WO2017117884A1 - 一种精细钢帘线拉拔加工性能优的高碳钢线材及制造方法 - Google Patents

一种精细钢帘线拉拔加工性能优的高碳钢线材及制造方法 Download PDF

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WO2017117884A1
WO2017117884A1 PCT/CN2016/079019 CN2016079019W WO2017117884A1 WO 2017117884 A1 WO2017117884 A1 WO 2017117884A1 CN 2016079019 W CN2016079019 W CN 2016079019W WO 2017117884 A1 WO2017117884 A1 WO 2017117884A1
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steel wire
wire
high carbon
fine
carbon steel
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PCT/CN2016/079019
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English (en)
French (fr)
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左锦中
陈海燕
张剑锋
许晓红
陈德
朱国荣
宗浩
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江阴兴澄特种钢铁有限公司
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Publication of WO2017117884A1 publication Critical patent/WO2017117884A1/zh

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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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
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    • C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
    • C21C5/52—Manufacture of steel in electric furnaces
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    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
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    • C21D6/00—Heat treatment of ferrous alloys
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    • 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
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • B21B1/22—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 plates, strips, bands or sheets of indefinite length
    • B21B2001/225—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 plates, strips, bands or sheets of indefinite length by hot-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60B—VEHICLE WHEELS; CASTORS; AXLES FOR WHEELS OR CASTORS; INCREASING WHEEL ADHESION
    • B60B27/00—Hubs
    • B60B27/02—Hubs adapted to be rotatably arranged on axle
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C19/00—Bearings with rolling contact, for exclusively rotary movement
    • F16C19/02—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows
    • F16C19/14—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows for both radial and axial load
    • F16C19/18—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows for both radial and axial load with two or more rows of balls
    • F16C19/181—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows for both radial and axial load with two or more rows of balls with angular contact
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    • F16C19/184—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows for both radial and axial load with two or more rows of balls with angular contact with two rows at opposite angles in O-arrangement
    • F16C19/186—Bearings with rolling contact, for exclusively rotary movement with bearing balls essentially of the same size in one or more circular rows for both radial and axial load with two or more rows of balls with angular contact with two rows at opposite angles in O-arrangement with three raceways provided integrally on parts other than race rings, e.g. third generation hubs
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    • F16C—SHAFTS; FLEXIBLE SHAFTS; ELEMENTS OR CRANKSHAFT MECHANISMS; ROTARY BODIES OTHER THAN GEARING ELEMENTS; BEARINGS
    • F16C2204/00—Metallic materials; Alloys
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    • F16C2204/70—Ferrous alloys, e.g. steel alloys with chromium as the next major constituent
    • F16C2204/72—Ferrous alloys, e.g. steel alloys with chromium as the next major constituent with nickel as further constituent, e.g. stainless steel

Definitions

  • the present invention relates to a high carbon steel wire which can be used as a tire radial cord after being drawn to a fine steel wire, and in particular, a high carbon steel wire which improves drawing workability and optimization of a drawing process, and a method of manufacturing the same.
  • the existing steel cord steel adopts a more complicated steel element component, which not only increases the raw material cost, but also has other adverse effects on the added trace elements.
  • the manufacturing process has also increased the difficulty.
  • it is possible to produce a high-carbon steel wire which is excellent in drawing processing performance for fine steel cords, has simple composition, simple process, and high production efficiency, and is urgently needed to be solved by those skilled in the art.
  • the object of the present invention is to provide a high-carbon steel wire for drawing fine steel cords, by simplifying the types of elements and optimizing the content of key elements, obtaining a composition having good mechanical properties and having a specific pearlite microstructure and composition. More compact steel wire, and the steel wire also fully meets the requirements of excellent wire drawing processing performance.
  • the present invention further provides a method of manufacturing a drawn fine steel cord high carbon steel wire.
  • the technical solution adopted by the present invention to solve the above technical problem is a high carbon steel wire with excellent drawing performance of fine steel cord, and the chemical composition of the steel wire is C: 0.60-1.00% by mass percentage. , Si: 0.10 ⁇ 0.60 ⁇ 3 ⁇ 4, Mn: 0.10 ⁇ 0.20 ⁇ 3 ⁇ 4, Cr: 0.20 ⁇ 0.50 ⁇ 3 ⁇ 4, S: ⁇ 0.01%, P: ⁇ 0.013%, Cu: ⁇ 0.05%, Ca: ⁇ 0.0010%, V ⁇ 0.005%, N: 0.0010 ⁇ 40%, and the solid solution N is 0.0010% or less, Al: ⁇ 0.0030%, Mo: ⁇ 0.02%, Ni: ⁇ 0.02%, B: ⁇ 0.0005%, balance is Fe And inevitable impurity elements. [0011] In the high carbon steel wire of the present invention, if necessary, the steel wire component further contains Ti : 0.0015% or less, but does not include 0.
  • the steel wire component further contains 0: 0.0025% or less, but does not include 0.
  • the steel wire component of the present invention reduces the contents of Al, Ti and N, reduces the influence of drawing performance caused by drawing hardening and brittle inclusions, adds Cr element, increases hardenability, and reduces the interlamellar spacing of pearlite. Conducive to the formation ratio of fine-grained pearlite (Sorstite) structure and improve the uniformity of the structure, so that the drawing performance is excellent; In addition, the content of Mn is reduced, the tendency of segregation and grain coarsening is lowered, and the mechanical properties are ensured. And carbon equivalent Ceq value, according to the design range of ⁇ ,
  • the present invention has been studied from various angles in order to improve the wire drawing processability of high-strength high-carbon steel wires, and as a result, it has been found that by adding a sufficient amount of Cr, the Cr element increases the hardenability and refines the pearlite pieces.
  • the layer spacing is beneficial to improve the formation ratio of the fine pearlite (sorbitite) structure and the uniformity of the microstructure, thereby effectively improving the strength and plastic deformation properties of the wire, helping to improve the drawing performance and suppressing the micro
  • the crack propagation can even reduce the number of pull passes and intermediate heat treatment.
  • the Cr content is higher than 0.20%, (preferably 0.25% or more, more preferably 0.30% or more), thereby significantly improving the plasticity index of the steel, significantly improving the wire drawing performance, and achieving a large Pulling deformation, saving intermediate heat treatment, improving production efficiency, saving energy consumption, and improving the final strength of the drawn steel wire; if the Cr content is excessive, it is easy to produce undissolved cementite phase, so that the phase transition ends It is easy to generate a supercooled structure such as troostite, martensite or bainite in the hot rolled wire or the drawn steel wire, the strength is too high, the plasticity is deteriorated, and the drawing workability of the steel is remarkably affected, so the present invention makes it
  • the upper limit is specified to be 0.50% (preferably 0.45% or less, more preferably 0.40% or less).
  • Mn acts as an element of the deoxidizing agent, and the strength of the steel material is improved by solid solution strengthening. Further, Mn fixes S in the steel in the form of MnS to prevent thermal embrittlement. In order to exert this effect, Mn needs to be controlled to 0.10% or more (preferably 0.15% or more).
  • Mn is an easy segregation element, especially the center segregation of the wire, which adversely affects the drawing processability, and the Mn element promotes the crystal.
  • the effect of grain growth is sensitive to the overheating of steel, and the content of refined grain elements in the steel is low; the Mn content is too high, causing the tensile strength of the wire to increase and the plasticity index to decrease, in order to obtain an excellent microstructure. , mechanical properties and drawing processing performance, Therefore, the present invention has a Mn content of 0.20% or less;
  • the Mn+Cr content needs to be controlled above 0.30%, and the Mn+Cr content needs to be controlled below 0.60% (preferably 0.
  • B has the effect of suppressing the precipitation of ferrite, and improves the hardenability; because of the low content of Al and Ti in the steel, the affinity of B and 0, N is strong, and BN is easily formed, which precipitates at the grain boundary, not only in the drawing process. The wire breakage easily occurs, and the toughness/ductility of the wire drawn at the end is significantly deteriorated.
  • the present invention has an upper limit of 0.0005% (preferably 0.0004% or less, more preferably 0.0003% or less).
  • N 0.0010-0.0040%
  • N causes embrittlement in the drawing process in the solid solution state, and the drawing performance is deteriorated. Therefore, it is necessary to precipitate in the form of nitride or the like using Ti, A1 or the like so that the solid solution N content is 0.0010% or less. If the N content is excessive, Ti, Al, B, etc. need to be added for curing to form nitride brittle inclusions, which is unfavorable for drawing processability, and is liable to be broken due to brittle inclusions; therefore, the upper limit is 0.0040% ( It is preferably 0.0035% or less, and more preferably 0.0030% or less. On the other hand, in order to make the N content less than 0.0010%, since it cannot be achieved from the manufacturing cost, the lower limit is 0.0010% or more (preferably 0.0015%).
  • A1N formed by bonding with N can effectively prevent austenite grain coarsening and function to prevent grain growth.
  • the control of deformable oxide inclusions is critical for the drawing processability and steel wire quality of steel cord steel.
  • the A1 content is too high, and the easily formed A1203 spinel and A1N are hard and brittle inclusions, which are polygonal.
  • the spherical characteristics are prone to breakage during the drawing and twisting of the steel wire, which deteriorates the drawing performance and significantly affects the quality and production efficiency of the steel wire.
  • the present invention has an upper limit of 0.0030% (preferably 0.0025% or less, more preferably 0.0015% or less).
  • Ti belongs to a strong solid N element, and the stoichiometric ratio of Ti/N is 3.42.
  • TiN formed by bonding with N can effectively prevent austenite grain coarsening and refine grains.
  • the formed TiN and Ti(CN) are hard and brittle inclusions in steel, high in hardness, light yellow to purple rose, and polygonal features are sharp and sharp.
  • no deformation, research shows that Ti inclusions with a size exceeding 5 ⁇ can easily cause broken wires during the drawing and twisting process of the steel wire, which deteriorates the drawing processing performance and significantly affects the production efficiency and the fatigue life of the steel wire. Therefore, the present invention strictly stipulates that the upper limit is 0.0015% (preferably 0.0010% or less, more preferably 0. 0005% or less);
  • the composition of other chemical components also needs to be appropriately adjusted, including the above-mentioned C, S i, P, s, o, etc., and the range of each component (element) composed of other chemical components.
  • the reasons for the restriction are as follows
  • C is a cost-effective strengthening element in steel, and the strength of the steel can be significantly improved by solid solution strengthening and precipitation strengthening.
  • the C content increases, the work hardening amount of the wire drawing and the strength after drawing increase. If the C content is less than 0.6%, it is difficult to obtain a pearlite structure excellent in wire drawing hardness. Therefore, the C content is 0.60% or more, (preferably 0.65% or more, and more preferably 0.70% or more).
  • the C content is too high, the tendency to form reticulated cementite in the austenite grain boundary will become higher and higher, not only in the drawing process, but also in the final drawing of the wire.
  • the toughness/ductility is significantly degraded.
  • the C content is 1.0% or less (preferably 0.95% or less).
  • Si is a deoxidizing element in the present steel, and is present in a ferrite phase in a pearlite structure in a solid solution-reinforced form, and functions to increase the strength of the steel after heat treatment.
  • the lower limit is 0.10% (preferably 0.15% or more)
  • the pearlite is The ductility of the ferrite phase is lowered, and the ductility after drawing is lowered, whereby the upper limit is made 0.60% (preferably 0.50% or less, more preferably 0.40% or less).
  • S is an unavoidable impurity, and it is easy to form defects such as MnS inclusions, and the drawing process performance is deteriorated. Accordingly, the present invention has an upper limit of 0.010% (preferably 0.009% or less, more preferably 0.008% or less).
  • P is an unavoidable impurity, and is liable to form defects such as segregation and inclusion, and in particular, ferrite is solid-solution-strengthened, and thus has a large influence on deterioration of drawing processability.
  • the invention has an upper limit of 0.013% (preferably 0. 0010% or less).
  • O is mainly present in the form of oxide inclusions such as A1203, MnO, CaO, SiO2 in steel.
  • Si-Mn alloy should be used for deoxidation. Instead of using aluminum or a higher alloy containing aluminum for deoxidation; after extensive research, the size and quantity of oxide inclusions in the steel significantly degrade the drawing processability of the steel wire, so the upper limit is made 0.0030% (preferably 0.0025% or less, more preferably 0.0020% or less).
  • the deoxidation of the Si-Mn alloy makes it difficult to make the 0 content less than 0.0008%, which cannot be achieved from the actual production. Therefore, the lower limit is 0.0080% or more (preferably 0.0010%).
  • the pearlite content is ⁇ 98%, and the remaining part is non-pearlite, including bainite, pro-eutectoid ferrite, cementite, etc.; area of non-pearlite The sum of the area ratios of the coarse-grained pearlite having a ratio of the apparent sheet spacing of 500 nm or more is ⁇ 10%.
  • the high carbon steel wire of the invention has an excellent microstructure, a pearlite content of more than 98%, a narrower interlamellar spacing of the pearlite, and a mechanical property index, which reduces the intermediate heat treatment and the drawing pass, from The raw material wire needs only at least one intermediate heat treatment, and can be drawn to a fine steel wire of 0.06 ⁇ 0.56mm diameter.
  • the present invention further provides a method for manufacturing a high carbon steel wire having excellent drawing performance of the above-mentioned fine steel cord, and the flow mainly includes:
  • the continuous casting slab is heated to 1200 ⁇ 1260 ° C, and the temperature is kept for 4 hours or more, and the furnace is fully improved.
  • the heating temperature enables the alloy elements such as Cr and C to be fully and uniformly dissolved in the austenite phase, which is uniformly precipitated in the subsequent cooling process, and is effective for controlling the fineness and uniformity of the microstructured pearlite layer.
  • the heating temperature is 1200 ° C or higher, more preferably 1220 ° C or higher, and the heating temperature is too high, and the austenite phase tends to be roughened and superheated. Therefore, the heating temperature is preferably 1260 ° C or lower.
  • rolling temperature is 1040 ⁇ 1100 ° C
  • rolling speed is set to 95 ⁇ 120 m / s
  • spinning temperature is controlled at 900 ⁇ 30 ° C
  • disc The Staller cooling line is air-cooled, and the cooling start temperature is 830 ° C ⁇ 930 ° C.
  • the cooling start temperature can ensure the steel in the austenite phase region. If the temperature is too high, the superheated rough microstructure is easily generated.
  • the cooling rate is above 15 ° C / s (preferably above 20 ° C / s), because the wire can not be achieved in the cooling roller Balanced cooling, cooling rate is below 50 ° C / s (preferably below 40 ° C / s); from 650 ° C to 580 ° C, cooling continues for 10 s or more (preferably 15 s or more, more preferably 20s or more), can better play the role of Cr element, better achieve the transformation of fine pearlite and uniformity of the structure, and obtain excellent mechanical properties.
  • the high carbon steel wire of the invention has an excellent microstructure, a pearlite content of more than 98%, a narrower interlayer spacing of the pearlite, and a mechanical property index, which reduces the intermediate heat treatment and the drawing pass,
  • the raw material wire only needs at least one intermediate heat treatment, which can be drawn to a fine wire of 0.06 ⁇ 0.56mm diameter.
  • FIG. 1 is a view showing a microstructure of a steel wire rod and a pitch of a pearlite sheet according to Embodiment 1 of the present invention
  • FIG. 2 is a view showing a microstructure of a steel wire rod and a pitch of a pearlite sheet according to Embodiment 2 of the present invention
  • FIG. 3 is a view showing a microstructure of a steel wire rod and a pitch of a pearlite sheet according to Embodiment 2 of the present invention.
  • Nb 0.001%
  • V 0.002%
  • Ni 0.01%
  • Ti 0.0004%
  • Cu 0.01%
  • Ca ⁇ 0.000 4%
  • N ⁇ 0.00206%
  • Mo 0.01%
  • balance is Fe and inevitable Impurity element.
  • the continuous casting billet is heated to above 1200 ° C, the residual oxygen in the furnace is controlled to be less than 5%, the heat is kept for 4 hours, and the high pressure water is descaled and then rolled: the rolling temperature is 1040 to 1100 ° C, The rolling process is divided into 39 passes, the rolling speed is set to 105 m/s, and the spinning temperature is controlled at 900 ⁇ 30 ° C.
  • the wire rod is air-cooled by the Steyr cooling line for cooling.
  • the equalizing cooling rate on the roller table needs to adjust the air volume of the No. 1-7 fan on the cooling line according to the seasonal ambient temperature.
  • the ambient temperature is 8 °C
  • the roller speed is 0.85 m/s
  • 1-7 fan is set. : 1 : 85 ⁇ 3 ⁇ 4 , 2 : 80 ⁇ 3 ⁇ 4 , 3 : 80 ⁇ 3 ⁇ 4 , 4 : 85 ⁇ 3 ⁇ 4 , 5 : 30 ⁇ 3 ⁇ 4 , 6 : 20% , 7 : 0% ; After the above air-cooled roller path, a uniform soxite structure was formed, and the Sorbite content was 98%. After the wire rod is taken offline, the sample is treated by aging treatment to detect the mechanical properties and structure of the wire rod.
  • the mechanical properties of the wire rod are as follows: tensile strength 1140 ⁇ 1180Mpa, surface shrinkage: 42 ⁇ 45 ⁇ 3 ⁇ 4; metallographic strip
  • the structure is a uniform soxite structure as shown in Fig. 1, and the ratio of sorbite is 98% or more.
  • Nb 0.001%
  • V 0.002%
  • Ni 0.01%
  • Ti 0.0004%
  • Cu 0.01%
  • Ca ⁇ 0.000 4%
  • N ⁇ 0.00207%
  • Mo 0.01%
  • balance is Fe and inevitable Impurity element.
  • the continuous casting billet is heated to above 1200 ° C, the residual oxygen in the furnace is controlled to be less than 6%, the heat is kept for 4 hours, and the high pressure water is descaled and then rolled: the rolling temperature is 1040 to 1100 ° C, The rolling process is divided into 39 passes, the rolling speed is set to 100 m/s, and the spinning temperature is controlled at 900 ⁇ 30 ° C.
  • the wire rod is cooled by Steyr Line air cooling, in order to achieve a balanced cooling rate on the cooling roller, the air volume of the No. 1-7 fan on the cooling line should be adjusted according to the seasonal ambient temperature.
  • the ambient temperature is 15 °C, and the roller speed is 0.85 m/s.
  • Nb 0.001%
  • V 0.002%
  • Ni 0.01%
  • Ti 0.0003%
  • Cu 0.01%
  • Ca ⁇ 0.000 4%
  • N ⁇ 0.00207%
  • Mo 0.01%
  • balance is Fe and inevitable Impurity element.
  • the continuous casting billet is heated to above 1200 ° C, the residual oxygen in the furnace is controlled to be less than 6%, the heat is kept for 4 hours, and the high pressure water is descaled and then rolled: the rolling temperature is 1040 to 1100 ° C, The rolling process is divided into 39 passes, the rolling speed is set at 110m/s, and the spinning temperature is controlled at 900 ⁇ 30°C. After the rolling is completed, the wire rod is air-cooled by the Steyr cooling line for cooling. The equalizing cooling rate on the roller table needs to adjust the air volume of the No. 1-7 fan on the cooling line according to the seasonal ambient temperature. The ambient temperature is 36 °C, the roller speed is 0.85 m/s, and the fan 1-7 is set.

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Abstract

本发明涉及一种精细钢帘线拉拔加工性能优的高碳钢线材，该钢线材的化学成分按质量百分比计为C：0.60～1.00%，Si：0.10～0.60%，Mn：0.10～0.20%，Cr：0.20～0.50%，S：≤0.01%，P：≤0.013%，Cu：≤0.05%，Ca：≤0.0010%，V≤0.005%，N：0.0010～0.0040%，并且固溶的N为0.0010%以下，Al：≤0.0030%，Mo：≤0.02%，Ni：≤0.02%，B：≤0.0005%，余量为Fe。通过优化钢线材中关键元素，获得一具备良好的力学性能、具有特定珠光体显微组织结构且成分更加简洁的钢线材，满足优异钢丝拉拔加工性能的要求。

Description

说明书
发明名称：一种精细钢帘线拉拔加工性能优的高碳钢线材及制造方 法
技术领域
[0001] 本发明属于在拉拔至精细钢丝后， 可用作轮胎子午帘线的高碳钢线材， 尤其是 改善了拉拔加工性能及拉拔工序优化的高碳钢线材及其制造方法。
背景技术
[0002] 随着世界经济的快速发展， 特别是中国经济的快速发展。 公路、 汽车、 交通等 行业还在快速发展， 汽车全钢载重子午胎、 轻载子午胎的比例不断提高， 市场 前景十分良好。 汽车的轻量化要求钢丝具有更高的强度。 如精细钢帘线在拔丝 加工及进一步生产等过程中， 因拉拔变形量大、 钢丝强度高， 很容易发生断线 ， 导致生产率下降以及质量低下。 为此拉丝后除了要求高强度、 高延展性外， 还要求有良好的拉丝加工性， 由此一直以来， 各种为满足上述要求的高品质高 碳钢线材被广泛地幵发。
[0003] 申请号 201180050074.0公幵的拉丝工艺优异的高碳钢线材， 为改善拉丝加工性 育 ， 通过添加充分的 Ti含量， 使 N变成 TiN， 极力减少钢种的固溶 N， 并且确保规 定量的固溶 B， 提高拉丝性能； 但是， 为固溶 N加 Ti而形成 TiN等 Ti化合物在钢中 以脆性夹杂物存在， 其硬度高， 呈多边形形貌， 在钢丝的拉拔及捻股过程容易 产生断丝， 显著影响钢丝质量和生产效率。
[0004] 申请号 201180012852.7公幵的拉丝加工性和拉丝后疲劳性优异的高碳钢线材， 为提高线材的拉拔性能和拉丝后的疲劳特性， 添加充分的 B含量， 使 B固溶 N作 为 BN化合物而微细析出， 但是为固溶 N而添加的 B形成过多的 BC与 Fe的化合物 会在盘条中心沿珠光体晶界聚集析出， 形成粗大的 BC中心网状化合物， 导致线 材在后道的拉拔过程中脆化， 使拉丝加工性恶化。
[0005] 申请号 200980100006.3公幵的延性优良的线材以及高强度钢线以及他们的制造 方法， 通过添加 Mo、 W中的一种或两种抑制 600°C以上高温区珠光体的生长， 进 而抑制粗片状珠光体的形成， 同吋提高淬火性抑制铁素体的生成， 提高索氏体 比例， 但是过剩的添加这些元素则抑制整个温度区珠光体生长， 使得冷却吋间 变长， 降低生产力， 同吋在盘条中心析出的 Mo2C和 W2C的化合物也会降低材料 的拉丝加工性。
[0006] 申请号 200980100006.3公幵的延性优良的线材以及高强度钢线以及他们的制造 方法， 通过添加 Mo、 W中的一种或两种抑制 600°C以上高温区珠光体的生长， 进 而抑制粗片状珠光体的形成， 同吋提高淬火性抑制铁素体的生成， 提高索氏体 比例， 但是过剩的添加这些元素则抑制整个温度区珠光体生长， 使得冷却吋间 变长， 降低生产力， 同吋在盘条中心析出的 Mo2C和 W2C的化合物也会降低材料 的拉丝加工性。
[0007] 综上， 现有钢帘线钢材为了满足良好的拉拔性能， 采用的是更加复杂的钢元素 成分， 不仅提高了原料成本， 所添加的微量元素往往也存在其他不良影响， 给 线材的制造工艺也增加了难度。 基于上述钢帘线的生产现状， 能够生产出一种 拉拔加工性能优的用于精细钢帘线， 成分简单， 且工艺简单、 生产效率高的高 碳钢线材是本领域技术人员迫切需要解决的技术问题。
技术问题
[0008] 本发明目的在于提供一种拉拔精细钢帘线高碳钢线材， 通过简化元素种类， 优 化关键元素的含量， 获得一具备良好的力学性能、 具有特定珠光体显微组织结 构且成分更加简洁的钢线材， 并且该钢线材也完全满足优异钢丝拉拔加工性能 的要求。
[0009] 本发明另外提供一种制造拉拔精细钢帘线高碳钢线材的制造方法。
问题的解决方案
技术解决方案
[0010] 本发明解决上述技术问题所采用的技术方案为， 一种精细钢帘线拉拔加工性能 优的高碳钢线材， 该钢线材的化学成分按质量百分比计为 C: 0.60-1.00% , Si: 0.10〜0.60<¾， Mn: 0.10〜0.20<¾， Cr: 0.20〜0.50<¾， S: <0.01% , P: <0.013% ， Cu: <0.05% , Ca: <0.0010% , V<0.005% , N: 0.0010〜議 40%， 并且固溶 的 N为 0.0010%以下， Al: <0.0030% , Mo: <0.02% , Ni: <0.02% , B : <0.0005 %, 余量为 Fe及不可避免的杂质元素。 [0011] 本发明的高碳钢线材中， 根据需要钢线材成分中还包含 Ti: 0.0015%以下， 但 不包含 0的情况。
[0012] 本发明的高碳钢线材中， 根据需要钢线材成分中还包含 0 : 0.0025%以下， 但 不包含 0的情况。
[0013] 本发明的钢线材成分中降低 Al、 Ti及 N含量， 减少拉拔硬化及脆性夹杂物引起 的拉拔性能影响， 添加 Cr元素， 增加淬透性， 缩小珠光体的片层间距， 有利于 细片状珠光体 （索氏体） 组织的形成比例及提高组织的均匀性， 使得拉拔性能 优异； 另外， 再减少 Mn的含量， 降低偏析、 晶粒粗化的倾向， 保证力学性能及 碳当量 Ceq值， 根据 ΟΛΜη的设计范围，
进一步地将 Mn+Cr所需含量之和控制在 0.30〜0.60<¾。 具体设计原理如下：
[0014] 本发明为了改善高强度高碳钢线材的拉丝加工性能， 从各种角度进行研究， 其 结果发现， 通过添加充分量的 Cr， Cr元素增加淬透性， 并且细化珠光体的片层 间距， 有利于提高细片状珠光体 （索氏体） 组织的形成比例及显微组织的均匀 性， 从而有效提高线材的强度及塑性变形性能， 有助于改善拉拔性能， 并抑制 微裂纹的扩展， 甚至可减少拉拔道次及中间热处理过程。 为了使上述效果充分 的发挥， 实践证明， Cr含量高于 0.20%， （优选为 0.25%以上， 更优选为 0.30%以 上） ， 从而明显改善了钢材的塑性指标， 显著改善拉丝加工性能， 实现大的拉 拔变形， 节省中间热处理， 提高生产效率、 节约能源消耗， 并提升了拉拔钢丝 的最终强度； 若 Cr含量过剩， 则易生产未溶解的渗碳体相， 使相变结束吋间延 长， 易在热轧线材或拉拔钢丝中产生屈氏体、 马氏体或贝氏体等过冷组织， 强 度过高， 塑性变差， 显著影响钢材的拉拔加工性， 因此本发明使其上限规定为 0. 50% (优选为 0.45%以下， 更优选为 0.40%以下） 。
[0015] Mn作为脱氧剂作用的元素， 通过固溶强化提高钢材的强度， 此外 Mn将钢中的 S以 MnS形式固定， 防止热脆化的效果。 为了发挥此效果， Mn需要控制在 0.10% 以上 （优选为 0.15%以上） ； 另一方面 Mn是容易偏析元素， 特别是线材的中心 偏析， 对拉拔加工性有不利影响， 其次 Mn元素促进晶粒长大的作用， 对钢的过 热敏感， 且本钢中的细化晶粒元素含量低； Mn含量过高， 引起线材的抗拉强度 升高， 塑性指标下降， 为了获得优良的显微组织、 力学性能及拉拔加工性能， 由此本发明使其 Mn含量为 0.20%以下；
[0016] 根据以上 QAMn的设计范围， 为获得满足客户及使用要求的最佳力学性能强度 及碳当量 Ceq值，
Mn+Cr含量需要控制在 0.30%以上， Mn+Cr含量需要控制在 0.60%以下 （优选为 0.
55%以下） 。
[0017] B: <0.0005%
[0018] B有抑制铁素体析出的效果， 提高淬透性； 因钢中的 Al、 Ti元素含量低， B与 0 、 N亲和力强， 易形成 BN， 于晶界析出， 不仅在拉丝过程中容易发生断线， 而 且在最终拉丝的线材的韧性 /延展性显著劣化。 由此本发明使其上限为 0.0005% ( 优选为 0.0004%以下， 更优选为 0.0003%以下） 。
[0019] N: 0.0010-0.0040%
[0020] N在固溶状态下在拉丝过程中会引起脆化， 使得拉丝性能劣化， 因此需要利用 Ti、 A1等以氮化物等形式析出， 使得固溶 N含量在 0.0010%以下。 若 N含量过剩， 则需增加 Ti、 Al、 B等进行固化， 形成氮化物脆性夹杂物， 对拉拔加工性不利， 容易因脆性夹杂物导致拉拔断丝； 因此使其上限为 0.0040% (优选为 0.0035%以 下， 更优选为 0.0030%以下） ； 另一方面， 为了使 N含量低于 0.0010%， 从制造成 本出发无法实现， 因此其下限为 0.0010%以上 （优选为 0.0015%) 。
[0021] A1: <0.0030%
[0022] A1: 作为脱氧有效元素， 通过与 N结合形成的 A1N可有效地防止奥氏体晶粒粗 化， 起到防止晶粒长大的作用。 可变形的氧化物夹杂的控制对钢帘线钢的拉拔 加工性能及钢丝品质非常关键， A1含量过高， 易形成的 A1203尖晶石类、 A1N类 属于硬脆的夹杂物， 呈多边形、 球形特征， 在钢丝的拉拔及捻股过程容易产生 断丝， 从而使得拉拔加工性能劣化， 并显著影响钢丝质量和生产效率。 由此本 发明使其上限为 0.0030% (优选为 0.0025%以下， 更优选为 0.0015%以下） 。
[0023] Ti: <0.0015%
[0024] Ti: 属于较强的固 N元素， Ti/N的化学计量比为 3.42， 通过与 N结合形成的 TiN 可有效地防止奥氏体晶粒粗化， 起到细化晶粒的作用， 但形成的 TiN、 Ti(CN)在 钢中属于硬脆的夹杂物， 硬度高、 呈浅黄色到紫玫瑰色、 多边形特征棱角锋利 ， 不变形， 研究表明， 尺寸超过 5μηι的 Ti夹杂物， 在钢丝的拉拔及捻股过程极容 易引起断丝， 从而使得拉拔加工性能劣化， 并显著影响生产效率和钢丝的疲劳 寿命。 由此本发明严格规定其上限为 0.0015% (优选为 0.0010%以下， 更优选为 0. 0005%以下） ；
[0025] 本发明的高碳钢线材中， 其它化学成分组成也需要适当的调整， 包括上述 C， S i， P， s， o等在内， 其它化学成分组成的各成分 （元素） 的范围限定理由如下
[0026] C: 0.60-1.00%
[0027] C是钢中经济有效的强化元素， 通过固溶强化和析出强化可明显提高钢的强度 ， 随着 C含量的增加， 拉丝吋的加工硬化量、 拉丝后的强度增大。 若 C含量低于 0 .6% , 则得到拉丝加工硬度优异的珠光体组织困难。 因此 C含量为 0.60%以上， ( 优选为 0.65%以上， 更优选为 0.70%以上） 。 另一方面， 若 C含量过高， 则在奥氏 体晶界生成网状初析渗碳体的趋势会越来越高， 不仅在拉丝过程中容易发生断 线， 而且在最终拉丝的线材的韧性 /延展性显著劣化。 由此 C含量为 1.0%以下 ( 优选为 0.95%以下） 。
[0028] Si: 0.10-0.60%
[0029] Si是本钢中的脱氧元素， 并以固溶强化形式存在于珠光体组织中的铁素体相， 发挥着提高钢热处理后强度的作用。 当 Si含量少而低于 0.10%吋， 脱氧效果和强 度提高效果不充分， 因此下限为 0.10% (优选为 0.15%以上） ， 另一方面， Si的 含量过高， 则使得所述珠光体中的铁素体相的延展性降低， 使得拉丝后的延展 性降低， 由此将其上限规定为 0.60% (优选为 0.50%以下， 更优选为 0.40%以下）
[0030] S: <0.010% (不含 0)
[0031] S是不可避免的杂质， 易形成 MnS系夹杂等缺陷， 而使拉拔加工性能劣化。 由 此本发明使其上限为 0.010% (优选为 0.009%以下， 更优选为 0.008%以下） 。
[0032] P: <0.013% (不含 0)
[0033] P是不可避免的杂质， 易形成偏析、 夹杂等缺陷， 特别是使得铁素体固溶强化 ， 因此对拉拔加工性能的劣化影响大。 由此本发明使其上限为 0.013% (优选为 0. 0010%以下） 。
[0034] 0： 0.0008-0.0030%
[0035] O在钢中主要以 A1203、 MnO、 CaO、 Si02等氧化物夹杂物形式存在， 为了得 到塑性区的 MnO-A1203-Si02复合低熔点可变形夹杂物， 应使用 Si-Mn合金进行 脱氧， 而不使用铝或含铝较高的合金进行脱氧； 经过大量研究， 钢中的氧化物 夹杂物尺寸、 数量， 显著劣化钢丝的拉拔加工性能， 因此规定使其上限为 0.0030 % (优选为 0.0025%以下， 更优选为 0.0020%以下） 。 另一方面， 采用 Si-Mn合金 脱氧， 难以使得 0含量低于 0.0008%， 从制造实际出发无法实现， 因此其下限为 0 .0008%以上 （优选为 0.0010%) 。
[0036] 力学性能满足： 钢线材成分中 C: 0.65—0.75% , 线材具有抗拉强度 1000〜1100 Mpa, 面缩≥45<¾； C: 0.75〜0.85<¾范围，线材具有抗拉强度 1100〜1200Mpa， 面 缩≥40<¾。
[0037] 本发明所得钢线材的金相组织中， 珠光体含量≥98%， 剩余部分为非珠光体， 包含贝氏体、 先共析铁素体、 渗碳体等； 非珠光体的面积率与表观片层间距为 5 OOnm以上的粗片状珠光体的面积率之和≤10%。
[0038] 本发明的高碳钢线材具有优异的显微组织结构， 珠光体含量在 98%以上珠光体 的片层间距更窄， 以及力学性能指标， 减少了中间热处理及拉拔道次， 从原材 料线材只需要至少一次中间热处理， 即可拉拔至 0.06〜0.56mm直径的精细钢丝
[0039] 本发明另提供一种制造上述精细钢帘线拉拔加工性能优的高碳钢线材的方法， 流程主要包括：
[0040] 冶炼符合钢线材化学成分的钢水， 锻造连铸坯， 炼钢采用高性能精炼合成澄， 保证了夹杂物具有良好的可变形性。 钢包保持超长吋间的夹杂物去除过程， 使 非金属夹杂物充分上浮， 保证了帘线钢的高纯净性。 选择专用的精炼澄和中间 包保护澄更好地吸附夹杂物。 连铸采用小方坯， 优选的采用大方坯连铸， 通过 大方坯幵坯， 解决了表面质量问题， 均质化问题， 夹杂物数量得到有效控制。 采用先进的末端电磁搅拌、 连铸轻压下先进装备程序， 降低材料的偏析。
[0041] 轧制前将连铸坯加热至 1200〜1260°C， 保温 4小吋及以上出炉， 通过充分提高 加热温度， 能够让 Cr、 C等合金元素充分而均匀溶解在奥氏体相中， 为后续冷却 过程中均匀析出， 有效地控制细化显微组织珠光体片层间距及均匀性做准备， 优选的加热温度为 1200°C以上， 更优选 1220°C以上， 此外， 加热温度过高， 奥氏 体相有粗化过热的趋势， 因此加热温度优选为 1260°C以下。
[0042] 高压水除鳞后进行轧制： 幵轧温度为 1040〜1100°C， 轧制速度设定 95〜120m/s ， 吐丝温度控制在 900±30°C; 轧制结束后， 盘条经斯太尔摩冷却线风冷， 冷却 幵始温度为 830°C〜930°C， 该冷却幵始温度能够保证钢在奥氏体相区， 温度过高 容易产生过热粗化显微组织； 因 Cr元素增加奥氏体的稳定性， 从冷却幵始温度 至 650°C， 冷却速率在 15°C/s以上 （优选为 20°C/s以上） ， 因线材在冷却辊道无法 实现均衡的冷却， 冷却速率在 50°C/s以下 （优选为 40°C/s以下） ； 从 650°C至 580 °C期间， 冷却持续吋间保持在 10s以上 （优选 15s以上， 更优选为 20s以上） ， 育 够更好地发挥 Cr元素的作用机理， 更好地实现细片状珠光体的转变及组织的均 匀性， 获得优良的力学性能指标。
发明的有益效果
有益效果
[0043] 本发明的高碳钢线材具有优异的显微组织结构， 珠光体含量在 98%以上珠光体 的片层间距更窄， 以及力学性能指标， 减少了中间热处理及拉拔道次， 从原材 料线材只需要至少一次中间热处理， 即可拉拔至 0.06〜0.56mm直径的精细钢丝 对附图的简要说明
附图说明
[0044] 图 1为本发明实施例 1钢线材显微组织及珠光体片间距图；
[0045] 图 2为本发明实施例 2钢线材显微组织及珠光体片间距图；
[0046] 图 3为本发明实施例 2钢线材显微组织及珠光体片间距图。
实施该发明的最佳实施例
本发明的最佳实施方式
[0047] 以下结合实施例对本发明作进一步详细描述。 [0048] 实施例 1
[0049] 熔炼 100吨下述所示化学成分组成的钢， 进行连续铸造， 制作截面尺寸 200mmx 200mm的连铸坯， 所得连铸坯的化学成分按照质量百分比计包括：
C: 0.82%, Si: 0.19%, Mn: 0.18%, S<0.006%,, P<0.008%, Cr: 0.35%, As ： 0.003%, Al: 0.0007%,
Nb: 0.001%, V： 0.002%, Ni: 0.01%, Ti: 0.0004%, Cu: 0.01%, Ca: <0.000 4%, N: <0.00206%, Mo: 0.01%, 余量为 Fe及不可避免的杂质元素。
[0050] 把连铸坯加热至 1200°C以上， 炉内残氧量控制在 5%以下， 保温 4小吋出炉， 高 压水除鳞后进行轧制： 幵轧温度为 1040〜1100°C， 轧制过程分 39道次轧制， 轧制 速度设定 105m/s， 吐丝温度控制在 900±30°C; 轧制结束后， 盘条经斯太尔摩冷却 线风冷， 为实现冷却辊道上均衡的冷却速率， 需根据季节环境温度， 调整冷却 线上 1-7号风机风量， 环境温度 8°C， 辊道速度 0.85m/s幵始， 设定 1-7号风机幵启 度： 1号： 85<¾， 2号： 80<¾， 3号： 80<¾， 4号： 85<¾， 5号： 30<¾， 6号： 20%, 7 号： 0%; 盘条经上述风冷辊道后， 形成均匀的索氏体组织， 索氏体含量 98%。 盘条下线后试样经吋效处理， 检测盘条的力学性能和组织， 盘条的力学性能指 标如下： 抗拉强度1140〜1180Mpa， 面缩： 42〜45<¾； 盘条的金相组织为图 1所 示的均匀的索氏体组织， 索氏体比例 98%以上。
[0051]
[0052] 实施例 2
[0053] 熔炼 150吨下述所示化学成分组成的钢， 进行连续铸造， 制作截面尺寸 200mmx 200mm的连铸坯， 所得连铸坯的化学成分按照质量百分比计包括：
C: 0.81%, Si: 0.18%, Mn: 0.18%, S<0.009%,, P<0.009%, Cr: 0.35%, As ： 0.003%, AL 0.0007%,
Nb: 0.001%, V： 0.002%, Ni: 0.01%, Ti: 0.0004%, Cu: 0.01%, Ca: <0.000 4%, N: <0.00207%, Mo: 0.01%, 余量为 Fe及不可避免的杂质元素。
[0054] 把连铸坯加热至 1200°C以上， 炉内残氧量控制在 6%以下， 保温 4小吋出炉， 高 压水除鳞后进行轧制： 幵轧温度为 1040〜1100°C， 轧制过程分 39道次轧制， 轧制 速度设定 100m/s， 吐丝温度控制在 900±30°C; 轧制结束后， 盘条经斯太尔摩冷却 线风冷， 为实现冷却辊道上均衡的冷却速率， 需根据季节环境温度， 调整冷却 线上 1-7号风机风量， 环境温度 15°C， 辊道速度 0.85m/s幵始， 设定 1-7号风机幵启 度： 1号： 85<¾， 2号： 80<¾， 3号： 80<¾， 4号： 85<¾， 5号： 20%, 6号： 15<¾， 7 号： 0%; 盘条经上述风冷辊道后， 形成均匀的索氏体组织， 索氏体含量 98%以 上。 盘条下线后试样经吋效处理， 检测盘条的力学性能和组织， 盘条的力学性 能指标如下： 抗拉强度 1170〜1200Mpa， 面缩： 44〜48<¾； 盘条的金相组织为图 2所示的均匀的索氏体组织， 索氏体比例 98%以上。
[0055]
[0056] 实施例 3
[0057] 熔炼 100吨下述所示化学成分组成的钢， 进行连续铸造， 制作截面尺寸 200mmx 200mm的连铸坯， 所得连铸坯的化学成分按照质量百分比计包括：
C: 0.82% , Si: 0.21% , Mn: 0.19% , S<0.004%,, P<0.008% , Cr: 0.34% , As ： 0.003% , Al: 0.0008% ,
Nb: 0.001% , V： 0.002% , Ni: 0.01% , Ti: 0.0003%, Cu: 0.01% , Ca: <0.000 4% , N: <0.00207% , Mo: 0.01%, 余量为 Fe及不可避免的杂质元素。
[0058] 把连铸坯加热至 1200°C以上， 炉内残氧量控制在 6%以下， 保温 4小吋出炉， 高 压水除鳞后进行轧制： 幵轧温度为 1040〜1100°C， 轧制过程分 39道次轧制， 轧制 速度设定 110m/s， 吐丝温度控制在 900±30°C; 轧制结束后， 盘条经斯太尔摩冷却 线风冷， 为实现冷却辊道上均衡的冷却速率， 需根据季节环境温度， 调整冷却 线上 1-7号风机风量， 环境温度 36°C， 辊道速度 0.85m/s幵始， 设定 1-7号风机幵启 度： 1号： 95% , 2号： 90<¾， 3号： 95%, 4号： 95% , 5号： 45<¾， 6号： 20% , 7 号： 10%; 盘条经上述风冷辊道后， 形成均匀的索氏体组织， 索氏体含量 98%以 上。 盘条下线后试样经吋效处理， 检测盘条的力学性能和组织，盘条的力学性能 指标如下： 抗拉强度 1140-1170Mpa， 面缩： 46-50%; 盘条的金相组织为图 3所示 的均匀的索氏体组织， 索氏体比例 98%以上。
本发明的实施方式
[0059] 在此处键入本发明的实施方式描述段落。 工业实用性
[0060] 在此处键入工业实用性描述段落。
序列表自由内容
[0061] 在此处键入序列表自由内容描述段落。

Claims

权利要求书
[权利要求 1] 一种精细钢帘线拉拔加工性能优的高碳钢线材， 其特征在于： 该钢线 材的化学成分按质量百分比计为 C: 0.60—1.00% , Si: 0.10—0.60% Mn: 0.10 0.20<¾ Cr: 0.20 0.50<¾ S: <0.01% , P: <0.013% Cu: <0.05% , Ca: <0.0010% , V<0.005% , N: 0.0010 40% ， 并且固溶的 N为 0.0010%以下， Al: <0.0030% , Mo: <0.02% , Ni <0.02% , B: <0.0005% , 余量为 Fe及不可避免的杂质元素。
[权利要求 2] 根据权利要求 1所述的精细钢帘线拉拔加工性能优的高碳钢线材， 其 特征在于： 钢线材成分中还包含 Ti: 0.0015%以下， 但不包含 0的情况
[权利要求 3] 根据权利要求 1所述的精细钢帘线拉拔加工性能优的高碳钢线材， 其 特征在于： 钢线材成分中还包含 0 : 0.0025%以下， 但不包含 0的情况
[权利要求 4] 根据权利要求 1所述的精细钢帘线拉拔加工性能优的高碳钢线材， 其 特征在于： 钢线材成分中 Mn+Cr的含量为 0.30 0.60<¾
[权利要求 5] 根据权利要求 1所述的精细钢帘线拉拔加工性能优的高碳钢线材， 其 特征在于： 钢线材成分中 C: 0.65 0.75%， 线材具有抗拉强度 1000 HOOMpa, 面缩≥45<¾； C: 0.75 0.85<¾范围，线材具有抗拉强度 1100 1200Mpa， 面缩≥40%
6.根据权利要求 1所述的精细钢帘线拉拔加 工性能优的高碳钢线材， 其特征在于： 钢线材的金相组织中， 珠光体 含量≥98%， 非珠光体的面积率与表观片层间距为 500nm以上的粗片 状珠光体的面积率之和≤ 10%
[权利要求 7] 根据权利要求 1或 5或 6所述的精细钢帘线拉拔加工性能优的高碳钢线 材， 其特征在于： 从原材料线材至少需要一次中间热处理， 可拉拔至 0.06 0.56mm直径的精细钢丝。
[权利要求 8] —种制造上述权利要求 1至 6所述精细钢帘线拉拔加工性能优的高碳钢 线材， 其特征在于： 冶炼符合钢线材化学成分的钢水， 锻造连铸坯， 将连铸坯加热至 1200 1260°C， 保温 4小吋及以上出炉， 高压水除鳞 后进行轧制： 幵轧温度为 1040〜1100°C， 轧制速度设定 95〜120m/s， 吐丝温度控制在 900±30°C; 轧制结束后， 盘条经斯太尔摩冷却线风冷 ， 冷却幵始温度为 830°C〜930°C， 从冷却幵始温度至 650°C期间， 冷 却速率控制在 15〜50°C/s; 从 650°C至 580°C期间， 冷却持续吋间保持 在 10s及以上。
[权利要求 9] 根据权利要求 8所述精细钢帘线拉拔加工性能优的高碳钢线材的制造 方法， 其特征在于： 从冷却幵始温度至 650°C期间， 所述冷却速率为 2 0〜40。C/s。
[权利要求 10] 根据权利要求 8所述精细钢帘线拉拔加工性能优的高碳钢线材的制造 方法， 其特征在于： 从 650°C至 580°C期间， 所述冷却持续吋间保持在 15s及以上。
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