CN102227512B - Steel wire for low-temperature annealing and method for producing same - Google Patents
Steel wire for low-temperature annealing and method for producing same Download PDFInfo
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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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
- 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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Abstract
Provided is a steel wire for low-temperature annealing which comprises, by mass%, C: 0.10% to 0.60%, Si: 0.01% to 0.40%, Mn: 0.20% to 1.50%, P: 0% to 0.040%, S: 0% to 0.050%, and N: 0.0005% to 0.0300%, and further comprises one or more selected from Cr: 0.03% to 0.4%, V: 0.03% to 0.2%, and Mo: 0.03% to 0.2%, with Fe and inevitable impurities as the remainder. The volume percent of pearlite structure is between 1.40*(C%)*100% and 100%, the volume percent of proeutectoid ferrite is between 0% and (1 - 1.25*(C%))*50%, and the volume percent of bainite structure is between 0% and 40%. The tensile strength is between 480 + 850*Ceq. MPa and 580 + 1130 Ceq. MPa.
Description
Technical field
The present invention relates to raw-material steel wire for low-temperature annealing and manufacture method thereof as mechanical parts such as the bolt by cold-forging forming, screw, nuts.Be particularly related to softening characteristic and ductility steel wire for low-temperature annealing and the manufacture method thereof good, that can under lower temperature, anneal brought by annealing.
The application is based on Japanese patent application 2009-262158 number that proposed on November 17th, 2009 and advocate its right of priority, quotes its content here.
Background technology
In cold forging, dimensional precision and the productivity of finished product are good, thereby when the mechanical parts such as the bolt of shaping steel, screw, nut, and the conversion from the forge hot carried out to cold forging is in the past enlarging.On the other hand, for cold forging, compare with forge hot, the deformation resistance of steel increases, and the energy of deformation of steel reduces, and therefore the load of mould is increased.Therefore, in cold forging, easily produce wearing and tearing or the damage that mould occurs or the problem such as processing crackle occurs in molded component.
In order to avoid these problems, require very high processibility for steel used in the cold forging.Therefore, make the hot rolling material softening by thermal treatments such as Spheroidizing Annealings in the past, thereby improved the processibility of steel.
Spheroidizing Annealing is by making cementite become the spherical processing that improves processibility, and it extensively processes to carry out as the softening of Cold Forging Steel.In this Spheroidizing Annealing, need about about 20 hours heat treatment time, therefore in recent years, for productivity and the cost that improves parts, the requirement of shortening heat treatment time, reduction annealing temperature or omission annealing is constantly surging.
In addition, for steel for mechanical structure, in order to ensure the intensity as mechanical part necessity, sometimes add the alloying elements such as Cr and Mo or V.If known have in steel these alloying elements of interpolation, then when softening anneal, the nodularization of cementite postponed, and the intensity after the annealing improves, and makes the ductility reduction, and forging is deteriorated.So, in the situation that add these alloying elements in the steel, in order to improve forging, adopt the methods such as Spheroidizing Annealing of carrying out more than 2 times.
In addition, in recent years, take the multifunction of the reduction of parts manufacturing cost and parts as purpose, component shape is also complicated.Therefore, the requirement of the processibility of the steel that use in the cold forging improved.About the processibility of Cold Forging Steel, the ductility of the generation of the deformation resistance of influential load on mould and impact processing crackle, the both sides in them or a side are suggested requirement as the processibility of Cold Forging Steel.The desired characteristic of the processibility of this Cold Forging Steel (deformation resistance or ductility) is different because of each purposes.
Based on such background, the technology as the forging that improves steel had proposed several different methods in the past.For example, clear very early is that 20～30% rough silk promotes the nodularization of cementite to make the method for steel softening and by repeatedly carrying out the softening technology such as method that Spheroidizing Annealing makes the steel softening by carry out relative reduction in area before Spheroidizing Annealing, and these technology were widely adopted in the past.
In addition, in patent documentation 1, disclose by the ferritic structure minute rate with hot rolling wire and be defined as more than the 30 area %, the total of bainite structure and martensitic stucture is defined as more than the 50 area % of remainder, can carry out at low temperature and with the short period of time method of the processing of the Spheroidizing Annealing behind the rough silk.In the method, the treatment temp of Spheroidizing Annealing is reduced, or shorten the treatment time, but the forgings such as the hardness after the annealing or limit rate of compression being equal with Spheroidizing Annealing material in the past, is inadequate from the aspect of processibility.
In addition, in patent documentation 2, manufacture method as case-hardened steel, disclose to have carried out relative reduction in area be after wire drawing more than 28% draws processing to the bainite volume fraction being suppressed at steel by the ferrite and pearlite organizational composition below 50%, carried out the method for Spheroidizing Annealing.In the method, the hardness after the Spheroidizing Annealing is low and even, the steel softening, but the ductility of steel is still insufficient.
In addition, in patent documentation 3, disclose by the pseudopearlite in the regulation steel tissue and bainite and ferritic area occupation ratio shortens the spheroidizing time, reduce the method for the deformation resistance of steel.In the method, sometimes need in the steel tissue, contain the pseudopearlite more than 10%, in the situation of the wire rod that therefore, steel grade that hardenability is low low at the content that is alloying element or wire diameter are large, need to after batching, improve speed of cooling, thereby have the problem that increases manufacturing cost.
The prior art document
Patent documentation
Patent documentation 1: TOHKEMY 2006-37159 communique
Patent documentation 2: TOHKEMY 2006-124774 communique
Patent documentation 3: TOHKEMY 2006-225701 communique
Summary of the invention
The problem that invention will solve
The object of the invention is to, the temperature when a kind of softening annealing that can make before the cold forging is provided reduces and be steel wire and manufacture method thereof soft and the excellent in cold forging property that ductility improves after this softening annealing.
Solve the method for problem
The present inventors are in order to improve the forging of steel wire, and the relation of the mechanical characteristics during to tissue before the annealing of steel and with the rough processing after annealing of these steel is investigated.
The present inventors find, if suppress just to analyse ferritic structure and bainite structure, tissue in the control steel wire, the main tissue that contains pearlitic structure that forms, even when then in steel wire, containing Cr or Mo, V etc. and hindering the element of cementite nodularizations, by carrying out under given conditions rough processing, with the steel wire intensity control in specific value, strength degradation when steel wire is carried out low-temperature annealing, ductility significantly improves.When making the cementite nodularization by rough processing and low-temperature annealing, if being analysed ferritic volume fraction, first in the tissue before rough suppress, the homodisperse tissue of rear cementite that then can obtain annealing, the ductility of steel wire significantly improves.Have, low-temperature annealing is for making the steel softening at A again
C1The annealing of carrying out below the point.
In addition, the present inventors find, just analyse in the tissue that mainly contains pearlitic structure of ferrite and bainite having suppressed, and when annealing, the size of the spheroidite uniformly tendency that becomes are arranged, and can suppress the generation of thick spheroidite.Thick spheroidite plays a role as the starting point of ductile failure, and therefore in order to improve the processibility of steel wire, it is effective suppressing this thick spheroidite.
In addition, the present inventors find: by suppressing bainite structure and the martensitic stucture in the steel wire, carried out rough and low-temperature annealing after, can make the steel wire softening by the strength decreased that makes steel wire, but also can improve ductility.Bainite structure and martensitic stucture are effectively for making the cementite nodularization, but dislocation desity is high.Therefore, in the such low temperature and the annealing of short period of time of low-temperature annealing, infer that the softening of steel wire is easily not enough.The present inventors are studied repeatedly based on above-mentioned experience, so that finished the present invention.The present invention is as described below.Have again, in the following, the content (mass percent) of C is expressed as (C%).
(1) steel wire for low-temperature annealing of a form of the present invention, contain C:0.10～0.60%, Si:0.01～0.40%, Mn:0.20～1.50%, P:0～0.040%, S:0～0.050%, N:0.0005～0.0300% in quality %, and further contain in Cr:0.03～0.4%, V:0.03～0.2%, Mo:0.03～0.2% more than a kind, remainder is made of Fe and inevitable impurity; Described steel wire has to contain just analyses ferritic structure, the metal structure of pearlitic structure and bainite structure, and the volume fraction of described pearlitic structure is more than 1.40 * (C%) * 100% and below 100%, it is described that just to analyse ferritic volume fraction be more than 0% and (1-1.25 * (C%)) * below 50%, the volume fraction of described bainite structure is 0%～40%, described volume fraction of just analysing ferritic structure, the volume fraction of described bainite structure and the volume fraction of described pearlitic structure add up to 95%～100%, tensile strength is that 480+850 * Ceq.MPa is above and below 580+1130 * Ceq.MPa.
Wherein, Ceq.=(C%)+(Si%)/7+(Mn%)/5+(Cr%)/9+(Mo%)/2+1.54 * (V%).
Have again, (C%), (Si%), (Mn%), (Cr%), (Mo%) and (V%) be respectively the content (quality %) of C, Si, Mn, Cr, Mo and V.
(2) above-mentioned (1) described steel wire for low-temperature annealing, in quality % can further contain in Al:0.001～0.060%, Ti:0.002～0.050%, Nb:0.005～0.100%, B:0.0001～0.0060%, Cu:0.01～0.3%, Ni:0.01～0.7%, Ca:0.0001～0.010%, Mg:0.0001～0.010%, Zr:0.0001～0.010% more than a kind.
(3) in above-mentioned (1) or (2) described steel wire for low-temperature annealing, the average block size of described pearlitic structure also can be 4 μ m～20 μ m.
(4) in the manufacture method of the steel wire for low-temperature annealing of a form of the present invention, comprise following operation: the heating steel billet that will have above-mentioned (1) or (2) described composition; Carry out hot rolling; Then, batch; Afterwards, constant temperature kept 30 seconds～150 seconds in 400 ℃～600 ℃ fused salt groove; Then, cool off; The enforcement relative reduction in area is more than 25+82 * F1% and is lower than 100% Wire Drawing.
The invention effect
According to the present invention, can steel be configured as complicated shape by cold forging, and the yield rate of steel and productivity improves, can reduce the processing charges of parts.In addition, according to the present invention, the temperature of softening annealing is reduced, and can reduce the thermal treatment expense, boost productivity.
Description of drawings
Fig. 1 is the diagram of relation of the tensile strength TS of the tensile strength TS of the steel wire before the expression annealing and the steel wire after the low-temperature annealing.
Fig. 2 is the diagram of the relation of the tensile strength TS after expression carbon equivalent Ceq. and the annealing.
Fig. 3 is the diagram of the relation of constriction value (the being also referred to as relative reduction in area) RA after expression carbon equivalent Ceq. and the annealing.
Fig. 4 is the diagram of the relation of expression F1 value and wire drawing relative reduction in area.
Fig. 5 is the diagram of relation of the volume fraction of expression C content (C%) and pearlitic structure.
Fig. 6 is the diagram of the relation of expression C content (C%) and the volume fraction of just analysing ferritic structure.
Fig. 7 is the diagram of expression carbon equivalent Ceq. and the relation of the tensile strength TS of the front steel wire of annealing.
Embodiment
Technology as improving the steel forging had proposed several different methods in the past.In the present invention, in order before cold forging, to carry out the softening annealing under the temperature lower than in the past annealing temperature, after the annealing of this softening, obtain soft and ductility is high, the steel wire of excellent in cold forging property, need to be with the organizational controls of steel wire (wire rod) specifically to organize.
Below, the steel wire for low-temperature annealing of one embodiment of the present invention is described.At first, the restriction reason of tissue described.
Surpass (1-1.25 * (C%)) * 50% if just analyse the volume fraction of ferrite (just analysing ferritic structure), then generate the inhomogeneous part of intensity because of the rear cementite skewness of annealing.If there is the inhomogeneous part of intensity, then add man-hour in forging, sometimes concentrate because of the distortion of part the cold forging crackle occurs.Therefore, just analyse ferritic volume fraction on be limited to (1-1.25 * (C%)) * 50%.In addition, just analyse ferrite owing to need in the tissue of steel wire, exist, therefore just analyse the lower of ferritic volume fraction and be limited to 0%.
Bainite structure is effectively for the nodularization of cementite, have the effect of the ductility that improves steel wire, but dislocation desity is high, and therefore the intensity after the low-temperature annealing improves sometimes.Therefore, the volume fraction of bainite structure on be limited to 40%.In addition, owing to need in the tissue of steel wire, not have bainite, so the lower of the volume fraction of bainite is limited to 0%.
Martensitic stucture improves the intensity after the annealing, therefore preferably it is suppressed at below 5%.
The nodularization of the cementite of pearlitic structure after for rough annealing is effectively, has the effect of the deformation resistance that reduces steel wire.In addition, in the large situation of the volume fraction of pearlitic structure, the deviation of the size of the spheroidized carburization body after the annealing reduces, and the ductility of steel wire improves.Be lower than at the volume fraction of pearlitic structure in 1.40 * (C%) * 100% the situation, the attenuating effect of deformation resistance and the raising effect of ductility reduce, so the lower of the volume fraction of pearlitic structure is limited to 1.35 * (C%) * 100%.
Have, the metal structure of steel wire contains just analyses ferrite, bainite and perlite again, the volume fraction of above-mentioned first volume fraction of analysing ferritic structure, bainite structure and the volume fraction of pearlitic structure add up to 95%～100%.
The miniaturization of the average block size of pearlitic structure has the effect of the Ferrite Grain Size after reducing to anneal, and is effective for improving ductility.In addition, the miniaturization by this average block size promotes the pearlitic decomposition of stratiform and the nodularization of cementite, thereby can shorten annealing time.If the average block size of this pearlitic structure then can shorten annealing time below 20 μ m, after annealing, guarantee enough ductility simultaneously.Therefore, the upper limit of the average block size of pearlitic structure is preferably 20 μ m.In addition, the restriction aspect on the mensuration of average block size considers, the lower limit of the average block size of pearlitic structure also can be 4 μ m.
Have again, in order to estimate the volume fraction of just analysing ferritic structure, pearlitic structure, bainite structure, adopt sweep electron microscope, with C section (with the length direction vertical section of the wire rod) photography photo of 1000 times multiplying powers to wire rod, obtain the area occupation ratio of each tissue by image analysis.Here, at the C of wire rod section, to near the top layer (surface) of wire rod, 1/4D section (from the surface of wire rod on the center position of wire rod at a distance of 1/4 part of the diameter of wire rod) and 1/2D section (centre portions of wire rod) carry out photo and photograph, the photography zone of position all is 125 μ m * 95 μ m separately.In addition, the area occupation ratio of the tissue that micro-minute surface (C section) is contained equates with the volume fraction of tissue, therefore will be evaluated as by each area occupation ratio of organizing that image analysis obtains the volume fraction of each tissue.
In the mensuration of the piece size of pearlitic structure, adopt the EBSD device.Respectively section, 1/4D section, 1/2D section near the top layer of the C section of wire rod have been measured the zone of 275 μ m * 165 μ m.Be that border more than 15 degree is defined as the piece crystal boundary from the crystal orientation image that adopts the ferrite (ferrite the pearlitic structure) that the EBSD device measures with azimuth difference.
In addition, in the steel wire of present embodiment, tensile strength TS is more than 480+850 * Ceq.MPa.During less than 480+850 * Ceq.MPa, the softening of the steel wire after the annealing is insufficient at tensile strength TS, and forging is deteriorated.In addition, in order fully to guarantee the energy of deformation of steel wire, tensile strength TS also can be for below 580+1130 * Ceq.MPa.Here, carbon equivalent Ceq. represents with following formula (1).
Ceq.＝(C％)+(Si％)/7+(Mn％)/5+(Cr％)/9+(Mo％)/2+1.54×(V％) (1)
Have again, (C%), (Si%), (Mn%), (Cr%), (Mo%) and (V%) be respectively the content (quality %) of C, Si, Mn, Cr, Mo and V.
The steel wire of present embodiment also can contain C:0.10～0.60%, Si:0.01～0.40%, Mn:0.20～1.50%, P:0～0.040%, S:0～0.050%, N:0.0005～0.0300% in quality %, and further contain in Cr:0.03～0.4%, V:0.03～0.2%, Mo:0.03～0.2% more than a kind.Below, the reason of the scope that limits these elements is described.Have, about the content of each element, below the % of record is quality % again.
C guarantees to add in the steel as the intensity of mechanical part.Be lower than at 0.10 o'clock at C content, can not guarantee the intensity as mechanical part necessity.In addition, if C content surpasses 0.60%, then forging is deteriorated.Therefore, the C content in the steel is defined as 0.10～0.60%.In order to guarantee more reliably the intensity of steel, C content is preferably 0.25～0.60%.In addition, in order to guarantee more reliably forging, C content more preferably 0.25～0.50%.
Si plays a role as deoxidant element, gives necessary intensity and hardenability to steel, is to improving the effective element of temper softening impedance.When Si content was lower than 0.01%, these effects were insufficient.In addition, if Si content surpasses 0.40%, then toughness and ductility are deteriorated, and hardness rises, and forging is deteriorated.Therefore, the Si content in the steel is defined as 0.01～0.40%.In addition, in order to improve more reliably temper softening impedance and forging, Si content is preferably 0.05～0.30%.
Mn gives necessary intensity and the necessary element of hardenability for steel.When Mn content was lower than 0.20%, the effect of giving intensity and hardenability was insufficient.If Mn content surpasses 1.50%, then hardness rises, and forging is deteriorated.Therefore, Mn content is defined as 0.20～1.50%.In addition, in order to guarantee more reliably intensity and forging, Mn content is preferably 0.30～0.90%.
Deformation resistance when P improves cold forging makes processibility deteriorated.In addition, P is to grain boundary segregation, because the embrittlement of grain boundaries behind the Q-tempering makes the toughness of steel deteriorated.Therefore, wish P in the reduce steel.So, with the ceiling restriction of P content 0.040%.This P content is preferably below 0.020%.In addition, the lower of P content is limited to 0%.
S is by the form with sulfide exists with the reaction of the alloying element such as Mn.These sulfide improve the machinability of steel.But, in steel, add S if surpass 0.050% ground, then forging is deteriorated, because the embrittlement of grain boundaries behind the Q-tempering makes toughness deteriorated.Therefore, with the ceiling restriction of S content 0.050%.This S content is preferably below 0.020%.In addition, the lower of S content is limited to 0%.
N adds with the fine purpose that turns to of austenite crystal.N is combined with alloying elements such as Al or Ti and is formed nitride, and these nitride play a role as the pinning particle, thereby make the crystal grain micronize.When N content is lower than 0.0005%, nitride separate out quantity not sufficient, because coarse grains makes ductility deteriorated.In addition, make N content surpass 0.0300% if add N, the dynamic strain aging that then produces because of solid solution N increases deformation resistance, thereby makes processibility deteriorated.Therefore, N content is defined as 0.0005～0.0300%.In order to guarantee more reliably ductility, deformation resistance is fully reduced, N content is preferably 0.0020～0.0150%.
Cr has the effect that improves hardenability and intensity.When Cr content is lower than 0.03%, do not improve the effect of hardenability and intensity.Make Cr content surpass 0.4% if add Cr, then transformation time prolongs, infringement productivity.Therefore, the Cr content in the steel is defined as 0.03～0.4%.In order further to boost productivity, Cr content is preferably 0.03～0.2%.In addition, in order further to improve hardenability and intensity, Cr amount more preferably 0.05～0.20%.
V has and improves hardenability or make fine Carbide Precipitation, put forward high-intensity effect.When V content is lower than 0.03%, do not improve the effect of hardenability and intensity.Make V content surpass 0.2% if add V, the thick carbide that then contains V because of formation makes these effects saturated.Therefore, the V content in the steel is defined as 0.03～0.2%.In order more effectively to improve hardenability and intensity, the V amount is preferably 0.05～0.15%.
Mo has the effect that improves hardenability and intensity.When Mo content is lower than 0.03%, do not improve the effect of hardenability and intensity.Make Mo content surpass 0.2% if add Mo, then transformation time prolongs, infringement productivity.Therefore, Mo content is defined as 0.03～0.2%.In addition, in order further to boost productivity, improve simultaneously hardenability and intensity, Mo content is preferably 0.05～0.15%.
In addition, in the steel wire of present embodiment, in order to improve the characteristic of the following stated, can in quality % contain in Al:0.001～0.060%, Ti:0.002～0.050%, Nb:0.005～0.100%, B:0.0001～0.0060%, Cu:0.01～0.3%, Ni:0.01～0.7%, Ca:0.0001～0.010%, Mg:0.0001～0.010%, Zr:0.0001～0.010% more than a kind.
Al adds with the purpose of the miniaturization of deoxidation and austenite crystal.Al plays a role as deoxidant element, is combined with N to form AlN in steel.This AlN plays a role as the pinning particle, makes the crystal grain micronize, thereby improves processibility.In addition, Al has by fixing solid solution N and suppresses dynamic strain aging, reduces the effect of deformation resistance.When Al content is lower than 0.001%, can not bring into play these effects.In addition, if Al content surpasses 0.060%, then the toughness of steel is deteriorated.Therefore, with the ceiling restriction of Al content 0.060%.So, when in steel, adding Al, the Al content in the steel is controlled at 0.001～0.060%.If consider the balance of above-mentioned effect and toughness, Al content more preferably 0.003～0.04%.
Ti and Nb form carbonitride.These carbonitrides are dispersed in the steel, play a role as the pinning particle, suppress thickization of crystal grain, improve processibility, improve simultaneously the intensity of steel.
Ti and C or N form compound, with the form existence of TiC, TiN or Ti (CN).These carbonitrides are effectively as the pinning particle, have the function of the intensity that improves steel.In addition, add Ti in order to effectively bring into play the effect of the raising hardenability that the B of interpolation described later brings by the N in the fixing steel.When Ti content is lower than 0.002%, can not embody above-mentioned effect.Make Ti content surpass 0.050% if add Ti, then above-mentioned effect is saturated, and hardness rises simultaneously, makes forging deteriorated.Therefore, when in steel, adding Ti, the Ti content in the steel is controlled at 0.002～0.050%.In addition, in order further to improve intensity and the forging of steel, Ti content is preferably 0.005～0.030%.
Nb is combined with N or C, and forming NbN, NbC or their complex inclusion is Nb (CN), effectively plays a role for thickization that suppresses austenite crystal.Therefore, Nb has the function of the intensity that improves steel.When Nb content was lower than 0.005%, the effect that suppresses thickization of austenite crystal was insufficient.Make Nb content surpass 0.10% if add Nb, then above-mentioned effect is saturated.So, when in steel, adding Nb, the Nb content in the steel is controlled at 0.005～0.10%.In addition, in order further to improve the intensity of steel, Nb content is preferably 0.01～0.05%.
B adds for improving hardenability.When B content was lower than 0.0001%, the effect that improves hardenability was insufficient.Make B content surpass 0.0060% if add B, then its effect is saturated.Therefore, when in steel, adding B, the B content in the steel is controlled at 0.0001～0.0060%.In addition, in order more effectively to improve hardenability, B content is preferably 0.0005～0.004%.
Cu improves the intensity of steel by precipitation strength.When Cu content is lower than 0.01%, do not improve the effect of the intensity of steel.Make Cu content surpass 0.3% if add Cu, then hot rolling is deteriorated.Therefore, when in steel, adding Cu, the Cu content in the steel is controlled at 0.01～0.3%.In addition, in order effectively to improve the intensity of steel, fully guarantee hot rolling simultaneously, Cu content is preferably 0.05～0.2%.
Ni has the effect of the ductility that improves hardenability and steel.When Ni content is lower than 0.01%, do not improve the effect of the ductility of hardenability and steel.Make Ni content surpass 0.7% if add Ni, then transformation time prolongs, infringement productivity.Therefore, when in steel, adding Ni, the Ni content in the steel is controlled at 0.01～0.7%.In addition, in order to be fully enhanced the effect of ductility, preferably contain Ni more than 0.02% by adding Ni.And, in order further to guarantee productivity, Ni content more preferably 0.02～0.5%.
O is contained in the steel inevitably, exists with the form of the oxide compound of Al or Ti etc.If O content is high, then forms thick oxide compound, thereby become the reason of fatigure failure.Therefore, wish O content is controlled at below 0.01%.In addition, as deoxidant element, can in steel, contain among Ca, Mg, the Zr more than a kind.When in steel, adding Ca, the Ca content in the steel is controlled at 0.0001～0.01%.When in steel, adding Mg, the Mg content in the steel is controlled at 0.0001～0.01%.When in steel, adding Zr, the Zr content in the steel is controlled at 0.0001～0.01%.Ca, Mg and Zr are effectively for deoxidation, have by making the oxide compound miniaturization improve the effect of fatigue strength.
In addition, the below describes the manufacture method of the steel wire of one embodiment of the present invention.
With satisfying the heating steel billet of the desired above-mentioned composition of steel wire of above-mentioned embodiment, carry out hot rolling, make the steel wire of desirable diameter.The steel wire that obtains after the hot rolling is batched cool to room temperature after constant temperature keeps.There is no particular limitation for coiling temperature after the hot rolling, but be generally 750 ℃ to 1000 ℃ scope.
Also there is no particular limitation for speed of cooling after batching.For example, if the wire rod of wire diameter 5～16mm is immersed in 400 ℃～600 ℃ the fused salt groove, then this wire rod is cooled with the speed of cooling more than 10 ℃/second usually.Speed of cooling and composition of steel affect the tissue of steel (steel wire).That is to say, when the content of the alloying elements such as C, Si, Mn, Cr, Mo, V, B, Nb was high, if improve speed of cooling, then the volume fraction of bainite structure increased.In addition, when the content of such alloying element hanged down, if speed of cooling reduces, then the volume fraction of ferritic structure increased.Therefore, as long as select composition of steel and speed of cooling just passable in the mode of the tissue that obtains stipulating.
After the steel wire with hot rolling batches, the steel wire constant temperature in 400 ℃～600 ℃ fused salt groove that batches was kept 30 seconds～150 seconds, then cool off.When the temperature of fused salt groove was lower than 400 ℃, the bainite structure in the steel wire divided rate (volume fraction) to increase, and the intensity of the steel wire after the annealing improves, and the phase transformation concluding time prolongs, infringement productivity.If the temperature of fused salt groove surpasses 600 ℃, then ferritic structure divides rate (volume fraction) to increase, and fused salt decomposes, infringement productivity.When the hold-time of steel wire in the fused salt groove is lower than 30 seconds, in the situation that the constant temperature phase transformation does not finish to be cooled, therefore generate martensitic stucture.In this case, the desired softening time lengthening of annealing, intensity rises, and makes processibility deteriorated.In addition, the hold-time of steel wire in the fused salt groove more than 150 seconds the time, infringement productivity.So, this hold-time is controlled at 30 seconds～150 seconds.
After steel wire is extracted out from the fused salt groove steel wire is cooled off, then carrying out relative reduction in area is the above Wire Drawing of 25+82 * F1%.Here, F1 value (above-mentioned F1) represents with following formula (2).
F1＝(Cr％)+(Mo％)/4+(V％)/3 (2)
When the relative reduction in area of Wire Drawing was lower than 25+82 * F1%, the softening of the steel wire after the annealing was insufficient, and forging is deteriorated.Therefore, the undergage with the relative reduction in area of Wire Drawing is decided to be 25+82 * F1%.Have, in order to make the steel wire softening more after the low-temperature annealing, the relative reduction in area of Wire Drawing is preferably below 50% again.In addition, owing to use as steel wire, so the relative reduction in area of Wire Drawing is lower than 100%.
Have, by softening, and ductility improves the steel wire of above-mentioned embodiment by carrying out low-temperature annealing again.When stress relief annealed temperature was lower than 650 ℃, intensity was high, the effect of softening is low.Be A in stress relief annealed temperature
C1When point is above, sneak into pearlitic structure in the tissue of the steel wire after annealing, intensity and the ductility of steel wire are deteriorated.Therefore, preferably be controlled at stress relief annealed temperature more than 650 ℃ and be lower than A
C1The point.The stress relief annealed hold-time, there is no particular limitation, but stability and productivity in order to improve quality are preferably 30 minutes～7 hours.A is arranged again
C1(℃) can calculate by following formula (3).
A
c1＝723-10.7×(Mn％)+29.1×(Si％)+16.9×(Cr％)(3)
Embodiment
For the composition of examination steel, by the carbon equivalent Ceq. (%) of following formula (1) calculating and the A that calculates by following formula (3)
C1(℃) see Table 1.Have, steel grade L is the high comparative example of Cr content again.
With the heating steel billet to 950 of these steel grades～1150 ℃, carry out the steel wire hot rolling until wire diameter is 5.5～14.5mm, after this rod rolling, adopt the fused salt groove on the rolling line, carry out under the conditions shown in Table 2 the constant temperature phase transformation and process, cool off.This cooled wire rod is carried out Wire Drawing by the relative reduction in area shown in the table 2.The groove of fused salt shown in the table 2 temperature, fused salt groove hold-time and wire drawing relative reduction in area etc. are respectively created conditions and the pearlitic structure of each wire rod of constant temperature phase transformation after processing, just analyse the volume fraction of ferritic structure and bainite structure, the average block particle diameter of pearlitic structure, the tensile strength TS of steel wire.The lower value of the lower value of the wire drawing relative reduction in area that in addition, lower value by the volume fraction of 1.40 * (C%) * 100% pearlitic structure that calculates, the first higher limit of analysing the volume fraction of ferritic structure that calculates by (1-1.25 * (C%)) * 50% are shown in the lump also in this table 2, calculates by 25+82 * F1%, the tensile strength that calculates by 480+850 * Ceq..
The level 13 and 15 of table 2 is after batching in the situation that carry out constant temperature phase transformation processing in the manufacture method in the past of the rolling loose winding cooling line of wire rod (Stelmor) cooling steel wire.Therefore, in above-mentioned level 13 and 15, the volume fraction of pearlitic structure is insufficient, just analyses the ferritic structure surplus.
The mechanical characteristics of the steel wire of the comparative example of making by following manufacture method (Spheroidizing Annealing in the past) shown in the table 3 in addition.At first, the steel billet to steel grade A～R under condition same as described above carries out rod rolling, after the wire rod that will obtain thus batches, cools off at the rolling loose winding cooling of wire rod line.Then, carrying out after relative reduction in area is 25% Wire Drawing, this wire rod is being heated to 740 ℃ with 4 hours heating-up times, be incubated 4 hours.Then, after the wire rod of this heat tracing is cooled to 650 ℃ with 15 ℃/hour speed of cooling, in atmosphere, let cool.Have again, in order to measure their mechanical characteristics, adopt the 9A test film of JIS Z2201, carry out tension test according to the test method of JIS Z2241, estimate tensile strength TS and constriction value RA.
Tensile strength TS shown in the table 4 after the low-temperature annealing and constriction value RA.Have again, the comparison with the mechanical characteristics of the Spheroidizing Annealing material in the past shown in the table 3 (material of usually annealing) also is shown in this table 4 in the lump." excellent " characterization in the table 4 is better than Spheroidizing Annealing material in the past.In addition, " can " characterization and in the past Spheroidizing Annealing material equal (tensile strength TS is in ± 10MPa, and constriction value RA is in ± 2%).In addition, " bad " characterization is poorer than Spheroidizing Annealing material in the past.
Table 3
Table 4
The characteristic of the steel wire of the steel grade L that the level 22 expression Cr content of table 4 are high.In this level 22, be 60% Wire Drawing even carry out relative reduction in area, the tensile strength TS after the low-temperature annealing is also high, and the softening characteristic of steel wire is poorer than Spheroidizing Annealing material in the past.On the other hand, from the level 1,2,4,6,7,11,12,14,16,17,19,21 of table 4,23～28 embodiment as can be known: even low-temperature annealing, mechanical characteristics according to the steel wire of these level manufacturings is compared with Spheroidizing Annealing material in the past, for equal or good.
Fig. 1 illustrates in the table 2 relation of the tensile strength TS after the low-temperature annealing of the tensile strength TS of level 8,9,10,11,12 steel wire of record and these steel.Have, in these levels 8,9,10,11,12 steel wire, composition of steel and tissue (minute rate of each tissue) are equal again, and tensile strength TS is different.As shown in Figure 1, as can be known: in the situation that tensile strength TS is 480+850 * Ceq.MPa above (for example being more than 1064 ℃), the tensile strength TS of the steel wire after the low-temperature annealing reduces, the steel wire softening.
Fig. 2 illustrates in the table 4 the carbon equivalent Ceq. of the steel wire of the level 29～46 of record in the level 1～28 of record and the table 3 and the relation of the tensile strength TS after the annealing.As shown in Figure 2, as can be known: in the embodiment of table 4, compare with Spheroidizing Annealing material in the past, the tensile strength TS of steel wire is low, the steel wire softening.
Fig. 3 illustrates in the table 4 the carbon equivalent Ceq. of the steel wire of the level 29～46 of record in the level 1～28 of record and the table 3 and the relation of the constriction value RA after the annealing.As can be known: in the embodiment of table 4, compare with Spheroidizing Annealing material in the past, the constriction value RA of steel wire is high, and ductility is good.
Fig. 4 is the diagram of the relation of the F1 value of the above-mentioned formula of usefulness (2) expression of level 1～12,14,16～21,23～28 steel wire of expression table 2 and wire drawing relative reduction in area.Have, the steel wire of these levels satisfies above-mentioned tissue (volume fraction of each tissue) and composition again.For the steel wire of " the softening characteristic is good " among Fig. 4, the tensile strength TS after the low-temperature annealing shown in the table 4 compares with Spheroidizing Annealing material in the past, below equal.For the steel wire of " softening bad characteristic ", the tensile strength TS of the tensile strength TS of the steel wire after low-temperature annealing ratio Spheroidizing Annealing material in the past is high.Like this, as can be known: in the situation that the wire drawing relative reduction in area is more than 25+82 * F1%, the softening characteristic good of the steel wire after the low-temperature annealing.
The relation of the C content (C%) of the level 1,2,4,6,7,11～17,19,21 of table 2 shown in Fig. 5,23～28 steel wire and the volume fraction (perlite divides rate) of pearlitic structure.As can be known: the volume fraction of the pearlitic structure in steel wire is during less than 1.40 * (C%) * 100 (%) (level 13 and 15), and is as shown in table 4, compares the mechanical properties of the steel wire after the low-temperature annealing with Spheroidizing Annealing material in the past.
Equally, shown in Fig. 6 with Fig. 5 in the identical level of level used steel wire C content and just analyse the relation of the volume fraction (just analysing ferrite minute rate) of ferritic structure.As can be known: during greater than (1-1.25 * (C%)) * 50 (%) (level 13 and 15), as shown in table 4 at the volume fraction of just analysing ferritic structure, compare the mechanical properties of the steel wire after the low-temperature annealing with Spheroidizing Annealing material in the past.
The relation of tensile strength TS before the carbon equivalent Ceq. of the level 1～21 of table 2 shown in Fig. 7 and 23～28 steel wire and the annealing.As can be known: in tensile strength TS ( level 1,2,4,6,7,11,12,14,16,17,19,21,23～28) when 480+850 * Ceq.MPa is above, as shown in table 4, after low-temperature annealing, can obtain and the equal above characteristic of Spheroidizing Annealing material in the past.
Utilizability on the industry
As described above, according to the present invention, can steel be configured as by cold forging the parts of complicated shape, can improve yield rate and the productivity of steel, reduce the processing charges of parts.In addition, according to the present invention, can reduce the temperature of softening annealing, reduce the thermal treatment expense, boost productivity.Therefore, steel wire of the present invention is suitable as the starting material of the mechanical parts such as bolt by cold-forging forming, screw, nut.
Claims (5)
1. steel wire for low-temperature annealing, it is characterized in that, contain C:0.10～0.60%, Si:0.01～0.40%, Mn:0.20～1.50%, P:0～0.040%, S:0～0.050%, N:0.0005～0.0300% in quality %, and further contain in Cr:0.03～0.14%, V:0.03～0.2%, Mo:0.03～0.2% more than a kind, remainder is made of Fe and inevitable impurity;
Described steel wire has to contain just analyses ferritic structure, the metal structure of pearlitic structure and bainite structure, the volume fraction of described pearlitic structure is more than 1.40 * (C%) * 100% and below 100%, it is described that just to analyse ferritic volume fraction be more than 0% and (1-1.25 * (C%)) * below 50%, the volume fraction of described bainite structure is 0%～40%, described volume fraction of just analysing ferritic structure, the volume fraction of described bainite structure and the volume fraction of described pearlitic structure add up to 95%～100%, tensile strength is more than 480+850 * Ceq.MPa and below 580+1130 * Ceq.MPa
Wherein, Ceq.=(C%)+(Si%)/7+(Mn%)/5+(Cr%)/9+(Mo%)/2+1.54 * (V%).
2. steel wire for low-temperature annealing according to claim 1 is characterized in that, in quality % further contain in the following element more than a kind:
Al：0.001～0.060%、
Ti：0.002～0.050%、
Nb：0.005～0.100%、
B：0.0001～0.0060%、
Cu：0.01～0.3%、
Ni：0.01～0.7%、
Ca：0.0001～0.010%、
Mg：0.0001～0.010%、
Zr：0.0001～0.010%。
3. steel wire for low-temperature annealing according to claim 1 and 2 is characterized in that, the average block of described pearlitic structure is of a size of 4 μ m～20 μ m.
4. the manufacture method of a steel wire for low-temperature annealing is characterized in that, has following operation:
The heating steel billet that will have claim 1 or 2 described compositions;
Carry out hot rolling;
Then, batch;
Afterwards, constant temperature kept 30 seconds～150 seconds in 400 ℃～600 ℃ fused salt groove;
Then, cool off;
Implement relative reduction in area and be 25+82 * F1% above and 44% above but be lower than 100% Wire Drawing,
Wherein, F1=(Cr%)+(Mo%)/4+(V%)/3.
5. the manufacture method of steel wire for low-temperature annealing according to claim 4 is characterized in that, described relative reduction in area is that 25+82 * F1% is above and 50% above but be lower than 100%.
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