CN107208208B - 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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- CN107208208B CN107208208B CN201580075308.5A CN201580075308A CN107208208B CN 107208208 B CN107208208 B CN 107208208B CN 201580075308 A CN201580075308 A CN 201580075308A CN 107208208 B CN107208208 B CN 107208208B
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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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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Abstract
The present invention relates to the carbon steel wire rod with high after hot rolling, wherein, composition of steel contains C:0.60~1.10% in terms of quality %, Si:0.02~2.0%, Mn:0.1~2.0%, Cr:0.3~1.6%, Al:0.001~0.05%, N is limited to 0.008% or less, P is limited to 0.020% or less, S is limited to 0.020% or less, surplus is Fe and inevitable impurity, the above are pearlite for the tissue of the carbon steel wire rod with high in terms of in the area ratio in the section vertical with length of wires direction 95%, the average platelet spacing of aforementioned pearlite is 50~100nm, region, that is, central part within the circle that the diameter since center in the section vertical with length of wires direction is D/2 relative to the diameter D of wire rod Pearlite block diameter average value be 5 μm < pearlite block diameter < 15 μm.
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 technique
For the carbon steel wire rod with high used in power transmission line cable, suspension bridge cable, various wireropes etc., after wire drawing
On the basis of having high-intensitive, high ductility, good wire-drawing workability is sought from the viewpoint of productivity.It to be found out from such
Hair, develops the high-carbon wire rod of various high-quality so far.
For example, proposing in patent document 1 due to the reduction of the solid solution N amount of the addition based on Ti and based on solid solution Ti's
The reduction of strain-aging and obtain the technology of good wire-drawing workability.In addition, in patent document 2, propose by by carburizing
Volume morphing control is spheroidizing, to obtain the technology of low-intensity and good wire-drawing workability.In patent document 3, propose
By determining each content of C, Si, Mn, P, S, N, Al and O in steel and controlling the second phase ferrite the area ratio and pearly-lustre
Body piece interlamellar spacing is not susceptible to obtain broken string and mold abrasion can be inhibited to make die life extended wire-drawing workability
The technology of excellent wire rod.In patent document 4, the carbon steel wire rod with high of C:0.6~1.1% is proposed, is following high ductility
Carbon steel wire rod with high: 95% or more is formed by pearlitic structrure, and the central part of hot rolling wire measures to obtain by EBSP device
The maximum value of pearlite block partial size of pearlite be 45 μm or less and average value is 10~25 μm.
Existing technical literature
Patent document
Patent document 1: special open 2012-097300 bulletin
Patent document 2: special open 2004-300497 bulletin
Patent document 3: special open 2007-327084 bulletin
Patent document 4: special open 2008-007856 bulletin
Summary of the invention
Problems to be solved by the invention
However, even with above-mentioned each technology, being more than the high-strength of 1300MPa if the experiment of people etc. according to the present invention
In the case where spending material, the addition by Ti may not necessarily be also accessed, the reduction of solid solution N makes defining for wire-drawing workability improvement
Effect.In addition, the intensity after wire drawing is low, is not suitable as the purposes of high-carbon steel wire for spheroidizing heat treatment.
The present invention be in view of such actual situation made of, become that intensity is high, wire-drawing workability for obtaining to provide
The steel wire rod of the raw material of good steel wire is project.
The solution to the problem
The present invention is the carbon steel wire rod with high as the raw material of high-intensitive steel wire, and purport is as described below.
(1) a kind of carbon steel wire rod with high, be hot rolling after carbon steel wire rod with high, composition of steel with quality % be calculated as C:0.60~
1.10%, Si:0.02~2.0%, Mn:0.1~2.0%, Cr:0.3~1.6%, Al:0.001~0.05%, Mo:0.20%
Below, Nb:0.05% or less, V:0.20% or less, Ti:0.05% or less, B:0.003% or less, N:0.008% or less, P:
0.020% or less and S:0.020% hereinafter, and surplus: Fe and inevitable impurity,
The tissue of the carbon steel wire rod with high in terms of in the area ratio in the section vertical with length of wires direction 95% the above are
Pearlite,
The average platelet spacing of aforementioned pearlite is 50~100nm,
The circle that the diameter since center in the section vertical with length of wires direction is D/2 relative to the diameter D of wire rod
Within the average value of region, that is, central part pearlite block diameter be greater than 5 μm and less than 15 μm,
Region, that is, peripheral part the section vertical with length of wires direction is since surface layer within 500 μm, pearlite
The aggregation degree of ferritic crystal orientation<110>in tissue is 1.3 or more,
The tensile strength of the carbon steel wire rod with high is 1300MPa or more.
(2) carbon steel wire rod with high according to (1), wherein contain Mo:0.02~0.20% in terms of quality %.
(3) carbon steel wire rod with high according to (1) or (2), wherein in terms of quality % containing Nb:0.002~0.05%,
1 kind among V:0.02~0.20%, Ti:0.002~0.05% or 2 kinds.
(4) carbon steel wire rod with high according to any one of (1)~(3), wherein in terms of quality % containing B:0.0003~
0.003%.
(5) carbon steel wire rod with high according to any one of (1)~(4), wherein in terms of quality % containing Si:0.02~
1.0%.
(6) carbon steel wire rod with high according to any one of (1)~(5), wherein the average value of pearlite block diameter is greater than 5 μ
M and less than 12 μm.
The effect of invention
According to the present invention it is possible to provide the tensile strength with 1300MPa or more and the high carbon steel wire rod with high of ductility
Deng contribution industrially is extremely significant.
Detailed description of the invention
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 the relationship for showing wire drawing logarithmic strain (very askew) and accumulating fracture rate.
Specific embodiment
The inventors of the present invention are as described above in order to solve the problems, such as, the tissue and heat treatment method for steel wire rod repeatedly into
The various investigation of row.As a result, obtaining the opinion of following (a)~(c).
(a) addition of Cr promotes the miniaturization of original γ partial size, the pearlite block diameter miniaturization after making phase transformation.
(b) average value of pearlite block diameter what is observed in the central part A (regulation) of wire rod is thinner, wire-drawing workability
It is the better.
(c) the ferrite crystal what is observed in the peripheral part B (regulation) in the section vertical with length of wires direction takes
To<110>orientation set in the case where, the Crystal Rotation in wire drawing becomes less, therefore can inhibit to be caused by shear stress
Gap generation.
The ferrite crystal orientation in the length of wires direction of steel wire rod and the block diameter of pearlite have not from center to surface layer
Same distribution.Fig. 1 shows the central part A and peripheral part B in the section vertical with length of wires direction.In the present specification, such as
Shown in the Fig. 1, centered on being defined relative to diameter of the wire rod of diameter Dmm since center for the region within the circle of 1/2D
Region within 500 μm since surface layer is defined as peripheral part B by portion A.
For pearlite block diameter, the central part A of Fig. 1 can be set as locating, pass through electron backscattered (Electron
BackScatter Diffraction, referred to as EBSD) method measures.For example, long with wire rod using colloidal silica particle pair
It spends the vertical section in direction and carries out mirror ultrafinish, the measurement using EBSD method is carried out near radial central part, iron element is made
The figure of body crystal orientation.For example, being that the rectangular area that every 1 side is 500 μm or more carries out in mapping area, configured with primitive shape
It is carried out for regular hexagon element, measuring interval are 0.5 μm of interval.
The aggregation degree of the ferrite crystal orientation<110>in length of wires direction can be by the way that the peripheral part B of Fig. 1 to be set as surveying
Positioning is set, and the crystal orientation of each pixel is marked in { 110 } pole figure and is measured.More specifically, ferrite crystal orientation <
110 > aggregation degree can use the measurement result of EBSD method and generate { 110 } pole figure, to obtained pole figure carry out texture
(Texture) parsing etc. measures.For aggregation degree, the random situation of crystal orientation is set as 1, is indicated with intensity ratio.
In addition, each hexagon shape pixel gives ferritic crystalline substance if identifying ferrite crystal orientation by EBSD method
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
Boundary with 9 ° or more ferrite crystal orientation inclination angle difference and the pixel boundary that is adjacent also be 9 ° or more such, have
In the continuous situation of pixel boundary of 9 ° or more of inclination angle difference, they are connected and is defined as pearlite block crystal boundary.
In the case where the pixel boundary extended from the triple point of pixel is 9 ° or more, pearlite block crystal boundary branch.Picture
For the condition that the crystal orientation difference on plain boundary is 9 ° or more on the way in intermittent situation, which is not considered as pearlite block
Crystal boundary and ignore.According to above form of thinking, defined in entire rectangular area have 9 ° or more ferrite gun parallax picture
The region is defined as a pearlite block, by pixel side in the case that pixel boundary surrounds a closed region by plain boundary
Boundary is defined as pearlite block crystal boundary.So operation shows pearlite block crystal boundary on the figure of ferrite crystal orientation, measures pearly-lustre
The block diameter of body.Wherein, it in the case that one of defined pearlite block below 25 pixels by constituting, is handled as noise
And ignore.Wherein, pearlite block is identical with pearlite tumor meaning.In addition, pearlite is lamellar pearlite.
For piece interlamellar spacing can by as follows so as to find out: with nital corrosion with length of wires direction
Vertical section, using SEM, in the visual field the smallest position of inner sheet interlamellar spacing shot again with multiplying power 10000, vertically
Ground is marked as 5 piece interlamellar spacings, by the length of 5 piece interlamellar spacings divided by 5.It should be noted that being regarded with the shooting of SEM at 10
It is carried out more than wild, calculated piece interlamellar spacing is divided by visual field number in each visual field, to obtain average value.
For wire-drawing workability, the test material of length 10m is impregnated in hydrochloric acid and scale removal, implements phosphorus after washing
Hydrochlorate coating processing carries out dry wire drawing processing to evaluate.Wire drawing can be used with die approach (entirety) angle
20 °, the WC-Co superhard alloy molding jig of 0.3 times or so of the shape that sizing (ベ ア リ Application グ) length is aperture carries out.It draws
Silk speed is set as 50m/ minutes, and the dry wire drawing lubricant based on odium stearate and calcium stearate can be used.
In the case where not breaking, reduce mold aperture to make section slip 20%, until generation broken string is
Only carry out wire drawing.Evaluation is terminated when the broken string number of total is 20 times, by the line footpath (line before wire drawing of test material
Diameter) D0 and the mold aperture D that breaks find out wire drawing degree according to the following formula.
Wire drawing degree (ε)=2 × ln (D0/D)
Under each wire drawing degree, the number being broken finds out fracture rate divided by 20 (overall test numbers), in addition extremely
Accumulation fracture rate until this finds out the accumulation fracture rate under each wire drawing degree.Fig. 2 is to judge that wire-drawing workability is good
The test result of wire coil as 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, in addition (wire drawing degree before this
1.7) when accumulation fracture rate 0.05, accumulation fracture rate is 0.3.Also, when wire drawing degree becomes maximum in 20 tests, tire out
Product fracture rate becomes 1.0.
In the present invention, accumulation fracture rate is found out from chart becomes 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.In turn, it accumulates
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 2.23 or more, more preferable wire-drawing workability is 2.53 or more, further preferably by wire drawing
Processability is evaluated as good for 2.95 or more.
(for steel wire rod)
Then, the ingredient of steel wire rod of the invention is illustrated.It should be noted that the % of quantity relating is matter
Measure %.
<for ingredient>
C
C is that tissue is made to become pearlite, improves the element of intensity.When C amount is less than 0.60%, the non-pearly-lustre such as grain boundary ferrite
Body tissue generates and damages wire-drawing workability, and the tensile strength of superfine steel wire also reduces.On the other hand, when C amount is more than 1.10%,
The non-pearlites tissue such as proeutectoid cementite generates, wire-drawing workability deterioration.Therefore, C amount is limited to 0.60~1.10% model
It encloses.It is preferred that C amount is set as 0.65% or more.
Si
Si is the element of the deoxidation for steel, it helps solution strengthening.Effect in order to obtain, 0.02% or more addition
Si.It is preferred that Si amount is set as 0.05% or more.On the other hand, when Si amount is more than 2.0%, surface is easy to produce in hot-rolled process
Decarburization, therefore the upper limit is set as 2.0%.It is preferred that Si amount is set as 1.0% hereinafter, being more preferably set as 0.5% or less.
Mn
Mn is the element for deoxidation, desulfurization, 0.1% or more addition.On the other hand, when Mn amount is more than 2.0%, pearlite
Phase transformation significantly postpones, and the time of patenting processing is elongated, therefore Mn amount is set as 2.0% or less.Mn amount be preferably 1.0% with
Under.
Cr
Cr is the element for making former γ partial size miniaturize, keep pearlitic structrure fine, it helps high intensity.In order to obtain
Effect, the Cr of 0.3% or more addition.On the other hand, when Cr amount is more than 1.6%, proeutectoid cementite is precipitated, and makes wire-drawing workability
It reduces, therefore the upper limit is set as 1.6%.It is preferably set to 1.3% or less.More preferably it is set as 1.0% or less.
Al
Al is the element with deoxidation, is necessary for reducing the oxygen amount in steel.However, Al content is insufficient
When 0.001%, it is difficult to obtain the effect.On the other hand, the oxide system field trash of Al hard easy to form, in particular, Al contains
When amount is more than 0.05%, the formation of coarse oxide system field trash becomes significantly, therefore the reduction of wire-drawing workability is significant.Cause
This, is set as 0.001~0.05% for the content of Al.More preferable lower limit is 0.01% or more, and the more preferable upper limit is 0.04% or less.
N
N is the intensity for being bonded to dislocation in cold-drawn wire processing and improving steel wire, the member for instead reducing wire-drawing workability
Element.In particular, the reduction of wire-drawing workability becomes significant when N content is more than 0.008%.Therefore, N content is limited to
0.008% or less.More preferably 0.005% or less.
P
P is easy segregation in steel, significant to postpone eutectoid phase transformation when segregation, and therefore, eutectoid phase transformation does not complete, easy to form
The martensite of hard.P content is limited to 0.02% or less by the problem in order to prevent.
S
S in large quantities in the presence of, form MnS in large quantities, reduce the ductility of steel, therefore be limited to 0.020% or less.It is more excellent
It is selected as 0.01% or less.
Mo
The addition of Mo is arbitrary.If addition, have the effect of improving the tensile strength of steel wire rod.The effect in order to obtain
Fruit, it is expected that the Mo of 0.02% or more addition.However, martensitic structure is easy to generate, and wire drawing adds when the content of Mo is more than 0.20%
Work reduces.Therefore, the content of Mo is preferably 0.02~0.20%.More preferably 0.08% or less.
V
The addition of V is arbitrary.If addition forms carbonitride in steel wire rod, reduce pearlite block diameter, improves and draw
Silk processability.Effect in order to obtain, it is expected that the V of 0.02% or more addition.However, existing thick when the content of V is more than 0.20%
The case where big carbonitride is easy to generate, and wire-drawing workability reduces.Therefore, the content of V is preferably 0.02~0.20%.It is more excellent
It is selected as 0.08% or less.
Nb
The addition of Nb is arbitrary.If addition forms carbonitride in steel wire rod, reduce pearlite block diameter, improves
Wire-drawing workability.Effect in order to obtain, it is expected that the Nb of 0.002% or more addition.However, when the content of Nb is more than 0.05%,
The case where there are coarse carbonitrides to be easy generation, and wire-drawing workability reduces.Therefore, the content of Nb be preferably 0.002~
0.05%.More preferably 0.02% or less.
Ti
The addition of Ti is arbitrary.If addition forms carbide or nitride in steel wire rod, reduce pearlite block
Diameter improves wire-drawing workability.Effect in order to obtain, it is expected that the Ti of 0.002% or more addition.However, the content of Ti is more than
When 0.05%, coarse carbide or nitride easy to form, there are wire-drawing workabilities to start the case where reducing.It is therefore preferable that
The content of Ti is set as 0.02~0.05%.More preferably 0.03% or less.
B
The addition of B is arbitrary.If addition, the solid solution N in steel wire rod is formed as BN, reduces the solid solution N in steel, improves
Wire-drawing workability.Effect in order to obtain, it is expected that the B of 0.0003% or more addition.However, when the content of B is more than 0.003%,
Coarse nitride is generated there are easy, the case where wire-drawing workability reduces.Therefore, the content of B be preferably 0.0003~
0.003%.More preferably 0.002% or less.
<for metallographic structure>
Then, the metallographic structure of steel wire rod of the invention is illustrated.
The area ratio
The non-pearlites group such as pro-eutectoid ferrite, proeutectoid cementite, which is woven in, becomes the original being cracked in final wire drawing
Cause.In embodiments of the present invention, in order to improve wire-drawing workability, the area ratio of pearlite is set as 95% or more.Surplus
For the non-pearlites tissue such as pro-eutectoid ferrite, proeutectoid cementite.It should be noted that above-mentioned metallographic structure can such as get off
It determines: the section relative to length of wires direction vertically cut off wire rod is cut as sample, after mirror ultrafinish, with scanning electricity
Sub- microscope is observed.In addition, the area ratio of each metallographic structure can make according to the result observed by scanning electron microscope
It is found out with planimetric method or point count.Preferably, multiplying power is observed, such as is set as 1000 times or more, the area of observation, such as
It is set as 1000 μm2More than.Such as when with point count determining the area ratio, measuring point is preferably set as 200 points or more.
The block diameter of pearlite
As above-mentioned opinion, when the block diameter (hereinafter also referred to as pearlite block diameter) of pearlite is greater than 15 μm, wire drawing
Property reduce, therefore be set as 15 μm or less.More preferably 12 μm or less.In addition, when pearlite block diameter is set as 5 μm or less, non-pearly-lustre
Body tissue increases, therefore is set as lower limit for 5 μm.
The aggregation degree of ferrite crystal orientation<110>
When ferrite crystal orientation<110>is collected in the peripheral part in the section vertical with length of wires direction, it can inhibit
Orientation rotation in wire drawing, inhibition are formed based on shear-deformable gap.In the present invention, which highlights, ferrite
The aggregation degree of crystal orientation<110>is set as 1.3 or more.Preferably 1.5 or more, 1.7 or more are more preferably.
It should be noted that the aggregation degree of pearlite block diameter and ferrite crystal orientation<110>can use as above-mentioned
Such EBSD method determines.
Piece interlamellar spacing
Based on pearlite, target is the tensile strength 1300MPa for making the steel wire rod for metallographic structure in the present invention
It above, is preferably 1350MPa or more, more preferably 1400MPa or more.The intensity in order to obtain is shown in aftermentioned embodiment
The average platelet spacing of pearlite need for 100nm or less.In addition, being removed when the average platelet spacing of pearlite is less than 50nm
Bainite structure other than pearlite is mixed, and cannot obtain target strength, and wire drawing hardening ratio reduces, therefore will
Lower limit is set as 50nm.
<for the manufacturing method of steel wire rod>
Then, the manufacturing method of steel wire rod of the invention is illustrated with specific example.It should be noted that with
Under explanation be merely used for illustrating example of the invention, not delimit the scope of the invention.
Steel wire rod of the invention carrys out the steel that melting has above-mentioned ingredient by conventional method, 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 which pearlitic transformation occurs 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 until (primary cooling), keep in this temperature range 30 seconds~180 seconds it
Afterwards, 300 DEG C (secondary coolings) are cooled to 2 DEG C/sec or more with the means of air cooling, water cooling, are cooled to room temperature with the means such as letting cool.
As long as being not particularly limited it should be noted that the diameter of wire rod may insure the necessary processing hardening when steel wire is made.
When the final rolling temperature of hot rolling is higher than 880 DEG C, the micronized effect of former γ partial size tails off, therefore is set as 880 DEG C or less.
In addition, pro-eutectoid ferrite can be precipitated in rolling, therefore lower limit is set as 740 DEG C when being rolled at less than 740 DEG C.
When cooling velocity under primary cooling is less than 25 DEG C/sec, former γ partial size coarsening, therefore by lower limit be set as 25 DEG C/
Second.Cooling more than 40 DEG C/sec is difficult in actually manufacture, therefore is set as 40 DEG C/sec or less.
When temperature being kept to be more than 650 DEG C, former γ partial size coarsening and strength reduction, therefore the upper limit is set as 650 DEG C.This
When outside, less than 550 DEG C, non-pearlite tissue increases, therefore lower limit is set as 550 DEG C.
When retention time was less than 30 seconds, pearlitic transformation is not completed, and non-pearlite tissue increases, therefore lower limit is set as 30
Second.In addition, the holding more than 180 seconds cause the deterioration of productivity, the shape avalanche of lamella pearlite and cause wire strength
It reduces, therefore the upper limit is set as 180 seconds.
In 2 coolings, when 300 DEG C or more of temperature ranges carry out the Slow cooling of 2 DEG C/sec of the deficiencies of furnace is cold, cause
The reduction of intensity, therefore the lower limit of the secondary cooling speed until near 300 DEG C is set as 2 DEG C/sec.It should be noted that being not required to
Comprehend from 300 DEG C of cooling velocities until room temperature.
Embodiment
Hereinafter, foring the system of steel wire rod described in embodiments of the present invention and steel wire rod while showing embodiment
The method of making specifically describes.It should be noted that embodiments illustrated below is only steel described in embodiments of the present invention
One example of the manufacturing method of wire rod and steel wire rod, the manufacturing method of steel wire rod and steel wire rod of the present invention is not
It is limited to following examples.
For shown in table 1 at the high-carbon steel hot rolling wire being grouped as, by changing hot-rolled condition shown in table 2,
It is but the ferrite crystal orientation<110>of the pearlite block diameter of central part, surface section for pearlitic structrure to make identical
The different wire rod of aggregation degree, tensile strength.These wire rods are evaluated with wire drawing critical strain.It is shown in table 3 the knot
Fruit.
[table 1]
| Steel grade | C | Si | Mn | Cr | Al | Mo | B | Nb | C | 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 following specific manufacturing method for illustrating these carbon steel wire rod with high.Chemistry as become wire rod shown in table 1
Ingredient is such, with converter melting makes the medium and small shaped blooms of 155mm square, is heated to 1150 DEG C or so the bloom breaking down
Afterwards, hot rolling is carried out in the range that the final temperature of rolling is 740 DEG C~880 DEG C, obtains the wire rod of diameter 10mm.
Wire rod after terminating for above-mentioned hot rolling is sprayed with nozzle at once by the cooling zone being arranged on rolling line
Penetrate the range that cooling water is cooled to 550 DEG C~650 DEG C.At this point, changing water and water cooling time, control reaches temperature.In addition, connecing
Wire rod is cooled to 650 DEG C~550 DEG C of range by air blast cooling with 5 DEG C/sec~25 DEG C/sec of cooling velocity.Later
It is kept for 60 seconds or so in the temperature range, to complete pearlitic transformation, is cooled to room temperature by air cooling.
Pearlite the area ratio (%), pearlite block diameter, piece interlamellar spacing, the ferrite crystal for measuring these steel wire rods respectively take
To, tensile strength.
Pearlite the area ratio is found out as follows, and the sample of mirror ultrafinish is carried out for cross section obtained from cutting wire rod, is used
The mixed liquor of nitric acid and ethyl alcohol etching, with 2000 times observe wire rod surface and center between central portion so as to find out.
For pearlite block diameter and piece interlamellar spacing, 62500 μm in the range of the center 5mm of steel wire rod2Region survey
It is fixed.Ferrite is orientated the EBSD measurement device that<110>aggregation degree uses TSL corporation, in the range within 500 μm away from surface 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
The broken string number of total is set as 20 times by work, the figure of the relationship of production wire drawing logarithmic strain and accumulation fracture rate, to accumulate fracture
The wire drawing logarithmic strain that rate is 50% is evaluated.It is shown in table 3 result.PBS is being averaged for pearlite block diameter.
The holding temperature of No.10 is high, therefore piece interlamellar spacing is big, tensile strength is insufficient.
The Cr amount of No.11 is low, and the miniaturization of pearlite block diameter is insufficient, therefore wire drawing critical strain becomes smaller.
The Mn amount of No.12 is more, and pearlitic transformation does not complete, and pearlite the area ratio is very small, therefore wire drawing is critical answers
Change becomes smaller.
The C amount of No.13 is high, and proeutectoid cementite generates, therefore pearlite the area ratio is small, and wire drawing critical strain becomes
It is small.
The retention time of No.14 is short, carries out secondary cooling before pearlitic transformation is completed, therefore pearlite the area ratio is small,
Wire drawing critical strain becomes smaller.
A cooling velocity of No.15 is small, former γ partial size coarsening, therefore pearlite block diameter is big, and wire drawing is critical to answer
Change becomes smaller.
The retention time of No.16 is long, the shape avalanche of lamella pearlite, and tensile strength is insufficient.
The final rolling temperature of No.17 is low, pro-eutectoid ferrite largely generates, and tensile strength is insufficient, and wire drawing is critical
Strain becomes smaller.
The final rolling temperature height of No.18, original γ partial size coarsening, therefore pearlite block diameter is big, wire drawing critical strain becomes
It is small.
The secondary cooling speed of No.19 is small, the shape avalanche of lamella pearlite, and tensile strength reduces.
Claims (6)
- Be the carbon steel wire rod with high after hot rolling 1. a kind of carbon steel wire rod with high, composition of steel with quality % be calculated as C:0.60~1.10%, Si:0.02~2.0%, Mn:0.1~2.0%, Cr:0.3~1.6%, Al:0.001~0.05%, Mo:0.20% or less, Nb: 0.05% or less, V:0.20% or less, Ti:0.05% or less, B:0.003% or less, N:0.008% or less, P:0.020% with Under and S:0.020% hereinafter, and surplus: Fe and inevitable impurity,The above are pearly-lustres for the tissue of the carbon steel wire rod with high in terms of in the area ratio in the section vertical with length of wires direction 95% Body,The average platelet spacing of the pearlite is 50~100nm,Within the circle that the diameter since center in the section vertical with length of wires direction is D/2 relative to the diameter D of wire rod The average value of region, that is, central part pearlite block diameter be greater than 5 μm and less than 15 μm,Region, that is, peripheral part the section vertical with length of wires direction is since surface layer within 500 μm, pearlitic structrure In ferritic crystal orientation<110>aggregation degree be 1.3 or more,The tensile strength of the carbon steel wire rod with high is 1300MPa or more.
- 2. carbon steel wire rod with high according to claim 1, wherein contain Mo:0.02~0.20% in terms of quality %.
- 3. carbon steel wire rod with high according to claim 1, wherein contain Nb:0.002~0.05%, V in terms of quality %: 0.02~0.20%, one kind or two or more among Ti:0.002~0.05%.
- 4. carbon steel wire rod with high according to claim 1, wherein contain B:0.0003~0.003% in terms of quality %.
- 5. carbon steel wire rod with high according to claim 1, wherein contain Si:0.02~1.0% in terms of quality %.
- 6. carbon steel wire rod with high according to any one of claims 1 to 5, wherein the average value of pearlite block diameter is greater than 5 μm And less than 12 μm.
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| 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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| CN107208208A CN107208208A (en) | 2017-09-26 |
| CN107208208B true CN107208208B (en) | 2019-08-23 |
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| EP (1) | EP3228721A4 (en) |
| JP (1) | JP6394708B2 (en) |
| KR (1) | KR101952527B1 (en) |
| CN (1) | CN107208208B (en) |
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| WO (1) | WO2016088803A1 (en) |
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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 |
| JP6528920B2 (en) * | 2017-05-18 | 2019-06-12 | 日本製鉄株式会社 | Wire rod and method of manufacturing steel wire |
| CN107723592B (en) * | 2017-09-30 | 2019-01-18 | 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 |
| MX2021008043A (en) * | 2019-03-06 | 2021-08-05 | Nippon Steel Corp | Hot-rolled steel sheet and production method therefor. |
| JP7352069B2 (en) * | 2019-07-26 | 2023-09-28 | 日本製鉄株式会社 | wire rod and steel wire |
| CN110669981B (en) * | 2019-10-02 | 2021-07-16 | 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 |
| KR102421642B1 (en) * | 2019-12-20 | 2022-07-18 | 주식회사 포스코 | Wire rod for bearing and methods for manufacturing 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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| CN102216482A (en) * | 2009-11-05 | 2011-10-12 | 新日本制铁株式会社 | High-carbon steel wire material with excellent processability |
| CN102959115A (en) * | 2011-03-14 | 2013-03-06 | 新日铁住金株式会社 | Steel wire material and process for producing same |
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| GB1477377A (en) * | 1973-12-17 | 1977-06-22 | Kobe Steel Ltd | Steel rod and method of producing steel rod |
| JPH06271937A (en) * | 1993-03-17 | 1994-09-27 | Kobe Steel Ltd | Production of high strength and high toughness hyper-eutectoid steel wire |
| JP3246210B2 (en) * | 1994-08-11 | 2002-01-15 | 株式会社神戸製鋼所 | High strength and high toughness hot-dip coated steel wire and method for producing the same |
| JP3737354B2 (en) * | 2000-11-06 | 2006-01-18 | 株式会社神戸製鋼所 | Wire rod for wire drawing excellent in twisting characteristics and method for producing the same |
| JP2004300497A (en) | 2003-03-31 | 2004-10-28 | Kobe Steel Ltd | Wire- or bar-shaped steel excellent in wire-drawing property, its production method and bearing part |
| JP5098444B2 (en) * | 2006-06-01 | 2012-12-12 | 新日鐵住金株式会社 | Method for producing high ductility direct patenting wire |
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| CN102216482A (en) * | 2009-11-05 | 2011-10-12 | 新日本制铁株式会社 | High-carbon steel wire material with excellent processability |
| CN102959115A (en) * | 2011-03-14 | 2013-03-06 | 新日铁住金株式会社 | Steel wire material and process for producing same |
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| EP3228721A1 (en) | 2017-10-11 |
| JPWO2016088803A1 (en) | 2017-10-05 |
| CN107208208A (en) | 2017-09-26 |
| MX2017006990A (en) | 2017-08-24 |
| JP6394708B2 (en) | 2018-10-03 |
| KR20170092630A (en) | 2017-08-11 |
| EP3228721A4 (en) | 2018-07-11 |
| WO2016088803A1 (en) | 2016-06-09 |
| KR101952527B1 (en) | 2019-02-26 |
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