CN113957357A - Hot-rolled wear-resistant steel and production method thereof - Google Patents
Hot-rolled wear-resistant steel and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 109
- 239000010959 steel Substances 0.000 title claims abstract description 109
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 27
- 238000005096 rolling process Methods 0.000 claims abstract description 63
- 238000005242 forging Methods 0.000 claims abstract description 37
- 238000001816 cooling Methods 0.000 claims abstract description 36
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 22
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 14
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 14
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 14
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 14
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 13
- 238000004512 die casting Methods 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 238000005098 hot rolling Methods 0.000 claims abstract description 7
- 238000010438 heat treatment Methods 0.000 claims description 33
- 230000009467 reduction Effects 0.000 claims description 17
- 229910052750 molybdenum Inorganic materials 0.000 claims description 16
- 238000003723 Smelting Methods 0.000 claims description 12
- 238000007670 refining Methods 0.000 claims description 12
- 229910052758 niobium Inorganic materials 0.000 claims description 9
- 238000010079 rubber tapping Methods 0.000 claims description 8
- 229910052729 chemical element Inorganic materials 0.000 claims description 6
- 238000000034 method Methods 0.000 abstract description 30
- 239000010936 titanium Substances 0.000 abstract description 26
- 229910045601 alloy Inorganic materials 0.000 abstract description 7
- 239000000956 alloy Substances 0.000 abstract description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract description 5
- 238000002360 preparation method Methods 0.000 abstract description 4
- 230000007547 defect Effects 0.000 abstract description 3
- 238000005728 strengthening Methods 0.000 abstract description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 12
- 229910001562 pearlite Inorganic materials 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 229910001566 austenite Inorganic materials 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 8
- 239000000463 material Substances 0.000 description 7
- 230000008569 process Effects 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 239000002245 particle Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 238000004321 preservation Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- 238000005204 segregation Methods 0.000 description 4
- 238000005299 abrasion Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000010970 precious metal Substances 0.000 description 3
- 238000003303 reheating Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 238000007599 discharging Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005065 mining Methods 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000013100 final test Methods 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000009740 moulding (composite fabrication) Methods 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 238000011112 process operation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- GFNGCDBZVSLSFT-UHFFFAOYSA-N titanium vanadium Chemical compound [Ti].[V] GFNGCDBZVSLSFT-UHFFFAOYSA-N 0.000 description 1
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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
- C22C38/18—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
- 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
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
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- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to hot-rolled wear-resistant steel and a production method thereof, belonging to the technical field of wear-resistant steel preparation. The weight percentage of the wear-resistant steel C: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060% of one or two of them, and the rest is Fe and inevitable impurity. The method comprises preparing a steel ingot; forging; hot rolling; and (4) laminar cooling. The wear-resistant steel with comprehensive performance superior to that of a conventional product is obtained by adopting a production process of die casting, forging and rolling and strengthening by using a titanium element with lower alloy cost. Solves the problems of high production cost, uneven structure and more internal defects of the existing wear-resistant steel.
Description
Technical Field
The invention relates to hot-rolled wear-resistant steel and a production method thereof, belonging to the technical field of wear-resistant steel preparation.
Background
At present, the engineering machinery industry in China is rapidly developed, wear-resistant steel is used as important steel for engineering machinery, is widely applied to mining machinery such as mining vehicles, grinders and conveying equipment, a large amount of precious metal elements are required to be added to the traditional wear-resistant steel, good wear resistance can be obtained only through heat treatment, and the wear-resistant steel has the defects of high alloy cost and high production cost.
The national patent, CN 109706399B, discloses a high titanium wear resistant steel and a preparation method thereof. The components by weight percentage are as follows: c: 0.15-0.28%, Mn: 0.9-1.5%, Si: 0.18-0.22%, Als: 0.02-0.06%, P is less than or equal to 0.020%, S is less than or equal to 0.015%, Ti: 0.30-0.60%, Mo: 0.15-0.32%, and the balance of Fe and inevitable impurities. The steel with the components is obtained by electric furnace smelting, LF refining, VD refining, die casting, hot rolling and heat treatment, wherein the heat treatment process comprises 800-960 ℃ quenching and 100-240 ℃ tempering.
The national patent, publication number CN 107099730B, discloses a method for manufacturing thin high Ti wear resistant steel NM360, which comprises the following components by weight percent: c: 0.16-0.20%, Mn: 0.8-1.5%, Si: 0.2-0.4%, P is less than or equal to 0.015%, S is less than or equal to 0.010%, Cr: 0.30-0.50%, Nb: 0.02-0.05%, N is less than or equal to 0.005%, Ti: 0.10-0.15%, Mo: 0.10-0.20%, B: 0.0005-0.0010%, and the balance of Fe and inevitable impurities. The steel is obtained by smelting, continuous casting, reheating, hot continuous rolling, ultra-fast cooling, quenching and tempering according to the components.
The national patent, publication No. CN 110055462B, discloses a dual-scale TiC particle composite reinforced low-alloy super wear-resistant steel and a manufacturing method thereof, wherein the steel comprises the following components in percentage by weight: c: 0.18-0.60%, Mn: 1.00-3.00%, Si: 0.30-1.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Ti: 0.2-1.0%, Mo: 0.10-0.50%, Cr: 0.20-0.40%, B: 0.0005-0.003 wt%, and the balance Fe and inevitable impurities, wherein the content of C, Ti is more than or equal to 0.10 wt% and less than or equal to 0.40 wt% of C-Ti/4. The preparation method comprises the steps of smelting, solidification forming, rolling, cooling and heat treatment, wherein during cooling, the rolled piece is cooled to 750 ℃ at an ultra-fast speed, and then the rolled piece is cooled in a heap. The hardness of the wear-resistant steel is HB360-550, and the wear resistance of the wear-resistant steel is 1.5-3.0 times that of the traditional wear-resistant steel with the same hardness.
In conclusion, the schemes described above all adopt a mode of alloying a large amount of precious metal elements to obtain wear-resistant steel with good wear resistance through heat treatment, but the alloy cost is high, and the alloy is not suitable for a wear-resistant steel process which can be produced by common hot continuous rolling, so that the production cost is high.
Disclosure of Invention
The invention aims to solve the technical problem that the existing wear-resistant steel is alloyed by adding a large amount of precious metal elements, is not suitable for common hot continuous rolling production and causes high production cost.
The technical scheme adopted by the invention for solving the technical problems is as follows: the hot-rolled wear-resistant steel comprises the following components in percentage by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060%, and the balance Fe and inevitable impurities.
A production method of hot-rolled wear-resistant steel comprises the following steps:
s1, preparing a steel ingot, wherein the steel ingot comprises the following components in percentage by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060% and the balance of Fe and inevitable impurities;
s2, forging to obtain a plate blank, wherein the starting forging temperature is 1100-1140 ℃, and the final forging temperature is 850-920 ℃;
s3, hot rolling to obtain a steel plate;
and S4, carrying out laminar cooling on the steel plate.
In the method, in step S1, steel ingots are prepared by electric furnace smelting, refining and die casting.
Wherein, in the method, the steel ingot is heated to 940-960 ℃ before the forging in the step S2, and the temperature is kept for 4-6 h; then heating to 1230-1250 ℃, and preserving the heat for 14-17 h.
Wherein, the first time and the second time of drawing in the step S2 of the method have the rolling reduction rate of more than or equal to 120mm, and round steel with the specification of less than phi 750mm is forged.
Furthermore, in the method, the round steel is drawn into a slab with the thickness of 200mm and the width of 1000-1500 mm.
Wherein, the plate blank prepared in the step S2 is placed into a heating furnace for heating, the tapping temperature is 1180 ℃ and 1220 ℃, and the furnace time is more than or equal to 180 min.
In the method, the accumulated deformation of rough rolling in the step S3 is more than or equal to 80%, and the thickness of the intermediate billet after rough rolling is 35-40 mm.
Further, in the method, the accumulated deformation amount of the finish rolling in the step S3 is more than or equal to 75 percent, the finish rolling temperature is 820-880 ℃, and the thickness of the steel plate after the finish rolling is 6-8 mm.
Wherein, in the step S4, the finish rolled steel plate is cooled by laminar flow, the cooling rate is 20-50 ℃/S, and the final cooling temperature is 560-640 ℃.
The invention has the beneficial effects that: the microstructure of the wear-resistant steel produced by the method is ferrite plus pearlite, the matrix structure has good impact toughness, the wear resistance is improved by micron-sized titanium precipitated phases, and the comprehensive performance of the wear-resistant steel is superior to that of the conventional wear-resistant steel which has high strength and hardness but poor toughness. The yield strength is more than or equal to 750MPa, the tensile strength is more than or equal to 900MPa, the elongation A is more than or equal to 16%, the microstructure is ferrite and a small amount of pearlite, the average grain size is 4-6 micrometers, the impact energy at minus 20 ℃ is more than or equal to 50J, the hardness HBW is more than or equal to 250, and the wear resistance is equivalent to NM 360. The method adopts a titanium alloying mode, has the characteristics of low alloy cost and production capability of common hot continuous rolling, greatly reduces the production cost and has stronger popularization. Promotes the development and popularization of steel for hot rolling engineering machinery and promotes the comprehensive utilization of vanadium-titanium resources. The method predicts the generating effect of 2000 yuan per ton of steel, and predicts the generating effect of 100 ten thousand yuan per year according to the yield of 500 tons per year.
Drawings
FIG. 1 is a schematic microstructure of example 1 of the present invention;
FIG. 2 is a schematic microstructure of example 2 of the present invention;
FIG. 3 is a schematic microstructure of example 3 of the present invention;
FIG. 4 is a schematic view of the microstructure of comparative example 1 of the present invention;
FIG. 5 is a schematic view of the microstructure of comparative example 2 of the present invention;
FIG. 6 is a schematic view of the microstructure of comparative example 3 of the present invention.
Detailed Description
The present invention will be further described with reference to the following examples and accompanying drawings.
As shown in fig. 1 to 6, the hot-rolled wear-resistant steel of the present invention comprises the following components by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060%, and the balance Fe and inevitable impurities. As can be understood by those skilled in the art, C and Si are important interstitial solid solution strengthening elements in steel, which are beneficial to improving the strength and hardness of the steel, wherein C can be combined with Ti to form TiC to be precipitated, and the micron-sized TiC is taken as hard particles to obviously shallow furrows when abrasive particles are worn, so that the wear resistance of the material is improved, but when the content of C and Si is higher, the plasticity of the material is easily reduced, so that the content of C is controlled to be 0.12-0.20%, and the content of Si is controlled to be 0.10-0.20%.
Mn is a replacement solid solution element and can improve the yield strength and the impact toughness of steel, but when the content of Mn is higher, casting blank segregation is easily formed, the structural uniformity of the material is influenced, and the impact toughness is reduced, so that the content of Mn is controlled to be 1.00-1.50%.
Ti and C can form micron-sized TiC, and the abrasion resistance is improved by making a furrow in abrasive particle abrasion become shallow, so the scheme forms the micron-sized TiC and the nano-sized TiC by controlled rolling and controlled cooling so as to simultaneously improve the abrasion resistance and the obdurability of steel. In addition, Ti and N are easy to combine to form liquated TiN, so that the toughness of the steel is obviously reduced. Therefore, the contents of Ti and N must be controlled, the scheme controls the content of N to be less than or equal to 0.0040 percent and the content of Ti to be 0.20 to 0.40 percent.
In addition, the scheme also requires to add one or two of Cr, Mo and Nb, wherein Nb can play a role in pinning austenite grain boundaries in the rolling process through Nb (CN), so that the structure is refined, Cr and Mo can promote the formation of a fine ferrite structure in the phase change process through improving hardenability, Mo can further refine the precipitation of nano TiC and promote the dispersion and the miniaturization of precipitated phases, and thus the toughness of the material is improved. Therefore, the proposal controls the Cr content to be 0.10-0.20%, the Mo content to be 0.10-0.20% and the Nb content to be 0.030-0.060%.
A production method of hot-rolled wear-resistant steel comprises the following steps:
s1, preparing a steel ingot, wherein the steel ingot comprises the following components in percentage by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060% and the balance of Fe and inevitable impurities;
s2, forging to obtain a plate blank, wherein the starting forging temperature is 1100-1140 ℃, and the final forging temperature is 850-920 ℃;
s3, hot rolling to obtain a steel plate;
and S4, carrying out laminar cooling on the steel plate. As can be understood by those skilled in the art, the method adopts the forging and rolling process to sufficiently press the defects in the steel ingot due to the fact that the steel prepared by the method has high titanium content and the risk of generating large-particle inclusions or shrinkage cavities and the like exists in the steel ingot after die casting. The method introduces a forging process to refine the crystal grains, thereby improving the wear resistance of the product.
Preferably, in step S1 of the above method, an ingot is prepared by electric furnace smelting, refining, and die casting. As can be understood by those skilled in the art, the method reduces the production cost by preparing the steel with the components into a steel ingot of 15-30t by adopting the conventional methods of electric furnace smelting, refining and die casting.
Preferably, in the method, the steel ingot is heated to 940-960 ℃ before the step S2 of forging, and the temperature is kept for 4-6 h; then heating to 1230-1250 ℃, and preserving the heat for 14-17 h. As can be understood by those skilled in the art, the two-stage heating is adopted before forging mainly to prevent the steel ingot from cracking due to too high heating speed, the first stage of heat preservation at 940-.
Preferably, in the method, the first time drawing and the second time drawing in the step S2 have the rolling reduction rate of more than or equal to 120mm, and round steel with the specification of less than phi 750mm is forged. The skilled person in the art can understand that the requirement that the first and second elongation rolling reduction rates during forging are more than or equal to 120mm is to enable the core of the steel ingot to be subjected to sufficient deformation to promote austenite recrystallization so as to refine the steel ingot structure, and meanwhile, the sufficient deformation can also promote the micron-sized TiC deformation-induced precipitation.
Preferably, in the method, the round steel is drawn into a slab with the thickness of 200mm and the width of 1000 and 1500 mm. As can be understood by those skilled in the art, for the convenience of subsequent process operation, the method preferably further draws the round steel into a slab with the thickness of 200mm and the width of 1000 and 1500mm, so as to facilitate the operation of the hot rolling process.
Preferably, the slab prepared in the step S2 is placed into a heating furnace for heating in the above method, the tapping temperature is 1180 ℃ and 1220 ℃, and the furnace time is more than or equal to 180 min. As can be understood by those skilled in the art, the slab reheating after the forging into the slab with the thickness of 200mm is to fully diffuse and dissolve alloy elements, promote the homogenization of the slab and reduce the composition segregation, and the tapping temperature is lower 1180-1220 ℃ to reduce the re-dissolution of the micron-sized TiC formed in the pre-process of the slab.
Preferably, in the method, the accumulated deformation of the rough rolling in the step S3 is more than or equal to 80%, and the thickness of the intermediate billet after the rough rolling is 35-40 mm. As can be understood by those skilled in the art, dynamic recrystallization of austenite mainly occurs in the rough rolling process, and the improvement of rolling deformation is beneficial to increasing the activation energy of the dynamic recrystallization of austenite, promoting the recrystallization of austenite, achieving the purposes of refining grains and promoting deformation-induced precipitation, so that the accumulated deformation of rough rolling is limited to be more than or equal to 80%.
Preferably, in the method, the accumulated deformation amount of the finish rolling in the step S3 is more than or equal to 75 percent, the finish rolling temperature is 820-880 ℃, and the thickness of the steel plate after the finish rolling is 6-8 mm. As can be appreciated by those skilled in the art, the finish rolling process is mainly rolling in the non-austenite recrystallization region, and in order to ensure that the original austenite in the process is sufficiently flattened, the accumulated deformation of the finish rolling is limited to be more than or equal to 75 percent. In addition, if the rolling temperature is too high and the structure is coarse, the finish rolling temperature is set in the range of 820-880 ℃.
Preferably, in the above method, in step S4, the finish-rolled steel sheet is subjected to laminar cooling, and is intensively cooled at a cooling rate of 20-50 ℃/S, and the final cooling temperature is 560-640 ℃. As will be appreciated by those skilled in the art, laminar cooling is the primary phase of the phase transformation of the material, and the tissue control objectives of the present invention are ferrite, a small amount of pearlite, and nanoscale secondary phase precipitation. Therefore, the cooling speed is controlled in a ferrite-pearlite transformation region, the cooling speed is not too high, otherwise bainite or martensite abnormal structures are easily generated in the core due to uneven cooling of the surface and the core, the cooling speed is not too low, otherwise coarse pro-eutectoid ferrite and pearlite are easily formed, and the toughness of the material is influenced. Therefore, the invention limits the cooling speed to the range of 20-50 ℃/s, and simultaneously sets the final cooling temperature to be 560-640 ℃ considering that the nose point temperature of TiC second phase precipitation is about 600 ℃.
Example 1
The chemical components are as follows by weight percent (%): 0.18 percent of C, 0.19 percent of Si, 1.21 percent of Mn, 0.005 percent of P, 0.003 percent of S, 0.039 percent of Als, 0.0035 percent of N, 0.11 percent of Cr, 0.36 percent of Ti and 0.20 percent of Mo, smelting, refining and die casting by an electric furnace to obtain 19t steel ingots, heating to 945 ℃ firstly, preserving heat for 4.5 hours, heating to 1241 ℃ and preserving heat for 14 hours, wherein the forging temperature is 1126 ℃, the primary drawing reduction is 120mm, the secondary drawing reduction is 120mm, and the final forging temperature is 865 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, wherein the tapping temperature is 1194 ℃, the furnace time is 207min, the rough rolling accumulated deformation is 82%, the intermediate blank after rough rolling is 36mm thick, the finish rolling accumulated deformation is 78%, the finish rolling temperature is 867 ℃, the steel plate after finish rolling is 8mm thick, the laminar cooling rate is 32 ℃/s, and the finish cooling temperature is 608 ℃.
The finished steel has the yield strength of 812MPa, the tensile strength of 925MPa, the elongation of 18.0 percent, the impact energy of 66J at the temperature of minus 20 ℃, the hardness of HBW275, a microstructure of ferrite and a small amount of pearlite and the average grain size of 5 microns.
Example 2
The chemical components are as follows by weight percent (%): c0.17, Si 0.16, Mn 1.49, P0.010, S0.003, Als0.027, N0.0028, Nb 0.049, Ti 0.24 and Mo 0.19, smelting, refining and die casting by an electric furnace to obtain a 22t steel ingot, heating to 959 ℃ for heat preservation for 5 hours, heating to 1236 ℃ for heat preservation for 15 hours, wherein the forging temperature is 1131 ℃, the primary drawing reduction is 125mm, the secondary drawing reduction is 121mm, and the finish forging temperature is 899 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, wherein the tapping temperature is 1206 ℃, the furnace time is 214min, the rough rolling accumulated deformation is 84%, the intermediate blank after rough rolling is 32mm thick, the finish rolling accumulated deformation is 81%, the finish rolling temperature is 872 ℃, the steel plate after finish rolling is 6mm thick, the laminar cooling rate is 36 ℃/s, and the finish cooling temperature is 578 ℃.
The yield strength of the finished steel is 800MPa, the tensile strength is 905MPa, the elongation is 22 percent, the impact energy at the temperature of minus 20 ℃ is 80J, the hardness is HBW260, the microstructure is ferrite and a small amount of pearlite, and the average grain size is 4.5 micrometers, which is shown in figure 2.
Example 3
The chemical components are as follows by weight percent (%): c0.15, Si 0.18, Mn 1.40, P0.008, S0.004, Als0.045, N0.0031, Ti 0.31 and Mo 0.20, and the 18t steel ingot is obtained by electric furnace smelting, refining and die casting, and is firstly heated to 950 ℃ and insulated for 5.5h, and then heated to 1240 ℃ and insulated for 16h, wherein the forging temperature is 1122 ℃, the first drawing reduction is 121mm, the second drawing reduction is 123mm, and the final forging temperature is 911 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, wherein the tapping temperature is 1217 ℃, the in-furnace time is 196min, the rough rolling accumulated deformation is 80%, the rough rolling intermediate blank is 40mm thick, the finish rolling accumulated deformation is 80%, the finish rolling temperature is 843 ℃, the finish rolling steel plate is 8mm thick, the laminar cooling rate is 27 ℃/s, and the finish cooling temperature is 627 ℃.
The finished steel has yield strength of 789MPa, tensile strength of 913MPa, elongation of 21 percent, impact energy of 71J at minus 20 ℃, hardness of HBW271, a microstructure of ferrite and a small amount of pearlite, and the average grain size of 5.5 microns.
Comparative example 1
The chemical components are as follows by weight percent (%): 0.12 percent of C, 0.18 percent of Si, 1.38 percent of Mn, 0.006 percent of P, 0.003 percent of S, 0.050 percent of Als0.050 percent of N, 0.0034 percent of Ti, 0.40 percent of Mo and 0.20 percent of Mo, heating to 960 ℃, preserving heat for 4 hours, heating to 1230 ℃, preserving heat for 12 hours, wherein the forging temperature is 1103 ℃, the first drawing reduction is 120mm, the second drawing reduction is 130mm, and the final forging temperature is 895 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, discharging the plate blank at 1193 ℃, keeping the furnace time for 188min, accumulating the deformation of the rough rolling for 82 percent, accumulating the deformation of the finish rolling for 78 percent, finishing the rolling at 885 ℃, finishing the plate blank by 8mm, cooling the laminar flow at a rate of 25 ℃/s and finishing the cooling temperature at 678 ℃.
The finished steel has the yield strength of 766MPa, the tensile strength of 861MPa, the elongation of 20.0 percent, the impact energy of 37J at the temperature of minus 20 ℃, the hardness of HBW95, the microstructure of ferrite and a small amount of pearlite and the average grain size of 10 microns. In the comparative example, the final cooling temperature is too high, so that large-size pro-eutectoid ferrite is formed, and the microstructure of the material is coarse.
Comparative example 2
The chemical components are as follows by weight percent (%): 0.14 percent of C, 0.19 percent of Si, 1.42 percent of Mn, 0.010 percent of P, 0.002 percent of S, 0.038 percent of Als, 0.0036 percent of N, 0.20 percent of Cr, 0.37 percent of Ti and 0.16 percent of Mo, smelting, refining and die casting by an electric furnace to obtain 22t steel ingots, heating to 920 ℃ firstly, keeping the temperature for 4 hours, heating to 1230 ℃ and keeping the temperature for 12 hours, the forging temperature is 1103 ℃, the first drawing reduction is 70mm, the second drawing reduction is 80mm, and the finish forging temperature is 895 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, discharging the plate blank at 1156 ℃, keeping the furnace time for 123min, accumulating 85% of rough rolling deformation, accumulating 73% of finish rolling deformation and finishing the finish rolling at 865 ℃, 8mm thick steel plate after finish rolling, wherein the laminar cooling rate is 65 ℃/s, and the finishing temperature is 338 ℃.
The finished steel has the yield strength of 644MPa, the tensile strength of 867MPa, the elongation of 17.5 percent, the impact energy of 11J at the temperature of minus 20 ℃, the hardness of HBW270, a microstructure of ferrite, martensite ribbon and a small amount of pearlite, and the average grain size of 8 microns. In the comparative example, the rolling reduction is low during ingot forging, the center of the steel ingot is not completely austenite recrystallized and cannot be completely crushed to realize ingot segregation, the steel ingot is inherited to the subsequent production process, the reheating temperature is low after the steel ingot is forged into a slab, the furnace time is short, the segregation cannot be completely diffused and homogenized, and the finished steel forms a banded structure.
Comparative example 3
The chemical components are as follows by weight percent (%): 0.08 percent of C, 0.20 percent of Si, 1.50 percent of Mn, 0.01 percent of P, 0.003 percent of S, 0.026 percent of Als, 0.0032 percent of N, 0.036 percent of Nb, 0.15 percent of Ti and 0.12 percent of Mo, smelting, refining and die casting by an electric furnace to obtain 20t steel ingots, heating to 951 ℃ for heat preservation for 6h, heating to 1246 ℃ for heat preservation for 16h, wherein the forging starting temperature is 1101 ℃, the first drawing reduction is 120mm, the second drawing reduction is 120mm and the final forging temperature is 883 ℃. And (3) obtaining a 200mm thick plate blank after forging, then sending the plate blank into a heating furnace, wherein the tapping temperature is 1220 ℃, the furnace time is 199min, the rough rolling accumulated deformation is 82%, the intermediate blank after rough rolling is 36mm thick, the finish rolling accumulated deformation is 83%, the finish rolling temperature is 881 ℃, the steel plate after finish rolling is 6mm thick, the laminar cooling rate is 34 ℃/s, and the finish cooling temperature is 603 ℃.
The yield strength of the finished steel is 795MPa, the tensile strength is 895MPa, the impact energy is 60J at minus 20 ℃, the hardness is HBW244, the microstructure is ferrite and a small amount of pearlite, and the average grain size is 5 microns.
The steels of examples 1 to 3 and comparative examples 1 to 3 were subjected to an abrasive wear test, and the final test results were compared with NM360, and the test data are shown in Table 1, whereby it is understood that the wear resistance of examples 1 to 3 is equivalent to that of NM360, and the wear resistance of comparative examples 1 to 3 is lower than that of NM 360.
Table 1 abrasive wear test data
Claims (10)
1. The hot-rolled wear-resistant steel is characterized by comprising the following components in percentage by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060%, and the balance Fe and inevitable impurities.
2. A production method of hot-rolled wear-resistant steel is characterized by comprising the following steps:
s1, preparing a steel ingot, wherein the steel ingot comprises the following components in percentage by weight: 0.12-0.20%, Mn: 1.00-1.50%, Si: 0.10-0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, Als: 0.025-0.050%, N is less than or equal to 0.0040%, Ti: 0.20-0.40%, and also comprises one or two chemical elements of Cr, Mo and Nb, wherein the ratio of Cr: 0.10-0.20, Mo: 0.10-0.20, Nb: 0.030-0.060% and the balance of Fe and inevitable impurities;
s2, forging to obtain a plate blank, wherein the starting forging temperature is 1100-1140 ℃, and the final forging temperature is 850-920 ℃;
s3, hot rolling to obtain a steel plate;
and S4, carrying out laminar cooling on the steel plate.
3. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: in step S1, the steel ingot is prepared by electric furnace smelting, refining and die casting.
4. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: step S2, heating the steel ingot to 940-; then heating to 1230-1250 ℃, and preserving the heat for 14-17 h.
5. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: in step S2, the first time and the second time of drawing are performed, the reduction rate is more than or equal to 120mm, and round steel with the specification less than phi 750mm is forged.
6. The production method of a hot-rolled wear-resistant steel according to claim 5, characterized in that: and then drawing the round steel into a slab with the thickness of 200mm and the width of 1000-1500 mm.
7. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: and (4) putting the plate blank prepared in the step S2 into a heating furnace for heating, wherein the tapping temperature is 1180-1220 ℃, and the furnace time is more than or equal to 180 min.
8. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: in the step S3, the accumulated deformation of rough rolling is more than or equal to 80%, and the thickness of the intermediate blank after rough rolling is 35-40 mm.
9. The production method of a hot-rolled wear-resistant steel according to claim 8, characterized in that: in the step S3, the accumulated deformation of the finish rolling is more than or equal to 75 percent, the finish rolling temperature is 820-880 ℃, and the thickness of the steel plate after the finish rolling is 6-8 mm.
10. The production method of a hot-rolled wear-resistant steel according to claim 2, characterized in that: step S4, carrying out laminar cooling on the finish rolled steel plate, and carrying out concentrated cooling at a cooling rate of 20-50 ℃/S, wherein the final cooling temperature is 560-.
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