WO2012157680A1 - 自転車のディスクブレーキロータ用マルテンサイト系ステンレス鋼板およびその製造方法 - Google Patents

自転車のディスクブレーキロータ用マルテンサイト系ステンレス鋼板およびその製造方法 Download PDF

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WO2012157680A1
WO2012157680A1 PCT/JP2012/062534 JP2012062534W WO2012157680A1 WO 2012157680 A1 WO2012157680 A1 WO 2012157680A1 JP 2012062534 W JP2012062534 W JP 2012062534W WO 2012157680 A1 WO2012157680 A1 WO 2012157680A1
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stainless steel
hardness
disc brake
less
martensitic stainless
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PCT/JP2012/062534
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English (en)
French (fr)
Japanese (ja)
Inventor
慎一 寺岡
小林　雅明
章宏 福田
服部　憲治
浩一 井内
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新日鐵住金ステンレス株式会社
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Priority to JP2013515182A priority Critical patent/JP5863785B2/ja
Priority to CN201280023714.3A priority patent/CN103534377B/zh
Publication of WO2012157680A1 publication Critical patent/WO2012157680A1/ja

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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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D8/0205—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
    • C21D8/0221—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
    • 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
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/42—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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
    • F16D65/00—Parts or details
    • F16D65/0006—Noise or vibration control
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
    • F16D65/00—Parts or details
    • F16D65/02—Braking members; Mounting thereof
    • F16D65/12—Discs; Drums for disc brakes
    • F16D65/125—Discs; Drums for disc brakes characterised by the material used for the disc body
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
    • F16D69/00—Friction linings; Attachment thereof; Selection of coacting friction substances or surfaces
    • F16D69/02—Composition of linings ; Methods of manufacturing
    • F16D69/027—Compositions based on metals or inorganic oxides
    • 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 martensitic stainless steel plate and a method for producing the same as a disc brake rotor of a bicycle, which are excellent in braking characteristics of a brake and excellent in press formability when processed into a rotor shape.
  • Bicycle disc brake rotors are required to have characteristics such as wear resistance, weather resistance, and lightness. Therefore, martensitic stainless steel or a composite material of martensitic stainless steel and aluminum is used. For martensitic stainless steel, SUS420J1 and SUS420J2 are generally used.
  • the disc brake rotor is hot-rolled stainless steel, cold-rolled after annealing, adjusted in shape and hardness, then processed into a predetermined shape by press molding, and hardened and tempered by heat treatment. Then, the disc brake rotor is manufactured through processes such as polishing and painting.
  • the same martensitic stainless steel is used for motorcycle disc brakes. Compared to a bicycle, it is a high-speed and heavy vehicle body, and therefore requires a high braking force. Therefore, it is manufactured by annealing a hot-rolled steel sheet of martensitic stainless steel and quenching it after press forming.
  • the wear resistance generally increases as the hardness of the steel increases. However, if the hardness is too high, a so-called “brake noise” occurs between the brake rotor and the pad. For this reason, the hardness of the disc brake rotor of a motorcycle cannot be made very high, and 34 ⁇ 3 HRC (Rockwell hardness C scale) is required.
  • low carbon (C) and low nitrogen (N) stainless steel is being applied to eliminate the tempering step after quenching.
  • a low carbon martensitic stainless steel with a weight ratio of C + N: 0.04 to 0.10% and Mn added to 1.0 to 2.5% is disclosed as a material for motorcycle disc brakes.
  • SUS420J1 and SUS420J2 that are generally used for bicycle disc brake rotors have a hardness of 50 HRC or more when quenched, and therefore need to be tempered. Therefore, a process is long and the improvement of the productivity is a subject.
  • martensitic stainless steel for motorcycles has insufficient quenching hardness as described above, and cannot be used for a disc brake rotor for bicycles. Further, there is a problem that squealing is likely to occur when carbon (C) is increased in order to increase the quenching hardness.
  • the present invention advantageously solves the above-mentioned problems of the prior art, suppresses the occurrence of squeal during braking, has excellent brake braking characteristics, and is used while being quenched, martensitic stainless steel for a disc brake rotor of a bicycle It aims at providing a steel plate and its manufacturing method.
  • Martensitic stainless steel for bicycle brake disc rotors needs to have a hardness of 38 HRC or higher in order to obtain the necessary braking force.
  • This hardness is characterized by being higher than the hardness of 32 HRC or more required for a motorcycle disc brake rotor.
  • an abnormal noise accompanied by vibration called “Brake noise” becomes a problem in a disc brake rotor of a bicycle. Squeaking can be suppressed by quenching and tempering stainless steel such as SUS420J1 and SUS420J2 to a hardness of 43 HRC or less.
  • the hardness is generally set to 38 HRC or less, and the hardness is controlled to 32 HRC or more necessary for obtaining braking force, and the hardness is controlled to 38 HRC or less which starts to squeal. Yes.
  • the hardness of the disc brake rotor of 38 HRC or more is required. Considering the variation in hardness after quenching, the hardness range of 38 to 43 HRC is considered necessary.
  • the structure after quenching is a structure in which carbides are slightly dispersed in the martensite matrix, and the precipitation amount is 0.04% in terms of the weight percentage of Fe. It is necessary to:
  • the gist of the present invention completed based on the above knowledge resides in the following martensitic stainless steel plate for a disc brake rotor of a bicycle and a manufacturing method thereof.
  • ⁇ p 420 [% C] +470 [% N] +23 [% Ni] +9 [% Cu] +7 [% Mn] ⁇ 11.5 [% Cr] ⁇ 11.5 [% Si] ⁇ 52 [% Al] ⁇ 12 [% Mo] -47 [% Nb] -7 [% Sn] -49 [% Ti] -48 [% Zr] -49 [% V] +189 (1) [% C] indicates the content (% by mass) of carbon (C).
  • [% N] [% Ni] [% Cu] [% Mn] [% Cr] [% Si] [% Al] [% Mo] [% Nb] [% Sn] [% Ti] [% Zr] [% V] is N, Cu, Mn, Cr, Si, Al, Mo, Nb, Sn, Ti, Zr, V, respectively. Content (mass%). 0 when no element is contained.
  • a martensitic stainless steel plate for a disc brake rotor of a bicycle characterized by being 0.04% or less.
  • cold rolling with a total rolling reduction of 20 to 70% is performed once, or intermediate annealing is performed 2
  • the cold rolling rate of finish cold rolling should be 20% or more
  • the hardness of cold rolled products or products that have been annealed and pickled after cold rolling should be 220HV to 260HV.
  • a martensitic stainless steel plate for a disc brake rotor for a bicycle that is excellent in braking characteristics as a disc disc rotor for a bicycle, for example, excellent in braking force and squealing performance, and used for quenching.
  • the industrial effect is very large.
  • FIG. 1A is a diagram showing the relationship between C + N and Rockwell hardness
  • FIG. 1B is a diagram showing the relationship between C + N and bicycle braking performance and squeal. It is a graph which shows the influence of the reduction rate (rolling rate) of finish cold rolling which affects the Vickers hardness of the martensitic stainless steel cold-rolled product in this embodiment, and the droop at the time of press molding.
  • FIG. 2 (a) is a diagram showing the relationship between the reduction ratio of finish cold rolling and the steel sheet hardness (Vickers hardness), and FIG. 2 (b) is the reduction ratio of finish cold rolling and the amount of punched holes. It is a figure which shows the relationship. The relationship between the precipitation amount of undissolved carbide (precipitation Fe amount) and the rate of rusting in a salt spray test in a bicycle disc brake rotor manufactured from a martensitic stainless steel cold-rolled product in this embodiment is shown.
  • C 0.070 to 0.120%) C increases the hardness during quenching, increases the austenite phase fraction during quenching heating, and increases the amount of martensite after quenching.
  • 0.070% or more is required.
  • the content is set to 0.120% or less.
  • 0.070 to 0.100% preferably 0.080% to 0.100%, more preferably 0.080 to 0.090% Is preferred.
  • N 0.015-0.060%
  • N is a component that increases the hardness of martensite during quenching and gives a sufficient amount of martensite as a strong austenite former. Therefore, 0.015% or more is necessary.
  • the upper limit of the N content is set to 0.060% or less in order to form bubble defects during casting and impair the corrosion resistance. In order to stably obtain the target hardness, it is desirable that the lower limit is 0.018% and the upper limit is 0.045%. More desirably, the lower limit is 0.019% and the upper limit is 0.040%.
  • Si is an element that reduces the amount of martensite during quenching and lowers the toughness, so the upper limit was made 0.50%. However, it is an element preferable for deoxygenation during steelmaking and improvement of hot water flow during casting, and improves operability and surface quality. Therefore, the lower limit was made 0.10%. However, considering the reduction of raw material costs and the improvement of productivity by shortening the refining time, it is desirable that the lower limit is 0.20% and the upper limit is 0.40%. More desirably, the lower limit is 0.25% and the upper limit is 0.035%.
  • Mn 1.0-1.48%
  • Mn is an austenite former and increases the amount of martensite during quenching. Further, as an effect unique to Mn, non-metallic inclusions (MnS) are formed and the hot workability is improved. Furthermore, it has the effect of increasing the solubility of nitrogen in the molten steel, and when nitrogen is added in a large amount, it exhibits the effect of suppressing the formation of bubble defects. In addition, similarly to Si, it has an effect as a deoxidizing element during steelmaking. In order to obtain such effects, the Mn content is at least 1.0%.
  • the Mn content is set to 1.4% or less.
  • the lower limit is 1.1% and the upper limit is 1.3%. More desirably, the lower limit is 1.15% and the upper limit is 1.25%.
  • P 0.035% or less
  • P is an element having a large solid solution strengthening ability and a ferrite former. Moreover, since it is an element harmful to corrosion resistance and toughness, it is preferable that it be as small as possible.
  • P is contained as an impurity in ferrochrome, which is a raw material of stainless steel, but it is very difficult to remove P from molten stainless steel, so it is preferable to make it 0.010% or more.
  • the P content is almost determined by the purity and amount of the ferrochrome raw material to be used. Since P is a harmful element, the purity of P of the ferrochrome raw material is preferably low. However, since low P ferrochrome is expensive, it is limited to 0.035% or less, which is a range in which the material and corrosion resistance are not greatly deteriorated. . Note that the content is preferably limited to 0.030% or less.
  • the upper limit of the content is preferably small, and is limited to 0.015% or less. Further, the smaller the S content, the better the corrosion resistance. However, reducing the sulfur content increases the desulfurization load, increases the production cost, and CaS formed in the slag with strengthening of the desulfurization mixes in the steel and impairs the corrosion resistance. % Is preferable.
  • the upper limit is preferably 0.010%. More preferably, the upper limit is 0.008%.
  • Ni is an austenite former like Mn and Cu and increases the amount of martensite during quenching.
  • the allowable upper limit is set to 0.3%.
  • the lower limit is preferably made 0.01% or more. In consideration of improvement of toughness after quenching, 0.05 to 0.15% is desirable.
  • Cr In order to ensure the corrosion resistance required for the brake disc, Cr needs to be 11.5% or more. However, since it is a ferrite former, it is necessary to add an austenite former (Ni, Cu, Mn) according to the Cr amount to ensure the austenite phase fraction during quenching heating. However, there is a limit to the adjustment of the phase balance by the austenite former for various reasons as described above or below. Therefore, the upper limit of the Cr content is set to 13.5%. In consideration of manufacturability and high temperature ductility, it is desirable that the lower limit is 11.8% and the upper limit is 13.2%. More preferably, the lower limit is 12.0% and the upper limit is 13.0%.
  • Cu is an austenite former that increases the amount of martensite during quenching and increases hardness.
  • the lower limit is preferably made 0.01% or more. Considering the efficiency of component management during production, it is preferably 0.02 to 0.05%.
  • V is an element mixed as an inevitable impurity from the alloy raw material. Excessive reduction requires the use of high-purity raw materials and increases raw material costs, so the lower limit is desirably 0.01%. On the other hand, the excessive content lowers the hardness of martensite due to the formation of carbonitrides, so the upper limit is 0.3%. In order to suppress the squealing of the brake disc rotor that accompanies the formation of a large carbonitride, it is more desirable to make it 0.1% or less.
  • Al 0.001 to 0.010%
  • Al is a strong deoxidizing element and adjusts the slag basicity during refining to increase the desulfurization ability of slag. Since the effect is stably obtained from 0.001%, the lower limit is made 0.001%. On the other hand, excessive addition increases the basicity of the slag and causes the water-soluble inclusion CaS to crystallize, thereby greatly impairing the corrosion resistance. Therefore, the upper limit is made 0.010% or less. In order to stably obtain the deoxygenation ability at the time of refining, it is more desirable to make it 0.003% to 0.008%.
  • C and N are elements that control the hardness of martensite, and in order to obtain HRC 38 to 44, which is an indispensable hardness for obtaining a braking force necessary for a bicycle disc brake rotor, C + N is set to 0. 09% or more and 0.15% or less are necessary.
  • the lower limit of C + N is 0.095%
  • the upper limit is 0.13%
  • more preferably the lower limit is 0.10% to 0.12%.
  • the content is preferably 0.11% to 0.13%.
  • ⁇ p 80 to 120 which is an index indicating the phase balance during hot rolling heating
  • the following formula (1) of ⁇ p is an index representing the quenching heating temperature and the phase balance during hot rolling heating for producing the material.
  • ⁇ p is set to 80 or more, preferably 85 or more. More preferably 90 or more.
  • the upper limit of ⁇ p is 120 or less, preferably 110 or less. More preferably, it is good to be 105 or less.
  • ⁇ p 420 [% C] +470 [% N] +23 [% Ni] +9 [% Cu] +7 [% Mn] -11.5 [% Cr] -11.5 [% Si] -52 [% Al] -12 [% Mo] -47 [% Nb] -7 [% Sn] -49 [% Ti] -48 [% Zr] -49 [% V] +189 (1)
  • the component described in the above formula means mass% of the component contained in the steel.
  • ⁇ p equation (1) is an index indicating the maximum value of the amount of austenite generated during heating at 1100 ° C., “Metal Treatment” 1964, p. This is an improvement of the Castro equation introduced in the documents 230 to 245, and is a well-known equation as an empirical equation for estimating the maximum phase fraction of the ⁇ phase.
  • Mo 0.05 to 0.5%
  • Sn 0.003 to 0.5%
  • Nb 0.03 to 0.15%
  • Ti 0.05 % Or less
  • Zr 0.05% or less
  • B 0.0005 to 0.0030%
  • a high-purity raw material is preferably used to limit the upper limit.
  • Mo 0.05-0.5%)
  • Mo may be added as necessary to enhance corrosion resistance, and the lower limit is preferably made 0.05% in order to exert its effect.
  • Mo is a ferrite former like Cr, and excessive addition reduces the austenite fraction at the time of quenching heating and lowers the quenching hardness, so is 0.5% or less.
  • it is an expensive element, and 0.1% to 0.3% is desirable in order to exhibit an effect of improving corrosion resistance commensurate with the addition and to suppress an increase in raw material cost.
  • Sn may be added as necessary to enhance the corrosion resistance, and in order to exert its effect, the lower limit is made 0.003%, preferably 0.03%.
  • Sn is a ferrite former like Cr and Mo, and excessive addition reduces the austenite fraction during quenching heating and lowers the quenching hardness, so is 0.5% or less.
  • 0.01% to 0.3% is desirable in order to exhibit an effect of improving corrosion resistance commensurate with the addition and to suppress an increase in raw material cost.
  • Nb 0.03-0.15%
  • the lower limit is preferably 0.03%.
  • the upper limit is made 0.15%.
  • 0.05 to 0.10% is more preferable.
  • the upper limit is preferably 0.05% or less.
  • the lower limit is preferably made 0.0005%.
  • Zr is preferably precipitated as hard coarse nitride ZrN so as to promote the squealing of the brake disc rotor
  • the upper limit is preferably set as necessary.
  • the upper limit is preferably 0.05% or less.
  • the lower limit is preferably made 0.0005%.
  • B (B: 0.0005% to 0.0030%) B may be added as necessary in order to improve the hot ductility during hot rolling and to reduce the yield reduction due to the ear cracks of the hot-rolled sheet, and in order to exert its effect, the lower limit is 0. .0005% or more is desirable. However, excessive addition impairs toughness and corrosion resistance due to precipitation of Cr2B and (Cr, Fe) 23 (C, B) 6, so the upper limit is made 0.0030%. In view of workability and manufacturing cost, 0.0008 to 0.0015% is more desirable.
  • the amount of precipitation of undissolved carbide is 0.04% or less as the amount of Fe
  • the amount of undissolved carbide in the martensite phase after quenching is preferably controlled to 0.04% or less as the amount of Fe precipitated as carbide.
  • the amount of solid solution C increases as the amount of undissolved carbide [(FeCr) 23 C 6 ] after quenching increases and the hardness of martensite increases. Further, it is preferable because it is possible to suppress a decrease in corrosion resistance due to sensitization accompanying carbide precipitation (sensitivity of stainless steel to intergranular corrosion due to precipitation of carbide at the grain boundary). In order to acquire the effect, 0.04% or less is desirable as the precipitation amount of Fe as a carbide. In order to measure the amount of Fe precipitated as carbide, a constant potential electrolytic etching method (SPEED method) using a non-aqueous solvent electrolyte was used.
  • SPEED method constant potential electrolytic etching method
  • the temperature range of 800 to 600 ° C. is preferably 0.3 ° C./s or more, preferably May be cooled at a cooling rate of 3 ° C./s or more, more preferably 10 ° C./s or more.
  • the manufacturing method of the martensitic stainless steel sheet according to the present embodiment is the method of manufacturing the martensitic stainless steel having the above steel composition, and after hot rolling the cast steel piece (slab) after steelmaking. Then, hot-rolled sheet annealing is performed, and after pickling, cold rolling is performed. In the cold rolling step, intermediate annealing-pickling and finish annealing-pickling are performed as necessary.
  • a smelting method is preferred in which the steel containing the essential components and components added as necessary is refined in a converter and subsequently subjected to secondary refining.
  • the molten steel is made into a slab according to a known casting method (continuous casting).
  • this slab is heated to a predetermined temperature and hot-rolled to a predetermined plate thickness to obtain a hot-rolled steel sheet (hot-rolled sheet).
  • the finish rolling finish temperature of hot rolling is in the range of 800 to 950 ° C.
  • the hot rolled steel sheet is wound into a coil. Cooling up to the winding is preferably performed by air cooling so that the winding temperature is in the range of 700 to 900 ° C.
  • a hot-rolled steel sheet is hard as it is hot-rolled and is difficult to cold-roll, it is annealed in, for example, a batch-type annealing furnace.
  • the annealing temperature is set to 800 to 900 ° C., and after the coldest point exceeds 800 ° C., annealing is performed for 1 to 10 hours, then cooled in the annealing furnace for a certain time, and then transferred to the outside of the furnace. Cool to room temperature.
  • the coldest point means a part where the temperature is most unlikely to rise in an object to be heated in a batch-type annealing furnace.
  • a hot-rolled coil the part that is in contact with the furnace bottom at the central part in the longitudinal direction of the coil is shown.
  • the surface oxide scale is removed by mechanical descaling such as shot blasting and chemical descaling with acid, and then cold rolling is performed to obtain a cold rolled product.
  • the cold rolling ratio of the cold rolled product is adjusted so that the hardness becomes 220 to 260 HV.
  • the annealing temperature at this time is preferably in the range of 650 to 750 ° C.
  • intermediate annealing and pickling are performed during cold rolling, but even in this case, the hardness can be adjusted by controlling the cold rolling rate of finish cold rolling. is there.
  • Intermediate annealing is performed in consideration of the capability of the cold rolling mill, because the hardness increases due to work hardening when the total cold rolling reduction ratio increases, but depending on the capability of the cold rolling mill, intermediate annealing may be omitted. It is also possible to manufacture by one cold rolling. Intermediate annealing also has the effect of increasing the thickness accuracy.
  • the total cold rolling rate of cold rolling performed once or twice is set to 20 to 70%, and the cold rolling rate of finish cold rolling is 20% or more.
  • the hardness of the cold-rolled product or the cold-rolled-annealed-pickled product is 220 HV to 260 HV.
  • the cold rolling is performed once or twice by appropriately selecting the thickness of the hot rolled sheet and the thickness of the product.
  • cold rolling may be performed twice.
  • the cold rolling of 1 time or 2 times can be selected suitably according to the installation and production amount to be used.
  • the cold-rolled product means a product that is shipped as cold-rolled, and is generally called a hard material.
  • the pickled product means a product finished by annealing and pickling after cold rolling (finish is 2D or 2B finish, see JIS G4305).
  • the hardness of the product can be controlled either by controlling the hardness by work hardening during cold rolling or by controlling the hardness at the annealing temperature.
  • the thickness accuracy of the product is improved, and it is possible to increase the thickness accuracy when press-molding into the shape of the disc brake rotor.
  • the improvement of the plate thickness accuracy can increase the working efficiency in the polishing process after quenching. Excessively increasing the cold rolling rate decreases productivity, so the total cold rolling rate is set to 70% or less.
  • the hardness of the cold-rolled sheet, or cold rolling, annealing, and pickling sheet be 220 to 260 HV.
  • the dimensional accuracy at the time of press forming is evaluated by the amount of sheared surface at the time of press forming (punching).
  • the cold rolling rate of finish cold rolling As a method for setting the hardness to 220 HV or higher, it is possible to set the cold rolling rate of finish cold rolling to 20% or higher, or by combining cold rolling and annealing at a cold rolling rate of 20% or higher. However, if the hardness is excessively high, the wear of the mold is accelerated, so 260 HV or less. Further, the finish cold rolling reduction ratio is preferably 60% or less.
  • the annealing for controlling the hardness is preferably performed, for example, in the range of 650 to 780 ° C. and in the range of 10 to 120 seconds.
  • the hot rolling temperature was set to 850 ° C. and hot rolling was performed to a plate thickness of 4 mm. .
  • hot-rolled sheet annealing was performed at 850 degreeC for 4 hours, and it cooled slowly to normal temperature in the furnace.
  • the hot-rolled steel sheet was shot blasted, washed with sulfuric acid, descaled, and then cold-rolled to obtain a cold-rolled product having a thickness of 1.8 mm.
  • the product was press-molded into a disc brake rotor shape for bicycles, then subjected to quenching treatment and surface polishing to obtain a disc brake rotor.
  • the hardness after quenching was measured with a Rockwell hardness meter.
  • the braking performance of the disc brake was evaluated in an actual vehicle running test, and the braking performance and squeal characteristics were rated in three stages.
  • the evaluation of braking performance is based on the braking performance test specified in JIS D9301, when the braking distance at 25 km / h is the braking distance L0 when the rotor is new, the brake hydraulic pressure is 1.0 MPa, and the wheel rotational speed is 2 rps.
  • Ratio of L0 and LB, L0 / LB is less than 0.7 x (failed), 0.7 or more and less than 0.9 ⁇ (failed), 0.9 or more ⁇ (pass level is excellent Was).
  • the evaluation of squeal is x (failure) when you can hear a squeal in a 45 dB environment at a brake hydraulic pressure of 1.0 MPa and a wheel speed of 2 rps. (Between and excellent ones), the interval between them was marked as ⁇ (failed).
  • the hardness after quenching is 38 HRC or more, and the braking force is increased. It can also be seen that when C + N exceeds 0.015%, the hardness becomes 44 HRC or more and squeal occurs. In the present invention, the hardness after quenching is aimed at 38 to 44 HRC.
  • the steel composition of the martensitic stainless steel used for investigating the relationship shown in FIG. 1 is 12.3% Cr, 0.3% Si, 1.1% Mn, 0.04% to 0.14%. C, 0.02% N, 0.027% P, 0.008% S, 0.2% Ni, 0.02% Cu, 0.04% V, 0.008% Al.
  • the martensitic stainless steel according to this embodiment was cast into a steel ingot, and then hot rolled to a plate thickness of 5 mm at a finish hot rolling temperature of 850 ° C. Then, after winding up at 780 degreeC, hot-rolled sheet annealing was performed at 850 degreeC for 4 hours, and it cooled slowly to normal temperature in the furnace. The hot rolled steel sheet was shot blasted, washed with sulfuric acid and descaled, and then the surface was ground to 1.8 to 5.0 mm. Subsequently, a cold rolled product having a thickness of 1.8 mm was obtained by cold rolling. The surface hardness of the product was measured with a Rockwell hardness meter.
  • the product was pressed into a disc brake rotor shape for bicycles, and the amount of dripping in the press holes was measured.
  • the amount of drool After performing a press test with a punch outer diameter of 18 mm, a die inner diameter of 19 mm, a clearance of 0.5 mm and a punching speed of 700 mm / min, the height of the person is measured over the circumference and the average is obtained. It was. An average height of 100 ⁇ m or more was evaluated as x (failed), 50 ⁇ m or more and less than 100 ⁇ m was evaluated as ⁇ (failed), and less than 50 ⁇ m was evaluated as ⁇ (acceptable level and excellent).
  • the steel composition of the martensitic stainless steel used to investigate the relationship shown in FIG. 2 is 12.3% Cr, 0.3% Si, 1.1% Mn, 0.08% C, 0.02. % N, 0.026% P, 0.008% S, 0.2% Ni, 0.02% Cu, 0.04% V, 0.003% Al.
  • the martensitic stainless steel according to the present embodiment was cast into a steel ingot, and then hot rolled to a plate thickness of 4 mm at a finish hot rolling temperature of 850 ° C. Then, after winding up at 780 degreeC, hot-rolled sheet annealing was performed at 850 degreeC for 4 hours, and it cooled slowly to normal temperature in the furnace. The hot-rolled steel sheet was shot blasted, pickled with sulfuric acid, descaled, and then cold-rolled to obtain a cold-rolled product having a thickness of 1.8 mm.
  • the product was press-molded into a disc brake rotor shape for bicycles, then subjected to quenching treatment at various heating temperatures, times and cooling rates, and surface polishing was performed to obtain a disc brake rotor.
  • a 20 ⁇ 30 mm plate was cut out from the disc brake rotor, and the entire surface was polished with sandpaper No. 600, and then the precipitate was extracted by the SPEED method, and the extracted precipitate was chemically analyzed to obtain Fe in the precipitation.
  • the amount of Cr was measured.
  • the corrosion resistance of the disc brake was rated by the rust area ratio after a 24-hour salt spray test.
  • the salt spray test was conducted according to JIS Z2371.
  • the area ratio of the rust was less than 10% (excellent at an acceptable level), 10% or more and less than 30% was evaluated as ⁇ (failed), and 30% or more was evaluated as x (failed).
  • the steel composition of the martensitic stainless steel used for investigating the relationship shown in FIG. 3 is 13.1% Cr, 0.3% Si, 1.4% Mn, 0.2Ni, 0.085% C. 0.015% N, 0.017% P, 0.003% S, 0.1% Ni, 0.2% Cu, 0.01% V, 0.01% Al.
  • the quenching hardness can be 38 HRC to 44 HRC. As a result, it is possible to achieve the braking performance and noise reduction necessary for a disc brake rotor of a bicycle.
  • the method for producing martensitic stainless steel according to the present invention by optimizing the cold rolling rate and controlling the hardness before press forming, it becomes possible to reduce dripping during press forming and quenching.
  • the amount of subsequent polishing can be reduced. Further, productivity can be improved, for example, the polishing load can be leveled.
  • the heating temperature range is 800 ° C. or higher, preferably 950 ° C. or higher, more preferably 1000 ° C. or higher and 1100 ° C. or lower, the holding time is 1 second to 20 minutes, and the cooling rate is 0.1 to 1000 ° C./s. This should be done under the following conditions.
  • the cooling rate in the case of a vacuum furnace, can be 0.1 to 10 ° C./s at 800 to 1100 ° C. (heating temperature) ⁇ 1 second to 20 minutes (holding time). In a continuous annealing furnace, the cooling rate can be 0.5 to 70 ° C./s at 800 to 1100 ° C. (heating temperature) ⁇ 1 to 600 seconds (holding time), or oil cooling, water cooling, or mold quenching.
  • the martensitic stainless steel disc brake rotor according to the present invention can increase the corrosion resistance by controlling the amount of undissolved carbide [(FeCr) 23 C 6 ], and can add value other than brake performance. Can be increased.
  • steel having the composition shown in Tables 1 and 2 (the balance is Fe and inevitable impurities) was melted and cast into a slab.
  • Tables 1 and 2 examples satisfying the present invention regarding the components are examples of the present invention.
  • steel material No. 28, 37 to 41, 28-2, 37-2, 39-2 the content of the selective element (Mo, Sn, Nb, B, Ti) exceeds the inevitable impurity level, and the content of the selective element The upper limit of the amount is also exceeded.
  • This slab was heated to 1230 ° C., then the finish temperature was in the range of 800 to 950 ° C., hot rolled to a plate thickness of 2.5 to 5.0 mm, and wound at 780 ° C. to obtain a hot rolled steel strip.
  • the hot-rolled steel sheet was annealed at 850 ° C. for 4 hours, and then slowly cooled in the furnace.
  • the hot-rolled annealed plate was shot blasted and washed with sulfuric acid to remove scale.
  • Cold rolling was performed to obtain a 1.8 mm cold rolled product.
  • some materials were subjected to intermediate annealing at 750 ° C. and pickling.
  • some materials were subjected to finish annealing at 700 ° C. after cold rolling and pickling.
  • a bicycle disc brake rotor was press-molded from cold-rolled products and cold-rolled annealed pickled products. The punched holes were measured and ranked by comparative evaluation. Furthermore, after quenching under various conditions shown in Tables 3 and 4 and polishing the surface, incidental parts were attached to form a disc brake rotor for a bicycle. Brake characteristics were evaluated by actual vehicle running tests. The braking characteristics were evaluated as braking force and squeal. Further, the corrosion resistance of the disc brake rotor was evaluated in a salt spray test for 24 hours. The salt spray test was conducted according to JIS Z2371. The above-described methods were used for these evaluation test methods and scoring.
  • Tables 3 and 4 show the above manufacturing conditions and evaluation results.
  • the final annealing temperature was (1) 600 to 700 ° C and (2) 700 to 800 ° C.
  • the martensitic stainless steel cold-rolled excellent in brake characteristics after quenching required for a bicycle disc brake rotor, and also in corrosion resistance and press formability. Products, cold rolled-annealed-pickled products can be obtained.
  • Test No. 33 No. No. 84 was inadequate in quenching conditions (the quenching heating time was short and the cooling rate was slow, that is, cooling at 0.5 ° C./s after heating at 1030 ° C. for 1 second), resulting in an increase in the amount of precipitated Fe and quenching The hardness became low. For this reason, brake braking performance was lowered and corrosion resistance was also lowered. No. No. 34 had a low C content, so the quenching hardness was low and the brake braking performance was lowered. No. Since 85 had a high C content, the quenching hardness was too high, and the squeal characteristics deteriorated. No.
  • the steel composition and manufacturing method of martensitic stainless steel of the present invention it becomes possible to improve the brake performance of the disc brake rotor of the bicycle, and the disc brake of the bicycle.
  • productivity can be improved, and added value such as corrosion resistance of the disc brake rotor can be improved. That is, the present invention has sufficient industrial utility value.

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