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 PDFInfo
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- 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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- steel wire
- carbon steel
- high carbon
- wire rod
- cooling
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- 229910000677 High-carbon steel Inorganic materials 0.000 title claims abstract description 73
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 79
- 239000010959 steel Substances 0.000 claims abstract description 79
- 229910052742 iron Inorganic materials 0.000 claims abstract description 21
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 14
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 10
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims description 50
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 45
- 239000000956 alloy Substances 0.000 claims description 32
- 238000007670 refining Methods 0.000 claims description 30
- 238000009749 continuous casting Methods 0.000 claims description 27
- 239000002893 slag Substances 0.000 claims description 27
- 238000000034 method Methods 0.000 claims description 24
- 229910001566 austenite Inorganic materials 0.000 claims description 22
- 238000003723 Smelting Methods 0.000 claims description 20
- 239000002184 metal Substances 0.000 claims description 20
- 229910052751 metal Inorganic materials 0.000 claims description 20
- 238000005096 rolling process Methods 0.000 claims description 20
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 17
- 239000002994 raw material Substances 0.000 claims description 16
- 230000009466 transformation Effects 0.000 claims description 15
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 12
- 229910052717 sulfur Inorganic materials 0.000 claims description 12
- 239000011593 sulfur Substances 0.000 claims description 12
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 8
- 239000008397 galvanized steel Substances 0.000 claims description 8
- 239000000203 mixture Substances 0.000 claims description 8
- 239000003245 coal Substances 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 6
- 238000009987 spinning Methods 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 238000003756 stirring Methods 0.000 claims description 4
- 229910052796 boron Inorganic materials 0.000 claims description 3
- 239000011261 inert gas Substances 0.000 claims description 2
- 239000003595 mist Substances 0.000 claims description 2
- 241001062472 Stokellia anisodon Species 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 230000000052 comparative effect Effects 0.000 description 25
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 22
- 238000010079 rubber tapping Methods 0.000 description 14
- 229910052757 nitrogen Inorganic materials 0.000 description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 12
- 229910001567 cementite Inorganic materials 0.000 description 10
- 238000006477 desulfuration reaction Methods 0.000 description 10
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 10
- 239000003795 chemical substances by application Substances 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 8
- 229910001562 pearlite Inorganic materials 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- 229910000859 α-Fe Inorganic materials 0.000 description 8
- 235000013339 cereals Nutrition 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 230000008569 process Effects 0.000 description 7
- 229910052786 argon Inorganic materials 0.000 description 6
- 230000023556 desulfurization Effects 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 229910052698 phosphorus Inorganic materials 0.000 description 5
- 239000000443 aerosol Substances 0.000 description 4
- 238000013019 agitation Methods 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 238000005554 pickling Methods 0.000 description 4
- 239000000047 product Substances 0.000 description 4
- 229910000914 Mn alloy Inorganic materials 0.000 description 3
- 241000209094 Oryza Species 0.000 description 3
- 235000007164 Oryza sativa Nutrition 0.000 description 3
- 229910000676 Si alloy Inorganic materials 0.000 description 3
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 238000005187 foaming Methods 0.000 description 3
- 239000010903 husk Substances 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 235000009566 rice Nutrition 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical compound OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 description 2
- MKYBYDHXWVHEJW-UHFFFAOYSA-N N-[1-oxo-1-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propan-2-yl]-2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidine-5-carboxamide Chemical compound O=C(C(C)NC(=O)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F)N1CC2=C(CC1)NN=N2 MKYBYDHXWVHEJW-UHFFFAOYSA-N 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 229910001563 bainite Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 230000003009 desulfurizing effect Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 238000005406 washing Methods 0.000 description 2
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 101001012040 Pseudomonas aeruginosa (strain ATCC 15692 / DSM 22644 / CIP 104116 / JCM 14847 / LMG 12228 / 1C / PRS 101 / PAO1) Immunomodulating metalloprotease Proteins 0.000 description 1
- 229910000639 Spring steel Inorganic materials 0.000 description 1
- MANBDHUBXBMZNV-UHFFFAOYSA-N [V]=[Si] Chemical compound [V]=[Si] MANBDHUBXBMZNV-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- 239000003513 alkali Substances 0.000 description 1
- 125000004432 carbon atom Chemical group C* 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 238000007747 plating Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000003786 synthesis reaction Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
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
- 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
- C21D9/525—Heat 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C1/00—Manufacture of metal sheets, metal wire, metal rods, metal tubes by drawing
- B21C1/02—Drawing metal wire or like flexible metallic material by drawing machines or apparatus in which the drawing action is effected by drums
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/005—Continuous casting of metals, i.e. casting in indefinite lengths of wire
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/16—Controlling or regulating processes or operations
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- 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
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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US15/117,072 US10316386B2 (en) | 2014-02-11 | 2014-02-18 | High-carbon steel wire rod and preparation method therefor |
EP14882598.7A EP3109335B1 (en) | 2014-02-11 | 2014-02-18 | High-carbon steel wire rod and preparation method therefor |
KR1020167021092A KR101860481B1 (ko) | 2014-02-11 | 2014-02-18 | 고탄소 강선재 및 그 제조 방법 |
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CN114653765B (zh) * | 2022-03-31 | 2024-03-22 | 宣化钢铁集团有限责任公司 | 一种1860Mpa级钢绞线的生产方法 |
CN115341134A (zh) * | 2022-09-02 | 2022-11-15 | 南京钢铁股份有限公司 | 一种高含硫含铝齿条用线材盘条生产方法 |
CN116875874A (zh) * | 2023-07-10 | 2023-10-13 | 辛集市澳森特钢集团有限公司 | 8.8级易热处理紧固件用钢的生产方法 |
CN116875874B (zh) * | 2023-07-10 | 2023-12-26 | 辛集市澳森特钢集团有限公司 | 8.8级易热处理紧固件用钢的生产方法 |
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EP3109335B1 (en) | 2019-07-31 |
KR20160105854A (ko) | 2016-09-07 |
EP3109335A4 (en) | 2017-10-04 |
US20170175221A1 (en) | 2017-06-22 |
CN103805861B (zh) | 2016-06-01 |
EP3109335A1 (en) | 2016-12-28 |
US10316386B2 (en) | 2019-06-11 |
CN103805861A (zh) | 2014-05-21 |
KR101860481B1 (ko) | 2018-05-23 |
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