EP1788105B1 - Federstahldraht mit Leistung der Beizen - Google Patents

Federstahldraht mit Leistung der Beizen Download PDF

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EP1788105B1
EP1788105B1 EP06021771A EP06021771A EP1788105B1 EP 1788105 B1 EP1788105 B1 EP 1788105B1 EP 06021771 A EP06021771 A EP 06021771A EP 06021771 A EP06021771 A EP 06021771A EP 1788105 B1 EP1788105 B1 EP 1788105B1
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Prior art keywords
rolling
wire rod
scale
concentration
range
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English (en)
French (fr)
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EP1788105A1 (de
Inventor
Nao Yoshihara
Fujio Koizumi
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Kobe Steel Ltd
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Kobe Steel Ltd
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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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/04—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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—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 a spring steel wire rod excellent in pickling performance, and more specifically a technology for improving pickling performance of a spring steel wire rod containing Si abundantly and further Cr, Cu, and Ni.
  • a spring steel wire rod according to the present invention is favorably used for: a valve spring used for the engine of an automobile or the like; a clutch spring; a brake spring; a suspension spring such as a stabilizer spring or a torsion bar spring; and other applications.
  • the chemical composition of a spring steel used for a valve spring, a suspension spring, or the like is stipulated in JIS G3565 to JIS G4801 for example and an appropriate steel type is used in accordance with the type of spring design.
  • a spring steel wire rod which can realize a high strength of about 1,600 MPa or higher in terms of the tensile strength of a spring material wire (a quenched and tempered material).
  • a spring is generally fabricated by heating a billet; subjecting the hot-rolled wire rod (the rolled wire rod) to filming treatment (surface coating treatment) by applying a lubricant to the surface if necessary; thereafter drawing the wire rod to a prescribed diameter; and applying forming (hot forming or cold forming).
  • the heating is usually carried out in an oxidizing atmosphere and hence an oxidation layer comprising Fe oxide called "rolling scale” or “scale” is formed on the surface of a rolled wire rod.
  • Fig. 1 shows a photograph of a cross section of a rolled wire rod bearing scale on the surface of the steel containing Si abundantly and further Cr, Cu, and Ni, the photograph being taken with an Fe-SEM.
  • the scale comprises, in order from the surface side, hematite (Fe 2 O 3 ), magnetite (Fe 3 O 4 ), wustite (FeO), and fayalite (2FeO ⁇ SiO 2 ).
  • hematite Fe 2 O 3
  • magnetite Fe 3 O 4
  • wustite FeO
  • fayalite 2FeO ⁇ SiO 2
  • fayalite is a low melting point oxide which is seen when a steel abundantly containing Si is used and is a material hard to exfoliate through ordinary pickling treatment.
  • a steel containing Si and Cr is heated to a temperature exceeding the eutectic temperature of fayalite and wustite (about 1,170°C)
  • a dense melt phase wherein those oxides are intricately interwound with each other is formed and then, when it is further heated to a temperature of 1,200°C or higher, Cr intrudes into the aforementioned melt phase and the fayalite, condenses at the interface with the base steel, and forms a condensed layer (the detail will be described later).
  • the Cr once condensed is very hard to remove through the succeeding processes and deteriorates pickling performance.
  • pickling performance deteriorates, scale remains after pickling treatment, hence the adhesiveness with a lubricant applied on the surface (used for surface coating treatment) lowers, and wire breakage may undesirably occur during drawing. Even when wire breakage does not occur, cracks (crevices) may occur during drawing and breakage may occur during spring forming (cold coiling).
  • a layer wherein Cu and Ni are concentrated is also formed between the steel (the base steel) and the scale.
  • the concentrated layer is seen when a steel contains Cu and Ni. It is known that: metals such as Cu and Ni which are nobler than iron are not oxidized by heating; hence such metals concentrate at the interface between scale and a base steel or in fayalite; and surface cracks caused by red shortness appear.
  • the melting point of Cu is about 1,080°C and a steel material is usually heated to a temperature higher than the melting point of Cu (about 1,100°C to 1,250°C for example) before hot-rolled, and hence it is estimated that: Cu in a molten state (of a liquid phase) is formed at the interface between scale and the base steel; the Cu intrudes into grain boundaries of the base steel and concentrates; the steel material does not withstand shearing stress or tensile stress any more during hot rolling; and surface cracks caused by red shortness appear.
  • Such a phenomenon is called liquid metal melt embrittlement and it is understood that the phenomenon resultantly deteriorates pickling performance.
  • JP-A No. 297026/1994 describes a method for preventing surface cracks by: adding Si in a steel; making Si exist in scale during the heating process preceding hot rolling; forming low melting point oxide liquid scale of an SiO 2 -FeO system; and thus taking the Cu molten liquid into the scale.
  • JP-A No. 223523/2004 describes a technology related to a method of heating a Cu containing steel material, the technology being proposed by the same applicants as those of JP-A No. 297026/1994 .
  • the patent application describes a method for controlling the temperature of a heating atmosphere and the oxygen concentration in the atmosphere with regard to the conditions of the heating before hot rolling as a method which makes it possible to prevent surface cracks caused by the concentration of Cu without such change of a steel composition as described in JP-A No. 297026/1994 .
  • JP-A No. 223523/2004 stated above describes a technology for preventing surface cracks caused by the concentration of Cu without the abundant addition of Si and by the technology the improvement of proof stress by the addition of Si cannot be obtained.
  • US-patent 5,846,344 describes a spring steel of high strength and high corrosion resistance.
  • a lowly decarburizable spring steel is disclosed in US-patent 5,951,944 .
  • Several compositions of steels are described by C. Wegst, M. Wegst in "Stahlischenl" 2004, 180 . V. K. Likhov et al., Steel in the USSR, 1988, 18, 81/3 , describes the assimilation of production of wire rod for manufacture of safety critical springs.
  • the present invention has been established in view of the above situation and the object thereof is to provide a spring steel wire rod having improved pickling performance in the case of a spring steel wire rod containing Si abundantly and further Cr, Cu, and Ni.
  • a spring steel wire rod according to the present invention which can solve the above problems is a spring steel wire rod as defined in the claims.
  • the spring steel wire rod contains C: 0.35% to 0.7% (by mass, the same is hereunder applied unless otherwise specified), Si: 1.5% to 2.50%, Mn: 0.05% to 1.0%, Cr: 0.05% to 1.9%, Cu: 0.05% to 0.7%, Ni: 0.15% to 0.8%, P: 0.02% or less (excluding 0%), and S: 0.02% or less (excluding 0%), and the balance thereof consists of Fe and unavoidable impurities, wherein the ratio of Si to Cu (Si/Cu) is in the range of 4.0 or more; and the difference between the concentration of Cu in the surface layer and the concentration of Cu in the steel is 0.50% or less and the difference between the concentration of Ni in the surface layer and the concentration of Ni in the steel is 1.00% or less.
  • a spring steel wire rod according to the present invention further contains at least one element selected from among the group comprising V: 0.07% to 0.4%, Ti: 0.01% to 0.1%, and Nb: 0.01% to 0.1%.
  • a spring according to the present invention which can solve the above problems is a spring fabricated from any one of the spring steel wire rods stipulated above.
  • a spring steel wire rod according to the present invention is excellent in pickling performance since the concentration of Cr and Ni in the surface layer thereof is considerably suppressed and the thickness of scale is very thin.
  • a spring is fabricated from a spring steel wire rod according to the present invention, a spring excellent in surface properties can be provided since the scale is easily exfoliated through a pickling process.
  • the present inventors have earnestly studied in order to improve the pickling performance of a spring steel wire rod containing Si abundantly and further Cr, Cu, and Ni.
  • the present inventors have found that, by properly controlling particularly, (i) a descaling process preceding hot rolling, and (ii) a hot-rolling process, the concentration of Cu and Ni on the wire rod surface (particularly the concentration of Cu and Ni in fayalite) is suppressed; the difference between the concentration of Cu in the surface layer and the concentration of Cu in the steel (hereunder may be abbreviated to " ⁇ Cu") and the difference between the concentration of Ni in the surface layer and the concentration of Ni in the steel (hereunder may be abbreviated to " ⁇ Ni”) are remarkably lowered; and thereby pickling performance outstandingly improves. And the present inventors have established the present invention.
  • a spring steel wire rod according to the present invention is a spring steel wire rod wherein: the spring steel wire rod comprises C: 0.35% to 0.7%, Si: 1.5% to 2.50%, Mn: 0.05% to 1.0%, Cr: 0.05% to 1.9%, Cu: 0.05% to 0.7%, Ni: 0.15% to 0.8%, P: 0.02% or less (excluding 0%), S: 0.02% or less (excluding 0%), and the balance consisting of Fe and unavoidable impurities; the ratio of Si to Cu (Si/Cu) is in the range of 4.0 or more; and the difference between the concentration of Cu in the surface layer and the concentration of Cu in the steel is 0.50% or less and the difference between the concentration of Ni in the surface layer and the concentration of Ni in the steel is 1.00% or less.
  • steel wire rod means a steel material (a rolled material) which is fabricated by heating and thereafter hot-rolling a billet into a linear shape, which is not yet subjected to pickling treatment.
  • C is an element which contributes to the enhancement of strength (hardness) after being quenched and tempered and improves durability in the air.
  • a C content is less than 0.35%, the above functions cannot be effectively exhibited.
  • a C content exceeds 0.7%, toughness and ductility deteriorate, cracks tend to propagate and durability lowers, and thus corrosion resistance is also badly affected.
  • a preferable C content is in the range of 0.39% to 0.54%.
  • Si is an element which contributes to the enhancement of strength as a solid solution hardening element and also can improve proof stress.
  • a Si content is less than 1.5%, the strength of a matrix is insufficient.
  • a Si content exceeds 2.50%, the ratio of fayalite in scale increases and pickling performance deteriorates.
  • a preferable Si content is in the range of 1.70% to 2.1%.
  • Mn is an element which enhances the hardenability of a steel. Mn is added by 0.05% or more in order to effectively exhibit such a function. When Mn is added in excess of 1.0% however, the hardenability increases, a supercooled structure tends to form, and drawability deteriorates. Further, when an annealing process is applied after hot rolling before pickling treatment with the aim of softening a wire rod in the same way as "a spring forming process (c)" which will be described later, the cost unavoidably increases. A preferable Mn content is in the range of 0.12% to 0.8%. In the present invention, as stated later, measures such as the reduction of a S content, the addition of another sulfide-forming element such as Cu, and others are taken in order to prevent MnS which functions as the origin of fracture from forming.
  • Cr is an element which makes rust formed on a surface amorphous and dense under corrosive conditions, contributes to the improvement of corrosion resistance, and effectively affects the enhancement of hardenability like Mn. Cr is added by 0.05% or more in order to exhibit such functions. When a Cr content exceeds 1.9% however, a supercooled structure tends to form during cooling after rolling and drawability deteriorates. When an annealing process is applied after hot rolling before pickling treatment with the aim of softening a wire rod in the same way as "a spring forming process (c)" which will be described later, the cost unavoidably increases.
  • a preferable Cr content is in the range of 0.15% to 1.75%.
  • Cu is an element which is electrochemically nobler than iron and has the function of improving corrosion resistance. Cu is added by 0.05% or more in order to effectively exhibit such a function. When a Cu content exceeds 0.7% however, the amount of Cu concentrated in a base steel surface layer, at the interface between a base steel and rolling scale, and in fayalite increases and pickling performance deteriorates.
  • a preferable Cu content is in the range of 0.20% to 0.5%.
  • Ni has the functions of enhancing toughness after quenching and tempering, making rust forming on a surface amorphous and dense under corrosive conditions, and thus improving corrosion resistance. Further, Ni has also the function of suppressing ferrite decarburization occurring before and during rolling. Ni is added by 0.15% or more in order to effectively exhibit such functions. When a Ni content exceeds 0.8% however, hardenability increases and a supercooled structure tends to form after rolling. In addition, the amount of retained austenite increases and spring hardness lowers. A preferable Ni content is in the range of 0.25% to 0.55%.
  • P segregates at prior austenite grain boundaries, embrittles the grain boundaries, and lowers resistance to delayed fracture. For that reason, a P content should be as small as possible.
  • the upper limit of a P content is set at 0.02% in view of industrial production.
  • a S content should be as small as possible.
  • the upper limit of a S content is set at 0.02% in view of industrial production.
  • the lower limit of a ratio Si/Cu is regulated.
  • fayalite formed by the addition of Si and the amount of Cu concentrated at the interface between a base steel and scale by the addition of Cu are properly controlled, and hence the Cu concentration into the fayalite is suppressed and ⁇ Cu lowers.
  • pickling performance improves (refer to the after-mentioned Example).
  • the upper limit of a ratio Si/Cu is set at 50 from the contents of Si and Cu described above.
  • a preferable ratio Si/Cu is in the range of 4.5 to 35.
  • a spring steel wire rod according to the present invention contains the aforementioned components and the balance thereof consists of Fe and unavoidable impurities.
  • the spring steel wire rod further contains at least one element selected from among the group comprising V: 0.07% to 0.4%, Ti: 0.01% to 0.1%, and Nb: 0.01% to 0.1%.
  • V 0.07% to 0.4%
  • Ti 0.01% to 0.1%
  • Nb 0.01% to 0.1%
  • V is an element which forms fine carbide and nitride and contributes to the improvement of resistance to hydrogen embrittlement. Further, V enhances fatigue resistance. In addition, V improves toughness and proof stress by, the crystal grain fractionizing effect and also contributes to the improvement of corrosion resistance and resistance to permanent set in fatigue. It is preferable to add V by 0.07% or more in order to effectively exhibit such functions. When V is added in excess of 0.4% however, the amount of carbide not dissolved in austenite increases during heating for hardening, sufficient strength and hardness cannot be obtained, the amount of retained austenite also increases, and the hardness of a spring lowers. A yet preferable V content is in the range of 0.1% to 0.2%.
  • Ti is an element which fractionizes prior austenite crystal grains after quenching and tempering and is effective in the improvement of resistance to hydrogen embrittlement. Further, Ti has the function of enhancing durability in the air. It is preferable to add Ti by 0.01% or more in order to effectively exhibit such functions. When Ti is added excessively however, coarse nitride tends to precipitate and durability in the air deteriorates. For that reason, it is preferable to set the upper limit of a Ti content at 0.1%. A yet preferable Ti content is in the range of 0.04% to 0.09%.
  • Nb is an element which forms fine precipitate comprising carbide, nitride, sulfide, and a composite compound thereof and thus contributes to the improvement of resistance to hydrogen embrittlement. Further, toughness and proof stress also improve by the crystal grain fractionizing effect. It is preferable to add Nb by 0.01% or more in order to effectively exhibit such functions. When Nb is added in excess of 0.1% however, the amount of carbide not dissolved in austenite increases during heating for hardening and an intended tensile strength cannot be obtained. A yet preferable Nb content is in the range of 0.02% to 0.05%.
  • ⁇ Cu is controlled to a low level of 0.50% or less.
  • the scale (the secondary scale) formed during hot rolling and during cooling after hot rolling particularly in the case of such a steel containing Si and Cu in quantities as a steel according to the present invention, cannot be easily removed through ordinary descaling treatment, Fe diffuses in the scale, and thereby Cu precipitates at the interface between the scale (fayalite) and the base steel or in fayalite. As a result, pickling performance deteriorates.
  • ⁇ Cu can be controlled to a low level.
  • a value ⁇ Cu is preferably 0.45% or less, and yet preferably 0.40% or less.
  • Fig. 2 comprises the graphs obtained by using a specimen prepared as stated below and measuring a Cu content from a surface to the center of the interior by EPMA quantitative linear analysis under after-mentioned conditions; and shows the relationship between a Cu concentration (%) and a distance from the surface.
  • Fe the point where the Fe strength (cps) of X-ray comes to the maximum when the EPMA quantitative linear analysis is applied in the same way as stated above is defined as a base steel interface (an interface between scale and a base steel).
  • the region between a surface and a base steel interface is defined as "a surface layer” and the maximum value of the Cu content in the surface layer is defined as "a Cu concentration in a surface layer.”
  • the state of such a surface layer varies also in accordance with components in a steel, fabrication conditions of a wire rod, and others but the surface layer contains at least fayalite.
  • ⁇ Ni is also controlled to a low level of 1.00% or less.
  • Ni is an element which contributes to the improvement of corrosion resistance like Cu as stated above and is the same as Cu also in the fact that Ni precipitates at the interface between scale (fayalite) and a base steel or in fayalite in a heating process and a hot-rolling process. As a result, pickling performance deteriorates.
  • it is necessary to suppress the concentration of Ni in the same way as Cu.
  • a value ⁇ Ni is preferably 0.90% or less, and yet preferably 0.85% or less.
  • a Ni concentration in a surface layer means the maximum Ni content obtained by using a specimen prepared by the same method as used in the measurement of "a Cu concentration in a surface layer” stated above and measuring a Ni content in the range of 0.3 mm from the surface toward the center of the interior by the EPMA quantitative linear analysis under the same conditions as described above.
  • Fig. 3 shows the relationship between a Ni concentration (%) and a distance from a surface.
  • a spring steel wire rod according to the present invention, it is preferable to control the thickness and the composition of scale in an appropriate manner as stated below and by so doing pickling performance is further improved.
  • a preferable thickness of scale is 40 ⁇ m or less. As it will be explained hereunder in detail, it is preferable that the thickness of scale is basically in the range of 5 to 35 ⁇ m in consideration of the exfoliation of scale caused by the crevices (cracks) formed in the scale.
  • the composition of scale basically satisfies the ranges of, in volume percentage, 2% to 10% (yet preferably 3% to 7%) as fayalite, 2% to 20% (yet preferably 10% to 18%) as wustite, 35% to 70% (yet preferably 37% to 50%) as magnetite, and 20% to 60% (yet preferably 30% to 55%) as hematite.
  • the composition of scale is controlled so that the percentage of fayalite which is hardly exfoliative may be reduced and the percentages of wustite and magnetite which are excellent in scale detachability may be increased, and hence pickling performance is further improved.
  • a spring steel wire rod according to the present invention has been explained above.
  • a method for fabricating a spring steel wire rod includes (i) a heating process, (ii) a soaking process, (iii) a descaling process preceding a hot-rolling process, and (iv) a hot-rolling process.
  • prescribed high-pressure water shower is applied in (iii) a descaling process preceding a hot-rolling process in order to rapidly remove scale including fayalite
  • prescribed cooling water shower is applied in (iv) a hot-rolling process in order to prevent Cu from concentrating in fayalite formed during hot rolling, and thereby it has been possible to suppress ⁇ Cu and ⁇ Ni to considerably low levels.
  • the present invention even though a steel containing Si abundantly and Cr, Cu, and Ni is used, the concentration of Cu and Ni in a surface layer is considerably suppressed, the thickness of scale is reduced, and hence it is possible to provide a spring having a tensile strength of about 1,600 MPa or more, excellent in surface properties.
  • Heating conditions are not particularly limited but basically a billet is heated to a temperature in the range of 700°C to 1,000°C (750°C to 900°C) at a heating rate of 10°C/min or higher.
  • a heating rate is lower than 10°C/min, the concentration of Cr into a surface layer cannot be prevented effectively.
  • a higher heating rate is desirable and a preferable heating rate is 15°C/min or higher.
  • a heating temperature exceeds the above range, the concentration of Cu and Ni advances and the amounts of Cu and Ni in the surface layer increase. In contrast, when a heating temperature is lower than the above range, heating is insufficient and hence rough rolling fails.
  • the process basically it is preferable to soak a billet for 20 to 60 minutes (yet preferably 30 to 50 minutes) at 1,050°C to 1,250°C (yet preferably 1,100°C to 1,200°C).
  • the soaking conditions are determined so as to prevent Cu and Ni from concentrating in a surface layer and suppress the progress of grain boundary oxidation.
  • the concentration of Cu and Ni tends to advance when a soaking temperature or a soaking time exceeds the above range, and in contrast the concentration of Cu into austenite crystal grain boundaries advances when a soaking temperature or a soaking time is lower than the above range.
  • a heating temperature in a heating process and a soaking temperature in a soaking process are not necessarily identical.
  • the soaking temperature is higher than the heating temperature by about 200°C to 300°C and the reason is that the temperature at the soaking rises during the residence time after heating before soaking.
  • high-pressure water shower for 1 to 10 seconds (preferably 3 to 7 seconds) with a water pressure in the range of 80 kgf/mm 2 (nearly 785 MPa) to 160 kgf/mm 2 (nearly 1,569 MPa), and preferably about 100 kgf/mm 2 (nearly 981 MPa) to 120 kgf/mm 2 (nearly 1,176 MPa) is applied.
  • a water pressure of the shower is lower than 80 kgf/mm 2 , the thickness of scale increases and that may undesirably cause surface defects caused by bite during hot rolling to appear, and the Cu concentration in a surface layer to increase.
  • a water pressure of the shower exceeds 160 kgf/mm 2 , the temperature of a billet before hot rolling lowers and rolling is hardly carried out.
  • prescribed cooling water shower is applied in order to prevent Cu from concentrating into fayalite formed during hot rolling and further control the composition of scale properly.
  • cooling with the shower is applied in a finish-rolling process after the application of rough rolling.
  • the flow rate of the shower water is preferably in the range of 100 to 200 t/hr, and yet preferably 120 to 180 t/hr.
  • the flow rate, of the shower water is less than 100 t/hr, the intended functions of removing scale (fayalite) and reducing ⁇ Cu and ⁇ Ni are not effectively exhibited.
  • the flow rate of the shower water exceeds 200 t/hr, a steel material is excessively cooled and a supercooled structure undesirably precipitates.
  • the finish-rolling temperature is in the range of 800°C to 1,000°C ( preferably 900°C to 950°C) mainly in order to properly control the thickness and the composition of scale.
  • a cooling rate is controlled to 4°C/sec to 20°C/sec (yet preferably 6°C/sec to 15°C/sec) in the temperature range of a temperature after the completion of the finish rolling to about 700°C.
  • a cooling rate is lower than 4°C/sec in the above temperature range, the thickness and the like of scale increase and pickling performance deteriorates.
  • a cooling rate exceeds 20°C/sec in the above temperature range, the retention time in the temperature range decreases, the percentage of wustite formed in the temperature range is reduced, and hence pickling performance deteriorates.
  • a spring fabricated from such a steel wire rod is also included.
  • scale flaws called red scale do not appear at all and it is possible to produce a spring which is outstandingly excellent in surface properties and has further improved fatigue resistance.
  • a method for fabricating a spring is not particularly limited and it is possible to adopt an ordinarily used method in an appropriate manner.
  • a spring can be fabricated through any one of the spring forming processes (a) to (c) below.
  • a rolled wire rod having low ⁇ Cu and ⁇ Ni values can be obtained and hence a spring outstandingly excellent in surface properties can be obtained by any of the methods described in the above spring forming processes (a) to (c).
  • pickling treatment can be processes by dipping a steel material either in a 5% to 25% H 2 SO 4 solution in the temperature range of 60°C to 90°C or in a 5% to 15% HCl solution in the temperature range of 20°C to 50°C.
  • a billet was heated to about 900°C at a heating rate of 15°C/min; thereafter soaked for 50 minutes at about 1,150°C, and subjected to descaling by applying high-pressure water shower for about 5 seconds under a water pressure of 100 kgf/mm 2 (nearly 981 MPa). Successively, the billet was subjected to rough rolling, thereafter subjected to finish rolling (the finish-rolling temperature was 920°C) while being cooled with the shower of 150 t/hr and, after the completion of the finish rolling, cooled at a cooling rate of 7°C/sec in the temperature range up to about 700°C.
  • the coiling temperature was 875°C.
  • a billet was heated to about 800°C at a heating rate of 20°C/min, thereafter soaked for 30 minutes at about 1,100°C, and subjected to descaling by applying high-pressure water shower for about 7 seconds under a water pressure of 150 kgf/mm 2 (nearly 1, 471 MPa). Successively, the billet was subjected to rough rolling, thereafter subjected to finish rolling (the finish-rolling temperature was 950°C) while being cooled with the shower of 130 t/hr, and, after the completion of the finish rolling, cooled at a cooling rate of 6°C/sec in the temperature range up to about 700°C.
  • the coiling temperature was 925°C.
  • a billet was heated to about 1,050°C at a heating rate of 15°C/min; thereafter soaked for 60 minutes at about 1,280°C; and subjected to descaling by applying high-pressure water shower for about 10 seconds under a water pressure of 50 kgf/mm 2 (nearly 490 MPa). Successively, the billet was subjected to rough rolling; thereafter subjected to finish rolling (the finish-rolling temperature was 1,000°C) while being cooled with the shower of 50 t/hr; and, after the completion of the finish rolling, cooled at a cooling rate of 2°C/sec in the temperature range up to about 700°C.
  • the coiling temperature was 980°C.
  • the wire rod forming process 3 represents a comparative example which did not satisfy the fabrication conditions stipulated in the present invention and all the processes of: the heating process (the heating temperature was too high); the soaking process (the soaking temperature was too high); the descaling process preceding the hot-rolling process (the water pressure was too low); and the hot-rolling process (the finish-rolling temperature was too high, the flow rate of the shower water was too low, and the cooling rate in the temperature range of the finish-rolling temperature to 700°C was too low) deviated from the conditions stipulated in the present invention.
  • a billet was subjected to heating, soaking, and descaling preceding rolling in the same way as the aforementioned wire rod forming process 3. Successively, the billet was subjected to finish rolling, cooling, and coiling in the same way as the aforementioned wire rod forming process 2.
  • the wire rod forming process 4 and the after-mentioned wire rod forming process 6 represents comparative examples which did not satisfy the fabrication conditions stipulated in the present invention and the processes of: the heating process (the heating temperature was too high); the soaking process (the soaking temperature was too high); and the descaling process preceding the hot-rolling process (the water pressure was too low) deviated from the conditions stipulated in the present invention.
  • a billet was subjected to heating, soaking, and descaling preceding rolling in the same way as the aforementioned wire rod forming process 1. Successively, the billet was subjected to finish rolling, cooling, and coiling in the same way as the aforementioned wire rod forming process 3.
  • the wire rod forming process 5 represents a comparative example which did not satisfy the fabrication conditions stipulated in the present invention and the hot-rolling process (the finish-rolling temperature was too high, the flow rate of the shower water was too low, and the cooling rate in the temperature range of the finish-rolling temperature to 700°C was too low) deviated from the conditions stipulated in the present invention.
  • a billet was subjected to heating, soaking, and descaling preceding rolling in the same way as the aforementioned wire rod forming process 3. Successively, the billet was subjected to finish rolling, cooling, and coiling in the same way as the aforementioned wire rod forming process 2.
  • Each of the steel wire rods thus fabricated was evaluated by measuring the values of ⁇ Cu and ⁇ Ni by the aforementioned methods, and measuring the pickling performance and the scale thickness in the following manner.
  • a fabricated steel wire rod was cut into test pieces 100 mm in length each and the test pieces were subjected to the following pickling test (beaker test) with the number of samples (n) per test being three.
  • the test here was carried out under the same conditions as pickling treatment adopted in commercial production.
  • Acid solution 15% sulfuric acid solution, containing an inhibitor (cationic amine derivative) by 0.5% to prevent a base steel from dissolving and ferrous iron by 20 g/L as an iron component,
  • a scale exfoliation ratio after pickling was defined by the percentage of the ratio of scale exfoliated at pickling (B) to the ratio of the originally existing scale (A which will be described later) (B/A x 100 (%)):
  • a % W 0 - W 1 / W 0 ⁇ 100 , wherein A was the ratio of originally existing scale (the ratio of scale to a steel wire rod), W 0 represents the weight (g) of the steel wire rod before being dipped (as rolled, bearing scale), and W 1 represents the weight (g) of the steel wire rod after dipped in the aforementioned acid solution at 60°C until the existing scale was completely exfoliated; and
  • B % W 01 - W 2 / W 01 ⁇ 100 , wherein B was the ratio of the scale exfoliated after pickled under the aforementioned conditions, W 01 represents the weight (g) of the steel wire rod before being dipped (as
  • the thickness (the maximum thickness) of scale on each of the fabricated steel wire rods was measured on the basis of a photograph (3,000 magnifications) taken with an Fe-SEM (a field emission type scanning electron microscope S-4500 made by Hitachi, Ltd.).
  • the steel wire rod when the thickness of scale measured as stated above was 40 ⁇ m or less, the steel wire rod was judged as acceptable.
  • a spring steel wire (an oil-tempered wire) 4.0 mm in diameter was fabricated from each of the aforementioned steel wire rods under the following conditions (corresponding to the aforementioned spring forming process (a)); Surface coating treatment ⁇ drawing (dry wire drawing) ⁇ oil tempering (heating temperature: 930°C, quenching oil temperature: 70°C, tempering temperature: 450°C, and cooling after tempering: water cooling).
  • the steel types A to K shown in Table 1 are the examples which satisfy the steel compositions stipulated in the present invention
  • the steel types I and J are the comparative examples wherein the ratios (Si/Cu) are lower than the range stipulated in the present invention
  • the steel type K is the comparative example wherein the Si content exceeds the range stipulated in the present invention.
  • the code “A-1” represents the case of using the steel type A shown in Table 1 and adopting the wire rod forming process 1 as the fabrication method
  • the code “A-2” represents the case of using the steel type A shown in Table 1 and adopting the wire rod forming process 2 as the fabrication method. The same is applied to other codes.
  • the cases of Nos. 1, 4, 7, 8, 11, 12, 15, 18, 19, 22, 23, and 26 are the invention examples wherein the values ⁇ Cu and ⁇ Ni stipulated in the present invention satisfy the ranges stipulated in the present invention and, in any of the cases, the scale exfoliation ratio is 100% and the pickling performance is outstandingly excellent. Further, as a result of examining the compositions of the scale of the wire rods by the X-ray diffraction method, it was confirmed that the composition was controlled in the desirable range in any of the cases (not shown in the tables). Furthermore, the surface properties of the oil-tempered wires fabricated from the aforementioned wire rods were good.
  • the tensile strength of the oil-tempered wires was measured in accordance with JIS Z2241 and resultantly it was confirmed that any of the oil-tempered wires had a high strength of about 1,900 to 2,100 MPa or more (not shown in the tables).
  • the cases of Nos. 29 to 32 are the comparative examples wherein the compositions of the steels deviate from the requirement of the present invention, thus the value ⁇ Cu or ⁇ Ni deviates from the range stipulated in the present invention, and hence the scale exfoliation ratio is low and intended pickling performance cannot be obtained. Further, the surface properties of the oil-tempered wires fabricated from such wire rods also deteriorate.
  • the spring steel wire rods were fabricated through the aforementioned spring forming process (a).
  • the spring forming process is not limited to the spring forming process (a) and it has been experimentally confirmed that a spring steel wire rod outstandingly excellent in surface properties can be obtained even when, for example, the aforementioned spring forming process (b) or (c) is adopted.

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Claims (4)

  1. Federstahlwalzdraht, umfassend:
    C: 0,35% bis 0,7% (Masse%, gleiches gilt nachfolgend soweit nicht anders spezifiziert);
    Si: 1,5% bis 2,50%;
    Mn: 0,05% bis 1,0%;
    Cr: 0,05% bis 1,9%;
    Cu: 0,05% bis 0,7%;
    Ni: 0,15% bis 0,8%;
    P: 0,02% oder weniger (ausgeschlossen 0%); und
    S: 0,02% oder weniger (ausgeschlossen 0%),
    und der Rest davon besteht aus Fe und unvermeidbare Verunreinigungen, wobei das Verhältnis von Si zu Cu (Si/Cu) in dem Bereich von 4,0 oder mehr liegt, und
    der Unterschied zwischen der Konzentration von Cu in der Oberflächenschicht und der Konzentration von Cu im Stahl 0,50% oder weniger beträgt und der Unterschied zwischen der Konzentration von Ni in der Oberflächenschicht und der Konzentration von Ni im Stahl 1,00% oder weniger beträgt,
    der Federstahlwalzdraht wird durch das Erwärmen und das anschließende Warmwalzen eines Stranges in eine lineare Form erhalten, dadurch gekennzeichnet, dass dieses Verfahren ein dem Warmwalzverfahren vorausgehendes Entzunderungsverfahren einschließt, wobei eine Wasserdusche für 1 bis 10 Sekunden mit einem Wasserdruck im Bereich von 80 kgf/mm2 bis 160 kgf/mm2 angewendet wird, und
    dass das Warmwalzverfahren das Kühlen mit einer Dusche in einem Fertigwalzverfahren nach der Anwendung des Vorwalzens einschließt, wobei die Fertigwalztemperatur im Bereich von 800° bis 1.000°C liegt, und wobei die Kühlrate in dem Temperaturbereich einer Temperatur nach der Beendigung des Fertigwalzens bis etwa 700°C auf 4°C/sec bis 20°C/sec reguliert wird.
  2. Federstahlwalzdraht, umfassend:
    C: 0,35% bis 0,7% (Masse%, gleiches gilt nachfolgend soweit nicht anders spezifiziert);
    Si: 1,5% bis 2,50%;
    Mn: 0,05% bis 1,0%;
    Cr: 0,05% bis 1,9%;
    Cu: 0,05% bis 0,7%;
    Ni: 0,15% bis 0,8%;
    P: 0,02% oder weniger (ausgeschlossen 0%);
    S: 0,02% oder weniger (ausgeschlossen 0%); und
    wobei der Federstahlwalzdraht ferner mindestens ein Element enthält, ausgewählt aus der Gruppe, umfassend:
    V: 0,07% bis 0,4%;
    Ti: 0,01 % bis 0,1 %; und
    Nb: 0,01 % bis 0,1 %,
    und der Rest davon besteht aus Fe und unvermeidbare Verunreinigungen, wobei das Verhältnis von Si zu Cu (Si/Cu) in dem Bereich von 4,0 oder mehr liegt, und
    der Unterschied zwischen der Konzentration von Cu in der Oberflächenschicht und der Konzentration von Cu im Stahl 0,50% oder weniger beträgt und der Unterschied zwischen der Konzentration von Ni in der Oberflächenschicht und der Konzentration von Ni im Stahl 1,00% oder weniger beträgt,
    der Federstahlwalzdraht wird durch das Erwärmen und das anschließende Warmwalzen eines Stranges in eine lineare Form erhalten, dadurch gekennzeichnet, dass dieses Verfahren ein dem Warmwalzverfahren vorausgehendes Entzunderungsverfahren einschließt, wobei eine Wasserdusche für 1 bis 10 Sekunden mit einem Wasserdruck im Bereich von 80 kgf/mm2 bis 160 kgf/mm2 angewendet wird, und
    dass das Warmwalzverfahren das Kühlen mit einer Dusche in einem Fertigwalzverfahren nach der Anwendung des Vorwalzens einschließt, wobei die Fertigwalztemperatur im Bereich von 800° bis 1.000°C liegt, und wobei die Kühlrate in dem Temperaturbereich einer Temperatur nach der Beendigung des Fertigwalzens bis etwa 700°C auf 4°C/sec bis 20°C/sec reguliert wird.
  3. Feder, hergestellt aus dem Federstahlwalzdraht nach Anspruch 1 oder 2.
  4. Verfahren zur Herstellung des Federstahlwalzdrahtes nach Anspruch 1 oder 2, dadurch gekennzeichnet, dass das Verfahren ein dem Warmwalzverfahren vorausgehendes Entzunderungsverfahren einschließt, wobei eine Wasserdusche für 1 bis 10 Sekunden mit einem Wasserdruck im Bereich von 80 kgf/mm2 bis 160 kgf/mm2 angewendet wird,
    das Warmwalzverfahren das Kühlen mit einer Dusche in einem Fertigwalzverfahren nach der Anwendung des Vorwalzens einschließt, wobei die Fertigwalztemperatur im Bereich von 800° bis 1.000°C liegt, und wobei die Kühlrate in dem Temperaturbereich einer Temperatur nach der Beendigung des Fertigwalzens bis etwa 700°C auf 4°C/sec bis 20°C/sec reguliert wird.
EP06021771A 2005-11-18 2006-10-17 Federstahldraht mit Leistung der Beizen Not-in-force EP1788105B1 (de)

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JP5215720B2 (ja) * 2008-04-28 2013-06-19 株式会社神戸製鋼所 鋼線材
CN102162068B (zh) * 2010-02-21 2013-07-31 宝山钢铁股份有限公司 一种弹簧钢及其制造和热处理方法
CN101928892B (zh) * 2010-08-27 2012-05-02 南京钢铁股份有限公司 一种弹簧钢圆钢及其生产工艺
CN102560263B (zh) * 2012-01-10 2014-10-01 石家庄钢铁有限责任公司 保淬透性高强度低温韧性弹簧钢
BR112017019994A2 (pt) 2015-04-08 2018-06-19 Nippon Steel & Sumitomo Metal Corporation membro de folha de aço tratada termicamente e método para produzir o mesmo
BR112017020003A2 (pt) 2015-04-08 2018-06-19 Nippon Steel & Sumitomo Metal Corporation membro de folha de aço tratada termicamente e método de produção do mesmo
JP6380658B2 (ja) * 2015-04-08 2018-08-29 新日鐵住金株式会社 熱処理用鋼板
JP6448529B2 (ja) * 2015-12-25 2019-01-09 株式会社神戸製鋼所 コイリング性に優れた鋼線およびその製造方法
JP6691452B2 (ja) * 2016-07-21 2020-04-28 株式会社神戸製鋼所 ばね用鋼線
CN106947921A (zh) * 2017-03-20 2017-07-14 石家庄钢铁有限责任公司 一种高速铁路弹条用耐腐蚀弹簧钢及其生产方法

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KR20080085802A (ko) 2008-09-24
EP1788105A1 (de) 2007-05-23
KR20070053124A (ko) 2007-05-23
US20070125455A1 (en) 2007-06-07
CN100462470C (zh) 2009-02-18
JP2007138259A (ja) 2007-06-07
KR100891764B1 (ko) 2009-04-07
CN1982494A (zh) 2007-06-20

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