Because of these demanded properties, a martensitic stainless steel plate is used for the brake disk of the two-wheeled vehicle.
  • Patent Literature 1 discloses an invention relating to a steel composition capable of stably obtaining a desired hardness in a wider quenching temperature range than that of a typical steel of a SUS420J2 steel, the steel composition being usable in the as-quenched state.
  • Patent Literature 1 is provided by reducing a C content and compensating narrowing of the austenitic single phase temperature range caused by the reduction of the C content, in other words, narrowing of the quenching temperature range, by adding Mn that is an austenite stabilizing element.
  • Patent Literature 2 discloses an invention relating to a steel sheet for a motorbike disk brake, the steel sheet being a low Mn steel and is used in the as-quenched state. This steel sheet is obtained by reducing Mn and simultaneously adding Ni and Cu having the same effect as an austenite forming element.
  • Patent Literature 3 discloses an invention relating to a method for improving heat resistance by adding Nb and Mo.
  • Patent Literature 4 discloses an invention relating to a disk material having an excellent heat resistance obtained by subjecting the disk material to a quenching treatment at a temperature higher than 1000 degrees C.
  • Patent Literature 5 discloses a brake disk having a martensitic structure in which a prior austenite grain has an average grain size of 8 ⁇ m or more
  • Patent Literature 6 discloses an invention in which martensite accounts for 75% or more and Nb accounts for from 0.10% to 0.60% at an area ratio of a quenched structure.
  • Patent Literature 7 discloses control of components to a limited range in which cracks are unlikely to be generated, since the above low-C martensitic stainless steel has a low hot workability and easily causes a so-called cracked edge at a widthwise end at the time of hot rolling.
  • Patent Literature 8 relates to a manufacturing method of a ferritic stainless steel strip. Particularly, Patent Literature 8 discloses optimum conditions for sheet bar heating in relation to a manufacturing method with a high productivity of a ferritic stainless hot-rolled steel strip having excellent moldability and material uniformity.
  • Patent Literature 1 JP-A-57-198249
  • Patent Literature 2 JP-A-8-60309
  • Patent Literature 3 JP-A-2001-220654
  • Patent Literature 4 JP-A-2005-133204
  • Patent Literature 5 JP-A-2006-322071
  • Patent Literature 6 JP-A-2011-12343
  • Patent Literature 7 JP-A-2008-285692
  • Patent Literature 8 JP-A-2000-61524
  • a jig is increasingly worn and temper softening of a material occurs by heat generated by friction caused during a processing. Accordingly, in order to reduce the polishing time without heat generation by friction caused during the processing, a polishing thickness is generally decreased. Here, an edge seam defect at the widthwise end of the steel strip has been problematic.
  • FIG. 1A shows an appearance of an edge seam defect in an actual product.
  • FIG. 1B shows a microscope photograph of a cross section of the edge seam defect in the actual product.
  • a typical manufacturing process of a hot-rolled steel strip includes: heating a slab having a thickness from 150 mm to 250 mm to a temperature ranging from 1100 degrees C. to 1300 degrees C.; rolling the slab to form a rough bar having a thickness from 20 mm to 40 mm using a rough hot rolling mill; subsequently, rolling the rough bar to form a plate having a thickness from 3 mm to 6 mm using a finish hot rolling mill; and coiling the obtained plate.
  • the slab expands widthwise, so that a part of an end surface of the slab becomes a surface of the rough bar. Since the end surface of the slab does not contact with the rolling roller at the beginning of the rough hot rolling, roughness of the end surface of the slab is large, which causes defects when the end surface of the slab is brought into contact with the rolling roller.
  • FIG. 2 is a photograph showing an end surface of a 20-mm-thick steel ingot obtained by hot-rolling an original 80-mm-thick steel ingot of each of various stainless steels in a laboratory. It is understood that the stainless steels are considerably different from each other in a level of roughness of the end surface thereof. Moreover, it is understood that roughness of the end surface of SUS410 steel is considerably changed depending on a hot-rolling heating temperature. Since roughness of the end surface of the slab in the rough hot rolling is caused by a difference in a deformation pattern caused by a difference in a crystal orientation between crystal grains of the slab, the roughness becomes noticeable when the crystals grains are large-sized.
  • ⁇ refers to ⁇ ferrite
  • ⁇ refers to austenite
  • a refers to ⁇ ferrite.
  • ferrite usually means a ferrite.
  • ⁇ ferrite is ferrite precipitated at A4 transformation point or higher.
  • ⁇ ferrite is ferrite precipitated at A3 transformation point or lower.
  • the structure of the common steel is micronized by another transformation of ⁇ / ⁇ in the hot-rolling heating and the rough hot rolling is performed in a ⁇ single phase in which recrystallization easily occurs, the structure of the common steel becomes finer also with the effect of micronizing crystal grains by recrystallization, so that edge seam defect is unlikely to occur.
  • the edge seam defect is likely to occur due to a large grain size.
  • ⁇ ferrite is not differentiated from a ferrite in a steel not forming a ⁇ single phase after solidification as in the ferritic stainless steel.
  • the low-C martensitic stainless steel since a temperature range in which the low-C martensitic stainless steel exhibits the austenitic single phase is narrow, the low-C martensitic stainless steel has a duplex structure of ⁇ ferrite and austenite in hot-rolling heating.
  • the edge seam defect is likely to occur because of the ⁇ ferrite at this time. Accordingly, the polishing thickness exceeding a depth of the edge seam defect is required in the polishing process after quenching of the disk brake, thereby hampering productivity.
  • the ⁇ ferrite fraction is measurable according to a phase diagram calculation method or a heat treatment test in a laboratory.
  • the duplex structure of austenite and martensite is rapidly cooled, since the austenitic phase forms a martensitic structure, the ⁇ ferrite phase is easily distinguished from the martensitic structure as a less deformed ⁇ ferrite phase.
  • the hot-rolled steel strip coiled after the finish hot-rolling exhibits a low toughness because of including the martensitic structure obtained by transformation of austenite. Accordingly, it is difficult to uncoil the hot-rolled steel strip without any treatment.
  • the hot-rolled steel strip can be uncoiled by being subjected to a hot-rolling and annealing in a box annealing furnace to temper martensite to ferrite and carbide.
  • the structure of the plate after hot-rolling and annealing is a structure of ferrite and carbide as shown in FIG. 3 . It is impossible to measure the ⁇ ferrite fraction.
  • the Murakami reagent is an aqueous solution of potassium ferricyanide. The solution is heated and a sample is immersed in the solution to be etched.
  • the Murakami reagent is usually used for distinguishing austenite from the ⁇ ferrite phase by coloring the ⁇ ferrite mixed in an austenite mother phase as seen in a solidification structure of the austenitic stainless steel. Although it was not expected at first that it became possible to distinguish the ⁇ ferrite in the hot-rolled and annealed steel plate of the martensitic stainless steel in which the ⁇ ferrite and ferrite were mixed, the ⁇ ferrite was able to be clearly distinguished as shown in FIG. 4 . The ⁇ ferrite is shown by a gray contrast part in FIG. 4 .
  • the ⁇ ferrite can be distinguished by evaluating the steel plate sample as described above.
  • FIG. 5 A relationship between the edge seam defect and the ⁇ ferrite amount is shown in FIG. 5 .
  • No edge seam defect is observed in the austenitic stainless steel having 0% ⁇ ferrite fraction.
  • a depth of the seam defect is increased.
  • an increase amount of the depth of the seam defect is small until the ⁇ ferrite fraction reaches 30%.
  • FIG. 6 shows forms of ends of (11% Cr, 12% Cr)-0.04% C-1.4% Mn-0.03% N steels respectively with the ⁇ ferrite fractions of 4% and 20% after subjected to hot-rolling in a laboratory.
  • the ⁇ ferrite fraction is low, an apparent cracked edge occurs.
  • the ⁇ ferrite fraction is strongly related to the depth of the edge seam defect and the cracked edge at the widthwise end of the steel plate.
  • the martensitic stainless steel in which the ⁇ ferrite fraction is controlled since the cracked edge is not observed and the depth of the edge seam defect is shallow, a grinding depth in a manufacturing process of the brake disk can be shallow, thereby improving productivity of the brake disk. Further, since the very end of the steel plate can be used, a yield is also improvable.
  • the inventors scrutinized the ⁇ ferrite amount of the hot-rolled and annealed steel plate, hot rolling operational conditions and the chemical compositions, and found a method effective for satisfying the surface quality, prevention of the cracked edge, and hardness and corrosion resistance required as the disk brake. Specifically, it is necessary to heat the rough bar by induction heating or the like to increase a temperature of the rough bar, the rough bar provided between the rough hot-rolling and the finish hot-rolling, in order to control the components to satisfy (1) the ⁇ ferrite amount in the hot-rolling heating and (2) various properties and in order to prevent (3) the ⁇ ferrite amount from being decreased due to lowering of the temperature during the rough rolling after being taken out of the hot-rolling heating furnace.
  • the hot-rolled steel plate and the hot-rolled and annealed steel plate of martensitic stainless steel used for a brake disk in which the edge seam defect is reduced and the widthwise end of the hot-rolled steel strip is prevented from forming a cracked edge, and a controlling method of a structure of the steel plates can be provided.
  • a solution of the problem of the invention specifically, a martensitic stainless steel (including a hot-rolled steel plate (which is not subjected to hot-rolling-and-annealing) and a hot-rolled and annealed steel plate)) used for a brake disk of a two-wheeled vehicle, and a manufacturing method of the martensitic stainless steel of the invention are described as follows.
  • a martensitic stainless steel used for a brake disk of a two-wheeled vehicle includes: in % by mass, C of 0.025% to 0.080%, Si of 0.05% to 0.8%, Mn of 0.5% to 1.5%, P of 0.035% or less, S of 0.015% or less, Cr of 11.0% to 13.5%, Ni of 0.01% to 0.50%, Cu of 0.01% to 0.08%, Mo of 0.01% to 0.30%, V of 0.01% to 0.10%, Al of 0.05% or less, and N of 0.015% to 0.060%; the balance being Fe and inevitable impurities; a DFE value defined by a formula (1) ranging from 5 to 30; and a ⁇ ferrite fraction observed in a cross section structure ranging from 5% to 30% by an area ratio,
  • DFE 12(Cr+Si) ⁇ 430C ⁇ 460N ⁇ 20Ni ⁇ 7Mn ⁇ 89 Formula (1).
  • the martensitic stainless steel further includes: in % by mass, one or two of Ti of 0.03% or less and B of 0.0050% or less.
  • the martensitic stainless steel further includes: in % by mass, Nb 0.30% or less.
  • the martensitic stainless steel further includes: in % by mass, one or two of Sn of 0.1% or less and Bi of 0.2% or less.
  • a manufacturing method of the martensitic stainless steel includes: heating a rough bar at a temperature ranging from 10 degrees C. to 50 degrees C.
  • the martensitic stainless steel is a hot-rolled steel plate that is not subjected to hot-rolling-and-annealing.
  • the martensitic stainless steel is a hot-rolled and annealed steel plate.
  • the hot-rolled steel plate and the hot-rolled and annealed steel plate used for the brake disk of a two-wheeled vehicle in which the edge seam defect is reduced on the widthwise end of the hot-rolled steel strip and the widthwise end thereof is prevented from forming a cracked edge, can be obtained.
  • the quality of each of the obtained steel plates is favorable in terms of an improvement in productivity and a yield of the brake disk.
  • FIG. 1A shows an appearance of an edge seam defect at a widthwise end of a hot-rolled and annealed steel strip of a martensitic steel used for a brake disk.
  • FIG. 1B shows a microscope image obtained by observing a cross section of the edge seam defect at the widthwise end of the hot-rolled and annealed steel strip of the martensitic steel used for the brake disk.
  • FIG. 2 is a photograph showing a surface of a widthwise end of a 20-mm-thick steel ingot obtained using a laboratory hot-rolling mill by rolling an original steel ingot cast in dimensions of 300 L ⁇ 180w ⁇ 80t (mm) in a laboratory, in order to demonstrate a generation process of the edge seam defect.
  • FIG. 3 is a photograph showing a structure (in which ferrite grains and carbides mainly appear) after being hot-rolled and annealed, the structure being a general cross-sectional structure of a hot-rolled and annealed plate of a 11% Cr-1% Mn-0.04% C-0.04% N steel.
  • the structure has been subjected to etching by aqua regia for a short period of time.
  • FIG. 4 is a photograph showing a distribution of ⁇ ferrite in a TD cross section of a hot-rolled and annealed steel strip of a 11% Cr-1% Mn-0.04% C-0.04% N martensitic stainless steel, in which an edge seam defect and a cracked edge are not observed, the photograph showing a ⁇ ferritic structure of the hot-rolled and annealed plate having a favorable quality in terms of the edge seam defect and cracked edge.
  • FIG. 5 illustrates a relationship between the depth of the edge seam defect and the ⁇ ferrite amount of a sample taken from each of several types of martensitic stainless steels used for the disk brake of a two-wheeled vehicle, in which each of the martensitic stainless steels was subjected to a change in the hot-rolling heating temperatures from 1100 degrees C. to 1280 degrees C. and hot-rolled to form a plate having a 3.8-mm thickness, the hot-rolled plate was annealed, subsequently, the hot-rolled coil was uncoiled and the sample was taken.
  • FIG. 6 is a photograph showing a relationship between a cracked edge on an end surface of a 3-mm-thick plate and a ⁇ ferrite amount affecting the cracked edge, in which the plate is obtained by heating a 50-mm steel ingot of 11-to-12% Cr-0.04% C-0.5-to-1.4% Mn-0.03% N steel to 1250 degrees C. at a laboratory and subsequently hot-rolling the steel ingot into the 3-mm-thick plate.
  • Exemplary embodiment(s) of the invention will be described below. Firstly, a reason why a steel composition of a stainless steel plate in an exemplary embodiment is limited will be described. A mark % with respect to the composition means a mass % unless otherwise particularly indicated.
  • C is an essential element for obtaining a predefined hardness of the stainless steel plate after quenching and is added in combination with N so as to attain a predefined hardness level.
  • an upper limit of C is defined to be 0.080% to maximize the effect of N without an excessive addition of C
  • the upper limit of the C content is desirably 0.060% in terms of hardness control and an improvement in corrosion resistance.
  • a lower limit of the C content is defined to be 0.025%.
  • the C content is desirably 0.040% or more in terms of stability of quenching hardness.
  • Si is required for deoxidation at melting and refining process and is also useful for inhibiting generation of oxidized scale at a quenching heat process. Since an effect of Si is exerted at 0.05% or more, a Si content is set at 0.05% or more. However, since Si is mixed in a raw material such as molten pig iron and an excessive decrease of the Si content increases cost, the Si content is desirably 0.20% or more. Moreover, since Si narrows an austenite single phase temperature region to impair a quenching stability, the Si content is defined to be 0.8% or less. However, the Si content is desirably 0.6% or less in order to decrease an additive amount of the austenite stabilizing element and reduce the cost.
  • Mn is an element to be added as a deoxidation agent and contributes to expansion of the austenite single phase region and an improvement in hardenability. Since an effect of Mn is clearly exerted at 0.5% or more, a Mn content is set at 0.5% or more.
  • the Mn content is desirably 1.1% or more in order to stably obtain the hardenability.
  • an upper limit of the Mn content is defined to be 1.5% or less in order to increase abrasion load.
  • the Mn content is desirably 1.3% or less.
  • P is an element contained as impurities in a raw material such as molten pig iron and a main raw material such as ferrochromium. Since P is a harmful element to toughness of a hot-rolled and annealed plate after quenching, a P content is defined to be 0.035% or less. P is preferably 0.030% or less. Since excessive reduction of P essentially requires use of a high purity raw material, leading to cost increase, a lower limit of P is preferably 0.010%.
  • the upper limit of the S content is preferably small and set at 0.015%.
  • the upper limit is more preferably 0.008%.
  • the lower limit of the S content is preferably set at 0.001%.
  • Cr is an essential element for ensuring oxidation resistance and corrosion resistance in the exemplary embodiment.
  • the Cr content of less than 11.0% does not exert these effects, while the Cr content of more than 13.5% narrows the austenite single phase region to impair hardenability. Accordingly, the Cr content is set in a range from 11.0% to 13.5%.
  • the Cr content is desirably 12.0% or more.
  • the Cr content is desirably 13.0% or less.
  • Ni From 0.01% to 0.50%
  • Ni is mixed as inevitable impurities in an alloy raw material of a ferritic stainless steel and is generally contained in a range from 0.01% to 0.10%. Moreover, Ni is an element effective for suppression of progress of pitting corrosion and the effect of Ni is stably exerted by the addition of 0.03% or more of Ni. Accordingly, a lower limit of a Ni content is preferably set at 0.03%. On the other hand, since a large added amount of Ni may deteriorate press formability due to solid-solution hardening in a hot-rolled and annealed steel plate, an upper limit of the Ni content is set at 0.50%. In consideration of alloy cost, the Ni content is desirably 0.15% or less.
  • Cu is effective for improving corrosion resistance of the martensitic structure including ⁇ ferrite and the effect of Cu is exerted at 0.01% or more. Moreover, a positive addition of Cu is occasionally performed in order to improve the hardenability as the austenite stabilizing element. However, since an excessive addition of Cu causes a decrease in the hot workability and an increase in the raw material cost, an upper limit of a Cu content is set at 0.08% or less. In consideration of generation of corrosion due to acid rain, a lower limit of the Cu content is desirably set at 0.02% or more. Moreover, in consideration of press formability of the hot-rolled and annealed steel plate, the Cu content is preferably 0.08% or less.
  • Mo is effective for improving corrosion resistance of the martensitic structure including ⁇ ferrite and the effect of Mo is exerted at 0.01% or more. Accordingly, a lower limit of a Mo content is set at 0.01%. Since Mo is effective for improving the hardenability and improving heat resistance after quenching, the Mo content is preferably 0.02% or more.
  • the steel is occasionally tempered by heating after quenching to cause a decrease in the hardness.
  • the improvement in heat resistance after quenching means a small decrease in the hardness, which is also referred to temper softening resistance.
  • a disk brake for use is subjected to quenching, a disk material is heated by resistance heat generated at the time of braking in use. Accordingly, this property is important.
  • an upper limit of the Mo content is set at 0.30% or less.
  • V From 0.01% to 0.10%
  • V is mixed as inevitable impurities in an alloy raw material of a ferritic stainless steel and is not easy to remove in the refining process. Accordingly, V is generally contained in a range from 0.01% to 0.10%. Moreover, V is an intentionally added element as needed since V forms a fine carbonitride to improve wear resistance of the brake disk and exerts an effect of improving corrosion resistance. Since an effect of V is stably exerted by the addition of 0.02% or more, a lower limit of a V content is preferably set at 0.02%, more preferably 0.03% or more. On the other hand, since an excessive addition of V may form large-sized precipitates, leading to deterioration of toughness after quenching, an upper limit of the V content is set at 0.10%. In consideration of the production cost and productivity, the V content is desirably set at 0.08% or less.
  • Al is an element to be added as a deoxidizing element and improve oxidation resistance. Since an effect of Al is exerted at 0.001% or more, a lower limit of an Al content is preferably set at 0.001% or more. On the other hand, since solid-solution hardening and formation of large-sized oxide inclusions may cause deterioration of toughness of the brake disk, an upper limit of the Al content is set at 0.05%. The Al content is preferably 0.03% or less. It is not a requisite to contain Al.
  • N is one of very important elements in the exemplary embodiment. Similarly to C, N is an essential element for obtaining a predetermined hardness after quenching and is added in combination with N so as to attain a predetermined hardness level.
  • quenching as the duplex structure of austenite and ferrite at the time of quenching heating, precipitation of Cr carbide, in other words, a sensitization phenomenon is likely to occur, leading to deterioration of corrosion resistance.
  • addition of nitrogen enables suppression of precipitation of Cr carbide, which may exert the effect of improving corrosion resistance. Since the effect is exerted at 0.015% or more, a N content is set at 0.015% or more.
  • an upper limit of the N content is set at 0.060%.
  • the N content is desirably 0.030% or more.
  • the N content is desirably 0.050% or less.
  • ⁇ ferrite which is represented by an area ratio, observed in a hot-rolled steel plate or a hot-rolled and annealed steel plate is defined in a range from 5% to 30%.
  • the amount of ⁇ ferrite in the steel affects generation of the edge seam defect and hot-rolled cracked edge at the time of hot rolling.
  • the ⁇ ferrite fraction is set at 5% or more.
  • the ⁇ ferrite fraction is set at 30% or less.
  • the ⁇ ferrite is observed in a cross section of the hot-rolled and annealed steel plate and the hot-rolled steel plate at the time of hot rolling, and evaluated through observation using a typical microscope.
  • a structure etching of the ⁇ ferrite is desirably performed by a method of immersing a sample in a solution provided by heating the Murakami reagent (an aqueous solution of potassium ferricyanide).
  • the DFE value When the DFE value is low, the ⁇ ferrite amount is decreased to increase a generating frequency of the cracked edge at hot rolling. Accordingly, the DFE value is set at 5 or more. When the DFE value is high, the ⁇ ferrite amount is increased to easily cause the edge seam defect. Accordingly, the DFE value is set at 20 or less. It should be noted that Cr, Si, C, N, Ni and Mn in the formula (1) indicate the respective contents (% by mass).
  • the following elements may be added in order to improve rust resistance, heat resistance, hot workability and the like.
  • Ti which forms carbonitride, is an element for suppressing a sensitization phenomenon by precipitation of chrome carbonitride and a decrease in corrosion resistance in a stainless steel.
  • a Ti content is preferably 0.001% or more.
  • an upper limit of the Ti content is set at 0.03% or less. In consideration of toughness in winter, the Ti content is desirably 0.01% or less. It is not a requisite to contain Ti.
  • B is an element effective for improving hot workability. Since the effect of B is exerted when a B content is 0.0002% or more, B may be added at 0.0002% or more. In order to improve hot workability in a wider temperature range, the B content is desirably set at 0.0010% or more. On the other hand, since excessive addition of B causes deterioration of hardenability due to composite precipitation of boride and carbide, an upper limit of the B content is set at 0.0050%. In consideration of corrosion resistance, the B content is desirably 0.0025% or less.
  • Nb which forms carbonitride, is an element for suppressing a sensitization phenomenon by precipitation of chrome carbonitride and a decrease in corrosion resistance in a stainless steel.
  • a Nb content is preferably 0.001% or more.
  • Nb is an element for largely improving heat resistance after quenching.
  • heat resistance means how the stainless steel is unlikely to be softened when receiving heat after quenching. In other words, heat resistance is also referred to as temper softening resistance.
  • an upper limit of the Nb content is set at 0.3%.
  • Mo in a range from 0.05% to 0.20% and Nb in a range from 0.05% to 0.20% are particularly preferable.
  • Sn is an element effective for improving corrosion resistance after quenching.
  • a Sn content is preferably 0.001% or more, more preferably 0.02% or more as needed. However, since excessive addition of Sn promotes edge cracking at hot rolling, the Sn content is preferably set at 0.10% or less.
  • Bi is an element for improving corrosion resistance. Although the mechanism is not clarified, it is deduced that addition of Bi decreases probability that MnS becomes a starting point of corrosion generation because Bi micronizes MnS that is likely to be the starting point. The effect is exerted when Bi is added at 0.01% or more. Since the effect is only saturated when Bi is added at more than 0.2%, an upper limit of the Bi content is set at 0.2%.
  • impurity elements are contained as long as the effect of the invention is not hampered.
  • P and S which are general impurity elements but also Zn, Pb, Se, Sb, H, Ga, Ta, Ca, Mg, Zr and the like are preferably reduced as much as possible.
  • content rates of these elements are controlled.
  • the respective contents are Zn ⁇ 100 ppm, Pb ⁇ 100 ppm, Se ⁇ 100 ppm, Sb ⁇ 500 ppm, H ⁇ 100 ppm, Ga ⁇ 500 ppm, Ta ⁇ 500 ppm, Ca ⁇ 120 ppm, Mg ⁇ 120 ppm, and Zr ⁇ 120 ppm.
  • a rough bar having a plate thickness from 20 mm to 40 mm is preferably heated at a temperature from 10 degrees C. to 50 degrees C.
  • the temperature for heating the rough bar is less than 10 degrees C.
  • the ⁇ ferrite amount is small to decrease hot workability, so that the cracked edge is likely to be generated.
  • the temperature for heating the rough bar is more than 50 degrees C.
  • the ⁇ ferrite amount is excessively large to increase a grain size, thereby increasing roughness of an end surface of the rough bar, so that deep edge seam defect is likely to be generated.
  • the temperature of the rough bar is increased also by increasing a slab heating temperature prior to the hot rolling process instead of heating by a rough bar heater.
  • the heating temperature in the hot rolling is desirably 1250 degrees C. or less.
  • the heating temperature in the hot rolling is less than 1150 degrees C., deformation resistance of the austenite mother phase is increased and the ⁇ ferrite amount is decreased, so that a ⁇ ferrite phase in a small amount is concentrically deformed to decrease hot-rolling deformability, whereby a cracked edge is generated to decrease a yield.
  • the heating temperature in the hot rolling is desirably 1150 degrees C. or more.
  • the martensitic stainless steel for a brake disk for a two-wheeled vehicle can exert effects in both of a hot-rolled steel plate without being subjected to hot-rolling-annealing, and a hot-rolled and annealed steel plate.
  • a steel having a component composition shown in Tables 1-1 and 1-2 was melted and cast to obtain a 200-mm-thick slab.
  • This slab was heated to a temperature in a range from 1150 degrees C. to 1250 degrees C. and subsequently subjected to a rough hot-rolling and a finish hot-rolling to obtain a 4-mm-thick hot-rolled steel plate, which was coiled in a temperature range of 750 degrees C. to 900 degrees C.
  • the coiled hot-rolled steel plate was heated in a range of an increasing temperature from 10 degrees C. to 50 degrees C. using a rough bar heater with use of induction heating between the rough hot-rolling and the finish hot-rolling.
  • the coiled hot-rolled steel plate was annealed in a box annealing furnace.
  • the box annealing furnace was heated up to a temperature range of 800 degrees C. to 900 degrees C.
  • the hot-rolled and annealed steel plate was evaluated in terms of the edge seam defect and the cracked edge.
  • the edge seam defect was judged as “Pass” when a depth of the edge seam defect was less than 150 ⁇ m, in which a judgment S was given when the edge seam defect was not visually observed; and a judgment A was given when the edge seam defect was visually observed.
  • the edge seam defect was judged as “Fail” (a judgment C).
  • the cracked edge was judged as: “Pass” (a judgment A) when no cracked edge having a depth of 10 mm or more was generated; and “Fail” (a judgment B) when a cracked edge having a depth of 10 mm or more was generated.
  • Pass a judgment A
  • Fail a judgment B
  • the cracked edge was judged as “Fail” (a judgment C).
  • a cross-sectional structure was observed using an optical microscope and a ⁇ ferrite amount was measured by image analysis. ⁇ ferrite appeared using the Murakami reagent.
  • the hot-rolled, annealed and pickled plate was quenched and a surface thereof was subjected to a polish finish (#80).
  • a JIS surface hardness quenching hardness
  • the plate having the surface hardness from 32 to 38 was judged as “Pass” and the plate not having the surface hardness from 32 to 38 was judged as “Fail.”
  • a disk brake was quenched under conditions of heating at an average heating rate of about 50° C./s to reach 1000 degrees C., keeping the temperature for one second after reaching 1000 degrees C., and cooling at an average cooling rate of 70° C./s to reach the ambient temperature.
  • the depth of the edge seam defect of 150 ⁇ m or less was judged as “Pass (A)” and the depth of the edge seam defect of more than 150 ⁇ m was judged as “Fail (B).”
  • the martensitic stainless steel plate of the invention used for the brake disk is a high-quality brake disk having favorable qualities of the edge seam defect and the cracked edge and being free from deterioration in hardness and corrosion resistance after quenching, which attains optimization of the ⁇ ferrite amount observed in the hot-rolled and annealed steel plate and the hot-rolled steel plate by controlling the component design and the hot rolling conditions.
  • the qualities of the edge seam defect and the cracked edge were further improved by heating the rough bar between the rough hot rolling and the finish hot rolling under the optimum conditions depending on the composition of each of the steel plates.
  • a material to which the invention is applied is used for the two-wheeled brake disk, whereby a yield is improvable and an examination burden is reducible, and further, productivity is improvable due to a shortening of the polishing time, so that the invention can increasingly contribute to the society.
  • the invention has a sufficient industrial applicability.

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