US20170283904A1 - Method for producing cold-formed steel springs - Google Patents

Method for producing cold-formed steel springs Download PDF

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Publication number
US20170283904A1
US20170283904A1 US15/508,356 US201515508356A US2017283904A1 US 20170283904 A1 US20170283904 A1 US 20170283904A1 US 201515508356 A US201515508356 A US 201515508356A US 2017283904 A1 US2017283904 A1 US 2017283904A1
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United States
Prior art keywords
steel wire
temperature
cooling
tempering
forming
Prior art date
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Abandoned
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US15/508,356
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English (en)
Inventor
Dieter Lechner
Marcel Groß
Heinz Georg Gabor
Marco Roland
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ThyssenKrupp AG
ThyssenKrupp Federn und Stabilisatoren GmbH
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ThyssenKrupp AG
ThyssenKrupp Federn und Stabilisatoren GmbH
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Filing date
Publication date
Priority claimed from DE102014112761.7A external-priority patent/DE102014112761B4/de
Priority claimed from DE102014112762.5A external-priority patent/DE102014112762B4/de
Application filed by ThyssenKrupp AG, ThyssenKrupp Federn und Stabilisatoren GmbH filed Critical ThyssenKrupp AG
Publication of US20170283904A1 publication Critical patent/US20170283904A1/en
Assigned to THYSSENKRUPP AG, ThyssenKrupp Federn und Stabilisatoren GmbH reassignment THYSSENKRUPP AG ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: GROSS, Marcel, ROLAND, Marco, GABOR, Heinz-Georg, LECHNER, DIETER
Abandoned legal-status Critical Current

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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
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21F—WORKING OR PROCESSING OF METAL WIRE
    • B21F3/00—Coiling wire into particular forms
    • B21F3/02—Coiling wire into particular forms helically
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21F—WORKING OR PROCESSING OF METAL WIRE
    • B21F35/00—Making springs from wire
    • 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
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • C21D11/005—Process control or regulation for heat treatments for cooling
    • 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
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/005—Ferrite
    • 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
    • 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
    • C21D2211/009—Pearlite
    • 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
    • F16F—SPRINGS; SHOCK-ABSORBERS; MEANS FOR DAMPING VIBRATION
    • F16F1/00—Springs
    • F16F1/02—Springs made of steel or other material having low internal friction; Wound, torsion, leaf, cup, ring or the like springs, the material of the spring not being relevant
    • F16F1/04—Wound springs

Definitions

  • the present invention relates to cold-formed springs and/or torsion bars, to a process for producing cold-formed springs and/or torsion bars, and to the use of a steel wire for production of cold-formed springs and/or torsion bars.
  • Torsion bars are also referred to, for example, as torque rod springs, stabilization torque rods or torsion bar springs.
  • Steel springs and torsion bar springs are used especially in motor vehicles, where steel springs are used, for example, to absorb road unevenness in shock absorber systems, and torsion bar springs to provide stabilization against tilting and distortion of the chassis, especially on motor vehicle cornering, on motor vehicle journeys over varying road surfaces and in the event of road unevenness.
  • the shaping of the steel wire to give springs and torsion bars can be effected by a cold and/or hot forming method.
  • the steel wire Prior to this shaping, the steel wire can undergo various preparation steps which affect the spring and strength properties.
  • the spring steel used for production of a steel spring and/or torsion bar spring is subjected to a thermomechanical forming (TMF) operation, in order to increase its strength and toughness usable for construction purposes and to improve further specific use properties of a material.
  • TMF thermomechanical forming
  • springs and/or torsion bars having high strength(s) can be produced with lower material input and hence low weight and material costs.
  • the prior art discloses a number of different methods which comprise a thermal treatment and then a forming operation. In the case of cold forming, the formability of the steel wire is limited, since the toughness and formability thereof decreases as a result of cold solidification with an increasing degree of forming.
  • the TMF is already used in the form of a skew rolling process, but here only on prefabricated individualized spring rods. Such a process is disclosed in DE 103 15 418 B3.
  • the TMF is effected on the spring rod by a one-stage skew rolling process directly prior to the hot winding of the helical springs.
  • the hot-formed spring is quenched in oil, which results in a martensitic structure.
  • DE 198 39 383 C2 describes a process for thermomechanical treatment of steel for torsion-stressed spring elements.
  • a starting material is rapidly heated to a temperature of 1080° C. and austenitized. Subsequently, the starting material is subjected to a TMF, which achieves recrystallization. Subsequently, without intermediate cooling, the starting material is hardened by quenching.
  • thermomechanical forming and tempering which is thus required results in the following disadvantages:
  • the spring of the invention has the advantage over conventional springs that the spring wire of the invention has higher toughness compared to conventional spring wires. Because of the higher toughness of the spring wire, the spring of the invention can be subjected to higher stresses. Further advantages of the spring of the invention are a lower weight compared to conventional springs and a longer lifetime. Moreover, the spring of the invention, compared to conventional springs, can especially be designed with smaller dimensions and a shorter spring length, which means that the spring of the invention can also be disposed in small spaces.
  • the torsion bar of the invention has the advantage over conventional torsion bars that the spring wire of the invention has higher toughness compared to conventional spring wires. Because of the higher toughness of the spring wire, the torsion bar of the invention can be subjected to higher stresses. A further advantage of the torsion bar of the invention is a longer lifetime compared to conventional torsion bars.
  • the process of the invention for producing springs and/or torsion bars has the advantage over conventional processes that the spring and/or torsion bar of the invention has a spring wire having a higher toughness compared to conventional spring wires.
  • a further advantage of the process of the invention is that it can be integrated simply and reliably into existing processes.
  • the process of the invention has the advantages that
  • the invention therefore provides a spring and/or torsion bar produced from a steel wire by cold forming by a process comprising the following steps:
  • the invention further provides a process for producing a spring and/or torsion bar, comprising the steps of:
  • the invention further provides for the use of a steel wire for production of cold-formed springs and/or torsion bars, comprising the steps of:
  • the formation of the pearlitic-ferritic structure puts the wire in an intermediate state in which the wire features high softness and hence also good amenability to handling. Because of this softness, it is possible to achieve separation of the TMF from the subsequent tempering in the process. In the period between the TMF and the tempering, the wire has much better amenability to handling, since it is not in a hardened form.
  • the invention can be implemented either in a spring or in a torsion bar, or else in a spring wire of the invention, or else in a process for producing the spring and/or torsion bar, or else the spring wire, and also in the use of a steel wire for production of the spring and/or torsion bar.
  • a spring is understood to mean a component made from a steel wire which yields under stress and, after the stress is relieved, returns to its original state. More particularly, a spring may be a component wound in helical or spiral form from steel wire or stretched or bent in the form of a rod. Examples of springs are selected from a group of helical springs, especially helical compression springs, helical tension springs, conical springs, elastic springs, flexible springs, especially spiral springs, wound torsion springs and combinations thereof.
  • a torsion bar is understood to mean a bar element wherein, when the torsion bar is fixed at both ends, the secured ends perform a pivoting motion about the axis of the bar element with respect to one another. More particularly, the mechanical stress takes place to a crucial degree through a torque that engages tangentially with respect to the rod element axis.
  • Torsion bars are also understood, for example, to mean a straight torsion bar, an angular torsion bar, a torsion bar spring, a torsion spring, a stabilization torsion bar, a stabilizer, a separated stabilizer and combinations thereof.
  • Cold forming in the context of the present invention is understood to mean forming of the steel wire below the recrystallization temperature. More particularly, formability is limited in cold forming since, as a result of the cold solidification, there is a decrease in the toughness and formability of a material, for example steel, with an increasing degree of forming. Examples of cold forming are cold winding, cold bending and combinations thereof.
  • the recrystallization temperature is that calcining temperature which, in the case of a cold-formed structure with a given degree of forming, leads to complete recrystallization within a limited period of time.
  • the recrystallization temperature does not have a fixed value but depends on the extent of the prior cold forming and the melting temperature of the material, especially the melting temperatures of steels. For example, in the case of steels, the recrystallization temperature is also dependent on the carbon content and the alloy of the particular steel.
  • the minimum recrystallization temperature is understood to mean the lowermost temperature at which there is still recrystallization, especially recrystallization of the structure of a steel wire.
  • Austenite start temperature in the context of the invention is understood to mean a temperature at which there is transformation to an at least partly austenitic structure. More particularly, at an austenitization temperature, there is transformation to an at least partly austenitic structure.
  • Tempering in the context of the present invention may be partial or complete tempering.
  • a heat transfer as occurs, for example, in step b) in the thermomechanical forming, in step d)I. in the heating, in step d)III. in the reheating and/or another heat transfer in the context of the invention, is understood to mean one selected from conduction of heat, especially conductive heating, radiation of heat, especially infrared radiation, heating by induction, convection, especially a heated fan, and combinations thereof.
  • a stabilizer in the context of the invention is also understood to mean a stabilization torsion bar. More particularly, sections of stabilizers and/or separated stabilizers are also understood to mean stabilizers of the invention.
  • the production of the spring and/or torsion bar is conducted with a steel wire having a carbon content in the range from 0.02% to 0.8% by weight. More particularly, in the context of the invention, steels having a carbon content in the range from 0.02% to 0.8% by weight are understood to mean hypoeutectoid steels.
  • thermomechanical forming in step b) is effected at a temperature equal to or greater than the austenite start temperature, preferably equal to or greater than the austenite end temperature, more preferably in the range from the austenite end temperature to 50° C. greater than the austenite end temperature.
  • Austenite end temperature in the context of the invention is understood to mean a temperature at which the transformation to an austenitic structure is complete.
  • the wire which is still in the form of a continuous wire, is rolled up, especially coiled, for storage or transport purposes.
  • the wire is uncoiled again. The subsequent tempering is thus completely decoupled from the TMF.
  • the process sequence of the invention also enables decoupling of the tempering from the TMF with regard to the temperature range. While the optimal forming temperature during the TMF is just above the austenitization temperature of the wire material, especially less than 50° C. above the austenitization temperature of the wire material, heating to significantly higher temperatures is advantageous for the tempering. Thus, in a preferred configuration, the tempering temperature is above the forming temperature, especially more than 50° C. above the austenitization temperature of the wire material. The separation of TMF and tempering in the process allows the optimal temperature to be established for each of the two steps.
  • a further advantage of the process sequence of the invention is that the decoupling of the two processes of tempering and TMF allows both processes to be conducted at (required) throughput rates of the wire that are optimal for the particular process.
  • the throughput rate of the wire in the TMF is not necessarily the same as in the tempering.
  • the slower of the two processes sets the throughput rate for both processes, meaning that one of the two processes does not work under optimal conditions, i.e. in an uneconomic manner.
  • a further advantage of the process of the invention and of the spring of the invention and/or the torsion bar is that the spring wire of the invention has a finer-grain structure compared to conventional spring wires.
  • the cooling of the wire in step c) is effected at least to a temperature below the minimum recrystallization temperature, preferably below a temperature of 200° C., more preferably below a temperature of 50° C.
  • the cooling after the TMF is preferably effected at such a low cooling rate as to ensure that a pearlitic-ferritic structure is established.
  • the person skilled in the art is able to employ the TTT diagram corresponding to the material, from which it is possible to read off the cooling rate.
  • the procedure proposed appears to be uneconomic compared to the known process, since the wire now has to be reheated for the cold forming process after the intermediate cooling.
  • the decoupling achieved thereby can avoid the disadvantages mentioned at the outset, which can be assessed as being better in technical terms and more economically advantageous than the advantages resulting from the integral manufacture.
  • the intermediate cooling can also be effected in a controlled manner with involvement of a heat exchanger, by means of which the waste heat from the cooling can again be available to the TMF or the subsequent tempering with quite a high efficiency.
  • an already pretreated wire for production of cold-formed steel springs, especially helical springs or torsion bar springs made from steel.
  • the wire has a temperature of less than 200° C., especially room temperature.
  • the wire has already been subjected to a thermomechanical forming operation and has a pearlitic-ferritic structure.
  • This wire is then tempered, the tempering comprising the following steps: heating of the wire to a tempering temperature above the austenitization temperature of the wire material and austenitization; quenching of the wire heated to tempering temperature for formation of a martensitic structure in the wire; annealing of the wire.
  • This is followed by the cold forming of the wire for production of the cold-formed steel springs.
  • the steel wire is heated in step d)I. to a temperature equal to or greater than the austenite start temperature, preferably equal to or greater than the austenite end temperature.
  • the quenching of the wire in step d)II. causes the steel wire structure to undergo at least partial conversion to martensite and the steel wire to be exposed to at least a martensite start temperature, whereby the quenching of the steel wire is preferably carried out to the first cooling temperature of the steel wire of less than or equal to 200° C.
  • Martensite start temperature in the context of the invention is understood to mean a temperature at which there is transformation to an at least partly martensitic structure.
  • the tempering of the steel wire in step d) establishes the hardness profile over the cross section of the steel wire.
  • the hardness of the steel wire can vary from the edge to the core of the steel wire. More particularly, the hardness can drop or rise or else be equal from the edge to the core of the steel wire. Preferably, the hardness drops from the edge to the core of the steel wire. For example, this can be effected by edge heating of the steel wire with subsequent recooling after one of steps d) to f).
  • the process is employed in the production of cold-formed helical springs. This involves cold winding of the wire to give steel springs; only after the cold winding of the helical springs are they separated from the wire, especially individualized.
  • the process is employed in the production of cold-formed torsion bar springs. This involves cutting the wire to length to give rods after the tempering. Thereafter, the rods are processed further by cold bending to give torsion bar springs, especially stabilizers for motor vehicle chassis.
  • edge heating and subsequent recooling of the steel wire is carried out, whereby the hardness increases from the edge to the core of the steel wire.
  • the steel wire is coiled.
  • a surface treatment of the steel wire is carried out, in which the surface of the steel wire is at least partly removed.
  • the spring produced by the process of the invention and/or the torsion bar have a martensite content of greater than 40% by volume, preferably greater than 80% by volume, more preferably greater than 90% by volume, most preferably greater than 95% by volume.
  • the process is conducted using a steel wire with a carbon content in the range from 0.02% to 0.8% by weight.
  • production of cold-formed springs and/or torsion bars is accomplished using a steel wire having a carbon content in the range from 0.02% to 0.8% by weight.
  • FIG. 1 a schematic diagram of the process of the invention in one embodiment of the invention
  • FIG. 2 a schematic diagram of the process of the invention in one embodiment of the invention
  • FIG. 3 a temperature profile for the embodiments according to FIGS. 1 and 2 .
  • FIGS. 1 to 3 are described together hereinafter.
  • a wound steel wire 1 is provided on a ring 10 .
  • the steel wire 1 is at first heated to a forming temperature T 1 of about 800° C., which is above the minimum recrystallization temperature of the steel wire, especially above the austenitization temperature Ac 3 of in the present case 785° C., 11 .
  • TMF thermomechanical forming
  • the heating 11 can be dispensed with when the TMF immediately follows a steel wire rolling process and the temperature of the steel wire is still at the desired forming temperature T 1 .
  • the thermomechanical forming 12 can be effected by multistage caliber rolling. Subsequently, the steel wire 1 is cooled 13 at such a slow rate that a partly ferritic-pearlitic structure, i.e. a soft structure, is established in the steel wire.
  • the cooling can be effected without any further intervention by simple storage at room temperature or ambient temperature, but the cooling is preferably effected in a controlled manner.
  • the steel wire 1 is coiled 14 , which is readily possible because of the soft microstructural state.
  • the steel wire 1 When the steel wire 1 is then coiled, it can be transported from one processing site to the next processing site and processed further there. In FIG. 3 , this is illustrated by a gap in the temperature profile after the coiling 14 .
  • a spring manufacturer can then purchase the steel wire 1 pretreated by thermomechanical forming from a steel wire manufacturer, and need not keep the equipment required for the TMF in house. This saves space and capital costs for the spring manufacturer.
  • the tempering of the steel wire 1 commences, and consequently need not follow the TMF directly (or even in terms of location).
  • Coiling 15 may also be followed by a processing operation, for example grinding 16 , prior to the tempering.
  • the steel wire is heated 17 to a hardening temperature T 2 distinctly above the austenitization temperature Ac 3 or the forming temperature T 1 .
  • the hardening temperature T 2 is about 950° C.
  • the heating is effected very quickly and is preferably conducted by inductive means.
  • the heating is effected at a heating rate of at least 50 K/s, preferably at least 100 K/s.
  • quenching 18 for example in a water or oil bath, which establishes an at least partly martensitic structure.
  • the steel wire 1 is annealed 19 .
  • the tempered steel wire 1 is then subjected to cold winding 20 ′ to give helical springs 3 ′ and then cut 21 from the steel wire 1 .
  • the tempered steel wire 1 is first cut 21 into individual spring rods 22 and then subjected to cold bending 20 ′′ to give torsion bar springs 3 ′′.
  • Springs and/or torsion bars of the above-described type are used, for example, in the production of motor vehicles, especially of motor vehicle chassis.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Springs (AREA)
  • Wire Processing (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
US15/508,356 2014-09-04 2015-07-15 Method for producing cold-formed steel springs Abandoned US20170283904A1 (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
DE102014112761.7A DE102014112761B4 (de) 2014-09-04 2014-09-04 Verfahren zum Herstellen von kaltgeformten Stahlfedern
DE102014112761.7 2014-09-04
DE102014112762.5 2014-09-04
DE102014112762.5A DE102014112762B4 (de) 2014-09-04 2014-09-04 Verfahren zum Herstellen von warmgeformten Stahlfedern
PCT/EP2015/066155 WO2016034319A1 (de) 2014-09-04 2015-07-15 Verfahren zum herstellen von kaltgeformten stahlfedern

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US15/508,356 Abandoned US20170283904A1 (en) 2014-09-04 2015-07-15 Method for producing cold-formed steel springs

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US (2) US10689726B2 (zh)
EP (4) EP3189165B1 (zh)
JP (2) JP2017530258A (zh)
KR (2) KR102332298B1 (zh)
CN (2) CN106795576B (zh)
BR (2) BR112017004224B1 (zh)
HU (2) HUE050515T2 (zh)
MX (2) MX2017002798A (zh)
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WO (2) WO2016034318A1 (zh)

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JP7227251B2 (ja) 2017-08-24 2023-02-21 ルソール リベルテ インコーポレイティド コイルバネ及びそれを作製する方法
CN111250559B (zh) * 2018-11-30 2021-09-24 郑州元素工具技术有限公司 一种环形钢丝的热处理方法
CN111926165B (zh) * 2020-08-13 2022-04-05 无锡金峰园弹簧制造有限公司 一种60Si2CrA弹簧钢的热处理工艺
CN112695182B (zh) * 2020-12-29 2022-11-11 山东康泰实业有限公司 一种车用扭力梁制造方法和车用扭力梁后桥总成
CN114346131B (zh) * 2021-12-31 2024-03-12 江苏三众弹性技术股份有限公司 一种钢丝制碟形弹簧的制造方法
CN115463994B (zh) * 2022-11-03 2023-03-24 广东神和新材料科技有限公司 一种汽车用精密不锈钢弹簧线材制造工艺

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