CN105401074B - High-strength wire material and steel wire and its manufacture method - Google Patents
High-strength wire material and steel wire and its manufacture method Download PDFInfo
- Publication number
- CN105401074B CN105401074B CN201510552724.1A CN201510552724A CN105401074B CN 105401074 B CN105401074 B CN 105401074B CN 201510552724 A CN201510552724 A CN 201510552724A CN 105401074 B CN105401074 B CN 105401074B
- Authority
- CN
- China
- Prior art keywords
- martensite
- less
- strength
- wire rod
- surplus
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/16—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling wire rods, bars, merchant bars, rounds wire or material of like small cross-section
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/008—Martensite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a kind of wire rod and steel wire for being used in cotton tyre cord etc., more specifically, there is provided a kind of manufacture method of high-strength wire material and steel wire and wire rod.According to an aspect of the present invention, the high-strength wire material, in terms of weight %, by C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：Less than 0.03%, surplus Fe and other inevitably impurity compositions, in terms of area fraction, micro organization is made up of 25~43% martensite and surplus ferrite., can be by controlling the heat treatment of alloying component and two stages according to the present invention, there is provided high-strength wire material, and can provide the high-tensile steel wires with excellent tensile strength using the wire rod.
Description
Technical field
The present invention relates to a kind of wire rod and steel wire for being used in cotton tyre cord, more specifically, it is related to a kind of high intensity line
The manufacture method of material and steel wire and wire rod.
Background technology
Cotton tyre cord etc. because its using characteristic, it is necessary to possess high intensity and excellent twisting property.Its main purpose is to carry
High service life, for example, when high-tensile steel wires are used in into a kind of all-steel cord as cotton tyre cord, its fatigue life is excellent
It is different, broken string situation is not susceptible under steam, can greatly improve driving safety.
The steel wire minimum strength to be possessed for being used in cotton tyre cord is 2800MPa, at present the intensity of commercial steel wire
4000MPa can be reached.In order to make it have excellent intensity, its tissue is needed to use fine pearlite tissue, processing method is adopted
With stretching or drawing method.Because fine pearlite tissue is different from its hetero-organization, due to the plasticity of pearlite
Greatly, therefore, when the pearlite being randomly formed when subtracting more than the 50% of face amount, is drawn very long, had using total along draw direction
Similar to the shape of complex tissue.In test, carry out being able to ensure that more than 5000MPa intensity during wet tensile.
High intensity is realized by the two methods of process technology raising, and described two methods are：1) C-Si-Mn is closed
The change of the alloying component such as C increments and Cr additions in gold system；2) except draw speed increase, every time subtract face amount increase in addition to
Maximally effective processing capacity increase etc..But C, Cr added etc. alloy amount it is excessive when, it may appear that change the when anaplasia of completion
It is long, or, crystal boundary forms proeutectoid cementite the problem of, in addition, processing capacity is to the alloying element of steel wire and the dependence of intensity
Property it is high, therefore there is limitation in processing capacity increase.
Also, the steel wire for being used in cotton tyre cord is the carbon steel using pearlite, therefore its composition is simple, is C-Si-Mn-
Cr.Such composition ties up to the whole world all without too big difference, therefore, it is necessary to develops a kind of by new derived from proper constituent system
Product.
Therefore, the material of two phase constitutions with ferrite and martensite is extensively studied since the nineties.Martensite
It is C oversaturated phases in BCC structures, although compared to cementite hardness and low intensity, there are many slip systems, therefore hold
Easily plastic deformation.This means the scope for applying processing capacity when being stretched is big.But martensite be compared to cementite more it is tough more
Hard phase, it is desirable to be able to absorb the ferrite base body phase of stretcher strain energy.Therefore, although for having ferrite and martensite
The materials of two phase constitutions widely studied, but do not apply in cotton tyre cord etc. also, because not establishing also
Optimal alloy composition and the heat treatment condition suitable for the alloying component.
The content of the invention
(1) technical problems to be solved
One aspect of the present invention will provide a kind of high-strength wire material, by controlling alloying component and implementing two stages
Heat treatment, forms two phase constitutions being made up of ferrite and martensite, thus provides high-strength wire material.
Another aspect of the present invention will provide a kind of manufacture method of high-strength wire material, by controlling alloying component and reality
The heat treatment in two stages is applied, forms two phase constitutions being made up of ferrite and martensite, thus the system of high-strength wire material is provided
Make method.
An additional aspect of the present invention will provide a kind of high-tensile steel wires, and it utilizes high-strength wire material of the invention.
(2) technical scheme
According to an aspect of the present invention, there is provided a kind of high-strength wire material, the high-strength wire material, in terms of weight %, by
C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：
Less than 0.03%, surplus Fe and it is other inevitably impurity composition, in terms of area fraction, micro organization by 25~43% horse
Family name's body and surplus ferrite composition.
According to another aspect of the present invention, there is provided a kind of manufacture method of high-strength wire material, comprise the following steps：Pass through
Hot rolled steel plate obtains wire rod, the steel plate, in terms of weight %, by C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0
~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：Less than 0.03%, surplus Fe and other inevitable impurity
Composition；Once it is heat-treated, makes its whole austenitizing by heating the wire rod, formed institute is then made by cooling
State austenite and be changed into martensite；Secondary heat treatment is carried out, for the stable martensite for passing through the wire rod being once heat-treated
In carbon, hold it in defined temperature, austenite and ferritic line and staff control then made it have by heating, and led to
Supercooling makes it have martensite and ferritic line and staff control.
According to a further aspect of the invention, there is provided a kind of excellent high-tensile steel wires of tensile strength, the high strength steel
Silk, in terms of weight %, by C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0~2.0%, N：0.005~0.02%, P：
Less than 0.03%, S：Less than 0.03%, surplus Fe and other inevitably impurity compositions, in terms of area fraction, micro organization
It is made up of 25~43% martensite and surplus ferrite.
Meanwhile the above-mentioned method solved the problems, such as does not have all features for enumerating the present invention.The present invention each feature and
Advantage and effect possessed by each feature, it can refer to following specific embodiment and understand in more detail.
(3) beneficial effect
, can be by controlling the heat treatment of alloying component and two stages, there is provided high-strength wire material, Er Qieli according to the present invention
The high-tensile steel wires with excellent tensile strength can be provided with the wire rod.
Embodiment
In order to obtain high-strength wire material and steel wire, present inventor has performed research, results verification, is forming ferrite and horse
While family name's body is to ensure high intensity, intensity is further improved by adding dynamic time effect caused by N, height can be produced
Intensity wire rod and the high-tensile steel wires using the high-strength wire material, the present invention complete on the basis of the studies above result.
Hereinafter, the composition of the wire rod to the present invention and steel wire is described in detail.Now, the content of component element represents
Weight %.
C (carbon)：0.05~0.15%
The element that C is for ensuring that the strength of materials and added, it is used for the formation of martensite.When the C content is less than
When 0.05%, it is difficult to ensure target strength, when the C content is more than 0.15%, the intensity of martensite is high, and is formed as block
Shape, therefore, in drawing process, cracking is produced in martensite and ferritic interface, causes to break in drawing process, because
This, it is preferable that the C content is limited in 0.05~0.15%, it is highly preferred that being limited in 0.07~0.10%.
Si (silicon)：0.5~1.5%
Si is added as ferritic element is stablized, for example, addition 0.1% Si can improve intensity 14~
16MPa or so.Also, when being heat-treated to two-phase region, Si is present in the crystal boundary of ferrite and austenite, therefore, has
Help to make the shape invariance of austenite into the effect of bulk.When Si contents are less than 0.5%, the interface shape of austenite becomes
It is uneven, it is difficult to ensure acicular martensite, when Si contents be more than 1.5% when, can be formed thickness fayalite (Fayalite,
Fe2SiO4) oxide scale layer, it is therefore preferred that the Si contents are limited in into 0.5~1.5%.
Mn (manganese)：1.0~2.0%
Mn is the element of stable austenite, and due to the addition of 0.05~0.15% C, therefore Mn is to improve quenching degree
And add.When the Mn contents of addition are less than 1.0%, during water hardening be difficult to fully (fully) forming martensite, when
When the Mn contents of addition are more than 2.0%, the serious center Mn lines of segragation that broken string is caused in drawing process are formed, therefore,
Preferably, the Mn contents are limited in 1.0~2.0%.
N (nitrogen)：0.005~0.02%
N and C are solid-solution in ferrite, are the elements for effectively improving intensity, when adding 0.1%, there is intensity to improve
80MPa effect.It is solid-solution in ferritic N and triggers dynamic strain aging (dynamic strain in drawing process
Aging), thus caused strength-enhancing effect is obvious.
When content is less than 0.005%, it is difficult to effectively produce dynamic time effect, when content is more than 0.02%, stretching is added
Work performance has an impact, and is possible to deteriorate torque characteristic.It is therefore preferred that the nitrogen content be limited in 0.005~
0.02%, it is highly preferred that being limited in 0.008~0.010%.
P (phosphorus) and S (sulphur)：Difference less than 0.03%
P and S is impurity, and its content is more low better, but wants for content to be limited in very low level, in steel making technology
For going deimpurity expense to increase.Also, the toughness of material reduces when the P and S content increase.Therefore, typically
In the case of, it is important that the upper limit of the P and S contents is controlled, in the present invention preferably by the upper limit of the P and S contents
Control respectively 0.030%.
Remaining composition of the present invention is iron (Fe).Simply, may be from raw material or surrounding ring in general manufacturing process
Border is inevitably mixed into the impurity added unintentionally, therefore can not exclude.As long as the technical staff of in general manufacturing process is
These impurity are will appreciate that, therefore are not particularly illustrated the full content on impurity in this manual.
According to an aspect of the present invention, the micro organization of wire rod is preferably the two-phase group being made up of ferrite and martensite
Knit (Dual Phase).
The area fraction of the martensite is preferably 25~43%.
When the area fraction of the martensite is less than 25%, it is difficult to which the target to be reached is strong after ensuring final stretching
Degree.In contrast, when the area fraction of the martensite is more than 43%, cracking is produced at the interface of ferrite and martensite,
The problem of in the presence of that can not be stretched.It is therefore preferred that the area fraction of the martensite is limited in 25~43%, more preferably
Ground, it is limited in 41~43%.
Also, the tensile strength of the wire rod can be 650~670MPa.
Meanwhile the sectional shrinkage (RA) of the wire rod is preferably more than 63%.
As described above, when steel wire sectional shrinkage (RA) every time be less than 63% when, in order to realize total draft, meeting
Road number excessively needed for increase, wire surface are relatively more compared to wire internal deformation, cause the deformation skewness of inside and outside
It is even, have a negative impact to the mechanical and physical property of final products, therefore it is not preferred.
The manufacture method of the high-strength wire material of another aspect of the present invention is described in detail.
The manufacture method comprises the following steps：
Wire rod, the steel plate, in terms of weight %, by C are obtained by hot rolled steel plate：0.05~0.15%, Si：0.5~
1.5%th, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：Less than 0.03%, surplus Fe and it is other not
Evitable impurity composition；
Once it is heat-treated, makes its whole austenitizing by heating the wire rod, then makes to be formed by cooling
The austenite be changed into martensite；
Secondary heat treatment is carried out, for the carbon in the stable martensite for passing through the wire rod being once heat-treated, is protected
Hold in defined temperature, austenite and ferritic line and staff control are then made it have by heating, and its tool is made by cooling
There are martensite and ferritic line and staff control.
According to an aspect of the present invention, in order to manufacture wire rod, first, the steel plate of mentioned component relation is met by hot rolling
To obtain wire rod.Now, hot rolling uses commonly used approach, is not particularly limited.
Once heat treatment and secondary heat treatment are carried out to the wire rod manufactured as described above.
Once it is heat-treated
Its whole austenitizing is made by the wire rod heated as described above Jing Guo hot rolling, is then once heat-treated work
Skill, the austenite for making to be formed are changed into martensite and cooled down.
In a Technology for Heating Processing, the wire rod is maintained at 950~1150 DEG C, then with 80 DEG C/more than s's
Speed is cooled to normal temperature.
Preferably, the keeping temperature of the wire rod is limited to 950~1150 DEG C.Its reason is, when the keeping temperature is low
When 950 DEG C, the grain size of austenite is small, therefore, needs to take a long time to suppress the formation of retained austenite, when described
When keeping temperature is more than 1150 DEG C, grain size is thick, causes martensite beam (packet) to become big, and tensile property declines.
When being cooled down after being kept at a temperature of described 950~1150 DEG C, it is preferable that cooling velocity is limited in into 80 DEG C/s
More than.
Its reason is, when the cooling velocity is less than 80 DEG C/s, the problem of forming retained austenite be present.It is in addition, cold
But speed is more big more is advantageous to suppress the formation of retained austenite, therefore its upper limit is not particularly limited.
Secondary heat treatment
As described above by the wire rod being once heat-treated, in order to stablize the carbon in martensite, hold it in defined
Temperature, austenite and ferritic line and staff control are then made it have by heating, and by cooling make it have martensite and
Ferritic line and staff control, thus carry out secondary heat treatment technique.
The secondary heat treatment technique is, will pass through the wire rod being once heat-treated in 50~150 DEG C of holdings 10~60
Minute, 750~850 DEG C are then allowed to warm to, and kept for 3~7 minutes, then it is cooled to often with 80 DEG C/more than s speed
Temperature.
Preferably, the keeping temperature for the wire rod being once heat-treated described in passing through is limited in 50~150 DEG C.Its reason is,
When the keeping temperature is less than 50 DEG C, the carbon in martensite is difficult to spread, when the keeping temperature is more than 150 DEG C, due to
Temperature is high, therefore improper from the aspect of the efficiency such as energy expenditure or the cost of technology.
Preferably, it is limited in the retention time of described 50~150 DEG C of keeping temperature 10~60 minutes.
Its reason is that, when being less than 10 minutes the retention time, the time needed for carbon spread is insufficient, when the holding
When time was more than 60 minutes, because carbon has fully spread, therefore from the aspect of the efficiency such as energy expenditure or the cost of technology not
Properly.
Preferably, the wire rod being once heat-treated described in passing through, 750~850 DEG C are warming up to after being kept at 50~150 DEG C.
Its reason is, when the temperature is less than 750 DEG C, martensite will not to be formed after cooling, or, because martensite fractions are small and difficult
To ensure target strength, when the temperature is more than 850 DEG C, the fraction increase of martensite, martensite are grown to bulk after cooling.
Preferably, programming rate when being warming up to 750~850 DEG C is limited in 2 DEG C/more than s.Its reason is, when heating speed
Spend for 2 DEG C/below s when, austenite can be changed into before target temperature is reached, cause grain size uneven.Do not have technically
Necessity limits the upper limit of the programming rate, simply considers suitably to enter from the economic aspect such as energy expenditure or the cost of technology
Row limits.
Preferably, the retention time is limited in 3~7 minutes at a temperature of described 750~850 DEG C.Its reason is, when described
When retention time is less than 3 minutes, fully it is transformed into martensite and stabilizes required time deficiency, it is big when the retention time
When 7 minutes, martensite grows and becomes block.
At a temperature of described 750~850 DEG C keep after cooled down when, it is preferable that by cooling velocity be limited in 80 DEG C/
More than s.Its reason is that, when the cooling velocity is less than 80 DEG C/s, austenite is possible to be transformed into pearlite.In addition, cooling
Speed is more big more is advantageous to transformation to martensite, therefore its upper limit is not particularly limited.
The high-tensile steel wires of another aspect of the present invention are described in detail.
The high-tensile steel wires of the present invention can be by carrying out stretch process to manufacture by the wire rod.The steel wire of the present invention, with
Weight % is counted, by C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0~2.0%, N：0.005~0.02%, P：
Less than 0.03%, S：Less than 0.03%, surplus Fe and other inevitably impurity compositions, in terms of area fraction, micro organization
It is made up of 25~43% martensite and surplus ferrite, so as to have excellent tensile strength.
Now, the tensile strength of the steel wire can be more than 4000MPa.Therefore, be highly suitable for as cotton tyre cord,
Steel wire rope, piano wire, bridge steel plate silk etc. are needed to have in the product of high intensity.
Also, the steel wire is in the application load and 100D (D of tensile strength × sectional area × 0.08：Steel wire diameter) bar
When torsion test is carried out under part, layering is not produced, the torque characteristic can with more than 25 times.
Wherein, the unit of the tensile strength is kg/mm2, the unit of the sectional area is mm2, the unit of the load is
Kg, the unit of the diameter is mm.
Hereinafter, the present invention is explained in more detail by embodiment.The embodiment being described below is intended merely to more
Add what is explained the present invention and illustrate, interest field of the invention is not limited to the embodiment.The right of the present invention
Content that scope is recorded by claims and the content that is rationally derived from the content define.
(embodiment)
50kg of the casting with constituent as shown in table 1 ingot casting, then sends out to suppress Mn and P etc. segregation
It is raw, 12 dipping (soaking) heat treatments more than hour are carried out at a temperature of 1250 DEG C, are then welded by steel billet-ingot casting
Connect, in furnace temp：1100 DEG C × 1 hour, hot-rolled temperature：1000 DEG C, spinning (laying head) temperature：950 DEG C, it is cold
But speed：Under 5 DEG C/s manufacturing condition, rolled wire manufactures hot rolling material (wire rod).
In order to form two phase constitutions of ferrite and martensite on the hot rolling material (wire rod) manufactured as described above, carry out
Secondary heat treatment technique.
In once heat treatment in the Technology for Heating Processing, kept for 10 points in batch furnace with 1150 DEG C of keeping temperature
Zhong Hou, it is quenched to normal temperature.
In secondary heat treatment in the Technology for Heating Processing, in order that by the hot rolling material (wire rod) that is once heat-treated
Carbon in martensite fully spreads, after being kept for 30 minutes with 100 DEG C of keeping temperature in toasting (baking) stove, with 5 DEG C/
S programming rate is warming up to 830 DEG C of keeping temperature, is quenched after then being kept for 5 minutes.
For the hot rolling material Jing Guo secondary heat treatment (wire rod) as described above, measurement cross-section (- 1/4D~center~+
1/4D positions) martensite fractions (Vm) and tensile strength (TS) and sectional shrinkage (RA), and in table 2 represent measurement knot
Fruit.
Then, used in stretch process business it is common under the conditions of, by the hot rolling material manufactured as described above (wire rod)
Dry type stretching and wet tensile are carried out, thus manufactures steel wire.
By the wire rod of table 1 below, every time subtracts face 20%, and total face amount that subtracts reaches 8.03 after stretching, often increases by 1 5.13
Region collection test piece and measure tensile strength, for by applying 8 stretch process amount the steel wire that manufactures, in tensile strength
The application load of × sectional area × 0.08 and 100D (D：Steel wire diameter) under conditions of measure torque characteristic, and its result is represented
In table 2.Wherein, the unit of the tensile strength in above-mentioned relation formula is kg/mm2, the unit of the sectional area is mm2, it is described
The unit of load is kg, and the unit of the steel wire diameter is mm.
[table 1]
[table 2]
It was found from the table 2, the martensite fractions of the wire rod cross-section of invention material 1 to 4 are 41~43%, now, are resisted
Zhang Qiangdu is 664~670MPa, and sectional shrinkage is 63~67% or so.In a comparative example, except excessive addition Si, Mn ratio
Outside example 6 and 7, other comparative examples have similar martensite fractions and mechanical property.
In the table 2, the test piece of comparative example 3 to 6 is broken in drawing process.The feature of these steel is to add
C：0.3%th, N：0.03 and 0.05%, Si：1.75%th, Mn：2.25%.This means ought excessively add the above-mentioned alloy referred to
During the content of element, in secondary heat treatment temperature, i.e., when being heat-treated (holding) at 830 DEG C of two-phase region heat treatment temperature
It can not be stretched.
Also, N has the function that the intensity based on the age-hardening occurred in drawing process improves, therefore when N content is small
Intensity can improve when 0.02%, but can not observe its effect when the N content is more than 0.02%.
In addition, the tensile strength for meeting the example 1 to 4 of the present invention is more than 4000MPa, and during application distorting stress
It is not layered, the value of display 26~28 times or so.In contrast, the display of comparative example 8 and 9 is anti-less than target tensile strength
Zhang Qiangdu.
Claims (5)
1. a kind of high-strength wire material, the high-strength wire material, in terms of weight %, by C：0.05~0.15%, Si：0.5~
1.5%th, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：Less than 0.03%, surplus Fe and it is other not
Evitable impurity composition,
In terms of area fraction, micro organization is made up of 25~43% martensite and surplus ferrite.
2. a kind of manufacture method of high-strength wire material, comprises the following steps：
Wire rod, the steel plate, in terms of weight %, by C are obtained by hot rolled steel plate：0.05~0.15%, Si：0.5~
1.5%th, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%, S：Less than 0.03%, surplus Fe and it is other not
Evitable impurity composition；
Once it is heat-treated, makes its whole austenitizing by heating the wire rod, formed institute is then made by cooling
State austenite and be changed into martensite；
Secondary heat treatment is carried out, for the carbon in the stable martensite for passing through the wire rod being once heat-treated, is held it in
Defined temperature, austenite and ferritic line and staff control are then made it have by heating, and horse is made it have by cooling
Family name's body and ferritic line and staff control,
The secondary heat treatment step is, will pass through described in the wire rod that is once heat-treated 10~60 points are kept at 50~150 DEG C
Clock, 750~850 DEG C are then allowed to warm to, and are kept for 3~7 minutes, is then cooled to often with 80 DEG C/more than s cooling velocity
Temperature.
3. the manufacture method of high-strength wire material according to claim 2 a, it is characterised in that heat treatment step
To be cooled to normal temperature after the wire rod is kept at 950~1150 DEG C with 80 DEG C/more than s cooling velocity.
4. the manufacture method of high-strength wire material according to claim 2, it is characterised in that in the secondary heat treatment step
In, programming rate during heating is 2 DEG C/more than s.
5. a kind of high-tensile steel wires, the high-tensile steel wires have excellent tensile strength, the high-tensile steel wires, with weight %
Meter, by C：0.05~0.15%, Si：0.5~1.5%, Mn：1.0~2.0%, N：0.005~0.02%, P：Less than 0.03%,
S：Less than 0.03%, surplus Fe and other inevitably impurity compositions,
In terms of area fraction, micro organization is made up of 25~43% martensite and surplus ferrite.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020140117817A KR101611724B1 (en) | 2014-09-04 | 2014-09-04 | Wire rod and steel wire having high strength and method manufacturing of wire rod |
| KR10-2014-0117817 | 2014-09-04 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN105401074A CN105401074A (en) | 2016-03-16 |
| CN105401074B true CN105401074B (en) | 2018-02-13 |
Family
ID=55466824
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510552724.1A Active CN105401074B (en) | 2014-09-04 | 2015-09-01 | High-strength wire material and steel wire and its manufacture method |
Country Status (2)
| Country | Link |
|---|---|
| KR (1) | KR101611724B1 (en) |
| CN (1) | CN105401074B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR102312327B1 (en) * | 2019-12-20 | 2021-10-14 | 주식회사 포스코 | Wire rod for high strength steel fiber, high strength steel fiber and manufacturing method thereof |
Family Cites Families (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001073081A (en) * | 1999-09-01 | 2001-03-21 | Nippon Steel Corp | Low yield ratio high tensile strength steel rod and its production |
| KR100742820B1 (en) * | 2005-12-27 | 2007-07-25 | 주식회사 포스코 | Steel wire having excellent cold heading quality and quenching property and method for producing the same |
| JP5194841B2 (en) * | 2008-01-31 | 2013-05-08 | Ｊｆｅスチール株式会社 | High-strength hot-dip galvanized steel sheet with excellent formability and manufacturing method thereof |
| JP5909143B2 (en) | 2012-04-13 | 2016-04-26 | 株式会社神戸製鋼所 | MAG welding method for hot rolled steel sheet and MIG welding method for hot rolled steel sheet |
-
2014
- 2014-09-04 KR KR1020140117817A patent/KR101611724B1/en active IP Right Grant
-
2015
- 2015-09-01 CN CN201510552724.1A patent/CN105401074B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| KR20160029220A (en) | 2016-03-15 |
| KR101611724B1 (en) | 2016-04-14 |
| CN105401074A (en) | 2016-03-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4018905B2 (en) | Hot rolled wire rod and bar for machine structure and manufacturing method thereof | |
| CN106811698B (en) | High-strength steel plate based on fine structure control and manufacturing method thereof | |
| CN110088326A (en) | Flat hot rolled bar product and its production method | |
| US20130037182A1 (en) | Mechanical part made of steel having high properties and process for manufacturing same | |
| CN108350549A (en) | The wire rod and its manufacturing method of non-quenching and tempering with excellent cold-workability | |
| CN104379791A (en) | Manganese-containing steel and production method therefor | |
| CN106661654A (en) | Method for manufacturing a high-strength steel sheet and sheet obtained by the method | |
| CN107109590A (en) | The high strength steel and its manufacture method for the resistant expansibility excellent of resistance to brittle crack | |
| CN101831594B (en) | Method for manufacturing high-strength steel plate used in low-temperature environment | |
| CN103210106B (en) | High-toughness cold-drawn non-heat-treated wire rod, and method for manufacturing same | |
| JPS61174322A (en) | Method for softening rolled material of machine structural steel | |
| CN108220773A (en) | High-strength wire material, heat treatment of wires and its manufacturing method with excellent drawability | |
| CN105401074B (en) | High-strength wire material and steel wire and its manufacture method | |
| JP3544131B2 (en) | Manufacturing method of medium carbon steel | |
| CN102549174B (en) | High-carbon soft wire rod not requiring softening treatment and manufacturing method thereof | |
| JP6600412B2 (en) | Non-heat treated wire excellent in strength and cold workability and method for producing the same | |
| CN107532262A (en) | The ultrahigh strength hot-rolled steel plate and its manufacture method of excellent in bending workability | |
| JP6390685B2 (en) | Non-tempered steel and method for producing the same | |
| US20200063228A1 (en) | Wire rod for springs with excellent corrosion fatigue resistance, steel wire, and manufacturing method thereof | |
| CN105401081B (en) | The manufacture method of the excellent high-strength wire material of draftability and high-tensile steel wires and wire rod | |
| KR101568494B1 (en) | Medium carbon soft wire rod and method for manufaturing the same | |
| CN107227425B (en) | Cold-heading carbon steel wire rod with high, processed goods and their manufacturing method using this | |
| JP5703934B2 (en) | Cold forging induction hardening steel, cold forging induction hardening steel bar, automobile undercarriage parts and automobile hub | |
| JPH06136441A (en) | Production of high strength and low yield ratio bar steel for reinforcing bar | |
| KR101461713B1 (en) | Wire rod having high toughness and method for manufacturing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| CP03 | Change of name, title or address | ||
| CP03 | Change of name, title or address |
Address after: Seoul, South Kerean Patentee after: POSCO Holdings Co.,Ltd. Address before: Gyeongbuk, South Korea Patentee before: POSCO |
|
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20230523 Address after: Gyeongbuk, South Korea Patentee after: POSCO Co.,Ltd. Address before: Seoul, South Kerean Patentee before: POSCO Holdings Co.,Ltd. |