EP3783120A1 - Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort - Google Patents

Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort Download PDF

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Publication number
EP3783120A1
EP3783120A1 EP19193224.3A EP19193224A EP3783120A1 EP 3783120 A1 EP3783120 A1 EP 3783120A1 EP 19193224 A EP19193224 A EP 19193224A EP 3783120 A1 EP3783120 A1 EP 3783120A1
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EP
European Patent Office
Prior art keywords
spring wire
weight
content
steel
spring
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.)
Granted
Application number
EP19193224.3A
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German (de)
English (en)
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EP3783120B1 (fr
Inventor
Lei HU
Dennis Wolf
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Vossloh Fastening Systems GmbH
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Vossloh Fastening Systems GmbH
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority to PL19193224.3T priority Critical patent/PL3783120T3/pl
Application filed by Vossloh Fastening Systems GmbH filed Critical Vossloh Fastening Systems GmbH
Priority to FIEP19193224.3T priority patent/FI3783120T3/fi
Priority to EP19193224.3A priority patent/EP3783120B1/fr
Priority to ES19193224T priority patent/ES2963989T3/es
Priority to CN202080059418.3A priority patent/CN114341387B/zh
Priority to US17/636,964 priority patent/US20220275490A1/en
Priority to PCT/EP2020/072650 priority patent/WO2021037567A1/fr
Publication of EP3783120A1 publication Critical patent/EP3783120A1/fr
Application granted granted Critical
Publication of EP3783120B1 publication Critical patent/EP3783120B1/fr
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Classifications

    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
    • 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
    • C22C38/06—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
    • C22C38/24—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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D6/02—Hardening by precipitation

Definitions

  • the invention relates to a spring wire which is made of a spring steel with a carbon content of 0.35-0.42% by weight.
  • the invention relates to a tension clamp for holding down a rail for rail vehicles in a rail fastening point, which is formed from such a spring wire, and a method for producing a spring wire of the type in question here.
  • the respective rail to be fastened is fastened to the subsurface that carries the track to which the rail belongs.
  • the subsurface can be formed by a conventional threshold made of wood or by thresholds or plates that are formed from a concrete or a plastic material.
  • the rail fastening point typically comprises at least one guide plate which rests laterally on the rail and, during use, dissipates the transverse forces acting on the rail into the ground, and a tension clamp which is braced against the ground the tension clamps. With the end of at least one spring arm, the tension clamp exerts an elastically resilient hold-down force on the rail foot, by means of which the rail is held pressed against the ground.
  • the hold-down forces can be applied particularly effectively by means of W-shaped or ⁇ -shaped tension clamps that act on the rail foot with the free ends of their two spring arms.
  • tension clamps of this type are the products explained under URL https://www.vossloh.com/de/ effort-undloesungen/ etcfinder/ (found on August 12, 2019).
  • the spring wires that are required to produce tension clamps typically have a circular diameter of 9-15 mm.
  • the individual sections of a tension clamp are either predominantly subjected to bending or torsion loads, with more or less strong proportions of the other form of load being added to the respective dominating load.
  • the usual manufacturing route for their manufacture comprises the steps of "casting molten steel into bars”, “heating the bars through” and “hot rolling the bars to form a spring wire”, “cooling the hot-rolled spring wire” and “depositing or winding the spring wire into a coil”, wherein the hot rolling is usually carried out in several steps, which include pre-rolling, intermediate rolling and finish rolling of the slab to form the spring wire.
  • the work steps to be carried out and the influencing variables to be observed are known to the person skilled in the art (see, for example Steel Primer, 2015, Verlag Stahleisen GmbH, Düsseldorf, ISBN 978-3-514-00815-1 ) ..
  • the tension clamps are cold-formed from the spring wires produced in this way.
  • rods are cut to length from the spring wires, which are then usually bent in several steps to form the tension clamp. In this way it is possible to produce tension clamps with a complex shape.
  • the tension clamps obtained are then subjected to a heat treatment in which they are heated to a temperature above Ac3 and then quenched in order to optimize their mechanical properties by hardening.
  • the aim is to set high tensile strengths Rm and high yield strengths Rp0.2.
  • a ratio of Rm / Rp0.2 of ⁇ 1 is sought in order to be able to apply high resilient hold-down forces with the tension clamps on the one hand and to be able to Extend the range of elastic deformability of the tension clamp and the associated fatigue strength to a maximum.
  • the tensile strengths Rm and elongation limits Rp0.2 for tension clamps of the type in question are in the range of 1200-1400 MPa.
  • thermomechanical rolling In addition to the alloying measures, the mechanical properties of a spring wire provided for the production of spring elements can also be improved by so-called “thermomechanical rolling”.
  • thermomechanical rolling which is aimed in particular at spring wire, which is intended for the production of spring loaded springs, the spring wire is hot-rolled in a temperature range in which its structure has not yet completely recrystallized, but which is above the Ar3 temperature of the steel. In this way, spring wires with a particularly fine structure can be produced, which contributes to high strength and optimized spring behavior of the tension clamp ( DE 195 46 204 C1 ).
  • thermomechanical forming in particular on the treatment of spring wire, which is intended for the production of torsion-loaded springs, the rod-shaped starting material is heated to a temperature above at a rate of at least 50 K / s the recrystallization temperature and then reshaped at a temperature at which a dynamic and / or static recrystallization of the austenite results.
  • the austenite of the formed product recrystallized in this way is quenched and tempered ( DE 198 39 383 A1 ).
  • the task has been to create a spring wire which can be cold-formed well even with diameters of at least 9 mm, but which has improved mechanical properties.
  • a spring wire which achieves this object has at least the features specified in claim 1.
  • a tension clamp for holding down rails for rail vehicles in a rail fastening point which solves this task, is formed from a spring wire made according to the invention.
  • a method that achieves the above object comprises, according to the invention, at least the work steps and features specified in claim 14. It goes without saying that when carrying out the method according to the invention, the person skilled in the art not only completes the method steps mentioned in the claims and explained in detail here, but also carries out all other steps and activities that are necessary in the practical implementation of such methods in the prior art Technique should be carried out regularly when the need arises.
  • a spring wire according to the invention is accordingly produced from a steel which, in% by weight, C: 0.35 - 0.42%, Si: 1.5 - 1.8%, Mn: 0.5 - 0.8%, Cr: 0.05 - 0.25%, Nb: 0.020 - 0.10%, V: 0.020 - 0.10%, N: 0.0040 - 0.0120%, Al: ⁇ 0.03%, and the remainder consists of iron and unavoidable impurities, the content of the sum of impurities being limited to at most 0.2% and the impurities including up to 0.025% P and up to 0.025% S.
  • the alloy concept provided according to the invention for the spring wire is based on the fact that the tensile strength Rm and the yield strength Rp0.2 are increased by adding additional alloying elements. This makes it possible to keep the carbon content and the associated cold deformability of the spring wire at an optimally low level for practical processing, while at the same time increasing the strength Rm and yield strength Rp0.2 significantly compared to the prior art.
  • the individual Alloy components and their contents in the alloy of a spring wire according to the invention have been determined as follows: Carbon (“C”) is present in the spring steel of a spring wire according to the invention in contents of 0.35-0.42% by weight in order to have good deformability, high toughness, good corrosion resistance and low sensitivity to stress- or hydrogen-induced cracking to ensure. C contents of at most 0.40% by weight, in particular less than 0.40% by weight, have proven particularly useful in terms of optimized ductility and the associated optimized deformability at room temperature.
  • Si Silicon
  • the high Si content ensures good resistance ("relaxation resistance") against a decrease in the strength values of the spring wire in the course of the heat treatment which tension clamps formed from spring wire according to the invention regularly pass through after their cold forming.
  • This requires Si contents of at least 1.5% by weight.
  • too high Si contents would reduce the toughness, increase the risk of decarburization in the course of the heat treatment and also contribute to the formation of coarse grains. Therefore, according to the invention, the Si content is limited to 1.8% by weight.
  • Manganese is present in the steel of a spring wire according to the invention in contents of 0.5-0.8% by weight in order to ensure that the spring steel is sufficiently hardenable.
  • Mn binds the sulfur, which is usually unavoidable in steel production-related, to MnS and thus prevents its harmful effect.
  • at least 0.5% by weight, in particular at least 0.50% by weight, of Mn in the steel are required, with an optimized effect at contents of at least 0.6% by weight, in particular at least 0.60% by weight or at least 0.7% by weight. Too high Mn contents would, however, worsen the brittle-ductile transition temperature (Ductile-Brittle-Temperature "DBTT”), therefore the Mn content is at most 0.8% by weight, in particular 0.80% by weight, limited.
  • DBTT brittle-ductile transition temperature
  • Chromium is present in the spring steel of a spring wire according to the invention in contents of 0.05-0.25% in order to further improve the hardenability of the steel.
  • the presence of Cr in the steel according to the invention ensures that the structure of a tension clamp formed from a spring wire according to the invention consists of more than 95 area% of martensite after hardening.
  • a C content of at least 0.05% by weight can reduce the carbon activity and the risk of surface layer decarburization during heat treatment.
  • the positive effects of Cr in the spring steel of a spring wire according to the invention can be used particularly reliably in that a Cr content of at least 0.1% by weight, in particular at least 0.10% by weight or in particular at least 0.18% by weight. -%, is provided. If the Cr content is above 0.25% by weight, on the other hand, there is a risk that the toughness and relaxation resistance of the spring steel would be impaired.
  • Aluminum is not required in the steel according to the invention for deoxidation during steel production, but can optionally be added to the spring steel in contents of up to 0.03% by weight in order to support the development of a fine-grain structure.
  • higher Al contents would impair the purity of the steel of a steel according to the invention and, as a result, its toughness due to an excessive formation of Al oxides or nitrides.
  • Niobium is of particular importance for the invention and is present in the spring steel of a spring wire according to the invention in contents of 0.02-0.1% by weight. Nb retards recrystallization during an im Temperature range recrystallization stop temperature - Ar3 temperature of the spring steel performed thermomechanical rolling, by which a particularly fine-grain structure of the spring wire according to the invention is obtained. At the same time, the presence of Nb limits the grain growth when the spring wire according to the invention is heated to the austenitizing temperature and held there during the heat treatment of the tension clamp formed from it.
  • the Nb content of the spring steel of a spring wire according to the invention can be at least 0.0250% by weight, at least 0.0280% by weight or at least 0.030% by weight. Nb can be used particularly effectively at contents of up to 0.070% by weight, in particular up to 0.050% by weight.
  • Vanadium is present in the spring steel of a spring wire according to the invention in contents of 0.020-0.10% by weight.
  • V forms carbides and nitrides with carbon and nitrogen, which are typically present as fine, for example 8-12 nm, in particular about 10 nm, carbonitride precipitates and, through precipitation hardening, contribute significantly to increasing the strength of a spring wire according to the invention.
  • V contributes in this way to the relaxation resistance of the spring steel from which a spring wire according to the invention is made.
  • the V content of the spring steel of a spring wire according to the invention can be at least 0.0250% by weight, at least 0.0280% by weight or at least 0.030% by weight.
  • V can be used particularly effectively at contents of up to 0.070% by weight, in particular up to 0.060% by weight.
  • Nb and V according to the invention results in high tensile strengths Rm and regularly approximately the same high Elongation limits Rp0.2, so that in a tension clamp made from spring wire according to the invention, the ratio Rm / Rp0.2 is regularly in the range of 1 - 1.2, which is optimal for its service life and spring behavior.
  • N Nitrogen
  • contents of 0.0040-0.0120% by weight (40-120 ppm) to enable the formation of vanadium nitrides or vanadium carbonitrides.
  • Excessively high N contents would, however, favor the stretching aging of the spring wire according to the invention, which would be diametrically opposed to the toughness of the spring wire according to the invention and the fatigue strength required by a tension clamp.
  • Negative effects of the presence of N in the spring steel of a spring wire according to the invention can be excluded particularly reliably by limiting the N content to a maximum of 0.0100% by weight (100 ppm).
  • tension clamps according to the invention ready for installation in a rail fastening point, regularly have a fineness of their structure which, determined according to ASTM E112, corresponds to at least ASTM 8. This corresponds to an improvement in the fineness of at least one of the granularity classes specified in ASTM E112 compared to a tension clamp, which is bent from a spring wire made from conventional 38Si7 steel.
  • the spring wire is thus subjected to a thermomechanical rolling step in the course of hot rolling, in which it is rolled at temperatures which are rolled below the recrystallization stop temperature and above the Ar3 temperature of the steel.
  • the “recrystallization stop temperature” is the temperature at which the spring wire has cooled down to such an extent that its previously austenitic structure no longer recrystallizes. Due to the thermomechanical rolling carried out in the temperature range specified according to the invention in combination with the alloy selected according to the invention, in particular due to the simultaneous presence of Nb and V, the particularly fine-grain structure is obtained, which characterizes a spring wire according to the invention in the hot-rolled state.
  • the cooling of the hot-rolled spring wire at the cooling speeds specified according to the invention and compliance with the winding temperatures of 550-650 ° C prescribed according to the invention ensure that a maximum hardness of the spring wire according to the invention is achieved as a result of precipitation hardening.
  • the “thermomechanical rolling” partial hot rolling step in a separate operation, which is carried out after the actual hot rolling of the spring wire.
  • the spring wire which is then hot-rolled, is first heated to austenitizing temperature, then cooled to a temperature below the recrystallization stop temperature but above the Ar3 temperature of the spring steel and hot-rolled at this temperature with a sufficient degree of deformation. This is followed by cooling and the laying down or winding of the spring wire as indicated in steps d) and e) of the method according to the invention.
  • a technologically and economically optimized variant of the method according to the invention provides that all partial steps of the Hot rolling (work step c)) can be completed in a continuous cycle, so that a thermomechanically finished hot-rolled spring wire is present when the spring wire leaves the hot-rolling section used.
  • a comparative melt V1 was melted, the C, Si, Mn, P, S and N contents of which corresponded to the requirements applicable to the known 38Si7 steel, but which also had an effective content of Cr.
  • the composition of the comparative melt C1 is also given in Table 1.
  • the recrystallization stop temperature of the respective spring steel, from which the respective spring wire E1-E5, V1 is produced can be determined experimentally in a manner known per se or can be estimated with the aid of empirically determined formulas.
  • the Ar3 and Ar1 temperatures of the respective spring steel from which the respective spring wire E1-E5, V1 is produced can be determined experimentally in a manner known per se, for example by means of dilatometry in a thermomechanical simulator.
  • the hot-rolled spring wires obtained were cooled at a cooling rate of 1-5 ° C./s to a winding temperature of 550-650 ° C., at which they were wound into a coil.
  • the spring wires in the coil were then cooled to room temperature.
  • rods were cut to length, which, after pickling and straightening carried out in a conventional manner, were bent in several cold stages, i.e. at room temperature, to a conventionally shaped, ⁇ -shaped tension clamp .
  • the tension clamps obtained were subjected to a heat treatment in which they were heated through to an austenitizing temperature of 850-950 ° C. so that their structure was completely austenitic.
  • the tension clamps that were austenitized in this way were then quenched in water so that their structure was martensitic to more than 95% by area.
  • the tension clamps After quenching, the tension clamps have undergone a tempering process during which they are brought to a temperature of 400 - 450 ° C over a period of 60 - 120 minutes the tempering temperature has been heated and held there. The tension clamps, which had been tempered in this way, were then cooled to room temperature in air.
  • the tensile strength Rm and the yield strength Rp0.2 were determined in accordance with DIN EN ISO 6892-1.
  • the impact energy KV-20 has been determined as a characteristic value for toughness.
  • the measured values obtained are listed in Table 2. It was found that not only the tensile strength Rm and the yield strength Rp0.2 of the tensioning clamps produced from spring steel E1 composed according to the invention in the manner according to the invention could be increased significantly with unchanged impact work KV-20 compared to the tensioning clamps made from the comparative steel V1, but also that the ratio Rm / Rp0.2 has also remained practically the same.
  • the tension clamps produced from the spring steels E1-E5 according to the invention had a significantly better fine-grain "ASTM" structure, determined in accordance with ASTM E112, than the tension clamps made from the comparative steel V1.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Springs (AREA)
EP19193224.3A 2019-08-23 2019-08-23 Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort Active EP3783120B1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
FIEP19193224.3T FI3783120T3 (fi) 2019-08-23 2019-08-23 Jousilanka, siitä muodostettu puristin ja menetelmä tällaisen jousilangan valmistamiseksi
EP19193224.3A EP3783120B1 (fr) 2019-08-23 2019-08-23 Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort
ES19193224T ES2963989T3 (es) 2019-08-23 2019-08-23 Alambre de resorte, pinza de sujeción formada a partir del mismo y procedimiento para producir un alambre de resorte de este tipo
PL19193224.3T PL3783120T3 (pl) 2019-08-23 2019-08-23 Drut sprężynowy, zacisk napinający uformowany z niego i sposób wytwarzania takiego drutu sprężynowego
CN202080059418.3A CN114341387B (zh) 2019-08-23 2020-08-12 张力夹以及生产这种张力夹的方法
US17/636,964 US20220275490A1 (en) 2019-08-23 2020-08-12 Spring Wire, Tension Clamp Formed Therefrom and Method for Manufacturing Such a Spring Wire
PCT/EP2020/072650 WO2021037567A1 (fr) 2019-08-23 2020-08-12 Serpentin, pince d'amarrage formée à partir de ce dernier et procédé de production d'un tel serpentin

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP19193224.3A EP3783120B1 (fr) 2019-08-23 2019-08-23 Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort

Publications (2)

Publication Number Publication Date
EP3783120A1 true EP3783120A1 (fr) 2021-02-24
EP3783120B1 EP3783120B1 (fr) 2023-09-27

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EP19193224.3A Active EP3783120B1 (fr) 2019-08-23 2019-08-23 Fil de ressort, pince de serrage formée à partir dudit fil de ressort et procédé de fabrication d'un tel fil de ressort

Country Status (7)

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US (1) US20220275490A1 (fr)
EP (1) EP3783120B1 (fr)
CN (1) CN114341387B (fr)
ES (1) ES2963989T3 (fr)
FI (1) FI3783120T3 (fr)
PL (1) PL3783120T3 (fr)
WO (1) WO2021037567A1 (fr)

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19546204C1 (de) 1995-12-11 1997-03-20 Max Planck Inst Eisenforschung Verfahren zur Herstellung von hochfesten Gegenständen aus einem Vergütungsstahl und Anwendung dieses Verfahrens zur Erzeugung von Federn
DE19839383A1 (de) 1998-07-20 2000-01-27 Muhr & Bender Verfahren zur thermomechanischen Behandlung von Stahl für torsionsbeanspruchte Federelemente
CN102719759B (zh) * 2012-07-12 2014-03-26 南车戚墅堰机车车辆工艺研究所有限公司 高速铁路扣件用弹条用钢及其冶炼生产方法
RU2512695C1 (ru) * 2012-12-26 2014-04-10 Общество с ограниченной ответственностью "Мультимодальный центр МИИТ" Способ изготовления упругой клеммы для рельсового скрепления и упругая клемма
CN105112774A (zh) * 2015-08-28 2015-12-02 浙江美力科技股份有限公司 高强韧性低中碳微合金风冷硬化弹簧钢及其成形和热处理工艺
CN105401072A (zh) * 2015-12-18 2016-03-16 马鞍山钢铁股份有限公司 含铌12.9级轨道交通移动装备用紧固件用钢及其热处理工艺

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH01116031A (ja) * 1987-10-29 1989-05-09 Nippon Steel Corp 靭性に優れた高Ｓｉ高炭素熱延鋼板の製造方法
JP2932943B2 (ja) * 1993-11-04 1999-08-09 株式会社神戸製鋼所 高耐食性高強度ばね用鋼材
EP0974676A3 (fr) * 1998-07-20 2003-06-04 Firma Muhr und Bender Procédé de traitement thermomécanique d'acier pour éléments de ressort de torsion
JP2001049337A (ja) * 1999-08-05 2001-02-20 Kobe Steel Ltd 疲労強度に優れた高強度ばねの製造方法
EP1589124B1 (fr) * 2003-01-27 2010-05-05 Nippon Steel Corporation Fil d'acier a forte teneur en carbone, a haute resistance et de grande durete, et procede de fabrication
JP4393467B2 (ja) * 2006-02-28 2010-01-06 株式会社神戸製鋼所 強伸線加工用の熱間圧延線材およびその製造方法
CN101716721B (zh) * 2009-12-23 2011-12-07 南京钢铁股份有限公司 一种弹簧钢盘条的生产工艺
BR112013004944A2 (pt) * 2010-08-30 2016-08-16 Kobe Steel Ltd vergalhão de arame de aço para mola de alta resistência excelente na capacidade de trefilação do arame, método de fabricação para ele e mola de alta resistência
JP5250609B2 (ja) * 2010-11-11 2013-07-31 日本発條株式会社 高強度ばね用鋼、高強度ばねの製造方法及び高強度ばね
CN109082592B (zh) * 2018-08-27 2020-08-18 河钢股份有限公司 一种综合性能良好耐腐蚀弹簧钢热轧盘条及其生产工艺
CN109735765B (zh) * 2019-01-17 2020-05-05 江苏利淮钢铁有限公司 一种大规格、超细晶、高强韧性弹簧钢及其生产方法

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19546204C1 (de) 1995-12-11 1997-03-20 Max Planck Inst Eisenforschung Verfahren zur Herstellung von hochfesten Gegenständen aus einem Vergütungsstahl und Anwendung dieses Verfahrens zur Erzeugung von Federn
DE19839383A1 (de) 1998-07-20 2000-01-27 Muhr & Bender Verfahren zur thermomechanischen Behandlung von Stahl für torsionsbeanspruchte Federelemente
CN102719759B (zh) * 2012-07-12 2014-03-26 南车戚墅堰机车车辆工艺研究所有限公司 高速铁路扣件用弹条用钢及其冶炼生产方法
RU2512695C1 (ru) * 2012-12-26 2014-04-10 Общество с ограниченной ответственностью "Мультимодальный центр МИИТ" Способ изготовления упругой клеммы для рельсового скрепления и упругая клемма
CN105112774A (zh) * 2015-08-28 2015-12-02 浙江美力科技股份有限公司 高强韧性低中碳微合金风冷硬化弹簧钢及其成形和热处理工艺
CN105401072A (zh) * 2015-12-18 2016-03-16 马鞍山钢铁股份有限公司 含铌12.9级轨道交通移动装备用紧固件用钢及其热处理工艺

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
"Stahl Fibel", 2015, VERLAG STAHLEISEN GMBH
DATABASE WPI Week 201624, Derwent World Patents Index; AN 2016-17839W, XP002797798 *

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US20220275490A1 (en) 2022-09-01
FI3783120T3 (fi) 2023-11-15
CN114341387B (zh) 2023-06-23
WO2021037567A1 (fr) 2021-03-04
EP3783120B1 (fr) 2023-09-27
ES2963989T3 (es) 2024-04-03
PL3783120T3 (pl) 2024-02-19

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