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WO2015120634A1 - 一种高碳钢线材及其制备方法 - Google Patents

一种高碳钢线材及其制备方法 Download PDF

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Publication number
WO2015120634A1
WO2015120634A1 PCT/CN2014/072186 CN2014072186W WO2015120634A1 WO 2015120634 A1 WO2015120634 A1 WO 2015120634A1 CN 2014072186 W CN2014072186 W CN 2014072186W WO 2015120634 A1 WO2015120634 A1 WO 2015120634A1
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Prior art keywords
steel wire
carbon steel
high carbon
wire rod
cooling
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PCT/CN2014/072186
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English (en)
French (fr)
Inventor
王雷
麻晗
李平
Original Assignee
江苏省沙钢钢铁研究院有限公司
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Application filed by 江苏省沙钢钢铁研究院有限公司 filed Critical 江苏省沙钢钢铁研究院有限公司
Priority to US15/117,072 priority Critical patent/US10316386B2/en
Priority to EP14882598.7A priority patent/EP3109335B1/en
Priority to KR1020167021092A priority patent/KR101860481B1/ko
Publication of WO2015120634A1 publication Critical patent/WO2015120634A1/zh

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    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D9/00Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21CMANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C1/00Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
    • B21C1/02Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/005Continuous casting of metals, i.e. casting in indefinite lengths of wire
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/16Controlling or regulating processes or operations
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C33/00Making ferrous alloys
    • C22C33/04Making ferrous alloys by melting
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/02Ferrous alloys, e.g. steel alloys containing silicon
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/04Ferrous alloys, e.g. steel alloys containing manganese
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/06Ferrous alloys, e.g. steel alloys containing aluminium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C38/00Ferrous alloys, e.g. steel alloys
    • C22C38/18Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32Ferrous alloys, e.g. steel alloys containing chromium with boron
    • CCHEMISTRY; METALLURGY
    • C21METALLURGY OF IRON
    • C21DMODIFYING 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
    • C21D8/00Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys

Definitions

  • the present invention belongs to the field of alloys, and in particular to a high carbon steel wire and a preparation method thereof. Background technique
  • High carbon steel wire can be used to produce high strength prestressed steel wire, steel stranded wire, spring steel wire, steel wire rope and steel cord. These products require high-carbon steel wire to be produced after repeated drawing, and the drawing reduction rate can reach 96%. The high drawing reduction rate inevitably has high requirements on the strength, plasticity, surface quality and purity of high carbon steel.
  • the prestressed steel wire and steel strand in the domestic market are mainly 1860 MPa grade products.
  • the raw materials used are mainly SWRH82B high carbon steel wires with a diameter of l l-13 mm, and the strength is usually between 1130 and 1200 MPa.
  • Prestressed steel strands of 1960 MPa or even 2100 MPa grades have also appeared.
  • the increase in steel strength can reduce the amount of steel used. For example, 2300MPa grade steel strands can be used in comparison with 1860MPa grade strands. About 24%, at the same time, the increase in steel strength can simplify the prestressed structure, reduce construction costs, and have significant economic and social benefits.
  • the vanadium-silicon composite micro-alloyed ultra-high strength wire rod disclosed in Chinese patent document CN103122437A and the preparation method thereof the wire rod comprises C 0.85-0.95%. Si 0.95-1.10%, Mn 0.50-0.60%. Cr 0.20-0.35%. Ti 0.01-0.05%. Al 0.005-0.050%. V 0.11-0.15%, also includes Ni 0.001-0.15%. Cu 0.001-0.25%. B 0.0001-0.005%. Nb 0.01-0.03%. Mo 0.001-0.03% One or several, the balance is iron and impurities.
  • the wire rod has high strength and its tensile strength is above 1370MPa. It can be used to produce 2140MPa grade prestressed steel strands.
  • the technical problem to be solved by the present invention is to provide a high carbon steel wire having a tensile strength of 1530 MPa or more and meeting the preparation requirements of a 2300 MPa grade prestressed steel strand.
  • the invention also provides a preparation method of the high carbon steel wire.
  • the high carbon steel wire of the present invention is calculated by weight percentage and includes the following components:
  • the high carbon steel wire further contains:
  • Nb is one or more of 0.01-0.03%.
  • the high carbon steel wire calculated by weight percentage, comprises the following components: C: 0.92% ; Si: 1.35%; Mn: 0.50%; Cr: 0.26%; V: 0.18%; Ti: 0.07%; The amount is Fe.
  • the high carbon steel wire of the present invention may contain trace amounts of unavoidable impurities during the preparation process, but does not affect the implementation of the present invention and the realization of the technical effects.
  • the preparation method of the high carbon steel wire comprises the following steps:
  • refining adding an alloy material containing one or more of Cr, Si, Mn, Al, Ti, V, B, Mo or Nb, refining is greater than or equal to 40 min;
  • step 4) rolling: keeping the empty coal ratio less than or equal to 0.7 heating, rolling the continuous casting billet obtained in step 3) at a temperature of 900 ° C to 1100 ° C, and the spinning temperature is 830-86 CTC;
  • Cooling Controlled cooling with stimulmo, maintaining a cooling rate of 8-l lK/s before austenite transformation, a cooling rate of 1-2K/S in the later stage of austenite transformation, and a final cooling temperature of more than 500 °C.
  • the degree of superheat is the difference between the casting temperature of the continuous casting and the melting point of the molten steel.
  • the empty coal ratio is the volume ratio of air used to the furnace to blast furnace gas.
  • the metal raw material is a mixture of scrap steel and molten iron.
  • the molten iron water is pre-desulfurized before desulfurization, and the sulfur content in the molten iron is less than 0.005%.
  • Step 2) Specifically: sequentially adding alloy materials containing Cr, Si, Mn, Al, Mo, Nb, Ti, V, refining, maintaining the alkalinity of the refining slag of 2.8-3.0, 15 min before the end of refining, adding the alloy containing B Material, inert gas soft agitation is greater than or equal to 15min.
  • Step 3) The continuous casting is divided into a cold and a second cooling; the cooling is water cooling, the control specific water amount is 4.1-4.5 L/kg ; the second cooling is aerosol cooling, and the control specific water amount is 1.8-2.0 L/ Kg.
  • the rolling in the step 4) includes rough rolling and finish rolling, and the continuous casting slab obtained in the step 3) is first subjected to rough rolling at 1000 ° C to 1100 ° C, and then finish rolling at a temperature of 900-95 CTC.
  • Step 5) The moving speed of the wire before the phase change is 0.8-1.3 m/s, the wind speed of the fan is 30-40 m/s; the moving speed of the wire in the late phase change is 0.6-0.8 m/s, and the wind speed of the fan is 0-10 m/s. .
  • the high carbon steel wire rod is used for preparing 2300 MPa grade prestressed steel wire, 2300 MPa grade prestressed steel strand wire and 7 mm 1960 MPa grade bridge cable galvanized steel wire.
  • Si is a ferrite strengthening element and can increase the strength of ferrite by solid solution strengthening.
  • the enrichment of Si at the ferrite/cementite interface helps to improve the thermal stability of the steel wire during heat treatment.
  • Si can increase the diffusion rate of C in austenite, which is conducive to the homogenization process of heating process C.
  • Si increases the activity of C, makes C and V easier to combine, and promotes the precipitation of VC in ferrite, but Excessive Si can cause decarburization and reduce surface quality.
  • Mn can eliminate or reduce the hot brittleness of steel caused by sulfur, thereby improving the hot workability of steel. Mn can also form a solid solution with Fe to increase the hardness and strength of ferrite and austenite in steel. Meanwhile, Mn is a carbide forming element and can enter a cementite to replace a part of iron atoms. Mn can reduce the critical transition temperature in steel and refine the pearlite, thus improving the strength of pearlitic steel. In addition, the ability of Mn to stabilize austenite structure is second only to Ni, which can significantly improve the quenching of steel. Permeability.
  • Cr is a strong carbide-forming element which is mainly present in steel in the cementite sheet to form alloy cementite by replacement.
  • the addition of Cr improves the stability of austenite and prevents the growth of crystal grains during hot rolling.
  • the addition of Cr causes the continuous cooling transition curve of steel to shift to the right, and the pearlite layer can be refined at the same cooling rate. spacing. Due to the presence of alloy cementite in the pearlite, the addition of Cr helps to improve the thermal stability of the cementite sheet.
  • V and C and N in the steel forms a diffused VNC, which in turn inhibits the growth of austenite grains during hot rolling.
  • V is also easy to form VC particles on the austenite grain boundary, which reduces the content of C element on the grain boundary, which can effectively inhibit the formation of reticulated cementite.
  • V will be in the pearlite during the phase transformation.
  • the precipitation of ferrite in the body acts as a precipitation strengthening effect on the high carbon steel wire rod, which is beneficial to improve the strength of the high carbon steel wire rod.
  • excessive V can cause difficulty in the control of high carbon steel wire.
  • Ti can fix the free nitrogen in the molten steel, avoiding the natural aging effect of the free nitrogen solid solution in the steel, avoiding the increase of the brittleness of the steel and improving the plasticity and toughness of the obtained steel.
  • Mo can significantly improve the hardenability of high carbon steel. At the same time, Mo can reduce the probability of occurrence of grain-like cementite in the grain boundary, and is beneficial to improve the plasticity of the high carbon steel wire rod. But excessive Mo will It will combine with Cr to separate the pearlite and bainite transformation curves, resulting in high carbon steel which is prone to bainite structure during continuous cooling.
  • A1 is a kind of active metal, which is easy to react with oxygen in molten steel to form A1 2 0 3 . It can be used as an important deep deoxidizer in steel to reduce the oxygen content in molten steel and reduce inclusions in molten steel. The purity of molten steel.
  • A1 can be combined with N in molten steel to form A1N, and fine A1N is precipitated in molten steel, which can suppress the growth of austenite grains during the subsequent heating before hot rolling, thereby reducing the austenite grain size.
  • B is easy to segregate at the grain boundary, and can inhibit the nucleation of the pro-eutectoid ferrite on the austenite grain boundary. However, B is easily combined with free nitrogen in the steel to form a brittle precipitate, which makes the wire rod brittle.
  • Nb combines with C and N in steel to form Nb(NC), which inhibits austenite grain growth.
  • Solid solution Nb can prevent grain growth by preventing recrystallization or dynamic recrystallization.
  • the high carbon steel wire of the present invention contains C, Si, Mn, Cr, V, Ti, Fe and impurities, wherein the V content is 0.16-0.20%, and in this range, the obtained high carbon steel wire is full Pearlite structure, the content of sorbite is above 95%, the spacing of pearlite sheets is between 80-100 ⁇ m, the microstructure is relatively uniform, and the addition of V inhibits the formation of reticular cementite, and the mechanical strength is more obvious. Improvement. At the same time, the Si content is maintained at 1.25-1.50%. It has been found through many experiments that when the Si content is above 1.2, the precipitation promoting effect of V is most significant.
  • the thickness of the decarburized layer is controllable, and the activity of C atoms in austenite is improved, and V and C are more easily combined, which significantly promotes the precipitation of V and greatly improves the high carbon steel.
  • the strength of the wire In the high carbon steel wire rod, combined with the addition of Mn, Cr, Ti, and the content control, the obtained high carbon steel wire rod has better mechanical properties, not only has high strength, but the average tensile strength can reach 1560 MPa. At the same time, it has good plasticity, the average shrinkage after shrinkage is 30%, and the elongation after break is 9% or more, which can meet the performance requirements of producing 2300MPa prestressed steel strands.
  • the addition of 0.02-0.08% of Ti can be combined with free N to form a dispersed fine TiN to fix the free nitrogen in the steel. Because the arc in the electric furnace smelting process ionizes the air, The nitrogen content in the molten steel is relatively high, and the free nitrogen solid solution in the steel will cause natural aging and increase the brittleness of the steel. Therefore, the free nitrogen content in the controlled steel is below 50 ppm, and 0.02-0.08% Ti is added. The added Ti fixes free nitrogen to form TiN, and controls the precipitation and growth of TiN by controlling the cooling rate of the slab and the heating temperature before hot rolling, thereby improving the strength of the obtained carbon steel wire.
  • the high carbon steel wire of the present invention further contains one or more of Mo, Al, B, and Nb.
  • Mo can obviously improve the hardenability of high carbon steel and reduce the interlamellar spacing of pearlite. At the same time, Mo can also reduce the probability of occurrence of grain boundary cementite, which is beneficial to improve the plasticity of high carbon steel wire rod.
  • A1 can play the role of deep deoxidation, which is beneficial to improve the purity of molten steel.
  • B can reduce the role of high carbon steel grain boundary ferrite.
  • the dispersion of fine carbides and partially solid solution Nb produced by Nb refines the grains of austenite and improves the strength and plasticity of the wire rod.
  • the high carbon steel wire of the present invention comprises C: 0.92%; Si: 1.35%; Mn: 0.50% ; Cr: 0.26% ; V: 0.18% ; Ti: 0.07% ; Under the ratio, the obtained high carbon steel wire has a tensile strength of 1575 MPa, a shrinkage value of 36% after breaking, and an elongation of 10% after breaking, and has excellent mechanical properties.
  • a method for preparing a high carbon steel wire according to the present invention which comprises hot metal pretreatment, electric furnace smelting, refining, continuous casting, and rolling.
  • controlling the rolling temperature and cooling rate can avoid decarburization and the formation of abnormal structures, and at the same time, the Sorbite ratio is over 95%.
  • the continuous casting process is divided into a cold and a second cold Wherein, the two colds are strongly cooled by the gas mist, and the obtained continuous casting billet has a compact structure and a small degree of microsegregation, which can ensure the uniformity of the rolled material.
  • the molten iron is first desulfurized, and the sulfur content in the molten iron is less than 0.005% to improve the purity of the molten steel, thereby reducing the pressure of desulfurization in the refining process, thereby further reducing the system
  • the inclusion content of the high carbon steel wire is guaranteed to ensure the performance of the wire.
  • the high carbon steel wire rod of the present embodiment has the composition shown in Table 1.
  • the preparation method includes the following: 1) Pre-desulfurization of molten iron: Desulfurization by KR method, and removal of molten molten iron by adding a desulfurizing agent CaO. Sulfur, to a sulfur content of less than 0.005%.
  • Electric furnace smelting Adding metal raw materials to the electric furnace, starting with smelting, using small voltage and current to start arcing, about 1 min, after the current is stabilized, gradually increase the voltage and current, and carry out the well.
  • the smelting process uses slag smelting to strengthen the slag and foaming enthalpy. Slag, avoid nitrogen increase; control end C content is 0.2%, P content is less than 11Oppm, tapping, controlled tapping temperature is 1590 °C, argon stirring pressure is IMPa, and high carbon steel is added when tapping to 1/3 Synthetic slag and 70% of the total amount of Cr, Si, Mn alloy materials; tapping to avoid slag, if there is slag phenomenon, need to carry out slag operation.
  • the metal raw material comprises 18 tons of scrap steel and 82 tons of molten iron;
  • Control superheat is equal to 30 °C, maintain constant speed of 2.50m/min, water cooling for one cold, 4.2L/kg for controlled water, and aerosol cooling for second cold zone, control water ratio is 1.9 L/kg, continuous casting into a billet with a cross section of 140mm X 140mm XI 6m, which can be used as a continuous casting billet;
  • step 5) Rolling: Keep the empty coal ratio less than 0.7.
  • the slab obtained in step 4) is first rough-rolled at 100CTC, and then finished at a temperature of 95CTC.
  • the spinning temperature is 830 °C.
  • Cooling Controlled by Steyr friction, maintaining a cooling rate of 9K/s before austenite transformation, wire running speed is 0.8m/s, wind speed of wind turbine is 30m/s; IK is used in the later stage of austenite transformation /s cooling rate, wire running speed is 0.8m / s, fan wind speed is 10m / s, cooling to 510 ° C.
  • Example 2 The high carbon steel wire of the present embodiment has the composition shown in Table 1, and the preparation method thereof includes the following 1) Pre-desulfurization of molten iron: Desulfurization by KR method, and removal of sulfur from molten molten iron by adding desulfurizing agent CaO to a sulfur content of less than 0.005%.
  • Electric furnace smelting Adding metal raw materials to the electric furnace, starting with smelting, using small voltage and current to start arcing, about 1 min, after the current is stabilized, gradually increase the voltage and current, and carry out the well.
  • the smelting process uses slag smelting to strengthen the slag and foaming enthalpy.
  • control end C content is 0.7%
  • P content is less than 11Oppm
  • tapping control tapping temperature is 161CTC
  • argon stirring pressure is O.lMPa
  • high carbon steel is added when tapping to 1/3 Synthetic slag and 70% of the total amount of Cr, Si, Mn alloy materials; tapping to avoid slag, if there is slag phenomenon, need to carry out slag operation.
  • the metal raw material comprises 30 tons of scrap steel and 70 tons of molten iron;
  • Control superheat is equal to 27 °C, maintain constant speed of 2.60m/min, water cooling for one cold, 4.5L/kg for controlled water, and aerosol cooling for second cold zone, control water ratio is 1.8 L/kg, continuous casting into a billet with a cross section of 140mm X 140mm XI 6m, which can be used as a continuous casting billet;
  • step 5 Rolling: Keep the empty coal ratio less than 0.7 heating, and firstly rough-roll the continuous casting blank obtained in step 4) at 110 CTC, and then finish rolling at a temperature of 90 CTC, and the spinning temperature is 860 °C.
  • Cooling Controlled cooling with Steyr, maintaining llK/s cooling rate before austenite transformation, wire running speed is 0.8m/s, fan wind speed is 30m/s; austenitic phase transformation is 2K later /s cooling rate, wire running speed is 0.7m / s, fan wind speed is 10m / s, cooling to 550 ° C.
  • Example 3 The high carbon steel wire of the present embodiment has the composition shown in Table 1, and the preparation method thereof includes the following Steps:
  • Pre-desulfurization of hot metal Desulfurization by KR method, adding desulfurizer CaO to remove sulfur from molten iron, to a sulfur content of less than 0.005%.
  • Electric furnace smelting Adding metal raw materials to the electric furnace, starting with smelting, using small voltage and current to start arcing, about 1 min, after the current is stabilized, gradually increase the voltage and current, and carry out the well.
  • the smelting process uses slag smelting to strengthen the slag and foaming enthalpy. Slag, avoid nitrogen increase; control end C content is 0.5%, P content is less than 11Oppm, tapping, control tapping temperature is 160CTC, argon stirring pressure is 0.6MPa, and high carbon steel special synthesis is added when tapping to 1/3 70% of the total amount of slag and Cr, Si, Mn alloy materials; tapping to avoid slag, if there is slag phenomenon, need to carry out slag operation.
  • the metal raw material comprises 15 tons of scrap steel and 85 tons of molten iron;
  • Control superheat is equal to 27 °C, maintain constant speed of 2.60m/min, water cooling for one cold, 4.1L/kg for controlled water, and aerosol cooling for second cold zone, control water ratio is 2.0 L/kg, continuous casting into a billet with a cross section of 140mm X 140mm XI 6m, which can be used as a continuous casting billet;
  • step 5 Rolling: Keep the empty coal ratio less than 0.7 heating, and firstly rough-roll the continuous casting slab obtained in step 4) at 105 CTC, and then finish rolling at a temperature of 93 CTC, and the spinning temperature is 840 °C.
  • Cooling Controlled by Steyr friction, maintaining 8K/s cooling rate before austenite transformation, wire running speed is 1.3m/s, fan wind speed is 40m/s; 2K in austenitic phase transformation later /s cooling rate, wire running speed is 0.6m / s, fan wind speed is 5m / s, cooling to 550 ° C.
  • Example 4 The high carbon steel wire of the present embodiment has the composition shown in Table 1, and the preparation method comprises the following steps:
  • Pre-desulfurization of molten iron Desulfurization by KR method, adding desulfurizer CaO to remove sulfur from molten molten iron, to a sulfur content of less than 0.005%;
  • Electric furnace smelting melting metal raw materials, smelting to a C content of 0.2%, P content less than HOppm, at 160CTC, tapping;
  • step 5 rolling: keeping the empty coal ratio equal to 0.5 heating, rolling the continuous casting slab obtained in step 3) at a temperature of 90 CTC, and the spinning temperature is 86 CTC;
  • Cooling The cooling is controlled by Steyr, the cooling speed of l lK/s is maintained before the austenite transformation, and the cooling rate of 2K/s is used in the later stage of austenite transformation, and the final cooling temperature is 540 °C.
  • Examples 5 to 11 High carbon steel wires of Examples 5 to 11 were prepared in the same manner as in Example 1 except that the composition thereof was as shown in Table 1.
  • Embodiment 12 The prestressed steel strand of this embodiment is prepared as follows:
  • Example 1 The high carbon steel wire of Example 1 was subjected to pickling phosphating.
  • the high carbon steel wire is sequentially drawn through 8 molds to obtain a steel wire; the drawing order is ⁇ 13.0 mm ⁇ O 11.4 mm ⁇ 0 10.0 mm— ⁇ 7.98 mm ⁇ 7.27 mm ⁇ 0 6.55 Mm ⁇ 0 5.48mm ⁇ 0 5.36mm ⁇ 0 5.02mm.
  • Embodiment 13 A prestressed steel wire of this embodiment is prepared as follows:
  • the high carbon steel wire is sequentially drawn through 8 molds to obtain a steel wire; the drawing order is ⁇ 13.0 mm ⁇ O 11.4 mm ⁇ 0 10.0 mm— ⁇ 7.98 mm ⁇ 7.27 mm ⁇ 0 6.55 Mm ⁇ 0 5.48mm ⁇ 0 5.36mm ⁇ 0 5.02mm.
  • the high carbon steel wire is sequentially drawn through 9 molds to obtain a steel wire; the drawing order is ⁇ 13.0 mm ⁇ O 11.5 mm ⁇ 0 10.2 mm ⁇ O 9.28 mm ⁇ 8.73 mm ⁇ 0 8.45 Mm ⁇ 0 8.15mm ⁇ 0 7.9mm ⁇ 0 7.4mm ⁇ 0 6.9mm.
  • the wire obtained by drawing is subjected to alkali washing, pickling, water washing, drying, and assist plating, and then hot-dip galvanizing treatment at 450 °C.
  • the hot-dip galvanized steel wire is stabilized at 38 CTC to obtain a galvanized steel wire for the bridge cable.
  • Example 15 The prestressed steel strand of this example was prepared by using the high carbon steel wire prepared in Example 11, and the preparation method was the same as that in Example 12.
  • Comparative Example 1-4 The high carbon steel wire of Comparative Example 1-4, whose composition is shown in Table 1, was prepared in the same manner as in Example 1.
  • Comparative Examples 5-8 The prestressed steel strands of Comparative Examples 5-8 were prepared using the high carbon steel wires prepared in Comparative Examples 1-4, respectively, and were prepared in the same manner as in Example 12. Effect Experimental Example To demonstrate the technical effects of the present invention, the following experiments were conducted on the products prepared in Examples 1-15 and Comparative Examples 1-8.
  • Comparative Example 3 1500 28% 7% 95% Comparative Example 4 1540 23% 7% 95%
  • Comparative Example 4 1540 23% 7% 95%
  • the addition of V and the addition of Si were respectively performed, and the addition amounts of Si in Comparative Examples 3 and 4 were respectively lower than 1.25 and higher than 1.50.
  • Examples 1-11 have superior mechanical properties, and the tensile strength averages 1568 MPa, which has high mechanical strength, and the average shrinkage after fracture is 33%. The average length is 9%, and it has better plasticity.
  • the tensile strength can reach 1575 MPa, the shrinkage after fracture is 36%, and the elongation after fracture is 10%, which has the most ideal mechanical properties.
  • Comparative Examples 1-4 the tensile strengths of Comparative Examples 1 and 2 were lower, and in Comparative Example 3, the tensile strength was only 1500 MPa, and the high carbon steel wire of Comparative Example 4 was decarburized severely and contracted. The rate cannot meet the usage requirements. It can be seen that the higher the content of Si, the more it promotes the precipitation of V and improves the mechanical properties. In the range of 1.25-1.50%, the precipitation promotion effect of V is most desirable.
  • the tensile strength and the maximum total elongation of the steel wire and steel strand are measured.

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Abstract

提供一种高碳钢线材及其制备方法。其中,所述高碳钢线材包括以下成分:C、Si、Mn、Cr、V、Ti及Fe。所述高碳钢线材,具有较为理想的力学性能,不仅具有较高的强度,平均抗拉强度可达1560MPa,同时,具有良好的塑性,平均断后收缩率值为30%,断后伸长率大于等于9%,可满足生产2300MPa的预应力钢绞线的性能要求。

Description

一种高碳钢线材及其制备方法
技术领域 本发明属于合金领域, 具体涉及一种高碳钢线材及其制备方法。 背景技术
高碳钢线材可用于生产高强度预应力钢丝、 钢绞线、 弹簧钢丝、 钢丝 绳及钢帘线等产品。 这些产品需高碳钢线材经过多次的拉拔来生产, 拉拔 减面率最高可以达到 96%。高的拉拔减面率必然对高碳钢材的强度、塑性、 表面质量及纯净度等方面具有较高的要求。
目前, 国内市场的预应力钢丝及钢绞线主要以 1860MPa级产品为主, 其所使用的原材料主要为直径在 l l-13mm的 SWRH82B高碳钢线材, 其强 度通常在 1130〜1200MPa之间。 目前也出现了 1960MPa乃至 2100MPa级 的预应力钢绞线。 在钢铁制造业, 开发高强度的钢材一直是该领域研发的 方向, 钢材强度的提高, 可减少钢材的使用量, 例如, 2300MPa级钢绞线 与 1860MPa级钢绞线相比, 钢材用量可以减少约 24%, 同时, 钢材强度的 提高还可简化预应力结构, 降低施工成本, 具有显著的经济与社会效益。
中国专利文件 CN103122437A公开的钒硅复合微合金化超高强度盘条 及其制备方法,该盘条包括 C 0.85-0.95%. Si 0.95-1.10%、 Mn 0.50-0.60%. Cr 0.20-0.35%. Ti 0.01-0.05%. Al 0.005-0.050%. V 0.11-0.15%, 还包括 Ni 0.001-0.15%. Cu 0.001-0.25%. B 0.0001-0.005%. Nb 0.01-0.03%. Mo 0.001-0.03%中的一种或几种,余量为铁和杂质。上述盘条具有较高的强度, 其抗拉强度在 1370MPa以上, 可用于生产 2140MPa级的预应力钢绞线,但 是, 上述盘条无法满足更高强度预应力的要求, 实现更高强度的预应力钢 绞线的制备仍是合金领域的研究热点。 发明内容 为此, 本发明所要解决的技术问题是提供一种抗拉强度在 1530MPa 以上, 可满足 2300MPa级预应力钢绞线的制备要求的高碳钢线材。 本发明还提供了所述高碳钢线材的制备方法。
本发明的高碳钢线材, 按重量百分比计算, 包括以下成分:
C 0.88-0.94%;
Si 1.25-1.50%;
Mn 0.45-0.55%;
Cr 0.25-0.45%;
V 0.16-0.20%;
Ti 0.02-0.08%; 余量为 Fe。
所述高碳钢线材还含有:
Mo 0.01-0.15%;
A1 0.001-0.10%;
B 0.0005-0.0015%;
Nb 0.01-0.03%中的一种或多种。 优选的,所述高碳钢线材,按重量百分比计算,包括以下成分: C:0.92%; Si: 1.35%; Mn:0.50%; Cr:0.26%; V:0.18%; Ti:0.07%; 余量为 Fe。 需要说明的是,本发明的高碳钢线材在制备过程中可能会含有微量的 不可避免的杂质, 但不影响本发明的实施及技术效果的实现。 所述的高碳钢线材的制备方法, 包括以下步骤:
1 ) 冶炼: 将金属原料熔融, 冶炼至 C含量为 0.2-0.7%, P含量小于 HOppm, 在 1590-161CTC下, 出钢; 所述金属原料中,熔融后的铁水占所述金属原料的总重量的百分比为 70-85%;
2) 精炼: 加入含 Cr、 Si、 Mn、 Al、 Ti、 V、 B、 Mo或 Nb中的一种 或多种的合金材料, 精炼大于或等于 40min;
3 ) 连铸: 控制过热度小于或等于 30°C, 保持 2.50-2.60m/min的恒拉 速, 得连铸坯;
4) 轧制: 保持空煤比小于或等于 0.7加热, 在温度 900°C-1100°C下 对步骤 3 ) 中得到的连铸坯进行轧制, 吐丝温度为 830-86CTC ;
5 ) 冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 8-l lK/s 的冷 却速度, 奥氏体相变后期采用 1-2K/S的冷却速度, 终冷温度大于 500°C。 其中, 所述过热度是连铸浇铸温度与钢液熔点之间的差值。所述空煤 比为加热炉所使用的空气与高炉煤气的体积比。 步骤 1 ) 中, 所述金属原料为废钢与铁水的混合物。 在步骤 1 ) 冶炼前, 先对熔融的铁水进行预脱硫处理, 脱硫至铁水中 硫含量小于 0.005%。
步骤 2) 具体为: 依次加入含 Cr、 Si、 Mn、 Al、 Mo、 Nb、 Ti、 V的 合金材料, 精炼, 保持精炼渣碱度为 2.8-3.0, 精炼结束前 15min, 加入含 B的合金材料, 惰性气体软搅拌大于或者等于 15min。 步骤 3 ) 中连铸分为一冷及二冷; 所述一冷为水冷, 控制比水量为 4.1-4.5L/kg; 所述二冷为气雾冷却, 控制比水量为 1.8-2.0L/kg。 步骤 4) 中所述轧制包括粗轧与精轧, 在 1000°C-1100°C下对步骤 3 ) 中得到的连铸坯先进行粗轧, 再在温度 900-95CTC下精轧。 步骤 5 )所述相变前线材移动速度为 0.8-1.3m/s,风机风速为 30-40m/s; 相变后期线材移动速度为 0.6-0.8m/s, 风机风速为 0-10m/s。 所述的高碳钢线材在制备 2300MPa级预应力钢丝、 2300MPa级预应 力钢绞线及 7mm 的 1960MPa级桥梁缆索镀锌钢丝中的应用。 Si是铁素体强化元素, 能够通过固溶强化提高铁素体的强度。 另外, Si在铁素体 /渗碳体界面的富集有助于提高钢丝在热处理过程中的热稳定 性。 Si可提高 C在奥氏体中的扩散速度, 有利于加热过程 C的均匀化过 程, 同时 Si提高了 C的活性, 使 C与 V更易结合, 进而促进 VC在铁素 体中的析出, 但过多的 Si会引起脱碳, 降低表面质量。
Mn能消除或减弱由于硫所引起的钢的热脆性, 从而改善钢的热加工 性能。 Mn还可与 Fe形成固溶体,提高钢中铁素体和奥氏体的硬度和强度; 同时, Mn是碳化物形成元素, 可进入渗碳体中取代一部分铁原子。 Mn 在钢中可以降低临界转变温度, 起到细化珠光体的作用, 从而提高了珠光 体钢的强度; 此外, Mn稳定奥氏体组织的能力仅次于 Ni, 可以显著地提 高钢的淬透性。
Cr是强碳化物生成元素, 它在钢中主要存在于渗碳体片层中通过置 换作用形成合金渗碳体。 Cr 的添加提高了奥氏体的稳定性, 可以阻止热 轧时晶粒的长大, 另外 Cr的添加使得钢的连续冷却转变曲线右移, 在相 同的冷速下可以细化珠光体片层间距。 由于珠光体中合金渗碳体的存在, Cr的添加有助于提高渗碳体片层的热稳定性。
V与钢中的 C、 N结合可形成弥散析出的 VNC, 进而抑制热轧时奥 氏体晶粒的长大。 V在相变初期还易于在奥氏体晶界上形成 VC颗粒, 降 低晶界上 C元素的含量,从而可以有效的抑制网状渗碳体的产生; 同时 V 在相变过程中会在珠光体中的铁素体间析出,对高碳钢线材起到析出强化 作用, 有利于提高高碳钢线材的强度。 但是, 过高的 V会引起高碳钢线 材组织控制困难。
Ti可固定钢液中的自由氮,避免自由氮固溶于钢中产生的自然时效现 象, 避免由此造成的钢脆性的增加, 提高得到的钢的塑性及韧性。
Mo可以明显地提高高碳钢的淬透性。 同时, Mo可以减少晶界上网 状渗碳体出现的几率, 有利于提高高碳钢盘条的塑性。但是过量的 Mo将 会与 Cr组合作用, 使珠光体与贝氏体转变曲线出现分离, 导致高碳钢在 连续冷却过程中极易出现贝氏体组织。
A1是一种活泼金属, 极易与钢水中的氧作用生成 A1203, 其在钢中可 作为重要的深脱氧剂使用, 降低钢水中的氧含量, 进而降低钢水中的夹杂 物, 提高钢水纯净度。 另外, A1可以与钢水中的 N结合生成 A1N, 细小 的 A1N在钢水中析出, 可以抑制随后热轧前加热过程中奥氏体晶粒的长 大, 进而减小奥氏体晶粒度。
B容易在晶界偏聚, 可以抑制先共析铁素体在奥氏体晶界上形核。但 是, B极易与钢中的自由氮结合形成脆性的析出相,从而使盘条产生脆性。
Nb可与钢中的 C、 N结合形成 Nb(NC), 抑制奥氏体晶粒长大。 固溶 Nb可以通过阻止再结晶或动态再结晶而阻止晶粒的长大。 本发明的上述技术方案, 相比现有技术具有以下优点:
( 1 ) 本发明的高碳钢线材, 含有 C、 Si、 Mn、 Cr、 V、 Ti、 Fe及杂 质, 其中, V含量在 0.16-0.20%, 此范围下, 得到的高碳钢线材为全珠光 体组织, 索氏体含量在 95%以上, 珠光体片层间距在 80-100μ m之间, 组织较为均匀, 且 V 的加入抑制了网状渗碳体的产生, 力学强度得到了 较为明显的提升。 同时, 保持 Si含量为 1.25-1.50%, 经多次实验发现, Si含量在 1.2以上时, 对 V的析出促进作用最为显著。 Si在 1.25-1.50% 的范围内时, 脱碳层厚度可控, 且可提高奥氏体中 C原子的活度, 使 V 与 C更易结合, 显著促进 V的析出, 大幅提高了高碳钢线材的强度。 所述高碳钢线材中, 结合 Mn、 Cr, Ti的添加, 及含量的控制, 使得 到的高碳钢线材具有较为理想的力学性能, 不仅具有较高的强度,平均抗 拉强度可达 1560MPa,同时,具有良好的塑性,平均断后收缩率值为 30%, 断后伸长率大于等于 9%,可满足生产 2300MPa的预应力钢绞线的性能要 求。 其中, 0.02-0.08%的 Ti的加入, 可以与自由 N结合形成弥散细小的 TiN来固定钢中的自由氮。 由于电炉冶炼过程中的电弧会电离空气, 使得 钢液中的氮含量比较高, 而自由氮固溶于钢中会产生自然时效现象, 增加 钢的脆性,因此,控制钢中的自由氮含量在 50ppm以下,并加入 0.02-0.08% 的 Ti, 添加的 Ti固定自由氮, 形成 TiN, 通过控制铸坯冷却速度与热轧 前加热温度来控制 TiN的析出与长大, 提高得到的碳钢线材的强度。
(2)本发明的高碳钢线材, 还含有 Mo、 Al、 B、 Nb中的一种或多种。 Mo可以明显地提高高碳钢的淬透性, 减小珠光体的片层间距, 同时 Mo也 可以减少晶界上网状渗碳体出现的几率, 有利于提高高碳钢盘条的塑性。 A1可起到深脱氧的作用, 有利于提高钢水的纯净度。 B可起到减少高碳钢 晶界铁素体的作用。 Nb产生的弥散析出细小碳化物以及部分固溶 Nb, 可 细化奥氏体的晶粒, 提高盘条的强度与塑性。
(3 ) 本发明的高碳钢线材, 包括 C:0.92%; Si: 1.35%; Mn:0.50%; Cr:0.26%; V:0.18%; Ti:0.07%; 余量为 Fe。 在该配比下, 得到的高碳钢线 材抗拉强度可达 1575MPa, 断后收缩值可达 36%, 断后伸长率可达 10%, 具有优越的力学性能。
(4) 本发明的高碳钢线材的制备方法, 包括铁水预处理、 电炉冶炼、 精炼、 连铸、 轧制。 在生产中, 控制轧制温度及冷却速度, 可避免脱碳及 异常组织的形成, 同时使索氏体化率达到 95%以上。
(5 )本发明的高碳钢线材的制备方法, 由于随着对抗拉强度要求的提 高, 产品的缺陷敏感性随之增加, 本发明的方法, 连铸过程连铸分为一冷 及二冷, 其中, 所述二冷, 采用气雾强冷, 由此得到的连铸坯组织致密、 微观偏析程度小, 可保证轧材的组织均匀性。
(6) 本发明的高碳钢线材的制备方法, 将铁水先进行脱硫, 至铁水中 硫含量小于 0.005%以提高钢水的纯净度, 可减轻精炼过程中脱硫的压力, 进而更好的减少制得的高碳钢线材的夹杂物含量, 保证线材的性能。
具体实施方式
表 1实施例 1-11及对比例 1-4的高碳钢线材的各组分含量
Figure imgf000008_0001
实施例 1
本实施的高碳钢线材, 其成分组成如表 1所示, 其制备方法包括以下 1 ) 铁水预脱硫: 采用 KR法脱硫, 加入脱硫剂 CaO脱除熔融的铁水 的硫, 至硫含量小于 0.005%。
2) 电炉冶炼: 将金属原料加入电炉, 冶炼开始时使用小电压电流起 弧, 约 lmin待电流稳定后逐渐提高电压电流, 进行穿井, 冶炼过程采用 流渣冶炼, 加强换渣, 造泡沬渣, 避免增氮; 控制终点 C含量为 0.2%、 P 含量小于 llOppm,出钢,控制出钢温度为 1590 °C,氩气搅拌压力为 IMPa, 出钢至 1/3时添加高碳钢专用合成渣与含 Cr、 Si、 Mn合金材料的总量的 70%; 出钢避免下渣, 如有下渣现象, 需进行倒渣操作。
其中, 所述金属原料包括废钢 18吨、 铁水 82吨;
3 ) 精炼: 依次加入剩余的含 Cr、 Si合金材料、 含 A1的合金材料、 含 Mo的合金材料、 含 Nb的合金材料、 含 Ti的合金材料及含 V的合金 材料, LF精炼, 控制精炼渣二元碱度为 2.8, (FeO) + (MnO) 1.0%, 精炼至钢液中各成分含量达到表 1中的选定数值; 精炼结束前 15min, 喂 入 SiCa线及 B线, 喂丝后氩气软搅拌 15min, 加入保温剂; 所述保温剂为碳化稻壳。
4) 连铸: 控制过热度等于 30°C, 保持 2.50m/min的恒拉速, 一冷采 用水冷, 控制比水量为 4.2L/kg, 二冷区采用气雾冷却, 控制比水量为 1.9L/kg, 连铸为横截面 140mm X 140mm X I 6m的方坯, 得连铸坯;
5) 轧制: 保持空煤比小于 0.7加热, 在 100CTC下对步骤 4) 中得到 的连铸坯先进行粗轧, 再在温度 95CTC下精轧, 吐丝温度为 830°C。
6) 冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 9K/s的冷却速 度,线材运行速度为 0.8m/s,风机风速为 30m/s;奥氏体相变后期采用 IK/s 的冷却速度, 线材运行速度为 0.8m/s, 风机风速为 10m/s, 降温至 510°C。 实施例 2 本实施的高碳钢线材, 其成分组成如表 1所示, 其制备方法包括以下 1 ) 铁水预脱硫: 采用 KR法脱硫, 加入脱硫剂 CaO脱除熔融的铁水 的硫, 至硫含量小于 0.005%。
2) 电炉冶炼: 将金属原料加入电炉, 冶炼开始时使用小电压电流起 弧, 约 lmin待电流稳定后逐渐提高电压电流, 进行穿井, 冶炼过程采用 流渣冶炼, 加强换渣, 造泡沬渣, 避免增氮; 控制终点 C含量为 0.7%、 P 含量小于 llOppm,出钢,控制出钢温度为 161CTC,氩气搅拌压力为 O.lMPa, 出钢至 1/3时添加高碳钢专用合成渣与含 Cr、 Si、 Mn合金材料的总量的 70%; 出钢避免下渣, 如有下渣现象, 需进行倒渣操作。
其中, 所述金属原料包括废钢 30吨、 铁水 70吨;
3 ) 精炼: 依次加入剩余的含 Cr、 Si合金材料、 含 A1的合金材料、 含 Mo的合金材料、 含 Nb的合金材料、 含 Ti的合金材料及含 V的合金 材料, LF精炼, 控制精炼渣二元碱度为 3.0, (FeO) + (MnO) 1.0%, 精炼至钢液中各成分含量达到表 1中的选定数值; 精炼结束前 15min, 喂 入 SiCa线及 B线, 喂丝后氩气软搅拌 15min, 加入保温剂; 所述保温剂为碳化稻壳。
4) 连铸: 控制过热度等于 27°C, 保持 2.60m/min的恒拉速, 一冷采 用水冷, 控制比水量为 4.5L/kg, 二冷区采用气雾冷却, 控制比水量为 1.8L/kg, 连铸为横截面 140mm X 140mm X I 6m的方坯, 得连铸坯;
5) 轧制: 保持空煤比小于 0.7加热, 在 110CTC下对步骤 4) 中得到 的连铸坯先进行粗轧, 再在温度 90CTC下精轧, 吐丝温度为 860°C。
6) 冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 llK/s的冷却 速度, 线材运行速度为 0.8m/s, 风机风速为 30m/s; 奥氏体相变后期采用 2K/s的冷却速度,线材运行速度为 0.7m/s,风机风速为 10m/s,降温至 550°C。 实施例 3 本实施的高碳钢线材, 其成分组成如表 1所示, 其制备方法包括以下 步骤:
1 ) 铁水预脱硫: 采用 KR法脱硫, 加入脱硫剂 CaO脱除熔融的铁水 的硫, 至硫含量小于 0.005%。
2) 电炉冶炼: 将金属原料加入电炉, 冶炼开始时使用小电压电流起 弧, 约 lmin待电流稳定后逐渐提高电压电流, 进行穿井, 冶炼过程采用 流渣冶炼, 加强换渣, 造泡沬渣, 避免增氮; 控制终点 C含量为 0.5%、 P 含量小于 llOppm,出钢,控制出钢温度为 160CTC,氩气搅拌压力为 0.6MPa, 出钢至 1/3时添加高碳钢专用合成渣与含 Cr、 Si、 Mn合金材料的总量的 70%; 出钢避免下渣, 如有下渣现象, 需进行倒渣操作。 其中, 所述金属原料包括废钢 15吨、 铁水 85吨;
3 ) 精炼: 依次加入剩余的含 Cr、 Si合金材料、 含 A1的合金材料、 含 Mo的合金材料、 含 Nb的合金材料、 含 Ti的合金材料及含 V的合金 材料, LF精炼, 控制精炼渣二元碱度为 2.9, (FeO) + (MnO) 1.0%, 精炼至钢液中各成分含量达到表 1中的选定数值; 精炼结束前 15min, 喂 入 SiCa线及 B线, 喂丝后氩气软搅拌 18min, 加入保温剂; 所述保温剂为碳化稻壳。
4) 连铸: 控制过热度等于 27°C, 保持 2.60m/min的恒拉速, 一冷采 用水冷, 控制比水量为 4.1L/kg, 二冷区采用气雾冷却, 控制比水量为 2.0L/kg, 连铸为横截面 140mm X 140mm X I 6m的方坯, 得连铸坯;
5) 轧制: 保持空煤比小于 0.7加热, 在 105CTC下对步骤 4) 中得到 的连铸坯先进行粗轧, 再在温度 93CTC下精轧, 吐丝温度为 840°C。
6) 冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 8K/s的冷却速 度,线材运行速度为 1.3m/s,风机风速为 40m/s;奥氏体相变后期采用 2K/s 的冷却速度, 线材运行速度为 0.6m/s, 风机风速为 5m/s, 降温至 550°C。 实施例 4 本实施的高碳钢线材, 其成分组成如表 1所示, 其制备方法包括以下 步骤:
1 )铁水预脱硫: 采用 KR法脱硫, 加入脱硫剂 CaO脱除熔融的铁水 的硫, 至硫含量小于 0.005%;
2) 电炉冶炼: 将金属原料熔融, 冶炼至 C含量为 0.2%, P含量小于 HOppm, 在 160CTC下, 出钢;
3 )精炼: 加入含 Cr、 Si、 Mn、 Al、 Ti、 V、 B合金材料,精炼 40min, 精炼渣碱度为控制为 2.8-3.0;
4) 连铸: 控制过热度等于 30°C, 保持 2.50m/min的恒拉速, 得连铸 坯;
5 ) 轧制: 保持空煤比等于 0.5加热, 在温度 90CTC下对步骤 3 ) 中得 到的连铸坯进行轧制, 吐丝温度为 86CTC ;
6)冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 l lK/s的冷却速 度, 奥氏体相变后期采用 2K/s的冷却速度, 终冷温度为 540°C。
实施例 5-11 实施例 5-11的高碳钢线材, 其成分组成如表 1所示, 其制备方法与实 施例 1相同。
实施例 12 本实施例的预应力钢绞线, 其制备方法如下:
1 ) 取实施例 1中的所述高碳钢线材进行酸洗磷化。
2) 将所述高碳钢线材依次通过 8个模具进行冷拔, 得钢丝; 所述拉拔次序依次为 Φ 13.0mm→O 11.4mm→0 10.0mm— Φ 7.98mm →Φ 7.27mm→0 6.55mm→0 5.48mm→0 5.36mm→0 5.02mm。
3 ) 将上述拉拔得到的钢丝进行合股并进行稳定化处理, 稳定化处理 温度为 380 ± 10°C, 即得预应力钢绞线。 实施例 13 本实施例的预应力钢丝, 其制备方法如下:
1 ) 取实施例 2中的所述高碳钢线材进行酸洗磷化。
2) 将所述高碳钢线材依次通过 8个模具进行冷拔, 得钢丝; 所述拉拔次序依次为 Φ 13.0mm→O 11.4mm→0 10.0mm— Φ 7.98mm →Φ 7.27mm→0 6.55mm→0 5.48mm→0 5.36mm→0 5.02mm。
3 ) 将上述拉拔得到的钢丝进行合股并进行稳定化处理, 稳定化处理 温度为 380 ± 10°C, 即得预应力钢丝。 实施例 14 本实施例的桥梁缆索镀锌钢丝, 其制备方法如下:
1 ) 取实施例 2中的所述高碳钢线材进行酸洗磷化。
2) 将所述高碳钢线材依次通过 9个模具进行冷拔, 得钢丝; 所述拉拔次序依次为 Φ 13.0mm→O 11.5mm→0 10.2mm→O 9.28mm →Φ 8.73mm→0 8.45mm→0 8.15mm→0 7.9mm→0 7.4mm→0 6.9mm。
3 )将上述拉拔得到的钢丝依次进行碱洗、 酸洗、 水洗、 干燥、 助镀, 然后在 450°C进行热镀锌处理。将热镀锌后的钢丝在 38CTC进行稳定化处理, 即得桥梁缆索用镀锌钢丝。
实施例 15 本实施例的预应力钢绞线, 采用实施例 11中制备得到的高碳钢线材 进行制备, 其制备方法与实施例 12中的方法相同。 对比例 1-4 对比例 1-4的高碳钢线材, 其成分组成如表 1所示, 其制备方法与实 施例 1相同。 对比例 5-8 对比例 5-8的预应力钢绞线, 分别采用对比例 1-4中制备得到的高碳 钢线材进行制备, 其制备方法与实施例 12中的方法相同。 效果实验例 为说明本发明的技术效果, 对实施例 1-15及对比例 1-8中制备得到的 产品进行以下实验。
1、 对实施例 1-11及对比例 1-4中制备得到的高碳钢线材进行实验:
( 1 ) 实验方法:
1.1力学性能的测定: 按照国标 GB/T228.1-2010进行, 测量所述高碳 钢线材的抗拉强度、 断后收缩率及断后伸长率。
1.2索氏体化率的测定: 采用 YB/T169-2000中的图像仪法进行测量。
(2) 实验结果: 表 2 实施例 1-11及对比例 1-4的高碳钢线材的各指标测试结果
抗拉强度 断后收缩 断后伸长率 索氏体化率
(MPa) 率 (%) (%) (%) 实施例 1 1565 32% 10% 96%
实施例 2 1550 35% 9% 95%
实施例 3 1570 33% 9% 96%
实施例 4 1545 33% 9% 96%
实施例 5 1570 32% 9% 97%
实施例 6 1585 25% 9% 96%
实施例 7 1595 28% 9% 96%
实施例 8 1575 33% 9% 94%
实施例 9 1570 30% 8% 95%
实施例 10 1555 33% 9% 97%
实施例 11 1575 36% 10% 97%
对比例 1 1230 35% 10% 90%
对比例 2 1420 35% 9% 95%
对比例 3 1500 28% 7% 95% 对比例 4 1540 23% 7% 95% 对比例 1与 2中, 分别为未加入 V与未加入 Si, 对比例 3与 4中 Si 的添加量分别为低于 1.25与高于 1.50。 实施例 1-11与对比例 1-4中的高 碳钢线材相比, 具有优越的力学性能, 抗拉强度平均为 1568MPa, 具有较 高的力学强度, 断后收缩率平均为 33%, 断后伸长率平均为 9%, 具有较 良好的塑性, 尤其是实施例 11, 抗拉强度可达 1575MPa, 断后收缩率为 36%, 断后伸长率为 10%, 具有最为理想的力学性能。 与此相比, 对比例 1-4中,对比例 1、2的抗拉强度较低,对比例 3,抗拉强度仅能达到 1500MPa, 对比例 4高碳钢线材脱碳严重, 且面缩率不能满足使用要求。可见, 并不 是 Si的含量越高, 越能促进 V析出, 提升力学性能的。 Si在 1.25-1.50% 的范围内, V的析出促进作用最为理想。
2、 对实施例 12-15及对比例 5-8中制备得到的预应力钢绞线、 预应力 钢丝及桥梁缆索镀锌钢丝进行实验:
( 1 ) 实验方法:
按照国标 GB/T228.1-2010中的方法对待测钢丝、钢绞线的抗拉强度与 最大力总伸长率进行测定。
(2) 实验结果:
表 3实施例 12-15与对比例 5-8的各指标测试实验结果
Figure imgf000015_0001
实施例 12、 13、 15与对比例 5-8中的预应力钢绞线相比, 强度达到了 2300MPa级预应力钢绞线的强度要求,且满足最大总伸长率大于 3.5%的指 标。 对比例 5-7的强度未达到 2300MPa, 而对比例 8的最大力总伸长率未 达到要求。此外,实施例 14中的桥梁缆索镀锌钢丝强度达到了 2015MPa, 最大力总伸长率达到 5.4%, 达到了 7mm桥梁缆索镀锌钢丝的力学性能要 求。 显然, 上述实施例仅仅是为清楚地说明所作的举例, 而并非对实施方 式的限定。 对于所属领域的普通技术人员来说, 在上述说明的基础上还可 以做出其它不同形式的变化或变动。 这里无需也无法对所有的实施方式予 以穷举。 而由此所引伸出的显而易见的变化或变动仍处于本发明创造的保 护范围之中。

Claims

权 利 要 求 书
1、一种高碳钢线材,其特征在于,按重量百分比计算,包括以下成分: C 0.88-0.94%;
Si 1.25-1.50%;
Mn 0.45-0.55%;
Cr 0.25-0.45%;
V 0.16-0.20%;
Ti 0.02-0.08%;
余量为 Fe。
2、 根据权利要求 1所述的高碳钢线材, 其特征在于, 还含有:
Mo 0.01-0.15%;
A1 0.001-0.10%;
B 0.0005-0.0015%;
Nb 0.01-0.03%中的一种或多种。
3、 根据权利要求 1或 2所述的高碳钢线材, 其特征在于, 按重量百分比 计算,包括以下成分: C:0.92%; Si: 1.35%; Mn:0.50%; Cr:0.26%; V:0.18%; Ti:0.07%; 余量为 Fe。
4、 根据权利要求 1-3任一所述的高碳钢线材的制备方法, 其特征在于, 包括以下步骤:
1 ) 冶炼: 将金属原料熔融, 冶炼至 C含量为 0.2-0.7%, P含量小于 HOppm, 在 1590-1610°C下, 出钢; 所述金属原料中,熔融后的铁水占所述金属原料的总重量的百分比为 70-85%; 2) 精炼: 加入含 Cr、 Si、 Mn、 Al、 Ti、 V、 B、 Mo或 Nb中的一种 或多种的合金材料, 精炼大于或等于 40min;
3 ) 连铸: 控制过热度小于或等于 30°C, 保持 2.50-2.60m/min的恒拉 速, 得连铸坯;
4) 轧制: 保持空煤比小于或等于 0.7加热, 在温度 900°C-1100°C下 对步骤 3 ) 中得到的连铸坯进行轧制, 吐丝温度为 830-860 °C ;
5 ) 冷却: 采用斯太尔摩控制冷却, 奥氏体相变前保持 8-l lK/s 的冷 却速度, 奥氏体相变后期采用 1-2K/S的冷却速度, 终冷温度大于 500°C。
5、根据权利要求 4所述的高碳钢线材的制备方法,其特征在于:步骤 1 ) 中, 所述金属原料为废钢与铁水的混合物。
6、 根据权利要求 4或 5所述的高碳钢线材的制备方法, 其特征在于: 在 步骤 1 ) 冶炼前, 先对熔融的铁水进行预脱硫处理, 脱硫至铁水中硫含量 小于 0.005%。
7、根据权利要求 4-6中任一所述的高碳钢线材的制备方法,其特征在于, 步骤 2) 具体为: 依次加入含 Cr、 Si、 Mn、 Al、 Mo、 Nb、 Ti、 V的合金 材料, 精炼, 保持精炼渣碱度为 2.8-3.0, 精炼结束前 15min, 加入含 B的 合金材料, 惰性气体软搅拌大于或者等于 15min。
8、根据权利要求 4-7中任一所述的高碳钢线材的制备方法,其特征在于, 步骤 3 ) 中连铸分为一冷及二冷; 所述一冷为水冷, 控制比水量为 4.1-4.5L/kg; 所述二冷为气雾冷却, 控制比水量为 1.8-2.0L/kg。
9、根据权利要求 4-8中任一所述的高碳钢线材的制备方法,其特征在于, 步骤 4) 中所述轧制包括粗轧与精轧, 在 1000°C-1100°C下对步骤 3 )中得 到的连铸坯先进行粗轧, 再在温度 900-95CTC下精轧。
10、权利要求 1-3中任一所述的高碳钢线材在制备 2300MPa级预应力钢丝、 2300MPa级预应力钢绞线及 1960MPa级桥梁缆索镀锌钢丝中的应用。
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