EP1403394A1 - Biegefestes Strukturbauteil aus rostfreiem Stahl für ein Zweiradfahrzeug - Google Patents

Biegefestes Strukturbauteil aus rostfreiem Stahl für ein Zweiradfahrzeug Download PDF

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Publication number
EP1403394A1
EP1403394A1 EP20030021820 EP03021820A EP1403394A1 EP 1403394 A1 EP1403394 A1 EP 1403394A1 EP 20030021820 EP20030021820 EP 20030021820 EP 03021820 A EP03021820 A EP 03021820A EP 1403394 A1 EP1403394 A1 EP 1403394A1
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EP
European Patent Office
Prior art keywords
mass
martensite
stainless steel
phase
resistance
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Withdrawn
Application number
EP20030021820
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English (en)
French (fr)
Inventor
Kouki Tomimura
Hiroshi Fujimoto
Kenichi Morimoto
Naoto Hiramatsu
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Nippon Steel Nisshin Co Ltd
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Nisshin Steel Co Ltd
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Publication date
Application filed by Nisshin Steel Co Ltd filed Critical Nisshin Steel Co Ltd
Publication of EP1403394A1 publication Critical patent/EP1403394A1/de
Withdrawn legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—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
    • C22C38/18—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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium

Definitions

  • the present invention relates to stainless steel-made structural members, excellent in corrosion resistance at welded heat-affected zones and deflection-resistance, of two-wheeled vehicles such as bicycles, motorcycles and wheelchairs.
  • Tire rims and frames of two-wheeled vehicles such as bicycles, motorcycles and wheelchairs are often exposed to a corrosive atmosphere.
  • material for such structural members have been changed from galvanized steel sheets to ferritic stainless steel sheets, e.g. SUS304.
  • the material shall be also good of weldability, since the structural . members are usually fabricated by welding.
  • JP61-73866A proposes a 10-20 mass % Cr-ferritic stainless steel improved in toughness, ductility and corrosion-resistance even at a welded part without buckling during welding by addition both of Ti and Nb at ratios of 0.1 ⁇ 0.3 mass % and 0.15-0.3 mass %, respectively.
  • the proposed stainless steel has the disadvantage that titanium inclusions often cause Ti streaks, due to addition of Ti at a high ratio.
  • JP62-164857A proposes another ferritic stainless steel for use as a tire rim member, wherein an austenite former(s), e.g. Ni, Mn or Cu, is added at a proper ratio to 12.5-17 mass % Cr-ferritic stainless steel with reduction of C and N contents so as to improve intergranular corrosion-resistance at a welded part without necessity of a stabilizing element such as Ti or Nb for toughness and workability. Control of a value-CE within a predetermined range is also reported for generation of a martensite phase. But, the stainless steel has poor strength regardless generation of martensite due to reduction of C and N contents to 0.04 mass % or less in total.
  • the steel may be strengthened by addition of alloying elements, but addition of the alloying elements raises steel costs.
  • the present invention aims at provision of cheap structural members such as tire rims and frames of two-wheeled vehicles, e.g. bicycles, motorcycles and wheelchairs, made of a stainless steel sheet or pipe improved in weldability, strength and deflection-resistance as well as corrosion-resistance at both of a welded heat-affected zone and a base metal part.
  • the present invention proposes a structural member made of a ferrite/martensite dual-phase stainless steel sheet.
  • a stainless steel for the purpose has a chemical composition consisting of C up to 0.04 mass %, Si up to 2.0 mass %, Mn up to 2.0 mass %, 10.0-20.0 mass % of Cr, Ni up to 4.0 mass %, Cu up to 3.0 mass %, N up to 0.12 mass %, optionally one or more of B up to 0.015 mass %, Mo up to 3.0 mass %, Ti up to 0.10 mass %, Nb up to 0.40 mass % and V up to 0.30 mass %, and the balance being Fe except inevitable impurities.
  • Tire rim members are usually fabricated from a stainless steel sheet, while frame members are usually fabricated from a stainless steel pipe. In any case, surface hardness of the stainless steel sheet or pipe is adjusted to HV 270 or more except welded parts.
  • the stainless steel sheet for use as the structural members is manufactured as follows: A steel strip having the specified composition is cold-rolled and then dual-phase annealed in a continuous annealing furnace. The dual-phase annealing is performed as finish heat-treatment by heating the steel strip at 850-1100°C in a ferrite/martensite dual-phase zone and then cooling the heated steel strip.
  • the inventors have researched and examined properties of stainless steel sheets necessary for structural members of two-wheeled vehicles, e.g. bicycles, motor cycles and wheelchairs, especially corrosion-resistance at a welded heat-affected zone and deflection-resistance from various aspects.
  • the following explanation is directed to members of bicycles, but the same properties are of course necessary for members of motorcycles and wheelchairs.
  • Main structural members of a bicycle are tire rims and frames. These members shall keep original shapes without strains, in order to stabilize a bicycling position.
  • Tire rims which come near surfaces of roads during bicycling, are exposed to a corrosive atmosphere, and also subjected to friction with a rubber brake. Pebbles or the like knock against the tire rims and frames. Accounting these practical conditions, the tire rims and frames shall have properties good of rigidity, corrosion-resistance, abrasion-resistance and dent-resistance.
  • Rigidity is improved by hardening the stainless steel at Vickers hardness of 270 or more and grain-refining a ferrite/martensite dual-phase so as to raise Young's modulus. Generation of martensite phase results in increase of strength and improvement of dent- and corrosion-resistance.
  • a stainless steel sheet When a stainless steel sheet is welded, it is heated up to 600-900°C with a welding heat. In such a high temperature zone, chromium carbonitride precipitates from a steel matrix and causes Cr-depleted zones in return. The Cr-depleted zones unfavorably accelerate sensitization and degrade corrosion-resistance.
  • Ferrite and martensite phases are of b.c.c. (body-centered-cubic) crystalline structure, wherein C and N are not substantially dissolved and carbonitride is likely to precipitate due to diffusion rates faster than an austenite phase of f.c.c. (face-centered-cubic) crystalline structure.
  • the martensite phase reverse-transforms to an austenite phase, wherein fairly large amounts of C and N are dissolved as compared with the ferrite or martensite phase, at a high temperature.
  • Carbonitride which has once precipitated in the ferrite or martensite phase, dissolves again in the austenite phase during reverse-transformation.
  • Precipitation of carbonitride which causes Cr-depleted zones and degrades sensitivity, is also avoided by rapidly heating the stainless steel to a high-temperature austenite zone so as to complete reverse-transformation in a short time.
  • Completion of reverse-transformation before precipitation of carbonitride is well explained by a kinetic theory. That is, when a stainless steel is heated up to the austenite zone, it passes through a temperature zone, wherein carbonitride precipitates in a ferrite or martensite phase, in a heating step, but precipitation of carbonitride begins after a certain incubation period.
  • the behaviors of C and N atoms during reverse-transformation means that sensitization is accelerated as increase of C and N contents, but suppressed as increase of a ratio of reverse-transformed martensite (in other words, a ratio of reverse-transformable martensite at a room temperature) in a dual-phase annealed state.
  • a ratio of reverse-transformable martensite at a room temperature is controlled in a specified relationship with C and N contents for dissolution of C and N atoms in the reverse-transformed austenite at an elevated temperature, in order to inhibit precipitation of chromium carbide and generation of Cr-depleted zones.
  • a stainless steel for use as structural members such as tire rims and frames contains various alloying elements at predetermined ratios as follows:
  • One or more ferrite formers such as Al may be further added in addition to the above-mentioned elements under an alloying design for formation of a ferrite/martensite dual-phase structure at a room temperature.
  • One or more of Y, Ca and REM (rare earth metals) may be also added for improvement of corrosion-resistance and hot-workability, as far as strength of a stainless steel sheet is not reduced by addition of these elements.
  • the stainless steel sheet is further defined by a sensitizing index and surface hardness, as follows:
  • a sensitizing index St within a range of from -31 to -7
  • chromium carbide precipitates in a steel matrix. Precipitation of chromium carbide means generation of Cr-depleted zones, sensitization and degradation of corrosion-resistance in the end. Factors for promotion of sensitization are C and N contents, while a factor for suppression of sensitization is a ratio of reverse-transformed austenite in a dual-phase annealed state, i.e. a ratio ⁇ (vol. %) of reverse-transformable martensite at a room temperature. In short, a stainless steel is less sensitized but improved in corrosion-resistance by properly controlling a sensitizing index St, which represents relationship of a ratio of martensite at a room temperature with C and N contents.
  • a sensitizing index St less than -31 means reduction of C and N contents to levels insufficient for hardness of HV 270.
  • a preferable sensitizing index St is within a range of from -28 to -10.
  • a stainless steel sheet with the controlled ratio of martensite is manufactured by annealing a hot-rolled steel sheet 12 hours at 780°C, cooling it as such in an oven, cold-rolling it at a reduction ratio of 80%, annealing the cold-rolled steel sheet 1 hour at 950°C and then cooling it in the open air, for instance.
  • Hardness of a stainless steel sheet is controlled by C and N contents in addition to a ratio of martensite.
  • the stainless steel sheet necessarily has surface hardness of HV 270 or more (preferably HV 300 or more) at a part free from weld heat-affection, in order to provide light-weighed structural members good of spring elasticity. If surface hardness is less than HV 270, use of thick structural members is unavoidable for fabrication of two-wheeled vehicles, resulting in heavy products.
  • a ratio of martensite not less than 25 vol. % (preferably 40 vol. %) at a room temperature is necessary for surface hardness of HV 270 or more.
  • Such a ratio of martensite is also effective for imparting dent- and abrasion-resistance to structural members of two-wheeled vehicles.
  • Each dual-phase annealed steel sheet was observed by a microscope to detect martensite in a view of 200 ⁇ m ⁇ 200 ⁇ m along its thickness direction. Volume ratios of martensite were calculated in 10 views every steel sheet and averaged.
  • a test piece sampled from each dual-phase annealed steel sheet was plastically formed and TIG-welded for fabrication of a tire rim member with a shape shown in Fig. 1.
  • TIG-welding was performed by a butt welding without use of a welding wire under the conditions of:
  • a welded part was flattened by grinding weld beads and finished together with a base metal part by #400 abrasive paper.
  • test piece of 100 mm ⁇ 150mm in size was sampled from the welded and finished steel sheet and examined by CASS test (whereby a test piece was immersed in a (5% NaCl + 0.26 g/l CuCl 2 + acetic acid) solution of pH 3.0-3.1 at 35 ⁇ 2°C) regulated under JIS H8502. After 200 hours-CASS test, the test piece was observed to detect rusts at a welded heat-affected zone. Results were evaluated as follows and illustrated in Fig. 2.
  • a steel sheet is weakened less than HV 270 due to shortage of C and N.
  • Test pieces sampled from each stainless steel sheet were plastically formed to a tire rim with a shape shown in Fig. 1 and TIG-welded to a steel pipe of 30 mm in diameter. TIG-welding was performed with a welding current of 150 A and a torch travelling speed of 500mm/minute. A welded part was flattened by grinding weld beads and then finished together with a base metal part by #400 abrasive paper.
  • Deflection-resistance was evaluated as permanent strain by a flexure test, whereby a test body R of a height h o along a direction L was prepared as a half-sized shape (shown in Fig. 3) imitating a tire rim, a weight W of 50 kg loaded on the test body R and unloaded, and then a height h 1 of the test body R along the direction L was measured and compared with the original height ho to calculate the permanent strain. A value of permanent strain less than 1 mm was evaluated as good deflection-resistance ( ⁇ ).
  • any tire rim and any steel pipe made of the inventive steels had base metal hardness of HV 270 or more without occurrence of rusts at both of base metal and welded parts.
  • the tire rims had permanent strains suppressed less than 1mm.
  • Comparative Steels H to K had chemical compositions or sensitizing indexes St out of the ranges defined by the present invention.
  • Comparative Steels H and I contained excess C and excess C + N, respectively, so that their welded heat-affected zones were poor of corrosion-resistance.
  • Comparative Steel J Tire rims and steel pipes made of Comparative Steels J was not composed of martensite/ferrite dual-phase structure and poor of hardness. Permanent strains were fairly larger than 1 mm. Comparative Steel J was also poor of corrosion- and deflection-resistance due to insufficient Cr content. Comparative Steel K was poor of corrosion-resistance at its welded heat-affected zone due to its higher sensitizing index St. Degradation of corrosion-resistance proves progress of sensitization caused by a welding heat.
  • Comparative Steel L corresponding to SUS430LX, was poor of deflection-resistance.
  • a ratio of martensite which can be reverse-transformed to austenite during dual-phase annealing, is controlled in a specified relationship with C and N contents without reduction of C and N contents so much, in a ferrite/martensite dual-phase stainless steel sheet. Due to the specified relationship, tire rims and frames of two-wheeled vehicles made of the stainless steel sheet are excellent in both of corrosion-resistance and deflection-resistance without sensitization of a welded heat-affected zone.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
EP20030021820 2002-09-27 2003-09-26 Biegefestes Strukturbauteil aus rostfreiem Stahl für ein Zweiradfahrzeug Withdrawn EP1403394A1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2002283413 2002-09-27
JP2002283413A JP3920185B2 (ja) 2002-09-27 2002-09-27 耐たわみ性に優れたステンレス鋼製の二輪車用タイヤリム材および二輪車用フレーム材

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EP (1) EP1403394A1 (de)
JP (1) JP3920185B2 (de)
CN (1) CN1490184A (de)
TW (1) TWI275649B (de)

Cited By (3)

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WO2014036091A1 (en) * 2012-08-31 2014-03-06 Ak Steel Properties, Inc. Ferritic stainless steel with excellent oxidation resistance, good high temperature strength, and good formability
CN106834965A (zh) * 2017-01-05 2017-06-13 宝钢不锈钢有限公司 一种双相不锈钢中厚板及其制造方法
FR3047254A1 (fr) * 2016-02-02 2017-08-04 Vallourec Tubes France Composition d'aciers aux proprietes anti-cokage ameliorees

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CN100516274C (zh) * 2007-08-20 2009-07-22 江阴市江东不锈钢制造有限公司 03Cr22Ni4NbN奥氏体-铁素体类不锈钢及其生产工艺
EP2677054B1 (de) * 2011-02-14 2020-03-25 Nippon Steel Corporation Duplex-edelstahl-blech oder -rohr und herstellungsverfahren dafür
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US20150275340A1 (en) * 2014-04-01 2015-10-01 Ati Properties, Inc. Dual-phase stainless steel
JP6142837B2 (ja) * 2014-04-15 2017-06-07 Ｊｆｅスチール株式会社 フェライト相とマルテンサイト相の２相からなる組織を有するステンレス鋼
JP6093063B1 (ja) * 2016-03-09 2017-03-08 日新製鋼株式会社 加工性に優れた高強度ステンレス鋼材とその製造方法
CN109778080A (zh) * 2019-01-22 2019-05-21 宋鑫 一种超高强度超高低温冲击压裂泵泵头体
CN109778066A (zh) * 2019-01-22 2019-05-21 宋鑫 可延长泵头体使用寿命的泵头体生产方法
JP7618443B2 (ja) * 2020-12-24 2025-01-21 日鉄ステンレス株式会社 曲げ性に優れるフェライト－マルテンサイト複相ステンレス鋼およびその製造方法

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US4594115A (en) * 1984-07-04 1986-06-10 Ugine Aciers Process for the manufacture of rods or machine wire of martensitic stainless steel and the products which are produced
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