CN107208208A - The carbon steel wire rod with high of excellent in wire-drawing workability - Google Patents
The carbon steel wire rod with high of excellent in wire-drawing workability Download PDFInfo
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- CN107208208A CN107208208A CN201580075308.5A CN201580075308A CN107208208A CN 107208208 A CN107208208 A CN 107208208A CN 201580075308 A CN201580075308 A CN 201580075308A CN 107208208 A CN107208208 A CN 107208208A
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- wire rod
- steel wire
- carbon steel
- pearlite
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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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
Abstract
The present invention relates to the carbon steel wire rod with high after hot rolling, wherein, composition of steel contains C in terms of quality %：0.60~1.10%, Si：0.02~2.0%, Mn：0.1~2.0%, Cr：0.3~1.6%, Al：0.001~0.05%, N is limited to less than 0.008%, P is limited to less than 0.020%, S is limited to less than 0.020%, surplus is Fe and inevitable impurity, the tissue of the carbon steel wire rod with high in terms of the area occupation ratio in the section vertical with length of wires direction more than 95% is pearlite, the average platelet spacing of foregoing pearlite is 50~100nm, and the average value in the pearlite block footpath since the i.e. central part in region within the circle that the diameter center is D/2 relative to the diameter D of wire rod in the section vertical with length of wires direction is 5 μm<Pearlite block footpath<15μm.
Description
Technical field
The present invention relates to the high-carbon after wire drawing used in various wireropes such as power transmission line cable, suspension bridge cable etc.
Steel wire rod.
Background technology
For the carbon steel wire rod with high used in power transmission line cable, suspension bridge cable, various wireropes etc., after wire drawing
Have on the basis of high intensity, high ductility, good wire-drawing workability is sought from the viewpoint of productivity ratio.To be obtained from such
Hair, develops the high-carbon wire rod of various high-quality so far.
For example, in patent document 1, it is proposed that due to the reduction of the solid solution N amounts of the addition based on Ti and based on solid solution Ti's
The reduction of strain-aging and the technology for obtaining good wire-drawing workability.In addition, in patent document 2, it is proposed that by by carburizing
Volume morphing control is spheroidizing, so as to obtain low-intensity and the technology of good wire-drawing workability.In patent document 3, it is proposed that
By determining each content of C, Si, Mn, P, S, N, Al and O in steel and controlling the second phase ferrite area occupation ratio and pearly-lustre
Body piece interlamellar spacing, the wire-drawing workability that mould abrasion extend die life is not susceptible to and can suppress so as to obtain breaking
The technology of excellent wire rod.In patent document 4, it is proposed that C：0.6~1.1% carbon steel wire rod with high, it is following high ductility
Carbon steel wire rod with high：More than 95% is formed by pearlitic structrure, and being determined by EBSP devices for the central part of hot rolling wire is obtained
The maximum of pearlite block particle diameter of pearlite be less than 45 μm and average value is 10~25 μm.
Prior art literature
Patent document
Patent document 1:JP 2012-097300 publications
Patent document 2:JP 2004-300497 publications
Patent document 3:JP 2007-327084 publications
Patent document 4:JP 2008-007856 publications
The content of the invention
Problems to be solved by the invention
If however, according to the experiment of the present inventor etc., even with above-mentioned each technology, high-strength more than 1300MPa
Spend material in the case of, may not necessarily also access the addition by Ti, solid solution N reduction and make wire-drawing workability improve it is clear and definite
Effect.In addition, for spheroidizing heat treatment, the low intensity after wire drawing is not suitable as the purposes of high-carbon steel wire.
The present invention is in view of such actual conditions are formed, to provide as obtaining intensity height, wire-drawing workability
The steel wire rod of the raw material of good steel wire is problem.
The solution used to solve the problem
The present invention is the carbon steel wire rod with high of the raw material of the steel wire as high intensity, and its purport is as described below.
(1) a kind of carbon steel wire rod with high, it is the carbon steel wire rod with high after hot rolling, and composition of steel contains C in terms of quality %：0.60~
1.10%th, Si：0.02~2.0%, Mn：0.1~2.0%, Cr：0.3~1.6%, Al：0.001~0.05%, N is limited to
Less than 0.008%, P is limited to less than 0.020%, S is limited to less than 0.020%, surplus is Fe and inevitable
Impurity, the tissue in terms of the area occupation ratio in the section vertical with length of wires direction more than 95% of the carbon steel wire rod with high is pearly-lustre
Body, the average platelet spacing of foregoing pearlite is 50~100nm, the section vertical with length of wires direction since the center
The average value in the pearlite block footpath of the i.e. central part in region within the circle that diameter is D/2 relative to the diameter D of wire rod is 5 μm<Pearl
Body of light block footpath<15μm.
(2) according to the carbon steel wire rod with high of (1), wherein, 500 the section vertical with length of wires direction is since top layer
Region within μm is the ferritic crystal orientation in peripheral part, pearlitic structrure<110>Aggregation degree be more than 1.3.
(3) according to the carbon steel wire rod with high of (1), wherein, further contain Mo in terms of quality %：0.01~0.2%.
(4) according to the carbon steel wire rod with high of (1), wherein, further contain Nb in terms of quality %：0.01~0.2%, V：0.01
1 kind among~0.2% or 2 kinds.
(5) according to the carbon steel wire rod with high of (1), wherein, further contain B in terms of quality %：0.0003~0.003%.
(6) according to the carbon steel wire rod with high of (1), wherein, Si：0.02~1.0%.
(7) according to the carbon steel wire rod with high of (1), wherein, the average value in pearlite block footpath is defined as 5 μm<Pearlite block footpath<12
μm。
The effect of invention
According to the present invention it is possible to provide tensile strength and ductility with more than 1300MPa high carbon steel wire rod with high
Deng contribution industrially is extremely notable.
Brief description of the drawings
Fig. 1 is the figure for showing central part A and peripheral part B in the section vertical with length of wires direction.
Fig. 2 is the figure for showing wire drawing logarithmic strain (very askew) and the relation of accumulation fracture rate.
Embodiment
The present inventor etc. enter repeatedly in order to solve problem as described above for the tissue and heat treatment method of steel wire rod
The various investigation of row.As a result, obtaining following (a)~(b) opinion.
(a) Cr addition promotes the miniaturization of original γ particle diameters, makes the pearlite block footpath miniaturization after phase transformation.
(b) average value in pearlite block footpath is thinner what is observed in the central part A (regulation) of wire rod, wire-drawing workability
It is better.
(c) ferrite crystal takes what is observed in the peripheral part B (regulation) in the section vertical with length of wires direction
To<110>In the case of orientation set, the Crystal Rotation in wire drawing becomes less, therefore can suppress to be caused by shear stress
Space generation.
The ferrite crystal orientation in the length of wires direction of steel wire rod and the Kuai Jingcong centers of pearlite have not to top layer
Same distribution.Fig. 1 represents central part A and peripheral part B in the section vertical with length of wires direction.In this manual, such as
Shown in the Fig. 1, by the wire rod relative to diameter Dmm centered on the region definition within the circle of a diameter of 1/2D center
Portion A, peripheral part B is defined as by the region within 500 μm top layer.
For pearlite block footpath, Fig. 1 central part A can be set to locate, pass through electron backscattered (Electron
BackScatter Diffraction, referred to as EBSD) method determines.For example, long using colloidal silica particle pair and wire rod
Spend the vertical section in direction and carry out mirror ultrafinish, the measure using EBSD methods is carried out near the central part of radial direction, iron element is made
The figure of body crystal orientation.For example, being that the rectangular area that every 1 side is more than 500 μm is carried out in mapping area, configured with primitive shape
Carried out for regular hexagon element, measuring interval are 0.5 μm of interval.
The ferrite crystal orientation in length of wires direction<110>Aggregation degree can by by Fig. 1 peripheral part B be set to survey
Positioning is put, and the crystal orientation of each pixel is marked in { 110 } pole figure to determine.More specifically, ferrite crystal orientation<
110>Aggregation degree can generate { 110 } pole figure using the measurement result of EBSD methods, texture is carried out to resulting pole figure
(Texture) parsing etc. is determined.For aggregation degree, the random situation of crystal orientation is set to 1, represented with strength ratio.
If in addition, identifying ferrite crystal orientation by EBSD methods, each hexagon shape pixel gives ferritic crystalline substance
The information of body orientation, as a result, the information of the differential seat angle of the boundary definition crystal orientation of adjacent pixel.As between two pixels
Border there is more than 9 ° of ferrite crystal orientation inclination angle difference and the pixel boundary that is adjacent is also such for more than 9 °, have
In the case of the pixel boundary of more than 9 ° of inclination angle difference is continuous, they are connected and pearlite block crystal boundary is defined as.
In the case where the pixel boundary extended from the triple point of pixel is more than 9 °, pearlite block crystal boundary branch.Picture
In the case that the crystal orientation difference on plain border is on the way interrupted for more than 9 ° of condition, the pixel boundary is not considered as pearlite block
Crystal boundary and ignore.Form of thinking more than, the picture for the ferrite gun parallax for possessing more than 9 ° is defined in whole rectangular area
Plain border, in the case that pixel boundary surrounds the region of a closing, is defined as a pearlite block, by pixel side by the region
Boundary is defined as pearlite block crystal boundary.So operation, shows pearlite block crystal boundary on the figure of ferrite crystal orientation, determines pearly-lustre
The block footpath of body.Wherein, in the case that one of defined pearlite block is constituted below 25 pixels, handled as noise
And ignore.Wherein, pearlite block is identical with pearlite knurl meaning.In addition, pearlite is lamellar pearlite.
It can be obtained for piece interlamellar spacing by following：With nital corrosion and length of wires direction
Vertical section, using SEM, for the minimum position of 10000 times of visual field inner sheet interlamellar spacings shot of multiplying power, vertically
Ground is scribed ss 5 piece interlamellar spacings, by the length divided by 5 of 5 piece interlamellar spacings.It should be noted that being regarded with SEM shooting at 10
Carried out more than wild, calculated piece interlamellar spacing divided by visual field number in each visual field, so as to obtain average value.
For wire-drawing workability, length 10m test material is impregnated in hydrochloric acid and implements phosphorus after scale removal, washing
Hydrochlorate aluminum coated steel, carries out dry wire drawing processing to evaluate.Wire Drawing can be used with die approach (entirety) angle
20 °, sizing (ベ ア リ Application グ) length carries out for the WC-Co superhard alloys molding jig of 0.3 times or so of the shape in aperture.Draw
Silk speed is set to 50m/ minutes, can use the dry wire drawing lubricant based on odium stearate and calcium stearate.
In the case of not breaking, in order that section slip reduces mould aperture for 20%, it is to occurring broken string
Only carry out Wire Drawing.Terminate and evaluate when the broken string number of times of total is 20 times, by the line footpath (line before wire drawing of test material
Footpath) D0 and the mould aperture D that breaks obtain Wire Drawing degree according to following formula.
Wire Drawing degree (ε)=2 × ln (D0/D)
Under each Wire Drawing degree, the number of times being broken divided by 20 (overall test numbers) and obtain fracture rate, it is plus extremely
Accumulation fracture rate untill this, obtains the accumulation fracture rate under each Wire Drawing degree.Fig. 2 is to judge that wire-drawing workability is good
It is used as the result of the test of the wire coil of benchmark.When Wire Drawing degree is 1.7, breaks are 1 time, and the accumulation fracture rate of the longitudinal axis is
0.05(1/20).When Wire Drawing degree is 1.9, breaks are 5 times and fracture rate is 0.25, add (Wire Drawing degree before this
1.7) during accumulation fracture rate 0.05, accumulation fracture rate is 0.3.Also, when Wire Drawing degree turns into maximum in 20 experiments, tire out
Product fracture rate turns into 1.0.
In the present invention, accumulation fracture rate is obtained from chart turns into 0.5 Wire Drawing degree, is defined as wire-drawing workability.
As shown in Fig. 2 judging that the wire-drawing workability that wire-drawing workability is the good wire coil as benchmark is 2.23.And then, accumulation
The Wire Drawing rate that fracture rate is 0.9 is 3.0, and the Wire Drawing rate that accumulation fracture rate is 1.0 is 3.12.Therefore, in the present invention,
Wire-drawing workability is evaluated as well for more than 2.23, more preferably wire-drawing workability is more than 2.53, further preferably by wire drawing
Processability is evaluated as good for more than 2.95.
(for steel wire rod)
Then, illustrated for the composition of the steel wire rod of the present invention.It should be noted that the % of quantity relating is matter
Measure %.
<For composition>
C
C improves the element of intensity to make tissue turn into pearlite.When C amounts are less than 0.60%, the non-pearly-lustre such as grain boundary ferrite
Body tissue is generated and damages wire-drawing workability, and the tensile strength of superfine steel wire is also reduced.On the other hand, when C amounts are more than 1.10%,
The non-pearlite such as proeutectoid cementite tissue is generated, wire-drawing workability deterioration.Therefore, C amounts are defined to 0.60~1.10% model
Enclose.It is preferred that C amounts are set into more than 0.65%.
Si
Si is the element of the deoxidation for steel, it helps solution strengthening.In order to obtain effect, addition more than 0.02%
Si.It is preferred that Si amounts are set into more than 0.05%.On the other hand, when Si amounts are more than 2.0%, surface is easily produced in hot-rolled process
Decarburization, therefore the upper limit is set to 2.0%.It is preferred that Si amounts are set into less than 1.0%, less than 0.5% is more preferably set to.
Mn
Mn is the element for deoxidation, desulfurization, addition more than 0.1%.On the other hand, when Mn amounts are more than 2.0%, pearlite
Phase transformation significantly postpones, and the time of patenting processing is elongated, therefore Mn amounts are set into less than 2.0%.Mn amounts be preferably 1.0% with
Under.
Cr
Cr is to make former γ particle diameters miniaturization, make the fine element of pearlitic structrure, it helps high intensity.In order to obtain
Effect, the Cr of addition more than 0.3%.On the other hand, when Cr amounts are more than 1.6%, proeutectoid cementite is separated out, and makes wire-drawing workability
Reduction, therefore the upper limit is set to 1.6%.It is preferably set to less than 1.3%.More preferably it is set to less than 1.0%.
Al
Al is the element with deoxidation, is necessary for reducing the oxygen amount in steel.However, Al content is not enough
When 0.001%, it is difficult to obtain the effect.On the other hand, Al easily forms the oxide system field trash of hard, and particularly, Al contains
When amount is more than 0.05%, the formation of thick oxide system field trash becomes notable, therefore the reduction of wire-drawing workability is notable.Cause
This, 0.001~0.05% is set to by Al content.More preferably lower limit is more than 0.01%, and more preferably the upper limit is less than 0.04%.
N
N is is bonded to the intensity that dislocation improves steel wire in cold-drawn wire processing, the member on the contrary reducing wire-drawing workability
Element.Particularly, when N content is more than 0.008%, the reduction of wire-drawing workability becomes notable.Therefore, N content is limited to
Less than 0.008%.More preferably less than 0.005%.
P
P easy segregations in steel, during segregation, significantly delay eutectoid phase transformation, therefore, eutectoid phase transformation is not completed, and is easily formed
The martensite of hard.In order to prevent the problem, P content is limited to less than 0.02%.
S
S in large quantities in the presence of, form MnS in large quantities, making the ductility of steel reduces, therefore is limited to less than 0.020%.It is more excellent
Elect less than 0.01% as.
Mo
Mo addition is arbitrary.If addition, the effect with the tensile strength for improving steel wire rod.In order to obtain the effect
Really, the Mo of addition more than 0.02% is expected.However, when Mo content is more than 0.20%, martensitic structure is easily generated, wire drawing adds
Work is reduced.Therefore, Mo content is preferably 0.02~0.20%.More preferably less than 0.08%.
V
V addition is arbitrary.If addition, carbonitride is formed in steel wire rod, reduces pearlite block footpath, improves and draws
Silk processability.In order to obtain the effect, the V of addition more than 0.02% is expected.However, when V content is more than 0.20%, existing thick
Big carbonitride is easily generated, the situation of wire-drawing workability reduction.Therefore, V content is preferably 0.02~0.20%.It is more excellent
Elect less than 0.08% as.
Nb
Nb addition is arbitrary.If addition, carbonitride is formed in steel wire rod, reduces pearlite block footpath, is improved
Wire-drawing workability.In order to obtain the effect, the Nb of addition more than 0.002% is expected.However, when Nb content is more than 0.05%,
There is thick carbonitride easily to generate, the situation of wire-drawing workability reduction.Therefore, Nb content be preferably 0.002~
0.05%.More preferably less than 0.02%.
Ti
Ti addition is arbitrary.If addition, carbide or nitride are formed in steel wire rod, reduces pearlite block
Footpath, improves wire-drawing workability.In order to obtain the effect, the Ti of addition more than 0.002% is expected.However, Ti content exceedes
When 0.05%, thick carbide or nitride is easily formed, there is a situation where that wire-drawing workability starts reduction.It is therefore preferable that
Ti content is set to 0.02~0.05%.More preferably less than 0.03%.
B
B addition is arbitrary.If the solid solution N in addition, steel wire rod is formed as the solid solution N in BN, reduction steel, improve
Wire-drawing workability.In order to obtain the effect, the B of addition more than 0.0003% is expected.However, when B content is more than 0.003%,
In the presence of easily generating thick nitride, the situation of wire-drawing workability reduction.Therefore, B content be preferably 0.0003~
0.003%.More preferably less than 0.002%.
<For metallographic structure>
Then, the metallographic structure for the steel wire rod of the present invention is illustrated.
Area occupation ratio
The non-pearlites such as pro-eutectoid ferrite, proeutectoid cementite, which are organized in, turns into the original being cracked in final wire drawing
Cause.In embodiments of the present invention, in order to improve wire-drawing workability, the area occupation ratio of pearlite is set to more than 95%.Surplus
For the non-pearlite tissue such as pro-eutectoid ferrite, proeutectoid cementite.It should be noted that above-mentioned metallographic structure can such as get off
It is determined that：The section that wire rod is vertically cut off relative to length of wires direction is cut as sample, after mirror ultrafinish, with scanning electricity
Sub- microscope is observed.In addition, the area occupation ratio of each metallographic structure can make according to the result observed by SEM
Obtained with planimetric method or point count.Preferably, multiplying power is observed, for example, is set to more than 1000 times, the area of observation, for example
It is set to 1000 μm2More than.For example when determining area occupation ratio with point count, measuring point is preferably set to more than 200 points.
The block footpath of pearlite
As above-mentioned opinion, when the block footpath (hereinafter also referred to as pearlite block footpath) of pearlite is more than 15 μm, Wire Drawing
Property reduction, therefore be set to less than 15 μm.More preferably less than 12 μm.In addition, when pearlite block footpath is set to less than 5 μm, non-pearly-lustre
The increase of body tissue, therefore it is set to lower limit by 5 μm.
Ferrite crystal orientation<110>Aggregation degree
Ferrite crystal orientation<110>When being collected in the peripheral part in the section vertical with length of wires direction, it can suppress
Orientation rotation in Wire Drawing, suppresses the space based on detrusion and is formed.In the present invention, the effect is highlighted, ferrite
Crystal orientation<110>Aggregation degree be set to more than 1.3.Preferably more than 1.5, more than 1.7 are more preferably.
It should be noted that pearlite block footpath and ferrite crystal orientation<110>Aggregation degree can be using as described above
Such EBSD methods are determined.
Piece interlamellar spacing
Metallographic structure in the present invention is based on pearlite, and target is to make the tensile strength of the steel wire rod for 1300MPa
Above, it is preferably more than 1350MPa, more preferably more than 1400MPa.In order to obtain being shown in the intensity, embodiment described later
The average platelet spacing of pearlite need for below 100nm.In addition, when the average platelet spacing of pearlite is less than 50nm, removing
Bainite structure beyond pearlite is mixed, it is impossible to obtain target strength, and Wire Drawing hardening ratio is reduced, therefore will
Lower limit is set to 50nm.
<For the manufacture method of steel wire rod>
Then, the manufacture method for the steel wire rod of the present invention is illustrated with specific example.It should be noted that with
Under explanation be merely used for explanation the present invention example, not delimit the scope of the invention.
The steel wire rod of the present invention has the steel of above-mentioned composition by conventional method come melting, is cast, for gained
To steel billet implement hot rolling and manufacture.Hot rolling is to carry out heating steel billet to 1150 DEG C or so.The final rolling temperature of hot rolling is 740
~880 DEG C.In order to occur pearlitic transformation after finish rolling, with the means such as air blast cooling, misting cooling, water cooling with 25 DEG C/sec~
40 DEG C/sec be cooled to and reach 550 DEG C~650 DEG C untill (once cool down), keep in this temperature range 30 seconds~180 seconds it
Afterwards, 300 DEG C (secondary coolings) are cooled to more than 2 DEG C/sec with the means of air cooling, water cooling, room temperature is cooled to the means such as letting cool.
As long as it should be noted that the diameter of wire rod may insure the necessary processing hardening when steel wire is made, being not particularly limited.
When the final rolling temperature of hot rolling is higher than 880 DEG C, the micronized effect of former γ particle diameters tails off, therefore is set to less than 880 DEG C.
In addition, when being rolled at less than 740 DEG C, pro-eutectoid ferrite can be separated out in rolling, therefore lower limit is set into 740 DEG C.
When cooling velocity under once cooling down is less than 25 DEG C/sec, former γ particle diameters coarsening, therefore by lower limit be set to 25 DEG C/
Second.Being cooled in actual manufacture more than 40 DEG C/sec is difficult, therefore is set to less than 40 DEG C/sec.
When keeping temperature is more than 650 DEG C, former γ particle diameters coarsening and intensity decreases, therefore the upper limit is set to 650 DEG C.This
When outside, less than 550 DEG C, the increase of non-pearlite tissue, therefore lower limit is set to 550 DEG C.
When retention time was less than 30 seconds, pearlitic transformation is not completed, the increase of non-pearlite tissue, therefore lower limit is set into 30
Second.In addition, the holding more than 180 seconds cause the deterioration of productivity ratio, the shape avalanche of lamella pearlite and cause wire strength
Reduction, therefore the upper limit is set to 180 seconds.
In 2 coolings, during the Slow cooling that temperature range more than 300 DEG C progress stove is cold etc. less than 2 DEG C/sec, cause
The lower limit of secondary cooling speed untill the reduction of intensity, therefore near 300 DEG C is set to 2 DEG C/sec.It should be noted that being not required to
Comprehend from 300 DEG C of cooling velocities untill room temperature.
Embodiment
Hereinafter, embodiment is shown while for the steel wire rod and the system of steel wire rod described in embodiments of the present invention
The method of making is specifically described.It should be noted that embodiments illustrated below is only the steel described in embodiments of the present invention
One example of the manufacture method of wire rod and steel wire rod, the manufacture method of steel wire rod and steel wire rod of the present invention is not
It is limited to following examples.
For the high-carbon steel hot rolling wire of the composition composition shown in table 1, by the hot-rolled condition shown in change table 2,
It is but pearlite block footpath, the ferrite crystal orientation of skin section of central part for pearlitic structrure so as to make identical<110>
The different wire rod of aggregation degree, tensile strength.These wire rods are evaluated with Wire Drawing critical strain.The knot is shown in table 3
Really.
[table 1]
| Steel grade | C | Si | Mn | Cr | Al | Mo | B | Nb | V | Ti | |
| A | 0.82 | 0.2 | 0.5 | 0.5 | 0.029 | - | - | - | - | - | Invention steel |
| B | 1.07 | 0.05 | 0.1 | 1.2 | 0.028 | - | - | - | - | - | Invention steel |
| C | 0.62 | 1.5 | 1.5 | 0.3 | 0.004 | 0.1 | - | - | - | - | Invention steel |
| D | 0.92 | 0.2 | 0.5 | 0.5 | 0.045 | - | 0.002 | - | - | - | Invention steel |
| E | 1.08 | 0.05 | 0.5 | 0.8 | 0.030 | - | - | 0.01 | 0.1 | - | Invention steel |
| F | 0.83 | 0.15 | 0.2 | 0.7 | 0.035 | - | - | - | - | 0.03 | Invention steel |
| G | 0.92 | 0.05 | 0.5 | 0.1 | 0.004 | - | - | - | - | - | Compare steel |
| H | 0.82 | 0.2 | 2.5 | 0.5 | 0.018 | - | - | - | - | - | Compare steel |
| I | 1.35 | 0.05 | 0.5 | 1 | 0.022 | - | - | - | - | - | Compare steel |
[table 2]
[table 3]
In the specific manufacture method of following these carbon steel wire rod with high of explanation.The chemistry of wire rod as shown in turning into table 1
Composition like that, uses converter melting, by the bloom breaking down, makes the medium and small shaped blooms of 155mm square, is heated to 1150 DEG C or so
Afterwards, it is 740 DEG C~880 DEG C of scope progress hot rolling in the final temperature of rolling, obtains diameter 10mm wire rod.
Wire rod after being terminated for above-mentioned hot rolling, by the cooling zone being arranged on rolling line, is sprayed with nozzle at once
Penetrate the scope that cooling water is cooled to 550 DEG C~650 DEG C.Now, water and water cooling time are changed, control reaches temperature.In addition, connecing
And wire rod is cooled to 650 DEG C~550 DEG C of scope by air blast cooling with 5 DEG C/sec~25 DEG C/sec of cooling velocity.Afterwards
Kept for 60 seconds or so in the temperature range, so as to complete pearlitic transformation, room temperature is cooled to by air cooling.
Pearlite area occupation ratio (%), pearlite block footpath, piece interlamellar spacing, the ferrite crystal for determining these steel wire rods respectively take
To, tensile strength.
Pearlite area occupation ratio is obtained as follows, and the sample of mirror ultrafinish is carried out for cross section obtained from cut-out wire rod, is used
The mixed liquor etching of nitric acid and ethanol, with the central portion between the surface and center of 2000 times of observation wire rods so as to obtain.
For pearlite block footpath and piece interlamellar spacing, 62500 μm in the center 5mm of steel wire rod scope2Region survey
It is fixed.Ferrite is orientated<110>Aggregation degree determines device using the EBSD of TSL company systems, in the scope within 500 μm away from top layer
62500μm2Area test.
Tension test is carried out based on JIS Z 2241.For wire-drawing workability, add as described above, carrying out dry wire drawing
Work, the broken string number of times of total is set to 20 times, the figure of wire drawing logarithmic strain and the relation of accumulation fracture rate is made, to accumulate fracture
Rate is evaluated for 50% wire drawing logarithmic strain.Result is shown in table 3.PBS is averaged for pearlite block footpath.
No.10 keeping temperature is high, therefore piece interlamellar spacing is big, tensile strength is not enough.
No.11 Cr amounts are low, and the miniaturization in pearlite block footpath is insufficient, therefore Wire Drawing critical strain diminishes.
No.12 Mn amounts are more, pearlitic transformation do not complete, pearlite area occupation ratio is very small, thus Wire Drawing it is critical should
Change diminishes.
No.13 C amounts are high, proeutectoid cementite generation, therefore pearlite area occupation ratio is small, and Wire Drawing critical strain becomes
It is small.
No.14 retention time is short, and secondary cooling is carried out before pearlitic transformation is completed, therefore pearlite area occupation ratio is small,
Wire Drawing critical strain diminishes.
A No.15 cooling velocity is small, former γ particle diameters coarsening, therefore pearlite block footpath is big, and Wire Drawing is critical should
Change diminishes.
No.16 retention time is long, the shape avalanche of lamella pearlite, and tensile strength is not enough.
No.17 final rolling temperature is low, pro-eutectoid ferrite is largely generated, and tensile strength is not enough, and Wire Drawing is critical
Strain diminishes.
No.18 final rolling temperature is high, original γ particle diameter coarsenings, therefore pearlite block footpath is big, and Wire Drawing critical strain becomes
It is small.
No.19 secondary cooling speed is small, the shape avalanche of lamella pearlite, tensile strength reduction.
Claims (7)
1. a kind of carbon steel wire rod with high, it is the carbon steel wire rod with high after hot rolling, and composition of steel contains C in terms of quality %：0.60~
1.10%th, Si：0.02~2.0%, Mn：0.1~2.0%, Cr：0.3~1.6%, Al：0.001~0.05%, N is limited to
Less than 0.008%, P is limited to less than 0.020%, S is limited to less than 0.020%, surplus is Fe and inevitable
Impurity, the tissue in terms of the area occupation ratio in the section vertical with length of wires direction more than 95% of the carbon steel wire rod with high is pearly-lustre
Body, the average platelet spacing of the pearlite is 50~100nm, the section vertical with length of wires direction since the center
The average value in the pearlite block footpath of the i.e. central part in region within the circle that diameter is D/2 relative to the diameter D of wire rod is 5 μm<Pearl
Body of light block footpath<15μm.
2. carbon steel wire rod with high according to claim 1, wherein, in the section vertical with length of wires direction since top layer
Region within 500 μm is the ferritic crystal orientation in peripheral part, pearlitic structrure<110>Aggregation degree be more than 1.3.
3. carbon steel wire rod with high according to claim 1, wherein, further contain Mo in terms of quality %：0.02~0.20%.
4. carbon steel wire rod with high according to claim 1, wherein, further contain Nb in terms of quality %：0.002~0.05%, V：
0.02~0.20%, Ti：It is one kind or two or more among 0.002~0.05%.
5. carbon steel wire rod with high according to claim 1, wherein, further contain B in terms of quality %：0.0003~0.003%.
6. carbon steel wire rod with high according to claim 1, wherein, Si：0.02~1.0%.
7. carbon steel wire rod with high according to claim 1, wherein, the average value in pearlite block footpath is defined as 5 μm<Pearlite block footpath<
12μm。
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014-247258 | 2014-12-05 | ||
| JP2014247258 | 2014-12-05 | ||
| PCT/JP2015/083879 WO2016088803A1 (en) | 2014-12-05 | 2015-12-02 | High-carbon-steel wire rod having excellent wire drawing properties |
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| Publication Number | Publication Date |
|---|---|
| CN107208208A true CN107208208A (en) | 2017-09-26 |
| CN107208208B CN107208208B (en) | 2019-08-23 |
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| CN201580075308.5A Active CN107208208B (en) | 2014-12-05 | 2015-12-02 | The carbon steel wire rod with high of excellent in wire-drawing workability |
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| Country | Link |
|---|---|
| EP (1) | EP3228721A4 (en) |
| JP (1) | JP6394708B2 (en) |
| KR (1) | KR101952527B1 (en) |
| CN (1) | CN107208208B (en) |
| MX (1) | MX2017006990A (en) |
| WO (1) | WO2016088803A1 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107723592A (en) * | 2017-09-30 | 2018-02-23 | 钢铁研究总院 | A kind of high-carbon wire rod steel and its production technology |
| CN108728739A (en) * | 2018-04-21 | 2018-11-02 | 张家港联峰钢铁研究所有限公司 | A kind of non-tempering high-carbon high-strength alloy spring steel 90SiMn and preparation method thereof that quenches |
| CN110669981A (en) * | 2019-10-02 | 2020-01-10 | 江苏省沙钢钢铁研究院有限公司 | Vanadium-boron composite microalloyed cord steel wire rod and production method thereof |
| CN111041368A (en) * | 2019-12-26 | 2020-04-21 | 芜湖新兴铸管有限责任公司 | High-performance 82B wire rod steel and production method thereof |
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|---|---|---|---|---|
| KR101917461B1 (en) | 2016-12-22 | 2018-11-09 | 주식회사 포스코 | High strength wire rod and heat-treated wire rod having excellent drawability and method for manufacturing thereof |
| MY196779A (en) * | 2017-05-18 | 2023-05-03 | Nippon Steel Corp | Wire rod, drawn steel wire, and method for manufacturing drawn steel wire |
| JP7352069B2 (en) | 2019-07-26 | 2023-09-28 | 日本製鉄株式会社 | wire rod and steel wire |
| KR102421642B1 (en) * | 2019-12-20 | 2022-07-18 | 주식회사 포스코 | Wire rod for bearing and methods for manufacturing thereof |
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| CN110669981A (en) * | 2019-10-02 | 2020-01-10 | 江苏省沙钢钢铁研究院有限公司 | Vanadium-boron composite microalloyed cord steel wire rod and production method thereof |
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| CN111041368A (en) * | 2019-12-26 | 2020-04-21 | 芜湖新兴铸管有限责任公司 | High-performance 82B wire rod steel and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| EP3228721A1 (en) | 2017-10-11 |
| EP3228721A4 (en) | 2018-07-11 |
| JP6394708B2 (en) | 2018-10-03 |
| JPWO2016088803A1 (en) | 2017-10-05 |
| WO2016088803A1 (en) | 2016-06-09 |
| CN107208208B (en) | 2019-08-23 |
| KR20170092630A (en) | 2017-08-11 |
| KR101952527B1 (en) | 2019-02-26 |
| MX2017006990A (en) | 2017-08-24 |
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