CN111254351B - High-performance hot-rolled wear-resistant steel sheet and production method thereof - Google Patents
High-performance hot-rolled wear-resistant steel sheet and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 122
- 239000010959 steel Substances 0.000 title claims abstract description 122
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000010438 heat treatment Methods 0.000 claims abstract description 21
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 10
- 239000000126 substance Substances 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims description 45
- 238000010583 slow cooling Methods 0.000 claims description 19
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 15
- 238000000034 method Methods 0.000 claims description 15
- 238000009749 continuous casting Methods 0.000 claims description 14
- 238000001816 cooling Methods 0.000 claims description 12
- 238000003723 Smelting Methods 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 7
- 239000000463 material Substances 0.000 claims description 6
- 238000007670 refining Methods 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 238000003756 stirring Methods 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 16
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- 238000005496 tempering Methods 0.000 abstract description 10
- 238000005260 corrosion Methods 0.000 abstract description 8
- 230000007797 corrosion Effects 0.000 abstract description 8
- 239000000203 mixture Substances 0.000 abstract description 7
- 239000010936 titanium Substances 0.000 description 19
- 239000011651 chromium Substances 0.000 description 13
- 229910001566 austenite Inorganic materials 0.000 description 10
- 238000005098 hot rolling Methods 0.000 description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 8
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- 230000000171 quenching effect Effects 0.000 description 8
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- 229910000746 Structural steel Inorganic materials 0.000 description 5
- 230000002401 inhibitory effect Effects 0.000 description 5
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 229910000734 martensite Inorganic materials 0.000 description 3
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- 241001062472 Stokellia anisodon Species 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000007664 blowing Methods 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
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- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000521 B alloy Inorganic materials 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910015372 FeAl Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000742 Microalloyed steel Inorganic materials 0.000 description 1
- 229910001182 Mo alloy Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 150000001768 cations Chemical class 0.000 description 1
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- 239000010955 niobium Substances 0.000 description 1
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- 150000002830 nitrogen compounds Chemical class 0.000 description 1
- 229910001562 pearlite Inorganic materials 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
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- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C22C38/04—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
- C22C38/26—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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
A high-performance hot-rolled wear-resistant steel sheet and a production method thereof are disclosed, wherein the steel comprises the following chemical components in percentage by weight: 0.15 to 0.20 percent of C, 0.9 to 1.2 percent of Si, 0.5 to 0.7 percent of Mn, 0.5 to 0.7 percent of Al, 0.8 to 1.2 percent of Cr0.02 to 0.04 percent of Nb0.010 to 0.020 percent of Ti, less than or equal to 1.7 percent of Al and Si, and the balance of Fe and inevitable impurities; p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, N is less than or equal to 0.0040 percent, H is less than or equal to 0.00015 percent, and O is less than or equal to 0.0020 percent. The high-strength hot-rolled wear-resistant steel plate with the thickness of 3-8mm is a product of the invention, and the surface hardness of the steel plate is more than HB 370; -20 ℃ low temperature toughness of more than 30J; tempering heat treatment is not needed; the composition is simple, and precious alloy is not contained; has good formability and corrosion resistance.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a high-performance hot-rolled wear-resistant steel sheet and a production method thereof, which can be used for manufacturing wear-resistant spare parts of engineering machinery such as mining vehicles, dump trucks, muck vehicles, concrete mixer trucks and the like.
Background
The high-performance wear-resistant steel sheet is widely applied to the fields of mining vehicles, dump trucks, muck vehicles, concrete mixer trucks and the like, and the thin-specification wear-resistant steel sheet can reduce the dead weight of the vehicle body and the like, increase the load capacity of the vehicle, greatly prolong the service life of the vehicle box body and the like, delay the overhaul period, save energy, reduce consumption, reduce environmental pollution and save resources. Therefore, in recent years, the amount of thin gauge (3 to 8 mm) high performance wear resistant steel sheets used has also increased year by year.
On one hand, the high-performance wear-resistant thin steel plate is required to have good processing performance and can meet the requirements of cold forming and welding processes of complex structures; on the other hand, the wear-resistant steel plate is required to have enough hardness and corrosion resistance so as to obtain good wear resistance under complex working conditions.
The common low-alloy wear-resistant steel medium plate is generally produced by quenching and low-temperature tempering, and the structure is low-carbon tempered martensite. However, when the thin wear-resistant steel plate, particularly the wear-resistant steel plate with the thickness of less than 8mm, is quenched, the plate shape is difficult to control and easy to deform. And because the wear-resistant steel sheet has high strength after heat treatment and is restricted by low tempering temperature and short tempering time, the internal stress of the steel sheet is large, and the steel sheet is difficult to flatten and cut. Therefore, the production difficulty of the thin-specification wear-resistant steel plate is high, and the production and application of the domestic high-performance thin-specification wear-resistant steel plate are limited to a certain extent.
The production technology of high-performance thin-specification wear-resistant steel plates at home and abroad is disclosed, for example:
1. chinese patent document CN201410807637.1 discloses 'a wear-resistant hot-rolled thin steel plate with good processing performance and a manufacturing method thereof', which solves the technical problems of poor bending performance, poor welding performance and incapability of meeting the wear resistance requirements under the working conditions of wet medium and dry medium existing in the existing hot-rolled wear-resistant steel plate. The invention provides a wear-resistant hot-rolled thin steel plate with good processing performance, which comprises the following chemical components in percentage by weight: 0.17-0.23% of C, Si: 0.05-0.40 percent of Mn, 1.20-1.80 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.015 percent of S, 0.015-0.050 percent of Al, 0.10-0.45 percent of Ti, Cu: 0.15 to 0.28 percent, and the balance of iron and inevitable impurities. The slurry conveying device can be used in the industries of engineering machinery, dump trucks, slurry conveying pipelines and the like. The invention also provides a manufacturing method of the wear-resistant steel plate, wherein the continuous casting plate blank is heated at 1220-1260 ℃ for 200-280 min and then is subjected to hot rolling, wherein the temperature rise speed of the continuous casting plate blank in the temperature range of 1100-1200 ℃ is 150 ℃/h; the hot rolling is a two-stage rolling process, the rough rolling is 6-pass continuous rolling, the rolling is carried out at the temperature above the austenite recrystallization temperature, and the finish temperature of the rough rolling is 1020-1070 ℃; the finish rolling is 7-pass continuous rolling, the rolling is carried out in an austenite non-recrystallization temperature region, the finish rolling temperature is 820-860 ℃, the finish rolling reduction rate is more than 75%, and the coiling temperature is 500-600 ℃. The invention relates to a wear-resistant hot-rolled thin steel plate, the structure of which is fine-grain blocky ferrite, granular bainite and a small amount of pearlite, and the grain size of the structure is 10-12 grades. The yield strength of a hot-rolled steel plate with the thickness of 2-8 mm is more than or equal to 450MPa, the tensile strength is more than or equal to 550MPa, the elongation after fracture is more than or equal to 24 percent, the d-1 a is qualified in a 180-degree bending test, the hardness HBW is 180-200, and the impact energy at 0 ℃ is more than or equal to 80J. The wear-resistant hot-rolled thin steel plate under the wet medium condition has the wear resistance 1.6-2.0 times that of a common Q345 hot-rolled steel plate and 1.4-1.8 times that of a high-strength hot-rolled structural steel S700 steel plate; the wear-resistant hot-rolled thin steel plate under the dry medium condition has the wear resistance 1.5-1.8 times that of a common Q345 hot-rolled steel plate and 1.3-1.6 times that of a high-strength hot-rolled structural steel S700 steel plate. The steel plate prepared by the method has good machining performance, and the hardness can reach HBW 180-200. The steel has good forming performance, but has lower hardness, high Ti content and difficult smelting and continuous casting; and can only meet the requirement of impact energy at 0 ℃ and cannot adapt to the use requirement of cold regions.
2. Chinese patent document CN107217202A discloses 'wear-resistant steel with Brinell hardness of 500 grade and manufacturing method thereof', which comprises the following chemical components by mass percent: 0.25-0.28% of C, 0.22-0.28% of Si, 1.15-1.24% of Mn, less than or equal to 0.01% of P, less than or equal to 0.005% of S, 0.2-0.25% of Cr, 0.01-0.015% of Cu, 0.03-0.05% of Al, 0.04-0.045% of Ni, 0.01-0.02% of Mo, 0.03-0.04% of Ti, 0.007-0.018% of V, less than or equal to 0.004% of B, and the balance of iron and inevitable impurities. The invention provides a manufacturing method of a wear-resistant steel sheet with Brinell hardness of 500. The steel plate has excellent wear resistance and higher toughness, and the surface of the steel plate has uniform compressive stress, so that the wear resistance and the fatigue resistance of the steel plate are enhanced.
3. Chinese patent document CN107099731A discloses 'a method for producing thin-gauge high-Ti wear-resistant steel NM360 by on-line quenching', which comprises the following components (wt%): 0.12 to 0.20 wt% of C, 0.2 to 0.4 wt% of Si, 0.75 to 1.5 wt% of Mn, 0.15 to 0.20 wt% of Mo, 0.30 to 0.50 wt% of Cr, 0.03 to 0.06 wt% of Nb, 0.1 to 0.15 wt% of Ti, 0.0005 to 0.0010 wt% of B, 0.015 wt% of P, 0.010 wt% of S, and the balance of Fe and inevitable impurities; in the patent, micro-Mo, Cr, Nb, Ti and B alloys are selected for microalloying, and the microstructure is controlled by controlling ultra-fast cooling and quenching after rolling, so that the performance strengthening effect of the alloy is fully exerted, and the addition amount of the alloy and the use amount of the precious alloy are reduced; the preparation process comprises the following steps: smelting and continuously casting into a blank; soaking; rolling; laminar cooling; and (4) coiling. The yield strength (ReL) of the hot-rolled structural steel sheet is more than or equal to 700MPa, the tensile strength (Rm) of the hot-rolled structural steel sheet is more than or equal to 750MPa, the wear resistance of the hot-rolled structural steel sheet is good, the hot steel sheet can be used for replacing cold steel, the thin steel sheet can be used for replacing thick steel sheet, and the requirement of high-strength steel for engineering structures can be met. The off-line quenching and tempering process of the traditional wear-resistant steel after hot rolling is simplified, the process flow is shortened, the alloy addition is reduced, the hardenability of the steel plate after direct ultra-fast cooling after rolling is increased by 1.4-1.5 times compared with the traditional reheating and quenching process, and the strength and toughness ratio of the steel is improved. The alloy has low hardness, contains more precious alloy Mo and has high cost; and the Ti content is higher, and the smelting and continuous casting difficulty is higher.
4. Patent document CN200880016192.8 discloses a wear-resistant steel sheet having excellent workability, which is characterized by containing, in mass%: c: 0.05 to 0.35%, Si: 0.05 to 1.0%, Mn: 0.1 to 2.0%, Ti: 0.1-1.2%, Al: 0.1% or less, further containing Cu: 0.1 to 1.0%, Ni: 0.1-2.0%, Cr: 0.1 to 1.0%, Mo: 0.05-1.0%, W: 0.05-1.0%, B: 0.0003 to 0.0030% of 1 or more species, the balance being Fe and unavoidable impurities. The production method comprises hot rolling the steel sheet having the above composition, and cooling to 400 ℃ or lower at a cooling rate of 2 ℃/s or lower. The rolling reduction at 920 ℃ or lower in hot rolling is 30% or more, and the rolling completion temperature is 900 ℃ or lower. The wear-resistant steel sheet of the present invention does not require heat treatment after hot rolling, can be used for various steel sheets for various uses requiring bending work in a hot rolled state, and has a Tensile Strength (TS) < 800MPa and a Yield Strength (YS) < 600MPa, and has excellent impact wear properties. The steel has low strength, high alloy contents of Cu, Ni, Mo, W and the like, high cost and difficult smelting and continuous casting of high Ti steel.
5. Influence of hot rolling temperature system on performance of high-strength hot-rolled wear-resistant coiled plate
[ meeting paper ] Thangwen, Zhanghan modest, Jiangjinzhu, 2006-second national Baogang academic annual meeting
The influence of hot rolling processes such as soaking temperature, finishing temperature, coiling temperature and the like on the structure and the performance of the Ti-containing low-carbon microalloyed steel is researched in a laboratory. The method is high-Ti high-strength steel, has low hardness and is difficult to smelt and continuously cast.
6. Research on plate shape control process of thin-specification wear-resistant steel plate XCHD500
[ journal articles ] Wang Xiao Shuang, Deng Yunwei, Wang Xiiaoshuang, Deng Yunfei- "Wide and Thick plates" [ 6 th 2014;
aiming at the problem of severe buckling at the initial stage of producing a wear-resistant steel plate XCHD500 with the thickness of 5mm by a 3500mm steckel mill, the plate shape of the wear-resistant steel plate is obviously improved by optimizing rolling equipment and process parameters of the Xingcheng special steel, and good plate shape conditions are created for subsequent heat treatment, so that the finally delivered steel plate meets the flatness requirement, and the Xingcheng special steel reaches the domestic advanced level in the aspect of controlling the flatness of the wear-resistant steel plate. The production process comprises the steps of off-line quenching and tempering after hot rolling.
7. 1150 MPa-level ultrahigh-strength hot-rolled wear-resistant steel structure and performance research
The conference paper Tang Wen Jun, Jiangjingzhu, Xudinghua, 2006 + 2006 national academic annual meeting of low alloy steel and microalloy non-quenched and tempered steel;
the ultrahigh-strength wear-resistant hot rolled strip with the tensile strength of 1150MPa is successfully trial-produced in a Bao steel 2050 hot continuous rolling unit, and typical mechanical properties of a 3mm thick coil plate in a rolling state comprise yield strength of 825MPa, tensile strength of 1165MPa, elongation of 14 percent and impact energy of 6.8J at 40 ℃. The method is V and Ti non-quenched and tempered steel, has high cost and is difficult to smelt and continuously cast. .
8. Development of 500CX high-strength steel plate for dumper box
[ academic paper ] love, 2014-northeast university: metallurgy engineering;
the technological parameters of steel making, refining, continuous casting and steel rolling of the 500CX high-strength wagon box plate produced by the general steel are researched, and meanwhile, the development technology of the 500CX high-strength steel plate for the wagon box of the general steel production dumper is deeply researched by combining the production technology and the production equipment of the general steel.
The yield strength ReL of the produced 500CX high-strength car trunk plate is more than or equal to 500MPa, the tensile strength Rm is 550-700 MPa, the cold bending (the width b of the sample is 35mm, the bending core diameter d is 3.0a (sample thickness)) is qualified, the impact work AK at normal temperature is 90-140J, and the components and the performance meet the requirements of products. The product prepared by the method has low strength and poor wear resistance.
As can be seen from the above-disclosed prior art, the existing thin gauge wear resistant steel sheet has the following disadvantages:
1. the heat treatment process is complex, and off-line quenching and tempering are required;
2. 0.1 to 0.5 percent of Ti is contained, and smelting and continuous casting are difficult;
3. hardness lower than HB 370;
4. the low-temperature toughness can not meet the requirement of cold areas at-20 ℃.
Disclosure of Invention
The invention provides a high-performance hot-rolled wear-resistant steel sheet and a production method thereof, which can be used for producing a high-strength hot-rolled wear-resistant steel plate with the thickness of 3-8mm, wherein the surface hardness of the steel plate is more than HB 370; -20 ℃ low temperature toughness of more than 30J; tempering heat treatment is not needed; the composition is simple, and precious alloy is not contained; has good formability and corrosion resistance.
In order to achieve the purpose, the invention adopts the following technical scheme:
a high-performance hot-rolled wear-resistant steel sheet comprises the following chemical components in percentage by weight: 0.15 to 0.20 percent of C, 0.9 to 1.2 percent of Si, 0.5 to 0.7 percent of Mn, 0.5 to 0.7 percent of Al, 0.8 to 1.2 percent of Cr, 0.02 to 0.04 percent of Nb, 0.010 to 0.020 percent of Ti, less than or equal to 1.7 percent of Al and Si, and the balance of Fe and inevitable impurities; impurity element control in steel: p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, N is less than or equal to 0.0040 percent, H is less than or equal to 0.00015 percent, and O is less than or equal to 0.0020 percent.
The reason for designing the elements of the invention is as follows:
c: in order to ensure high strength of the steel plate and the hardness of HB370 or above, the equivalent carbon content is required to ensure, the hardness of the steel plate is correspondingly increased along with the increase of the carbon content in a certain range, and simultaneously, a certain carbon content can form carbide precipitation with Cr to increase the wear resistance. If the carbon content is too high, the plasticity and the toughness are reduced, the welding performance is reduced, and in order to ensure that the steel plate has high surface hardness, good welding performance, forming performance and low-temperature toughness, the content of C is controlled to be 0.15-0.20 percent;
si: the steel plate is a non-carbide forming element, mainly has the effects of inhibiting carbide precipitation, improving the shaping of the steel plate and simultaneously playing the roles of solid solution strengthening and deoxidation, but excessive Si can reduce the welding performance and influence the toughness, so the content of Si is controlled to be 0.9-1.2 percent;
mn: the main effect is solid solution strengthening, when the content is more than 0.5%, the supersaturation degree of carbon in martensite can be improved, the improvement of strength and hardness is facilitated, the cost is low, but when the content is more than 0.7, center segregation is easy to form, and when the content of the carbon in the center is higher, the center of a plate blank tends to crack easily; therefore, the Mn content in the invention is controlled to be 0.5 to 0.7 percent
Nb: the steel is a strong carbon and nitrogen compound forming element, and mainly has the main functions of inhibiting the growth of crystal grains during heating by forming fine carbonitride in the steel and has a certain precipitation strengthening function during curling; nb is added to the steel to increase the recrystallization temperature of the steel sheet by inhibiting the austenite grain boundary motion. A proper amount of Nb is added into the steel plate, and when the steel plate is austenitized at high temperature, the undissolved NbC plays a role in nailing and rolling austenite grain boundaries, thereby preventing the austenite grain boundaries from being coarsened excessively. Nb dissolved in austenite inhibits austenite recrystallization in the controlled rolling process, and refines austenite grains. However, if the Nb content is too high, coarse NbC is formed, which affects the mechanical properties of the steel sheet. Therefore, the addition amount of Nb in the invention is 0.02% to 0.04%.
Ti: compared with other alloy elements, the alloy is low in price, can form compounds with nitrogen, carbon and sulfur, forms fine titanium carbonitride in steel, can effectively inhibit the growth of crystal grains during heating, and has higher forming temperature of the compounds of titanium and nitrogen. Therefore, the titanium is added in the amount of more than or equal to 0.01 percent, and when the content is too high (more than 0.02 percent), too much coarse TiN is formed in the steel, so that the low-temperature toughness and the cold bending property of the steel plate are reduced, therefore, the adding amount of the Ti is controlled to be 0.010 to 0.020 percent, and the [ N ] is controlled to be less than or equal to 0.0040 percent, so that the formation of too much TiN is avoided.
Cr: the surface passivation of the steel can be promoted, and with the increase of the Cr content, the passivation film which tends to be stable can obviously reduce the corrosion rate of the steel and improve the corrosion resistance of the steel; in addition, Cr can reduce the critical cooling speed, improve the hardenability of the steel plate and is beneficial to forming a martensite structure. Chromium is a strong carbide forming element, can form a plurality of carbides in steel, and improves the strength and hardness of the steel plate after being curled at the temperature of 300-400 ℃, thereby improving the wear resistance. When the Cr content is more than 0.8%, the strengthening and corrosion resistance effects are obvious, and the weldability is reduced due to excessive addition of Cr, so that the invention controls the Cr: 0.8 to 1.2 percent.
Al: non-carbide forming element, which is mainly used for inhibiting carbide precipitation, improving low-temperature toughness and shaping of the steel plate, simultaneously playing a role in solid solution strengthening and deoxidation, and Al also has the function of improving corrosion resistance, and can be used as spinel oxide (Fe) of a rust layer304) In the formation of stable spinel complex oxides (FeAl)204) The rust layer is made cation-selective and the invasion of chloride ions is suppressed. But the content exceeding 0.7 increases the risk of clogging of the continuous casting nozzle. The invention therefore controls Al: 0.5 to 0.7 percent.
Because Al and Si have the function of jointly promoting and inhibiting the precipitation of carbides, and the welding performance is prevented from being influenced by excessive addition of alloy elements, the Al + Si is controlled to be less than or equal to 1.7 percent.
The low-alloy high-strength wear-resistant steel plate is produced by adopting a process of on-line or off-line quenching and off-line low-temperature tempering, and the steel plate has the characteristics that the hardness of more than 370 Brinell hardness and good toughness can be achieved by air cooling after hot rolling and curling without carrying out the heat treatment.
The thickness of the finished steel plate is 3-8mm, the surface hardness is more than HB370, and the low-temperature toughness at-20 ℃ is more than 30J.
A production method of a high-performance hot-rolled wear-resistant steel sheet comprises the technical processes of molten iron pretreatment, converter smelting, refining, slab continuous casting, casting blank slow cooling, heating, rolling, laminar cooling, coiling and cover feeding slow cooling;
carrying out molten iron pretreatment, smelting by adopting a converter, refining by top blowing or top-bottom combined blowing, and carrying out microalloying, wherein the impurity content in the steel is controlled to be in the range of the components; during refining, the [ N ] of the molten steel is strictly controlled to be less than or equal to 0.0040%, the [ O ] is strictly controlled to be less than or equal to 0.0020%, and the [ H ] is strictly controlled to be less than or equal to 0.00015%, and the center segregation is reduced by adopting electromagnetic stirring or soft reduction in continuous casting;
after continuous casting, heating and slow cooling are needed, the charging temperature is more than or equal to 500 ℃, the heating speed is less than or equal to 50 ℃/H, the slow cooling time is more than or equal to 30 hours at the temperature of 600-700 ℃, and the hydrogen content and the casting internal stress in the steel billet can be effectively removed by the heating and slow cooling. Slowly cooling the slab to the temperature of 100-200 ℃, and cleaning the slab with the temperature; casting defects can be reduced while occurrence of cutting cracks can be avoided.
The thickness of a casting blank in the rolling process is 135-230 mm, the charging temperature is more than or equal to 600 ℃, the heating temperature before rolling is 1200-1250 ℃, and the heating and heat preservation time is controlled to be 1.0-1.5 min/mm in order to ensure that the alloy can be fully dissolved;
two-stage controlled rolling is adopted during rolling, the aim is to fully refine the hot-rolled structure, the rolling initial temperature in the rough rolling stage is more than or equal to 1100 ℃, and the final rolling temperature is controlled to be more than or equal to 1030 ℃; in the rolling process of the rough rolling stage, austenite is subjected to the processes of dynamic recrystallization, static recrystallization and dynamic recovery, so that austenite grains are refined;
the finish rolling temperature is 1030-1080 ℃, the rolling speed is 5-15 m/s, and the finish rolling temperature is 850-890 ℃; the cooling speed is more than or equal to 20 ℃/s, the coiling is carried out at the temperature of 300-400 ℃, the coiled material enters a slow cooling cover for slow cooling, the heat preservation and slow cooling time of the slow cooling cover is more than or equal to 36 hours, the material is cooled to the temperature of below 200 ℃, and the material is cooled to the room temperature by air.
The invention adopts the production process of slow cooling after low-temperature curling, the low-temperature curling can keep higher strength and hardness of the steel plate, and the slow cooling is carried out for a long time by adopting the heat-insulating cover after the curling, thereby being beneficial to obtaining high plasticity and better toughness; and the residual stress of the steel plate is reduced.
Compared with the prior art, the invention has the beneficial effects that:
the invention relates to a high-performance hot-rolled wear-resistant steel sheet and a production method thereof, which can be used for producing a high-strength hot-rolled wear-resistant steel plate with the thickness of 3-8mm, wherein the surface hardness of the steel plate is more than HB 370; -20 ℃ low temperature toughness of more than 30J; tempering heat treatment is not needed; the composition is simple, and precious alloy is not contained; has good formability and corrosion resistance.
Detailed Description
The following examples are provided to further illustrate the embodiments of the present invention:
the chemical compositions of the steel of the embodiment of the invention are shown in table 1, two rolling process parameters (shown in table 2) are adopted in each embodiment of the chemical compositions, and the performance test results of the embodiment of the invention are shown in tables 3, 4 and 5.
TABLE 1 chemical composition in wt% of steel grades of the examples of the invention
TABLE 2 Rolling Process parameters for examples of the invention
TABLE 3 mechanical Properties of examples of the invention
TABLE 4 Cold bending Properties at 180 ℃ in examples of the invention
TABLE 5 tensile mechanical Properties of the examples of the invention
Claims (2)
1. The high-performance hot-rolled wear-resistant steel sheet is characterized in that the steel comprises the following chemical components in percentage by weight: 0.15 to 0.20 percent of C, 1.0 to 1.5 percent of Si, 0.5 to 0.7 percent of Mn, 0.5 to 0.7 percent of Al, 0.8 to 1.2 percent of Cr, 0.010 to 0.03 percent of Nb, 0.010 to 0.030 percent of Ti, less than or equal to 1.7 percent of Al and Si, and the balance of Fe and inevitable impurities; impurity element control in steel: p is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, N is less than or equal to 0.0040 percent, H is less than or equal to 0.00015 percent, and O is less than or equal to 0.0020 percent;
the production method of the high-performance hot-rolled wear-resistant steel sheet comprises the technical processes of molten iron pretreatment, converter smelting, refining, slab continuous casting, casting blank slow cooling, heating, rolling, laminar cooling, coiling and cover feeding slow cooling;
during refining, the N content of the molten steel is controlled to be less than or equal to 0.0040%, the O content is controlled to be less than or equal to 0.0020%, and the H content is controlled to be less than or equal to 0.00015%, and electromagnetic stirring or soft reduction is adopted for continuous casting;
heating and slow cooling are carried out after continuous casting, the charging temperature is more than or equal to 500 ℃, the heating speed is less than or equal to 50 ℃/H, the slow cooling time is more than or equal to 30 hours at the temperature of 600-700 ℃, and the slab strip temperature is cleaned when the slab temperature is 100-200 ℃;
the thickness of a casting blank in the rolling process is 135-230 mm, the charging temperature is more than or equal to 600 ℃, the heating temperature before rolling is 1200-1250 ℃, and the heating and heat preservation time is controlled to be 1.0-1.5 min/mm;
the rolling initial temperature in the rough rolling stage is more than or equal to 1100 ℃, and the final rolling temperature is controlled to be more than or equal to 1030 ℃;
the finish rolling temperature is 1030-1080 ℃, the rolling speed is 5-15 m/s, and the finish rolling temperature is 850-890 ℃; the cooling speed is more than or equal to 20 ℃/s, the coiling is carried out at the temperature of 300-400 ℃, the coiled material enters a slow cooling cover for slow cooling, the heat preservation and slow cooling time of the slow cooling cover is more than or equal to 36 hours, the material is cooled to the temperature of below 200 ℃, and the material is cooled to the room temperature by air.
2. The high-performance hot-rolled wear-resistant steel sheet as claimed in claim 1, wherein the thickness of the finished steel sheet is 3-8mm, the surface hardness is more than HB370, and the low-temperature toughness at-20 ℃ is more than 30J.
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| CN111607741B (en) * | 2020-06-28 | 2021-10-22 | 武汉钢铁有限公司 | Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 370 and production method thereof |
| CN111607735B (en) * | 2020-06-28 | 2021-10-01 | 武汉钢铁有限公司 | Hot-rolled wear-resistant steel with Brinell hardness of more than or equal to 420 and production method thereof |
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101627142A (en) * | 2007-02-23 | 2010-01-13 | 克里斯塔尔公司 | Cold rolled and continuously annealed high strength steel strip and method for producing said steel |
| CN102952996A (en) * | 2013-01-04 | 2013-03-06 | 鞍钢股份有限公司 | High-elongation cold-rolled TRIP steel plate and preparation method thereof |
| CN103154279A (en) * | 2010-10-12 | 2013-06-12 | 塔塔钢铁艾默伊登有限责任公司 | Method of hot forming a steel blank and the hot formed part |
| CN104195445A (en) * | 2014-09-02 | 2014-12-10 | 青岛永通电梯工程有限公司 | Alloy steel |
| CN105779879A (en) * | 2014-12-23 | 2016-07-20 | 鞍钢股份有限公司 | Production method of cold-rolled non-oriented electrical steel thin strip |
| CN106591721A (en) * | 2016-12-14 | 2017-04-26 | 宁波翔博机械有限公司 | Steel plate having high elongation percentage and preparation method thereof |
| CN109207849A (en) * | 2018-09-26 | 2019-01-15 | 武汉钢铁有限公司 | High-strength high-plasticity 1000MPa level hot rolled steel plate and preparation method |
| CN110453146A (en) * | 2019-08-21 | 2019-11-15 | 首钢集团有限公司 | A kind of Cr alloying steel of no yield point elongation and preparation method thereof |
-
2020
- 2020-01-21 CN CN202010071563.5A patent/CN111254351B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101627142A (en) * | 2007-02-23 | 2010-01-13 | 克里斯塔尔公司 | Cold rolled and continuously annealed high strength steel strip and method for producing said steel |
| CN103154279A (en) * | 2010-10-12 | 2013-06-12 | 塔塔钢铁艾默伊登有限责任公司 | Method of hot forming a steel blank and the hot formed part |
| CN102952996A (en) * | 2013-01-04 | 2013-03-06 | 鞍钢股份有限公司 | High-elongation cold-rolled TRIP steel plate and preparation method thereof |
| CN104195445A (en) * | 2014-09-02 | 2014-12-10 | 青岛永通电梯工程有限公司 | Alloy steel |
| CN105779879A (en) * | 2014-12-23 | 2016-07-20 | 鞍钢股份有限公司 | Production method of cold-rolled non-oriented electrical steel thin strip |
| CN106591721A (en) * | 2016-12-14 | 2017-04-26 | 宁波翔博机械有限公司 | Steel plate having high elongation percentage and preparation method thereof |
| CN109207849A (en) * | 2018-09-26 | 2019-01-15 | 武汉钢铁有限公司 | High-strength high-plasticity 1000MPa level hot rolled steel plate and preparation method |
| CN110453146A (en) * | 2019-08-21 | 2019-11-15 | 首钢集团有限公司 | A kind of Cr alloying steel of no yield point elongation and preparation method thereof |
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