CN1840729A - High carbon steel wires excellent in spinnability and method for producing same - Google Patents
High carbon steel wires excellent in spinnability and method for producing same Download PDFInfo
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- CN1840729A CN1840729A CN 200510062916 CN200510062916A CN1840729A CN 1840729 A CN1840729 A CN 1840729A CN 200510062916 CN200510062916 CN 200510062916 CN 200510062916 A CN200510062916 A CN 200510062916A CN 1840729 A CN1840729 A CN 1840729A
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Abstract
The invention relates to high-carbon steel wires comprises 0.65-1.20% of C, 0.05-1.2% of Si, 0.2-1.0% of Mn, 0-0.35% of Cr, 0-0.02% of P and S, wherein over 80% of the metallic structure comprises pearlite structure.
Description
Technical field
The present invention relates to a kind of high-carbon steel wire wire rod, it has the enhanced stretch resistance that has reduced in wortle when being in hot-rolled state, but and has a good stringiness.
Background technology
Become very thin silk for standing to stretch, to be used for steel wire cord or semi-conductor slitting saw wire rod, employed be carbon content be about 0.7 to 0.8% and diameter be that 5.0mm or above high-carbon steel wire wire rod are (corresponding to JIS G3502:SWRS72A, SWRS82A).If these high-carbon steel wire wire rods rupture in wire-drawing operation, productivity will be subjected to remarkable weakening.Occur for fear of this situation, but need the high-carbon steel wire wire rod to have excellent stringiness.
Up to now, but in order to obtain to have the high-carbon steel wire wire rod of excellence stringiness, adopted and wherein after hot rolling, used the water cooling wire rod, make it stand the air blast cooling then, so that the structure of described wire rod becomes the method for fine pearlite structure, or wherein make described wire rod before the drawing process or during stand once more in the middle of patent method once or twice.
Recently, require the high carbon steel steel wire should have littler silk footpath.For satisfying this requirement and from improving the angle of productivity, satisfied provide direct patent material, or direct wire drawing material, will make it possible to like this before the wire drawing or during omit patent.In order to boost productivity, the high-carbon steel wire wire rod is required to have the more excellent anti-breaking property and the die head life-span of improvement more and more.
In order to satisfy this requirement, but the various technology that are used to improve high-carbon steel wire wire rod stringiness have been proposed.For example, day disclosure unexamined patent application 3-60900 has proposed the technology of a kind of control stretching intensity and coarse perlite ratio, described coarse perlite is amplifying under 500 times the opticmicroscope and can discern, and contained coarse pearlitic suitable numerical value depends on the carbon equivalent of high-carbon steel wire wire rod in the perlite.
Japanese Patent Application Publication 2000-63987 has proposed a kind of like this technology, wherein the average aggregate structure diameter of high-carbon steel wire wire rod Medium pearlite structure is set to 150 μ m or littler, and the average layer gap is set to 0.1 to 0.4 μ m, but improves stringiness thus.Incidentally, aggregate structure is meant the zone of its Medium pearlite thin layer direction (lamellar direction) for rule.A plurality of aggregate structures form tubercle or block (block), and described tubercle or block are the constant zones of the orientation of wherein ferrite matrix.As described in these technology, the wire rod after the hot rolling is produced by the following: regulate its coiling temperature by water-cooled, regulate water cooler by Stelmor then and regulate blast volume.
According to the day disclosure technology described in the unexamined patent application 3-60900, exist with about amount of 10% to 30% because have the coarse perlite in rough layer gap, therefore improved the die head life-span.Yet, but this technology has the good inadequately and imperfect shortcoming of stringiness of the anti-property broken during wire drawing, and these two shortcomings all need direct patent material, or direct wire drawing material.
The technology of Japanese Patent Application Publication 2000-63987 can be improved the die head life-span by making coarse slightly for example to 0.1 to the 0.4 μ m in described lamellar spacing.Make that described lamellar spacing is coarse so slightly will to cause average aggregate structure diameter coarse to 40 μ m or above (referring to the processing and implementation example).This is insufficient for direct patent material or the direct desired resistance to fracture of wire drawing material.
United States Patent (USP) 6,783,609 have proposed a kind of like this technology, wherein in order to improve the life-span of die head, except reducing the nodular median size of perlite, also make the wide slightly intensity that reduces wire rod in pearlitic lamellar spacing, wherein said nodular physical meaning is meant certain numerical value or littler crystal grain.Described technology has been improved anti-breaking property, but and reached excellent stringiness, even have under the pearlitic texture situation of wide relatively lamellar spacing.
Japanese Patent Application Publication 11-302743 has proposed a kind of technology of producing the high-tensile steel wires wire rod, even wherein during transportation cause wire rod may produce under the situation of defective with the rigid structure that forms carrying out plastic deformation on the steel surface subsequently, anti-breaking property does not degenerate yet.According to described technology, wherein 70% or above structure be that the high-carbon steel wire wire rod of perlite or bainite or both mixtures is heated to 300 ℃ to 600 ℃ temperature and kept 100 seconds or the shorter time before wire drawing, then place or water cools off described wire rod by former state.
Japanese Patent Application Publication 2001-179325 has proposed a kind of coil that makes and has stood slowly cooling and remollescent technology.Yet this technology is not intended for use in direct patent material or the direct wire drawing material.This technology discloses particularly, on the hot rolling postcooling conveying belt speed of cooling of coil be by regulating steel composition, slowly austenitic particle diameter during the cooling beginning, silk footpath, ring apart from and slowly the temperature in the cooling control.
Yet, United States Patent (USP) 6,783, but 609 and the technology of Japanese Patent Application Publication 11-302743 do not mention enhanced stretch resistance and the improvement stringiness of eliminating the wire drawing die head, but and do not have direct patent material or direct desired enough stringinesss of wire drawing material.In addition, the high-carbon steel wire wire rod (Japanese Patent Application Publication 2001-179325) after the softening simply hot rolling but also good inadequately on stringiness.
Summary of the invention
The present invention finishes for solving described problem, aim to provide a kind of can before the wire drawing or during omit the high-carbon steel wire wire rod of patent, but this wire rod when hot-rolled state under the situation that wire drawing die head enhanced stretch resistance reduces stringiness good, and provide a kind of method of producing described high-carbon steel wire wire rod.
According to the present invention, to achieve these goals, a kind of high-carbon steel wire wire rod is provided, but its stringiness is good and comprise: by quality %, 0.65% to 1.20% carbon, 0.05% to 1.2% silicon, 0.2% to 1.0% manganese and 0.35% or the chromium of following (comprising 0%), also comprise quantitative limitation separately and be 0.02% or following p and s, wherein surplus is iron and unavoidable impurities, wherein 80% or above metal construction constituted the and (relation of λ/Ceq)+290 that between average tensile strength TS of high-carbon steel wire wire rod (MPa) and average lamellar spacing λ (nm), has TS≤8700/ √ by pearlitic texture.In this expression formula, in view of the content of carbon in the high-carbon steel wire wire rod is %C, the content of manganese is %Mn, after the content of chromium is %Cr, so Ceq equals %C+%Mn/5+%Cr/4.
According to the present invention, to achieve these goals, a kind of method of producing high carbon steel wires excellent in spinnability also is provided, when wherein after rolling end, making the high-carbon steel wire wire rod be cooled to room temperature, wire rod is set at 60 seconds to 200 seconds from 450 ℃ of cooling times that are cooled to 300 ℃, thereafter wire rod is cooled to room temperature.
The inventor illustrates following discovery.High-carbon steel wire wire rod actual average tensile strength TS (actual tensile strength) is lower than under the situation of the high-carbon steel wire wire stretching intensity (prediction tensile strength) that average layer gap lambda and carbon equivalent Ceq by wire rod predicted therein, but it is good just to have obtained a kind of like this high-carbon steel wire wire rod stringiness, its before the wire drawing or during can omit patent, and in the wire drawing die head, have the enhanced stretch resistance of reduction with the state after the hot rolling.
TS in the expression formula represents the actual average tensile strength, 8700/ √ on expression formula the right (the prediction tensile strength of the high-carbon steel wire wire rod that the expression of λ/Ceq)+290 is calculated by the actual Ceq and the average lamellar spacing λ of described wire rod.Ceq=%C+%Mn/5+%Cr/4 in the expression formula is set in the present invention at first.
Be Controlled refrigerative high-carbon steel wire wire rod is made of pearlitic texture after hot rolling, and described perlite is the stratiform cementite with certain lamellar spacing.As in the present invention, when the actual average tensile strength TS of high-carbon steel wire wire rod satisfies described expression formula and less than prediction during tensile strength, suppose in the structure of this high-carbon steel wire wire rod, the mechanical property of stratiform cementite has been softened, and the laminate structure of described high-carbon steel wire wire rod is kept simultaneously.
According to softening processing of above-mentioned routine for the high-carbon steel wire wire rod, the chap of lamellar spacing λ own.If the lamellar spacing λ in the expression formula of prediction average tensile strength becomes big, actual tensile strength will can not become and be lower than the prediction tensile strength, and promptly different with the present invention, the prediction tensile strength becomes littler.In addition, the anti-property broken becomes good inadequately in wire drawing, thus, but will can not get direct patent material or the direct desired stringiness of wire drawing material.Should be noted that high-carbon steel wire wire rod of the present invention is different from traditional only being softened to reduce the wire rod of tensile strength etc. under as-annealed condition.
In addition, under the situation of the high-carbon steel wire wire rod that is not softened of stratiform cementite, the actual average tensile strength TS of wire rod becomes higher therein.Different with the present invention, the actual average tensile strength can not become and is lower than the prediction tensile strength, predicts that promptly tensile strength becomes following.As a result, as in the simple remollescent described in the aforementioned techniques is any, the anti-property broken becomes not enough during the wire drawing, but will can not obtain the stringiness of direct patent material or the direct desired satisfaction of wire drawing material thus.
The prediction that the prediction tensile strength is come free actual average lamellar spacing λ and carbon equivalent Ceq.In other words, alleged here prediction average tensile strength is the prediction average tensile strength corresponding to actual average lamellar spacing λ and carbon equivalent Ceq in the actual softening degree of stratiform cementite or the high-carbon steel wire wire rod.More specifically, described prediction tensile strength is that high-carbon steel wire wire rod laminate cementite is not softened or the average tensile strength when softening according to a conventional method or near its tensile strength.Should be noted that prediction average tensile strength of the present invention is not pure calculating or statistics remollescent basis, but the basis of softening restriction, it can be predicted by lamellar spacing and carbon equivalent and be kept in actual high-carbon steel wire wire rod laminate structure simultaneously.
This relation (basis) between the actual average tensile strength of high-carbon steel wire wire rod of the present invention and the prediction average tensile strength is necessary, because in the present invention, even the mechanical property of stratiform cementite has been softened, can not measure the softening of layered cementite own direct quantitatively.
Even consider that layered cementite remollescent structure and stratiform cementite not remollescent structure can not be distinguished under structure observation method conventional such as TEM or SEM, this relation also is necessary.
Like this, in the present invention, not only the tensile strength of high carbon steel and conventional sample are softening and be minimized, and the mechanical property of stratiform cementite also is softened, and layered structure is kept simultaneously.As a result, after wire drawing, as required, tensile strength reduction amount is little of the degree by work hardening under the common drawing condition and the resulting predetermined tensile strength of thermal treatment.The slight reduction of this tensile strength can be used to before the wire drawing or during omit patent, but and can provide stringiness good and high-carbon steel wire wire rod that under hot-rolled state, in the wire drawing die head, have low enhanced stretch resistance.
Description of drawings
Figure 1 shows that between the prediction average tensile strength (A) of the actual average tensile strength TS (B) of high-carbon steel wire wire rod and steel wire wire rod difference with respect to described wire rod from 450 ℃ of explanatory views that are cooled to 300 ℃ cooling time; With
Figure 2 shows that high-carbon steel wire wire stretching resistance reduction amount and described wire rod is cooled to the explanatory view that concerns between cooling time of 300 ℃ from 450 ℃.
The description of preferred embodiment
(metal construction)
In the present invention, in the high-carbon steel wire wire rod 80% or above metal construction be pearlitic texture.This pearlitic texture is meant ferrite and cementite with lamellated form structure arranged arranged side by side, and it transforms by eutectoid when austenitic state cools off at the steel wire wire rod and obtains.But be the high strength and the stringiness that fundamentally guarantee the steel wire wire rod, it is necessary making metal construction become this pearlitic texture.If the pearlitic texture ratio is less than 80% of metal construction, and the ratio of crossing cold junction structure such as bainite is more than 20% of metal construction, but the stringiness of so described steel wire wire rod is can not be getable basically.
(tensile strength)
In the present invention, as mentioned above, make the actual average tensile strength TS (actual tensile strength) of high-carbon steel wire wire rod be lower than the tensile strength (prediction tensile strength) of the high-carbon steel wire wire rod that actual average lamellar spacing λ and actual carbon equivalent Ceq by the high-carbon steel wire wire rod predicted.If do not make the actual average tensile strength be lower than the prediction tensile strength, just can not obtain can before the wire drawing or during omit patent, and under hot-rolled state, in the wire drawing die head, demonstrate the enhanced stretch resistance and the high carbon steel wires excellent in spinnability of reduction.
As the known fact, tensile strength TS (MPa) is determined by lamellar spacing S (μ m) usually, and has TS=σ 0+KS
-1/2Relation, wherein σ 0 and K are constant.
On the basis that concerns between tensile strength and the lamellar spacing, the inventor attempts to make from actual layer gap prediction tensile strength and its laminate cementite is not softened or near-earth is approaching as far as possible by the average tensile strength of traditional way remollescent high-carbon steel wire wire rod.For this reason, in view of the actual layer gap lambda (nm) and the actual carbon equivalent Ceq of high-carbon steel wire wire rod, the inventor is by expression formula 8700/ √ (λ/Ceq)+290 define prediction tensile strength.In this expression formula,, also define Ceq by expression formula Ceq=%C+%Mn/5+%Cr/4 in view of the carbon content in the high-carbon steel wire wire rod is that % carbon, manganese content are that %Mn, chromium content are %Cr.
As mentioned above, the stratiform cementite of high-carbon steel wire wire rod be not softened or by traditional way remollescent situation under, actual tensile strength can not become and be lower than prediction average tensile strength defined above.On the contrary, described prediction average tensile strength becomes littler.As a result, under any situation, it is not enough that the anti-property broken in the wire drawing becomes, so but can not obtain as directly patent material or the directly satisfied stringiness of wire drawing material.
That is, the actual average tensile strength with high-carbon steel wire wire rod of remollescent stratiform cementite becomes the prediction tensile strength that is lower than described high-carbon steel wire wire rod.On the other hand, be not softened or in a conventional manner under the remollescent situation, its actual average tensile strength TS becomes the prediction average tensile strength that is higher than the high-carbon steel wire wire rod at the stratiform cementite of high-carbon steel wire wire rod.
As mentioned above, the present invention is intended to the mechanical property of soften layer globular cementite, keeps the stratiform cementite structure of described high-carbon steel wire wire rod simultaneously.Remollescent high-carbon steel wire wire rod with the difference that does not have actual average tensile strength TS between the remollescent wire rod is thus: have about 30MPa under the situation of relative low-carbon (LC) at wire rod, have about 200MPa under the relative high-carbon situation at wire rod.(seeing the processing and implementation example).Equally, in the difference that the mechanical property with the prediction tensile strength of aforesaid method remollescent wire rod and wherein said high-carbon steel wire wire rod and layered cementite is softened be: have at wire rod under the situation of relative low carbon content and be low to moderate, even and have at wire rod under the situation of high relatively carbon content less than about 50MPa less than about 10MPa with the prediction tensile strength TS between other method remollescent wire rod.(seeing the processing and implementation example).
The reason that difference in the tensile strength is so little is: the prediction tensile strength of high-carbon steel wire wire rod is not the simple extension intensity by carbon equivalent Ceq prediction, but having considered the actual average lamellar spacing λ of described high-carbon steel wire wire rod after and the value of predicting.Another reason is: the mechanical property of stratiform cementite is softened, and the stratiform cementite structure of high-carbon steel wire wire rod is kept simultaneously.
In addition, in the present invention,, in other words,, need take special heat treating method for the mechanical property of soften layer globular cementite for the actual average tensile strength TS that makes the high-carbon steel wire wire rod prediction tensile strength less than described wire rod.Described heat treating method is performed such, so that when after rolling end the high-carbon steel wire wire rod being cooled to room temperature, will be used for wire rod was remained on 60 seconds to 200 seconds from 450 ℃ of periods that are cooled to 300 ℃, then is cooled to room temperature.
In the present invention, the tensile strength of high-carbon steel wire wire rod is not greatly to reduce as in simple the softening, but slightly be reduced to such degree, with the tensile strength that obtains being scheduled to, for example, be by work hardening under the drawing condition of routine, perhaps heat-treat as required after the wire drawing and slightly to reduce.The slight process that reduces of tensile strength can dispense before the wire-drawing operation or during patent, and the enhanced stretch resistance that helps to obtain to show in the wire drawing die head under hot-rolled state reduces and high carbon steel wires excellent in spinnability.
(composition of steel wire)
Hereinafter, will explain the chemical ingredients of high-carbon steel wire wire rod of the present invention, and the reason that limits each element.These are to be the necessary or preferred information of satisfied performance institute as high strength, high fatigue characteristic and the stranded property of high steel wire, but these performances are applicable to steel wire cord that requires very thin steel wire and stringiness and semi-conductor slitting saw steel wire.
Be the characteristic that meets the demands, according to the present invention, the essentially consist of high-carbon steel wire wire rod comprises: by quality %, 0.65% to 1.20% carbon, 0.05% to 1.2% silicon, 0.2% to 1.0% manganese and 0.35% or the chromium of following (comprising 0%), 0.02% or following phosphorus and 0.02% or following sulphur, wherein surplus is iron and unavoidable impurities.
As requested, except that basal component, high-carbon steel wire wire rod of the present invention also comprises and is selected from one or more following compositions, by quality %, 0.005% to 0.30% vanadium, 0.05% to 0.25% copper, 0.05% to 0.30% nickel, 0.05% to 0.25% molybdenum, 0.10% or following niobium, 0.010% or following titanium, 0.0005% to 0.0050% boron, and 2.0% or following cobalt, or one or more are selected from following composition: 0.0005% to 0.005% calcium, 0.0005% to 0.005% REM, and 0.0005% to 0.007% magnesium.
(carbon: 0.65% to 1.20%)
Carbon is economical and effectively strengthens element.Along with carbon content increases, the intensity in the wire drawing after work hardening amount and the wire drawing also increases.Elemental carbon is also effective on reduction ferrite amount.In order to make these effects can reach satisfied degree, the carbon content of high carbon steel must for 0.65% or more than.Yet, if carbon content is too high, in the austenite crystal boundary, will produce netted pro-eutectoid cementite, break to such an extent as to not only in wire drawing, be easy to generate, and after final wire drawing, but the stringiness of very thin steel wire and toughness and ductility all significantly worsen, the deterioration of the stranded property of simultaneous High Speed Steel Wire.The upper limit of carbon content is set at 1.20%.
(silicon: 0.05% to 1.2%)
Silicon is the necessary element of steel-deoxidizing, and particularly the deoxidation when aluminium does not exist is needed.The ferrite that silicon comprises by being dissolved in the perlite mutually in, also effective for after patent, improving intensity, and described perlite forms after malleableize thermal treatment.If silicone content is lower than 0.05%, deoxidation effect and intensity enhancing effect will all can not reach satisfied degree.Therefore, the lower limit set of silicone content is 0.05%.If silicone content is too high, will be difficult to utilize the drawing process of mechanical descaling (hereinafter referred to as MD); In addition, after ferritic ductility that comprises in the perlite and the wire drawing very the ductility of light gage wire all will worsen.The upper limit of silicone content is set at 1.20%.
(manganese: 0.2% to 1.0%)
Equally, manganese is effective reductor as silicon.Under the not aluminiferous certainly situation of high-carbon steel wire wire rod of the present invention, not only, show desoxydatoin effectively by adding silicon but also adding manganese.Manganese not only plays the effect that the sulphur in the steel is fixed as MnS and strengthens the toughness and the ductility of steel thus, and also effective on the proeutectic ferrite to eliminate in the rolling raw material in the hardenability that strengthens steel.If manganese content is lower than 0.2%, will be less than effect.For these interaction energies are effectively embodied, the lower limit set of manganese content is 0.2%.On the other hand, because manganese is easy to generate segregation, thus can cause segregation above 1.0% excessive manganese content, and in the isolation portion of manganese, produced cold junction structure such as bainite and martensite, but damage stringiness subsequently therefrom.The upper limit of manganese is set at 1.0%.
[chromium: 0.35% or following (comprising 0%)]
Chromium is the optional element that adds.Different with other optional elements, when containing chromium in the high-carbon steel wire wire rod, near-earth is near the average tensile strength of high-carbon steel wire wire rod as far as possible need to make it, and the stratiform cementite of described wire rod is not softened or is softening according to a conventional method.Therefore, be used for proximate Ceq calculation expression, the content of chromium should be considered by the expression formula of prediction average tensile strength.The present invention limits that to decide chromium content be 0.35% or following (comprising 0%).
Chromium not only improves hardenability, and pearlitic laminate structure is attenuated, thereby makes perlite thin.Therefore, but chromium is effective aspect the stringiness of the intensity of improving very thin high carbon steel steel wire and wire rod.For this effect is embodied effectively, the amount of preferred contained chromium be 0.005% or more than.If the amount of being somebody's turn to do is too high, will form undissolved cementite easily, it is elongated that perhaps the needed time is finished in conversion, and the result may form this cold junction structure such as martensite and the bainite crossed in the hot rolled wire rod, and worsens MD character.The upper limit of chromium content is set at 0.35%.
(one or more in vanadium, copper, nickel, molybdenum, niobium, titanium, boron and the cobalt)
Each of vanadium, copper, nickel, molybdenum, niobium, titanium, boron and cobalt all has similar effect on the enhancing steel.Therefore, for the effect that makes these elements effectively embodies, randomly comprise one or more of these elements.
(vanadium: 0.005% to 0.30%)
Vanadium is effective to improving hardenability, and produces the very thin steel wire of high strength.For described effect is embodied effectively, the amount of the optional vanadium that comprises be 0.005% or more than.If contained vanadium is too many, carbide will excessively produce, thereby reduce the content of the carbon that will be used for the stratiform cementite.Can cause intensity to reduce so on the contrary, or produce the second a large amount of phase ferrites.The upper limit of content of vanadium is set at 0.30%.
(copper: 0.05% to 0.25%)
Copper is not only effective to strengthening steel, and also effective to the erosion resistance that improves unusual light gage wire, also can improve the de-scaling performance among the MD, therefore can prevent the trouble of institute's die head that uses such as wearing and tearing.For described effect is embodied effectively, the amount of the optional copper that comprises be 0.05% or more than.If the content of copper is too high,, also will produces magnetite in the steel matrix under the bubble, thereby cause the deterioration of MD character even, also will form bubble on the wire surface so after the rolling end wire rod being maintained at about under 90 ℃ the high temperature.Also have, copper and reaction of Salmon-Saxl cause CuS to emanate in grain boundary, so in the wire rod manufacturing processed, steel ingot or wire rod can produce flaw.The upper limit of copper content is set at 0.25%.
(nickel: 0.05% to 0.30%)
Nickel not only strengthens steel, also improves the ductility effect of cementite, but improves the ductility as stringiness and so on effectively thus.For this effect is embodied effectively, the amount of the optional nickel that comprises be 0.05% or more than.Because the nickel costliness, so the upper limit of nickel is set to 0.30%.
(molybdenum: 0.05% to 0.25%)
Molybdenum is for improving hardenability and very the intensity of light gage wire is effective.For this effect is embodied effectively, the amount of the optional molybdenum that comprises be 0.05% or more than.If contained molybdenum is too many, carbide is with excessive generation, thereby reduction will be used for the content of the carbon of stratiform cementite.Reduce intensity so on the contrary, and excessively produce the second phase ferrite.The upper limit of molybdenum is set at 0.25%.
(niobium: 0.020% to 0.10%)
Niobium strengthens steel effectively, and suppresses austenitic recovery, recrystallization and grain growing.This quickens pearlitic conversion, further reduces tensile strength TS, makes nodular size small, but and improvement stringiness.For these effects are embodied effectively, the amount of the optional niobium that comprises be 0.02% or more than.If the content of niobium surpasses 0.10%, but will considerably worsen owing to the over-drastic precipitation strength makes stringiness.The upper limit of content of niobium is set at 0.10%.
(titanium: 0.005% to 0.010%)
Titanium not only improves the intensity of steel, and improves the ductility of wire rod by forming carbide or nitride.For these effects are embodied effectively, the amount of the optional titanium that comprises be 0.005% or more than.If the content of titanium surpasses 0.010%, but will considerably worsen owing to the over-drastic precipitation strength makes stringiness.The upper limit of titanium content is set at 0.010%.
(boron: 0.0005% to 0.0050%)
Boron is effective for the ferritic formation of grain boundary that improves ductility and suppress to be produced in the patent.Boron in the wire rod can play and suppress the ferritic effect of grain boundary, and described ferrite can become the starting point that causes leafing, can help to suppress leafing thus more undoubtedly.For these effects are embodied effectively, the amount of the optional boron that comprises be 0.0005% or more than.If contained boron is too many, the free boron that can show this effect may reduce, thereby causes being easy to generate coarse compound, and ductility is worsened.The upper limit of boron content is set at 0.0050%.
(cobalt: 0.005% to 2.0%)
Cobalt not only strengthens steel, and suppresses the formation of pro-eutectoid cementite, but improves hardenability and stringiness thus.Therefore, the amount of the optional cobalt that comprises be 0.005% or more than, as preferred lower value.If contained cobalt is too many, the perlite in the patent transforms will need the longer time, and consequence is that productivity worsens.The upper limit of cobalt contents is set at 2.0%.
(one or more in calcium, REM and the magnesium)
Calcium, REM and magnesium are effective for forming fine oxide compound and make austenite become close grain in steel.For this effect is embodied effectively, the amount of one or more of optional institute calcic, REM and magnesium be 0.0005% or more than, as the preferred lower value of each element.If the amount of contained calcium, REM and magnesium surpasses 0.005% respectively, surpass 0.005% and surpass 0.007%, it is coarse that the oxide compound that will form will become, thereby but cause stringiness to worsen.Therefore, be respectively to this tittle capping content, more specifically, should contain 0.0005% to 0.005% calcium, 0.0005% to 0.005% REM and 0.0005% to 0.007% magnesium.
(phosphorus: 0.02% or following)
Phosphorus is a kind of impurity element, and is low more good more.Especially in ferritic sosoloid forms, but phosphorus has very big influence to the deterioration of stringiness.Therefore, in the present invention, the content of phosphorus be set at 0.02% or below.
(sulphur: 0.03% or following)
Sulphur also is impurity element, produces MnS as inclusion, but and the infringement stringiness, therefore, the content of sulphur be set at 0.03% or below.
Nitrogen also is the impurity element that is dissolved in the ferrite, and it can cause age hardening, and reason is the heat that is produced during the wire drawing, but like this reduction of stringiness is had great effect.Therefore, nitrogen content is low more good more.The content of preferred nitrogen be set at 0.005% or below.
(manufacture method)
Then, the optimum condition of producing high-carbon steel wire wire rod of the present invention below will be described.
In the present invention, as mentioned above, the actual average tensile strength TS of high-carbon steel wire wire rod is set to the prediction tensile strength that is lower than the high-carbon steel wire wire rod.In other words, production can advantageously be finished by traditional basically method, and difference is: after rolling finishing with the high-carbon steel wire wire rod from 450 ℃ of cycles that are cooled to 300 ℃, the described cooling period is used to the mechanical property of soften layer globular cementite.
More specifically, the high carbon steel fusing with described chemical constitution makes it stand continuous casting then, or makes its steel ingot stand breaking down formation steel billet.Then, if desired, heat described steel billet after, finishing temperature is set in for example 1050 ℃ to 800 ℃, to finish hot rolling.Finishing temperature is made as is lower than 1050 ℃ or following meeting and causes austenitic recovery, recrystallization and grain growing to be suppressed, thereby make tubercle fine.If the lower limit of described finishing temperature is too low, it is too big that the load on the roller mill becomes, and therefore is set at 800 ℃ or higher preferred 900 ℃ or higher temperature.
Cooling conditions under the control after the finish rolling below will be described.Incidentally, though control cooling conditions down is different because of the diameter that depends on wire rod, even the silk footpath after the finish rolling be as 3 to 8mm, described diameter is the common thread directly scope of high-carbon steel wire wire rod, and the cooling conditions under this controls is also applicable.
Cooling wire rod to 450 ℃ carries out under the condition of quenching basically, so that described high-carbon steel wire wire rod 80% or above metal construction become pearlitic texture.Specifically, preferred described quenching is for example forced to carry out under the cooling by means of the refrigerative step by step of water-cooled, air blast cooling or the combination of these methods under for example 5 ℃/second or higher high speed of cooling.Such pressure cooling can make described high-carbon steel wire wire rod 80% or above metal construction become pearlitic texture, and suppresses austenitic recovery, recrystallization and grain growing, thereby makes the perlite tubercle fine.
The speed of cooling that is lower than 5 ℃/second has following shortcoming: being cooled to the temperature that surpasses 450 ℃ needs the longer time, causes surpassing the longer residence time under 450 ℃ the temperature.This makes stratiform cementite structure chap particulate form, thereby causes described wire rod to carry out easier separation or tear, so the wire rod easier fracture that becomes during the wire drawing.On the other hand, if speed of cooling surpasses 20 ℃/second, the de-scaling performance may worsen.
In the present invention, wire rod is cooled to 300 ℃ be set at cooling time (residence time) in cycle of 60 seconds to 200 seconds from 450 ℃.If beyond this scope, can not be met the wire rod of the tensile strength relational expression defined in the present invention cooling time, even described pearlitic texture is optimized by the controlled chilling of being implemented.For example, when the wire temperature that will keep surpasses 450 ℃, as mentioned above, the stratiform cementite will become coarse grained form, but stringiness worsens subsequently.If the wire temperature that will keep is lower than 300 ℃, as mentioned above, can not make the actual average tensile strength TS of high-carbon steel wire wire rod be lower than the prediction tensile strength of high-carbon steel wire wire rod.In other words, when keeping layered cementite structure, can not make the mechanical property of layered cementite softening, but therefore can not improve stringiness.
If wire rod is shorter than 60 seconds from 450 ℃ of cooling times (residence time) that are cooled to 300 ℃, can not make the actual average tensile strength TS of high-carbon steel wire wire rod be lower than the prediction tensile strength of high-carbon steel wire wire rod.In other words, can not make the mechanical property of stratiform cementite softening, but therefore can not improve stringiness.
Therefore if wire rod was longer than 200 seconds from 450 ℃ of cooling times (residence time) that are cooled to 300 ℃, intensity will be returned to virgin state, can not make the actual average tensile strength TS of high-carbon steel wire wire rod be lower than the prediction tensile strength of high-carbon steel wire wire rod.In other words, when keeping stratiform cementite structure, can not make the mechanical property of layered cementite softening, but therefore can not improve stringiness.
Thus, be cooled to 300 ℃ be set in cooling time (residence time) in cycle of 60 seconds to 200 seconds from 450 ℃, need to guarantee that the wire rod cooling conveyor line after the hot rolling has certain length in order to make wire rod.Incidentally, if the conveying belt line is short, just wire rod can not be remained on the time of pre-fixed length in the temperature range.After having guaranteed a certain length, just can be by cooling cowl at a slow speed is installed, or control the speed of cooling that is used for coil on the cooling conveyor by regulating the air blast cooling air volume, described air capacity depends on the condition the spacing of composition, gauge or diameter of wire and coil such as steel.
For behind the controlled chilling up to the cooling of room temperature, following selection can be arranged: as leave standstill cooling, slowly cooling and fast cooling.In being cooled to the process of room temperature,, described wire rod can be remained on this temperature if the temperature of wire rod is lower than 300 ℃.
Embodiment
[embodiment 1]
Below embodiment of the present invention will be described.In embodiment 1, the controlled chilling condition by various changes (particularly with wire rod from 450 ℃ of cooling times that are cooled to 300 ℃) obtains the high-carbon steel wire wire rod, but estimates the mechanical property stringiness and the enhanced stretch resistance of described wire rod then.
Among the composition shown in the following table 1, jointly use the high carbon steel steel billet of the 3rd class steel and carry out hot rolling, under the different condition A to G shown in the table 2, carry out controlled chilling subsequently, be the steel wire wire rod of 5.5mm to produce diameter.From the air blast cooling of coiling temperature to 450 ℃, as the indication of passing judgment on, the A in the table 2, B, C, E, F and G can be strong air blast coolings, and D is weak air blast cooling.
For these steel wire wire rods, average intensity TS and the RA (area of minimizing: %) measuring the percentage ratio (%), average layer gap (nm) of perlite area, obtain by tension test.Measuring result is shown in Table 3.Incidentally, as for RA (%) and tensile strength TS, the wire rod sample that arbitrary extracting is continuous 4 meters long, 16 JIS9B samples of wire rod continuous drawing that from then on extract again, and, set mean value by this 16 JIS9B samples and measured RA, be used for tensile strength.
The perlite area percent is to determine by the following: the cutting wire rod obtains sample, the cross section of sample is finished to minute surface, with nitric acid and the described sample of alcoholic acid mixing solutions etching, and the structure of observing central position between wire surface and the center with the SEM scanning electronic microscope of 1000 times of diameters (amplify).
The average layer gap obtains by the following method: carry out mirror polish according to above same procedure, according to above same procedure etched sample, observe the central position of etched sample with SEM, in 10 visual fields, obtain 5000 times photo, be used in the photo in each visual field, three the bests (finest) in each visual field or inferior good point-rendering are perpendicular to the line segment of thin slice, determine the lamellar spacing from the length of each line segment with through the number of leaves of described line segment, on average the lamellar spacing in all line segments.
On the basis of component shown in the table 1, calculate Ceq=%C+%Mn/5+%Cr/4.Then, by the expression formula of Ceq and the average layer gap lambda that obtains, and expression formula 8700/ √ (λ/Ceq)+290 the determine prediction average tensile strength (A) of every kind of high-carbon steel wire wire rod.Magnitude relationship between the prediction average tensile strength TS (A) that also has every kind of high-carbon steel wire wire rod that obtains simultaneously and the actual average tensile strength TS (B) of described high-carbon steel wire wire rod, and (A) and the difference (B) [(A)-(B)].The result who obtains also is shown in 3.
Thereafter, by non-patent, through the dry drawing wire machine of multistep, making described steel wire wire rod with 400 meters/minute drawing speeds is diameter 2.3mm through direct wire drawing, but estimates stringiness then.In view of described wire drawing is handled, described wire rod is impregnated in the hydrochloric acid to implement complete de-scaling, then, be the surface of lubricated described steel wire wire rod, handle on the surface of every kind of steel wire wire rod forming the zinc phosphate film by zinc phosphate.
Have again, measure the enhanced stretch resistance value of described 2.3mm diameter wire rod.By means of monoblock (singleblock) drawing wire machine, make described wire rod stand wire drawing with 15 meters/minute speed, measure enhanced stretch resistance (kgf) with loadometer simultaneously.Die approach angle is set in 15 °.Calculate the reduction numerical value of enhanced stretch resistance simultaneously, to compare with the enhanced stretch resistance value of comparing embodiment 1 in the table 3.The result who obtains also lists in table 3.
It is evident that from table 1 and 2 the steel wire wire rod of the embodiment of the invention 3 to 6 shown in the table 3 comprises the 3rd class steel that belongs to chemical constitution in the scope of the invention, wherein at least 94% metal construction is a pearlitic texture.Also have, for the condition of rolling back controlled chilling, with described wire rod from 450 ℃ be cooled to 300 ℃ cooling time B to F within the scope of the present invention.
As a result, in the embodiment shown in the table 33 to 6, the actual average tensile strength TS (B) of high-carbon steel wire wire rod is lower than the prediction average tensile strength (A) of described steel wire wire rod.Like this, as shown in table 3, in the big part (diameter 5.5mm to 2.3mm) in silk footpath but stringiness is good, and little in little part (diameter 2.3mm to the 2.0mm) enhanced stretch resistance in silk footpath.Its enhanced stretch resistance reduction amount is greater than the enhanced stretch resistance reduction amount of comparing embodiment 1.
In the comparing embodiment 1 and 2, used the 3rd class steel that belongs to chemical constitution in the scope of the invention, wherein at least 95% metal construction is a pearlitic texture, but with wire rod from 450 ℃ of cooling times that are cooled to 300 ℃ than 60 seconds weak points, wherein at (A) with too short (B).As a result, in comparing embodiment 1 and 2, the actual average tensile strength TS (B) of every kind of high-carbon steel wire wire rod is higher than the prediction average tensile strength (A) of described steel wire wire rod.As a result, but a part stringiness that the footpath is big is quite good, but the enhanced stretch resistance of a part that the footpath is little is big, and enhanced stretch resistance reduction amount is more much smaller than the enhanced stretch resistance reduction amount in the processing and implementation example of the present invention.
Equally, in the comparing embodiment 7, used the 3rd class steel that belongs to chemical constitution in the scope of the invention, wherein at least 93% metal construction is a pearlitic texture, but wire rod has been exceeded 200 seconds time upper limit from 450 ℃ of cooling times that are cooled to 300 ℃, wherein oversize in (G).As a result, in comparing embodiment 7, the actual average tensile strength TS (B) of described high-carbon steel wire wire rod is higher than the prediction average tensile strength (A) of described steel wire wire rod.As a result, but a part stringiness that the footpath is big is quite good, but the enhanced stretch resistance of a part that the footpath is little is big, and enhanced stretch resistance reduction amount is widely less than the enhanced stretch resistance reduction amount in the processing and implementation example of the present invention.
Illustrated in figures 1 and 2 is the explanatory view of listed result in the table 3.The actual average tensile strength TS (B) that Figure 1 shows that every kind of high-carbon steel wire wire rod with respect to the difference between the prediction average tensile strength (A) of described steel wire wire rod (MPa: length axis) with wire rod from 450 ℃ be cooled to 300 ℃ cooling time (second: relation axis of abscissa).Figure 2 shows that enhanced stretch resistance reduction amount with respect to wire rod from 450 ℃ be cooled to 300 ℃ cooling time (second: relation axis of abscissa).Numerical value among Fig. 1 and Fig. 2 is corresponding to the numerical value of embodiment in the table 3.In Fig. 1 and Fig. 2, though in other embodiment and comparing embodiment, use solid line, just used dotted line in the embodiments of the invention 4, reason is that the cooling conditions among the embodiment 4 is weak air blast cooling D (softening).
By that obtain among the embodiment and result illustrated in figures 1 and 2, as can be seen, in the present invention wire rod is set at 60 seconds to 200 seconds significance from 450 ℃ of cooling periods that are cooled to 300 ℃, relate to the average tensile strength TS that sets every kind of high-carbon steel wire wire rod and be TS≤8700/ √ (λ/Ceq)+290, and amplify enhanced stretch resistance reduction amount.In addition, from embodiment, it can also be seen that, but the significance of the qualifications of institute as a result that reduces to stringiness and in minor diameter steel wire part enhanced stretch resistance among the present invention.
[table 1]
| Number | The chemical constitution of steel (quality %, remaining is iron and impurity) | Note | |||||||||||||||||
| Carbon | Silicon | Manganese | Phosphorus | Sulphur | Chromium | Vanadium | Copper | Nickel | Molybdenum | Niobium | Titanium | Cobalt | Calcium | Boron | REM | Magnesium | *Ceq | ||
| 1 2 3 4 5 6 7 | 0.68 0.72 0.81 0.86 0.98 1.05 1.15 | 0.05 0.18 0.25 0.21 0.14 0.23 0.75 | 0.41 0.50 0.40 0.72 0.40 0.55 0.77 | 0.008 0.011 0.009 0.010 0.015 0.008 0.004 | 0.008 0.004 0.009 0.010 0.011 0.007 0.007 | 0.00 0.00 0.00 0.00 0.00 0.28 0.00 | - 0.10 - - - - 0.25 | - - - - 0.05 - - | 0.01 - - - - - - | 0.01 - - - - - - | - - - 0.01 - - - | 0.01 - - - - - - | - - - - 1.2 - - | 0.0010 - - - - - - | - - - - 0.003 0.002 - | 0.0050 0.001 0.001 0.003 0.002 0.002 0.002 | 0.0011 - - - - - - | 0.76 0.82 0.89 1.00 1.06 1.23 1.30 | Inventive embodiments |
| 8 9 10 | 1.30 0.98 0.77 | 0.20 1.50 0.08 | 0.45 0.70 1.10 | 0.005 0.015 0.011 | 0.090 0.090 0.012 | 0.25 0.10 0.00 | - 0.05 - | - - - | - - - | - - - | - - - | - - - | - - - | - - - | - - - | 0.004 0.003 0.002 | - - - | 1.45 1.15 0.99 | Comparing embodiment |
Ceq＝％C+％Mn/5+％Cr/4
[table 2]
| Number | The condition of finish rolling | Controlled rolling condition after the finish rolling | Remarks | ||
| Gauge or diameter of wire (mm) | Coiling temperature (℃) | Air blast cooling conditions (speed of cooling is an average cooling rate) from coiling temperature to 450 ℃ | From 450 ℃ of cooling times (second) that are cooled to 300 ℃ | ||
| A | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 12 | Comparing embodiment |
| B | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 45 | Comparing embodiment |
| C | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 60 | Inventive embodiments |
| D | 5.5 | 850 | Be cooled to 670 ℃ and be cooled to 450 ℃ with 10 ℃/second with 5 ℃/second | 60 | Inventive embodiments |
| E | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 120 | Inventive embodiments |
| F | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 180 | Inventive embodiments |
| G | 5.5 | 850 | Cool off with 12 ℃/second speed monotonously | 220 | Comparing embodiment |
[table 3]
| Sequence number | The type of steel | Controlled chilling condition second | Rolled wire structure perlite area percent (%) | The mechanical property of rolled wire | The feature of rolled wire | Remarks | |||||||
| RA (％) | Average layer gap (nm) | Wire rod intensity TS (MPa) B | Wire rod intensity TS (MPa) A of prediction | B≤A | A-B | But stringiness (from 5.5mm diameter to 2.3 mm diameter) | Enhanced stretch resistance (from 2.3mm diameter to 2.0 mm diameter) (kgf) | *Enhanced stretch resistance reduction amount (kgf) | |||||
| 1 2 3 4 5 6 7 | 3 3 3 3 3 3 3 | A B C D E F G | 97 95 99 98 94 96 93 | 42 42 40 38 41 39 41 | 125 123 125 131 127 122 128 | 1100 1065 1008 978 978 1025 1110 | 1024 1030 1024 1007 1018 1033 1015 | B＞A B＞A B＜A B＜A B＜A B＜A B＞A | -76 -35 16 29 40 8 -95 | ○ ○ ○ ○ ○ ○ ○ | 280 275 250 235 245 253 282 | 0 5 30 45 35 27 -2 | Comparing embodiment comparing embodiment inventive embodiments inventive embodiments inventive embodiments inventive embodiments comparing embodiment |
*Enhanced stretch resistance reduction amount is the difference with the enhanced stretch resistance of comparing embodiment 1
[embodiment 2]
Then, by the results are shown in the table 4 of obtaining among the embodiment 2.In embodiment 2, the steel wire wire rod of forming 1 to 10 diameter in the table 1 and be 5.5mm is rolling by the condition in the table 2, and what make same steel type then stands different controlled chilling condition A (comparing embodiment) and E (inventive embodiments) in pairs.The high carbon steel that obtains is thus stood then as the wire drawing in embodiment 1 same procedure.
Then, according to as the same procedure among the embodiment 1, the average intensity TS that measures and estimate the perlite area percent (%), RA (%) of high-carbon steel wire wire rod, obtains by tension test, average layer gap (nm) but stringiness, enhanced stretch resistance and enhanced stretch resistance reduction amount.The result who obtains is as shown in table 4.Enhanced stretch resistance reduction amount shown in the table 4 is under the steel of same type, comparing embodiment below and the comparison between the embodiments of the invention (difference), and difference is the controlled chilling condition after rolling.
Reference table 4 now carries out the comparison between following: comparing embodiment 8 and inventive embodiments 9, comparing embodiment 10 and inventive embodiments 11, comparing embodiment 12 and inventive embodiments 13, comparing embodiment 14 and inventive embodiments 15, comparing embodiment 16 and inventive embodiments 17, comparing embodiment 18 and inventive embodiments 19 and comparing embodiment 20 and inventive embodiments 21.It is evident that relatively from these, even in the steel type is 1 to 7, chemical constitution belong in the scope of the invention and 80% or above metal construction be under the situation of steel wire wire rod of pearlitic texture, the condition of rolling therein back controlled chilling (with wire rod from 450 ℃ of cooling times that are cooled to 300 ℃) is corresponding to the comparing embodiment of A (too short) time, and the actual average tensile strength TS (B) of described high-carbon steel wire wire rod is higher than the prediction average tensile strength (A) of described steel wire wire rod.As a result, but the stringiness of the big part in silk footpath is quite good, but the enhanced stretch resistance of the little part in silk footpath is big, and enhanced stretch resistance reduction amount is widely less than wherein corresponding to the enhanced stretch resistance reduction amount in the embodiment of the invention of the controlled chilling condition of E.
This trend also is correct for the comparing embodiment in the table 4 22 and 23, but because in these comparing embodiments, used the steel type 8 (carbon is too high) that exceeds the scope of the invention, even so also break owing to pro-eutectoid cementite in the major diameter part, like this, infeasible in the little part of diameter to the measurement of enhanced stretch resistance.
This also is correct for the comparing embodiment in the table 4 24 and 27, wherein because of the steel type 9 (silicon is too high) and the steel Class1 0 (manganese is too high) that have used in the table 1 that exceeds the scope of the invention, even so also break owing to crossing the cold junction structure in the big part of diameter, like this, the enhanced stretch resistance of the part that the energy measurement diameter is not little.
The above results shows, the chemical constitution that limits among the present invention, but and among the present invention to tensile strength and wire rod is significant for the stringiness and the enhanced stretch resistance reduction effect of the little part in silk footpath from 450 ℃ of qualifications of cooling time that are cooled to 300 ℃.
[table 4]
| Number | The type of steel | The controlled chilling condition | Rolled wire structure perlite area percent (%) | The mechanical property of rolled wire | The feature of rolled wire | Remarks | |||||||
| RA (％) | Average layer gap (nm) | Wire rod intensity TS (MPa) B | Wire rod intensity TS (MPa) A of prediction | B≤A | A-B | But stringiness (from the 5.5mm diameter to the 2.3mm diameter) | Enhanced stretch resistance (from 2.3mm diameter to 2.0 mm diameter) (kgf) | *Enhanced stretch resistance reduction amount (kgf) | |||||
| 8 9 10 11 12 13 14 15 16 17 18 19 20 21 22 23 24 25 26 27 | 1 1 2 2 3 3 4 4 5 5 6 6 7 7 8 8 9 9 10 10 | A E A E A E A E A E A E A E A E A E A E | 97 93 94 96 97 94 94 96 97 95 92 98 97 96 93 91 78 72 76 77 | 42 40.4 42 40 42 41 38 37.5 41 41 31 35 39 35 31 32 30 31 28 26 | 135 143 150 130 125 127 115 119 131 133 115 113 125 125 119 119 - - - - | 953 921 1010 975 1100 978 1121 1041 1220 1051 1320 1175 1340 1152 1488 1234 1477 1650 1540 1645 | 943 929 933 981 1024 1018 1101 1088 1073 1067 1190 1198 1177 1177 1250 1250 - - - - | B＞A B＜A B＞A B＜A B＞A B＜A B＞A B＜A B＞A B＜A B＞A B＜A B＞A B＜A B＞A B＜A - - - - | -10.23 7.73 -76.75 5.96 -75.89 40.30 -19.72 46.53 -147.41 15.69 -130.25 22.68 -162.77 25.23 -237.46 16.35 - - - - | 00000000000000 steel wire fractures (pro-eutectoid cementite) steel wire fractures (pro-eutectoid cementite) steel wire fracture (crossing air-cooled structure) steel wire fracture (crossing air-cooled structure) steel wire fracture (crossing air-cooled structure) steel wire fracture (crossing air-cooled structure) | 194 161 245 225 280 245 312 284 265 221 320 284 320 284 do not have evaluation not estimate does not have evaluation not have to estimate not evaluation does not have evaluation | 33 20 35 28 44 36 36 - - - - - - | Comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment inventive embodiments comparing embodiment comparing embodiment comparing embodiment comparing embodiment comparing embodiment comparing embodiment |
*Enhanced stretch resistance reduction amount is the difference with the enhanced stretch resistance of comparing embodiment 1
As mentioned above, the invention provides a kind of high-carbon steel wire wire rod and preparation method thereof, in described high-carbon steel wire wire rod, before the wire drawing and during can omit patent, but and demonstrate good stringiness and in the wire drawing die head, showing low enhanced stretch resistance under the hot-rolled state.
Claims (4)
1. high carbon steel wires excellent in spinnability, it comprises by the carbon of quality % 0.65% to 1.20%, 0.05% to 1.2% silicon, 0.2% to 1.0% manganese and 0.35% or the chromium of following (comprising 0%), also comprise quantitative limitation separately and be 0.02% or following p and s, wherein
80% or above metal construction constitute by pearlitic texture; With
Show following relation between average tensile strength TS of described high-carbon steel wire wire rod (MPa) and the average lamellar spacing λ (nm):
(λ/Ceq)+290, wherein the content in view of carbon in described high-carbon steel wire wire rod is %C to TS≤8700/ √, and the content of manganese is %Mn, and the content of chromium is % chromium, Ceq=%C+%Mn/5+%Cr/4.
2. high-carbon steel wire wire rod according to claim 1, it also comprises at least a following composition that is selected from: 0.005% to 0.30% vanadium, 0.05% to 0.25% copper, 0.05% to 0.30% nickel, 0.05% to 0.25% molybdenum, 0.020 to 0.10% niobium, 0.005 to 0.010% titanium, 0.0005% to 0.0050% boron, and 0.005 to 2.0% cobalt.
3. high carbon steel wires excellent in spinnability according to claim 1, it also comprises at least a following composition that is selected from: 0.0005% to 0.005% calcium, 0.0005% to 0.005% REM, and 0.0005% to 0.007% magnesium.
4. method of producing according to the high-carbon steel wire wire rod described in the claim 1, wherein, with described high-carbon steel wire wire rod from rolling end postcooling to the process of room temperature, be used for described wire rod was remained on 60 seconds to 200 seconds from 450 ℃ of periods that are cooled to 300 ℃, then be cooled to room temperature.
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| CN102021491A (en) * | 2010-11-24 | 2011-04-20 | 东阳市中洲钢带有限公司 | Steel belt for high-elasticity ultrathin sole slice and production process thereof |
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| CN101680069B (en) * | 2007-06-05 | 2012-07-04 | Posco公司 | High carbon steel sheet superior in fatiugue lifeand manufacturing method thereof |
| CN102021491A (en) * | 2010-11-24 | 2011-04-20 | 东阳市中洲钢带有限公司 | Steel belt for high-elasticity ultrathin sole slice and production process thereof |
| CN102732788A (en) * | 2012-03-26 | 2012-10-17 | 镇江耐丝新型材料有限公司 | Novel microalloyed steel for high speed spiral cutting steel wires |
| CN105324503A (en) * | 2013-06-24 | 2016-02-10 | 新日铁住金株式会社 | High-carbon steel wire rod and method for manufacturing same |
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