CN102227512A - 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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- CN102227512A CN102227512A CN2010800033289A CN201080003328A CN102227512A CN 102227512 A CN102227512 A CN 102227512A CN 2010800033289 A CN2010800033289 A CN 2010800033289A CN 201080003328 A CN201080003328 A CN 201080003328A CN 102227512 A CN102227512 A CN 102227512A
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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
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
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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 as the raw-material low-temperature annealing of mechanical parts such as the bolt by cold-forging forming, screw, nut with steel wire and manufacture method thereof.Be particularly related to the softening characteristic brought by annealing and ductility good, can under lower temperature, carry out the annealed low-temperature annealing with steel wire and manufacture method thereof.
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, the dimensional precision and the productivity of finished product are good, thereby when mechanical parts such as the bolt of shaping steel, screw, nut, are enlarging to the conversion of cold forging from the forge hot of carrying out in the past.On the other hand, for cold forging, compare with forge hot, the distortion impedance of steel is increased, and the energy of deformation of steel reduces, and therefore the load to mould increases.Therefore, in cold forging, be easy to generate wearing and tearing or the damage that mould takes place or problem such as processing crackle takes place 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 is extensively handled with the softening of steel as cold forging and carries out.In this Spheroidizing Annealing, need about about 20 hours heat treatment time, therefore in recent years, for productivity and the cost that improves parts, shortening heat treatment time, reduction annealing temperature or omission annealed require constantly surging.
In addition, for steel for mechanical structure,, add alloying elements such as Cr and Mo or V sometimes in order to ensure as the mechanical part necessary strength.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, the cold forging deterioration.So, in steel, add under the situation of these alloying elements, in order to improve cold forging, adopt the methods such as Spheroidizing Annealing of carrying out more than 2 times.
In addition, in recent years, be purpose with the reduction of parts manufacturing cost and the multifunction of parts, component shape is also complicated.Therefore, the requirement to the processibility of the steel that use in the cold forging improves.About cold forging with the processibility of steel, the ductility of the distortion impedance of influential load to mould and the generation of influence processing crackle, both sides in them or a side are suggested requirement as cold forging with the processibility of steel.This cold forging is different because of each purposes with the desired characteristic of processibility (distortion impedance or ductility) of steel.
Based on such background, the technology as the cold 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 ferritic structure branch rate 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 the method for the processing of the Spheroidizing Annealing behind the rough silk at low temperature and with the short period of time with hot rolling wire.In the method, the treatment temp of Spheroidizing Annealing is reduced, or shorten the treatment time, but cold forgings such as 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 in that 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 that are made of ferrite and pearlitic structure 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 pseudopearlite in the regulation steel tissue and bainite and ferritic area occupation ratio shortens the spheroidizing time, reduce the method for the distortion impedance of steel.In the method, sometimes need in the steel tissue, contain the pseudopearlite more than 10%, under the situation of the wire rod that steel grade therefore low at the content that is alloying element, that hardenability is low or line footpath are big, need batch back raising 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 objective of the invention is to, the temperature when a kind of softening annealing that can make before the cold forging is provided reduces and is steel wire and manufacture method thereof soft and the excellent in cold forging property that ductility improves in this softening annealing back.
Solve the method for problem
Present inventors are in order to improve the cold forging of steel wire, and the relation of the mechanical characteristics of tissue before the annealing of steel with the rough processing after annealing of these steel the time is investigated.
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 rough processing under given conditions, 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 back 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, 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 tendency uniformly 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, present inventors find: by suppressing bainite structure and the martensitic stucture in the steel wire, carried out rough and low-temperature annealing after, reduce and can make the steel wire softening by the intensity that makes steel wire, but also can improve ductility.Bainite structure and martensitic stucture are effectively for making the cementite nodularization, but the dislocation desity height.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 not enough easily.Present inventors study 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) the low-temperature annealing steel wire 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 comprises Fe and unavoidable impurities; 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 low-temperature annealing steel wire, 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) use in the steel wire in above-mentioned (1) or (2) described low-temperature annealing, the average block size of described pearlitic structure also can be 4 μ m～20 μ m.
(4) use in the manufacture method of steel wire in the low-temperature annealing of a form of the present invention, comprise following operation: the steel billet heating 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,, softening annealed temperature is reduced, and can reduce the thermal treatment expense, boost productivity according to the present invention.
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 preceding steel wire of annealing.
Embodiment
Technology as improving the steel cold 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, obtaining the steel wire of soft and ductility height, excellent in cold forging property after the annealing of this softening, need be specific tissue with the organizational controls of steel wire (wire rod).
Below, the low-temperature annealing of one embodiment of the present invention is described with steel wire.At first, the qualification reason to tissue describes.
Surpass (1-1.25 * (C%)) * 50% if just analyse the volume fraction of ferrite (just analysing ferritic structure), then generate the uneven part of intensity because of the back cementite skewness of annealing.If there is the uneven part of intensity, then add man-hour in forging, concentrate because of partial distortion sometimes the cold forging crackle takes place.Therefore, just analyse ferritic volume fraction on be limited to (1-1.25 * (C%)) * 50%.In addition, just analyse ferrite, therefore just analyse the following of ferritic volume fraction and be limited to 0% owing to need in the tissue of steel wire, exist.
Bainite structure is effectively for the nodularization of cementite, has the effect of the ductility that improves steel wire, but the dislocation desity height, 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 following 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 distortion impedance that reduces steel wire.In addition, under the big situation of the volume fraction of pearlitic structure, the deviation of the size of the nodularization cementite after the annealing reduces, and the ductility of steel wire improves.Be lower than at the volume fraction of pearlitic structure under 1.40 * (C%) * 100% the situation, the attenuating effect of distortion impedance and the raising effect of ductility reduce, so the following 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 crystal grain diameter after reducing to anneal, and is effective for improving ductility.In addition, promote the nodularization of lamellated pearlitic decomposition and cementite by the miniaturization of this average block size, 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 that 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, to the C section of wire rod (wire rod with the vertical section of length direction) photography photo, obtain the area occupation ratio of each tissue with 1000 times multiplying powers by image analysis.Here, at the C of wire rod section, to near the top layer (surface) of wire rod, 1/4D portion (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 portion (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 the volume fraction of each tissue by each area occupation ratio of organizing that image analysis obtains.
In the mensuration of the piece size of pearlitic structure, adopt the EBSD device.Respectively portion, 1/4D portion, 1/2D portion near the top layer of the C section of wire rod have been measured the zone of 275 μ m * 165 μ m.Is 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, the cold forging deterioration at tensile strength TS.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 Ji Zai % 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 as the mechanical part necessary strength.In addition, if C content surpasses 0.60%, cold forging deterioration then.Therefore, the C content in the steel is defined as 0.10～0.60%.In order to guarantee the intensity of steel more reliably, C content is preferably 0.25～0.60%.In addition, in order to guarantee cold forging more reliably, C content more preferably 0.25～0.50%.
Si plays a role as deoxidant element, gives necessary strength and hardenability to steel, is to improving temper softening impedance effective elements.Be lower than at 0.01% o'clock at Si content, these effects are insufficient.In addition, if Si content surpasses 0.40%, then toughness and ductility deterioration, hardness rises, the cold forging deterioration.Therefore, the Si content in the steel is defined as 0.01～0.40%.In addition, in order to improve temper softening impedance and cold forging more reliably, Si content is preferably 0.05～0.30%.
Mn gives necessary strength and the necessary element of hardenability for steel.Be lower than at 0.20% o'clock at Mn content, the effect of giving intensity and hardenability is insufficient.If Mn content surpasses 1.50%, then hardness rises, the cold forging deterioration.Therefore, Mn content is defined as 0.20～1.50%.In addition, in order to guarantee intensity and cold forging more reliably, Mn content is preferably 0.30～0.90%.
Distortion impedance when P improves cold forging makes the processibility deterioration.In addition, P makes the toughness deterioration of steel to grain boundary segregation because of the embrittlement of grain boundaries behind the Q-tempering.Therefore, hope reduces the P in the steel as far as possible.So, with the ceiling restriction of P content 0.040%.This P content is preferably below 0.020%.In addition, the following of P content is limited to 0%.
S is by the form with sulfide exists with the reaction of alloying element such as Mn.These sulfide improve the machinability of steel.But, in steel, add S if surpass 0.050% ground, cold forging deterioration then is because of the embrittlement of grain boundaries behind the Q-tempering makes the toughness deterioration.Therefore, with the ceiling restriction of S content 0.050%.This S content is preferably below 0.020%.In addition, the following of S content is limited to 0%.
N adds with the fine purpose that turns to of austenite crystal.N combines with alloying elements such as Al or Ti and forms nitride, and these nitride play a role as the pinning particle, thereby make the crystal grain micronize.Be lower than at 0.0005% o'clock at N content, nitride separate out quantity not sufficient, because of thickization of crystal grain makes the ductility deterioration.In addition, make N content surpass 0.0300% if add N, then the dynamic strain aging that is produced because of solid solution N increases the distortion impedance, thereby makes the processibility deterioration.Therefore, N content is defined as 0.0005～0.0300%.In order to guarantee ductility more reliably, the distortion impedance is fully reduced, N content is preferably 0.0020～0.0150%.
Cr has the effect that improves hardenability and intensity.Be lower than at 0.03% o'clock at Cr content, 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 the hardenability of raising or makes fine carbide separate out, improve the effect of intensity.Be lower than at 0.03% o'clock at V content, do not improve the effect of hardenability and intensity.Make V content surpass 0.2% if add V, then the thick carbide that 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.Be lower than at 0.03% o'clock at Mo content, 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 hardenability and intensity simultaneously, 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, combines 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 distortion impedance.Be lower than at 0.001% o'clock at Al content, can not bring into play these effects.In addition, if Al content surpasses 0.060%, the toughness deterioration of steel then.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 above-mentioned effect and flexible balance, 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 the intensity of steel simultaneously.
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 so that bring into play effect of adding the raising hardenability that B brought described later effectively by the N in the fixing steel.Be lower than at 0.002% o'clock at Ti content, 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 the cold forging deterioration.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 the intensity and the cold forging of steel, Ti content is preferably 0.005～0.030%.
Nb combines with N or C, and forming NbN, NbC or their complex inclusion is Nb (CN), plays a role effectively for thickization that suppresses austenite crystal.Therefore, Nb has the function of the intensity that improves steel.Be lower than at 0.005% o'clock at Nb content, the effect that suppresses thickization of austenite crystal is 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.Be lower than at 0.0001% o'clock at B content, the effect that improves hardenability is 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.Be lower than at 0.01% o'clock at Cu content, do not improve the effect of the intensity of steel.Make Cu content surpass 0.3%, then hot rolling deterioration if add Cu.Therefore, when in steel, adding Cu, the Cu content in the steel is controlled at 0.01～0.3%.In addition, in order to improve the intensity of steel effectively, 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.Be lower than at 0.01% o'clock at Ni content, 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 fully to be improved 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 height then forms thick oxide compound, thereby becomes reason of fatigue destruction.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, below the manufacture method of the steel wire of one embodiment of the present invention is described.
With satisfying the steel billet heating 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, keep postcooling to room temperature at constant temperature.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 line footpath 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 influence the tissue of steel (steel wire).That is to say that when the content of 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 hot rolled steel wire is batched, the steel wire constant temperature in 400 ℃～600 ℃ fused salt groove that batches was kept 30 seconds～150 seconds, cool off then.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, be cooled under the situation that does not have to finish in the constant temperature phase transformation, therefore generate martensitic stucture.In this case, the desired softening time lengthening of annealing, intensity rises, and makes the processibility deterioration.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 was controlled at 30 seconds～150 seconds.
After steel wire is extracted out from the fused salt groove steel wire is cooled off, carrying out relative reduction in area then is the above Wire Drawing of 25+82 * F1%.Here, F1 value (above-mentioned F1) is represented 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, the cold forging deterioration.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 ℃, the effect of intensity height, softening was low.In stress relief annealed temperature is A
C1When point is above, sneak into pearlitic structure in the tissue of the steel wire after annealing, the intensity of steel wire and ductility deterioration.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.
The steel billet of these steel grades is heated to 950～1150 ℃, and carrying out the steel wire hot rolling directly is 5.5～14.5mm until line, after this rod rolling, adopts the fused salt groove on the rolling line, carries out the constant temperature phase transformation under the conditions shown in Table 2 and handles, and cools 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 handling, 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 to batch the cooling steel wire is gone up in the back at the rolling loose winding cooling line of wire rod (Stelmor) under the situation of not carrying out constant temperature phase transformation processing manufacture method in the past.Therefore, in above-mentioned level 13 and 15, the volume fraction of pearlitic structure is insufficient, just analyses the ferritic structure surplus.
In addition, 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.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 on 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, put cold.Have again,, adopt the 9A test film of JIS Z2201, carry out tension test, estimate tensile strength TS and constriction value RA according to the test method of JIS Z2241 in order to measure their mechanical characteristics.
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 annealing usually) 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 embodiment of the level 1,2,4,6,7,11,12,14,16,17,19,21,23～28 of table 4 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 steel wire of level 8,9,10,11,12 of record and these steel.Have, in the steel wire of these levels 8,9,10,11,12, composition of steel and tissue (the branch rate of each tissue) are equal, tensile strength TS difference again.As shown in Figure 1, as can be known: at tensile strength TS is under the situation of (for example being more than 1064 ℃) more than 480+850 * Ceq.MPa, and 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 height of steel wire, 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 steel wire of level 1～12,14,16～21,23～28 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 height of the tensile strength TS of the steel wire after low-temperature annealing ratio Spheroidizing Annealing material in the past.Like this, as can be known: under the wire drawing relative reduction in area is situation 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 steel wire of the level 1,2,4,6,7,11～17,19,21,23～28 of table 2 shown in Fig. 5 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 branch 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 the parts of complicated shape by cold forging, can improve yield rate and the productivity ratio of steel, reduce the processing charges of parts. In addition, according to the present invention, can reduce the temperature of softening annealing, reduce the heat treatment expense, boost productivity. Therefore, steel wire of the present invention is suitable as the raw material of the mechanical parts such as bolt by cold-forging forming, screw, nut.
Claims (4)
1. low-temperature annealing steel wire, 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:0.03～0.4%, V:0.03～0.2%, Mo:0.03～0.2% more than a kind, remainder comprises Fe and unavoidable impurities;
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. low-temperature annealing steel wire 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. low-temperature annealing steel wire 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. a low-temperature annealing is characterized in that having following operation with the manufacture method of steel wire:
The steel billet heating 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;
It is above and be lower than 100% Wire Drawing to implement relative reduction in area and be 25+82 * F1%, wherein, and F1=(Cr%)+(Mo%)/4+ (V%)/3.
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2011062012A1 (en) | 2011-05-26 |
| KR101382664B1 (en) | 2014-04-07 |
| JPWO2011062012A1 (en) | 2013-04-04 |
| CN102227512B (en) | 2013-10-23 |
| JP4842407B2 (en) | 2011-12-21 |
| KR20110083688A (en) | 2011-07-20 |
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