CN116287970A - HB 450-grade wear-resistant steel with excellent welding performance and production method thereof - Google Patents
HB 450-grade wear-resistant steel with excellent welding performance and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 46
- 239000010959 steel Substances 0.000 title claims abstract description 46
- 238000003466 welding Methods 0.000 title claims abstract description 24
- 238000004519 manufacturing process Methods 0.000 title claims description 16
- 238000001816 cooling Methods 0.000 claims abstract description 37
- 238000005096 rolling process Methods 0.000 claims abstract description 34
- 238000000034 method Methods 0.000 claims abstract description 15
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 238000002791 soaking Methods 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 238000009749 continuous casting Methods 0.000 claims abstract description 5
- 238000005520 cutting process Methods 0.000 claims abstract description 5
- 238000005299 abrasion Methods 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 description 12
- 239000000956 alloy Substances 0.000 description 12
- 229910001566 austenite Inorganic materials 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 9
- 229910000859 α-Fe Inorganic materials 0.000 description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 5
- 229910000734 martensite Inorganic materials 0.000 description 5
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 238000005496 tempering Methods 0.000 description 4
- 239000013078 crystal Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000005272 metallurgy Methods 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 239000003245 coal Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000009466 transformation Effects 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
-
- 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
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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
- C21D8/0247—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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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Abstract
The invention discloses HB450 grade wear-resistant steel with excellent welding performance, which comprises the following chemical components in percentage by weight: c:0.10 to 0.18 percent, si:0.1 to 0.3 percent, mn:0.5 to 1.5 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, als:0.03 to 0.06 percent, nb:0.02 to 0.03 percent of Ti: 0.005-0.02%, cr:0.1 to 0.3 percent, B:0 to 0.0003 percent, and the balance of Fe and impurities; comprises the following steps of smelting, continuous casting, heating, rough rolling, finish rolling, cooling, coiling and transverse cutting; in the heating process, the temperature of the second adding soaking end section is 1200-1250 ℃, the second adding soaking time is more than or equal to 40min, and the total furnace time is controlled to be more than or equal to 120min; the outlet temperature in the rough rolling process is 1020-1080 ℃, and the thickness of the intermediate billet is 30-50 mm; the initial rolling temperature in the finish rolling process is 910 ℃ to 980 ℃, and the finish rolling finishing temperature is 850 ℃ to 890 ℃; in the cooling process, FT7 is immediately cooled to 600-700 ℃ at a cooling rate of 30-50 ℃/s, air-cooled for 2-8 s, and then cooled to below 100 ℃ at a cooling rate of 200-300 ℃/s for coiling.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to HB 450-grade wear-resistant steel and a production method thereof.
Background
In recent years, with the rapid increase of steel production and usage amount, alloy elements are excessively consumed, and the price of some alloy elements is increased, so that an iron and steel plant obtains an intolerable place, and the alloy element usage amount is reduced, thus the method is an unprecedented task for iron and steel researchers.
The low-alloy high-strength wear-resistant steel is widely applied to mechanical equipment such as metallurgy, mines, building materials, railways, electric power, coal and the like, has severe use environment, provides strict requirements on weldability, formability, wear resistance and the like, and also provides higher requirements on the weldability of the wear-resistant steel along with continuous upgrading and upgrading of downstream user products such as commercial vehicles and the like, and the traditional wear-resistant steel for quenching and tempering is filled with more precious alloy at home and abroad, so that the cost is increased due to higher alloy content, the welding performance is poor, and the bottleneck for limiting popularization of the wear-resistant steel in downstream industries such as dumpers and the like is formed.
Publication number CN102605234a provides a HB400 grade wear-resistant steel plate and a manufacturing method thereof, the components in weight percentage are: c:0.08 to 0.24 percent, si:0.1 to 0.3 percent, mn:0.7 to 1.7 percent, cr:1.0%, mo:0.6%, B:0.0005 to 0.004 percent, ti: 0.005-0.04%, and the balance Fe and trace impurity elements, adopting casting-rolling control-tempering heat treatment process to produce, the performance is excellent, but the grade is HB400 grade only, and the alloy also contains noble elements such as Mo, and the like, the manufacturing flow is long, and the market competitiveness is not enough.
The invention patent of publication No. CN1109919A provides a low alloy wear-resistant steel, which comprises the following components in percentage by weight: c:0.5 to 0.6 percent, si:0.9 to 1.2 percent, mn:1.4 to 1.7 percent, cr:1.35 to 1.60 percent, mo:0.3 to 0.5 percent, V:0.05 to 0.10 percent of Ti:0.03 to 0.06 percent, re: 0.02-0.04%, better strength and wear resistance, high C content up to 0.5-0.6%, and high cost and directly affected welding performance due to the addition of a large amount of alloy elements for improving hardenability.
Therefore, the existing wear-resistant steel has the technical problems of high alloy cost, poor welding performance and the like, so that component process design is necessary to improve the welding performance.
Disclosure of Invention
The invention aims to provide HB450 grade wear-resistant steel with excellent welding performance and a production method thereof, and the HB450 grade wear-resistant steel with excellent welding performance is obtained by controlling a structure through optimizing rolling and cooling processes through reasonable component process design, reducing the use of alloy elements and lowering the cost.
In order to achieve the above purpose, the following technical scheme is adopted:
the HB450 grade wear-resistant steel with excellent welding performance comprises the following chemical components in percentage by weight: c:0.10 to 0.18 percent, si:0.1 to 0.3 percent, mn:0.5 to 1.5 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, als:0.03 to 0.06 percent, nb:0.02 to 0.03 percent of Ti: 0.005-0.02%, cr:0.1 to 0.3 percent, B:0 to 0.0003 percent, and the balance of Fe and impurities.
The production method of the HB450 grade wear-resistant steel comprises the processes of smelting, continuous casting, heating, rough rolling, finish rolling, cooling, coiling and transverse cutting.
According to the scheme, in the heating process, the temperature of the second adding and soaking end section is 1200-1250 ℃, the second adding and soaking time is more than or equal to 40min, and the total furnace time is controlled to be more than or equal to 120min.
According to the scheme, the outlet temperature in the rough rolling process is 1020-1080 ℃, and the thickness of the intermediate billet is 30-50 mm.
According to the scheme, the initial rolling temperature in the finish rolling process is 910-980 ℃, and the finish rolling finishing temperature is 850-890 ℃.
According to the scheme, in the cooling process, FT7 is immediately cooled to 600-700 ℃ at a cooling rate of 30-50 ℃/s, air-cooled for 2-8 s, and then cooled to below 100 ℃ at a cooling rate of 200-300 ℃/s for coiling.
The reasons for setting the component ranges and the technical key points in the invention are as follows:
c is the cheapest element for improving the strength of the material, and the hardness and strength are improved with the increase of the carbon content, but the toughness and welding performance are reduced. Comprehensively considering that the weight percentage of C is 0.10 to 0.18 percent;
si can reduce the diffusion rate of carbon in ferrite, promote ferrite formation, and also deteriorate the surface quality. Comprehensively considering that the weight percentage of Si is preferably 0.1 to 0.3 percent;
mn obviously reduces Ar1 temperature and austenite decomposition speed, improves supercooled austenite stability, promotes austenite release stress, increases residual austenite content in a final structure, and improves cold bending performance, but if the Mn content is too high, tempering brittleness can be increased, serious center segregation is caused, and the Mn weight percentage is preferably 0.5-1.5% comprehensively considered.
Als can deoxidize in steel, reduce the content of inclusions, and also play a role in refining grains, and comprehensively consider that Als is 0.03-0.06%;
ti can combine with N to generate stable TiN in the solidification process of steel, and can strongly block the migration of austenite grain boundaries, thereby refining austenite grains. Considering comprehensively, the Ti weight percentage is preferably 0.005-0.02%;
nb has extremely strong affinity with C, N in steel to form stable Nb (C, N) compounds, the stable Nb (C, N) compounds are induced to separate out in the controlled rolling process, and are dispersed and distributed along the austenite grain boundary to serve as nucleation points of phase transformation, so that recrystallization can be effectively prevented, ferrite nucleation rate is improved, the effect on grain refinement is remarkable, and the weight percentage of Nb is preferably 0.02-0.03% by comprehensive consideration;
cr can improve hardenability, can improve tempering stability, reduce the cooling rate of the obtained martensite, but too high Cr reduces workability and weldability, and is suitable for comprehensively considering that the weight percentage of Cr is 0.1% -0.4%;
the quenching degree can be greatly improved by adding a trace amount of B into the steel, but when B is too much, the B is easy to enrich in crystal boundaries, the crystal boundary bonding energy can be reduced, so that the steel plate is more prone to fracture along the crystal when being subjected to impact load, and the low-temperature impact energy of the steel plate is reduced, and therefore, the addition amount of B in the invention is less than or equal to 0.0003 percent.
P, S is a harmful impurity element in steel, P in steel is easy to form segregation in steel, toughness and welding performance of steel are reduced, S is easy to form plastic sulfide, layering is generated on a steel plate, and performance of the steel plate is deteriorated, so that the lower the P, S content is, the better, and the P, S content of steel is less than or equal to 0.015% and the S is less than or equal to 0.005% comprehensively considered.
Compared with the prior art, the invention has the following effects:
the invention adopts lower finishing temperature, can fully refine the prior austenite grains, directly influences nucleation and growth of ferrite grains in the subsequent air cooling process, and further influences the size and quantity. In addition, the size of the martensite lath after final rapid cooling is thinned, and the strength is improved, so that higher strength and hardness are obtained under the condition of certain ferrite.
The invention can lead the steel plate to generate gradient fine ferrite along the thickness section in the air cooling stage of the cooling process, and form a large amount of martensite in the subsequent ultra-fast cooling stage, thereby ensuring the strength and the hardness and improving the toughness.
The invention has simple components and low alloy content, and reduces the cost; meanwhile, the welding performance is excellent, and the preheating-free welding can be realized.
The invention has better welding performance than the same-grade quenched and tempered wear-resistant steel, low post-welding hardening tendency and obviously reduced cracking risk.
Drawings
Fig. 1: a weld zone hardness profile for the product obtained in example 2;
fig. 2: weld zone hardness profile of the product obtained in comparative example 1.
Detailed Description
The following examples further illustrate the technical aspects of the present invention, but are not intended to limit the scope of the present invention.
The specific embodiment provides HB450 grade wear-resistant steel with excellent welding performance, which comprises the following chemical components in percentage by weight: c:0.10 to 0.18 percent, si:0.1 to 0.3 percent, mn:0.5 to 1.5 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, als:0.03 to 0.06 percent, nb:0.02 to 0.03 percent of Ti: 0.005-0.02%, cr:0.1 to 0.3 percent, B:0 to 0.0003 percent, and the balance of Fe and impurities.
The specific embodiment also provides a production method of the HB450 grade wear-resistant steel, which comprises smelting, continuous casting, heating, rough rolling, finish rolling, cooling, coiling and transverse cutting processes.
Specifically, in the heating process, the temperature of the final section of the secondary addition soaking is 1200-1250 ℃, the secondary addition soaking time is more than or equal to 40min, and the total furnace time is controlled to be more than or equal to 120min.
Specifically, the outlet temperature in the rough rolling process is 1020-1080 ℃, and the thickness of the intermediate billet is 30-50 mm.
Specifically, the initial rolling temperature in the finish rolling process is 910-980 ℃, and the finish rolling finishing temperature is 850-890 ℃. The prior austenite grains can be fully refined by adopting lower finishing temperature, so that the nucleation and growth of ferrite grains in the subsequent air cooling process are directly influenced, and the size and quantity are further influenced. In addition, the size of the martensite lath after final rapid cooling is thinned, and the strength is improved, so that higher strength and hardness are obtained under the condition of certain ferrite.
Specifically, in the cooling process, FT7 is immediately cooled to 600-700 ℃ at a cooling rate of 30-50 ℃/s, air-cooled for 2-8 s, and then cooled to below 100 ℃ at a cooling rate of 200-300 ℃/s for coiling. The air cooling stage can lead to the formation of gradient fine ferrite on the steel plate along the thickness section, and a large amount of martensite is formed in the subsequent ultra-fast cooling stage, so that the strength and the hardness are ensured, and the toughness is improved.
The chemical components and the weight percentages of the HB450 grade wear-resistant steel with excellent welding performance in examples 1-10 are shown in Table 1, and the chemical components and the weight percentages of the traditional wear-resistant steel in comparative examples 1-2 are shown in Table 1.
TABLE 1
| C/％ | Si/％ | Mn/％ | P/％ | S/％ | Als/％ | Nb/％ | Ti/％ | Cr/％ | Mo/％ | |
| Example 1 | 0.15 | 0.23 | 1.2 | 0.007 | 0.015 | 0.04 | 0.023 | 0.018 | 0.25 | - |
| Example 2 | 0.11 | 0.1 | 0.5 | 0.007 | 0.015 | 0.04 | 0.027 | 0.005 | 0.26 | - |
| Example 3 | 0.12 | 0.19 | 0.8 | 0.014 | 0.007 | 0.05 | 0.027 | 0.015 | 0.3 | - |
| Example 4 | 0.18 | 0.2 | 1.1 | 0.015 | 0.007 | 0.04 | 0.029 | 0.009 | 0.27 | - |
| Example 5 | 0.14 | 0.11 | 1.3 | 0.008 | 0.005 | 0.04 | 0.021 | 0.013 | 0.22 | - |
| Example 6 | 0.11 | 0.15 | 1.4 | 0.006 | 0.009 | 0.06 | 0.029 | 0.017 | 0.27 | - |
| Example 7 | 0.18 | 0.1 | 0.5 | 0.01 | 0.005 | 0.03 | 0.03 | 0.008 | 0.29 | - |
| Example 8 | 0.14 | 0.16 | 0.7 | 0.013 | 0.015 | 0.05 | 0.025 | 0.006 | 0.15 | - |
| Example 9 | 0.17 | 0.25 | 1.1 | 0.015 | 0.01 | 0.06 | 0.027 | 0.011 | 0.28 | - |
| Example 10 | 0.13 | 0.26 | 0.6 | 0.009 | 0.011 | 0.04 | 0.025 | 0.006 | 0.15 | - |
| Comparative example 1 | 0.19 | 0.3 | 1.4 | 0.012 | 0.003 | 0.034 | — | 0.020 | 0.30 | 0.22 |
| Comparative example 2 | 0.21 | 0.2 | 1.2 | 0.011 | 0.004 | 0.04 | — | 0.023 | — | 0.34 |
The HB450 grade wear-resistant steel with excellent welding performance and the production method adopt smelting, continuous casting, heating, rough rolling, finish rolling, cooling, coiling and transverse cutting process routes, wherein,
1) Heating: the temperature of the second adding soaking end section is 1200-1250 ℃, the second adding soaking time is more than or equal to 40min, and the total furnace time is controlled to be more than or equal to 120min.
2) Rough rolling: the outlet temperature of rough rolling is 1020-1080 ℃, and the thickness of the intermediate billet is 30-50 mm.
3) Finish rolling: the finish rolling temperature is 910 ℃ to 980 ℃, and the finish rolling finishing temperature is 850 ℃ to 890 ℃.
4) Cooling and coiling: cooling immediately after FT7 is carried out, cooling to 600-700 ℃ at a cooling rate of 30-50 ℃/s, cooling to 100 ℃ at a cooling rate of 200-300 ℃/s after air cooling for 2-8 s, and coiling.
Specific process data for the production process characteristics in examples 1-10 and comparative examples 1-2 are shown in tables 2, 3.
TABLE 2
TABLE 3 Table 3
The performance of HB450 grade wear resistant steels with excellent welding performance obtained in examples 1-10 and comparative examples 1-2 according to GB/T228 and GB/T231 national standards are shown in Table 4.
TABLE 4 Table 4
| Examples | Yield strength/MPa | Tensile strength of/MPa | A/％ |
| Example 1 | 1225 | 1399 | 9.6 |
| Example 2 | 1222 | 1270 | 10.3 |
| Example 3 | 1175 | 1232 | 9.8 |
| Example 4 | 1127 | 1267 | 9.7 |
| Example 5 | 1176 | 1244 | 9.9 |
| Example 6 | 1234 | 1325 | 10.3 |
| Example 7 | 1194 | 1367 | 9.3 |
| Example 8 | 1240 | 1285 | 10.2 |
| Example 9 | 1215 | 1343 | 9.7 |
| Example 10 | 1225 | 1298 | 10.3 |
| Comparative example 1 | 1134 | 1358 | 10 |
| Comparative example 2 | 1111 | 1330 | 11.2 |
The weld zone hardness profile of the product obtained in example 2 is shown in FIG. 1, and the weld zone hardness profile of the product obtained in comparative example 1 is shown in FIG. 2. As can be seen by comparison, in FIG. 1, there is no apparent hardening area in each area after welding, while the welding area of the quenched and tempered NM450 has an apparent hardening area, which is prone to cracking during welding and application.
The foregoing is merely a preferred embodiment of the present invention, and it will be apparent to those skilled in the art that modifications and variations can be made without departing from the inventive concept.
Claims (6)
1. The HB450 grade wear-resistant steel with excellent welding performance is characterized by comprising the following chemical components in percentage by weight: c:0.10 to 0.18 percent, si:0.1 to 0.3 percent, mn:0.5 to 1.5 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, als:0.03 to 0.06 percent, nb:0.02 to 0.03 percent of Ti: 0.005-0.02%, cr:0.1 to 0.3 percent, B:0 to 0.0003 percent, and the balance of Fe and impurities.
2. The production method of the HB450 grade wear-resistant steel is characterized by comprising the following steps of smelting, continuous casting, heating, rough rolling, finish rolling, cooling, coiling and transverse cutting.
3. The method for producing HB450 grade wear-resistant steel according to claim 2, wherein in the heating process, the temperature of the second addition soaking end section is 1200-1250 ℃, the second addition soaking time is more than or equal to 40min, and the total furnace time is controlled to be more than or equal to 120min.
4. The method for producing HB450 grade wear-resistant steel according to claim 2, wherein the outlet temperature in the rough rolling process is 1020-1080 ℃, and the thickness of the intermediate billet is 30-50 mm.
5. The method for producing HB450 grade abrasion resistant steel according to claim 2 wherein the initial rolling temperature in the finish rolling process is 910℃to 980℃and the finish rolling finishing temperature is 850℃to 890 ℃.
6. The method for producing HB450 grade wear-resistant steel according to claim 2, wherein in the cooling process, FT7 is immediately cooled to 600 ℃ to 700 ℃ at a cooling rate of 30 ℃ to 50 ℃/s, and after air cooling for 2 to 8 seconds, cooling to below 100 ℃ at a cooling rate of 200 ℃ to 300 ℃/s, and coiling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202211102245.6A CN116287970A (en) | 2022-09-09 | 2022-09-09 | HB 450-grade wear-resistant steel with excellent welding performance and production method thereof |
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008255451A (en) * | 2007-04-09 | 2008-10-23 | Jfe Steel Kk | Method for producing abrasion resistant steel sheet |
| CN107829026A (en) * | 2017-10-19 | 2018-03-23 | 武汉钢铁有限公司 | A kind of Thin Specs 980MPa levels dual phase steel and its processing method |
| CN111607736A (en) * | 2020-06-28 | 2020-09-01 | 武汉钢铁有限公司 | Wear-resistant steel with excellent welding performance and production method thereof |
| CN113637894A (en) * | 2021-06-30 | 2021-11-12 | 武汉钢铁有限公司 | Leveling-free and tempering-free HB 450-grade wear-resistant steel and production method thereof |
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Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008255451A (en) * | 2007-04-09 | 2008-10-23 | Jfe Steel Kk | Method for producing abrasion resistant steel sheet |
| CN107829026A (en) * | 2017-10-19 | 2018-03-23 | 武汉钢铁有限公司 | A kind of Thin Specs 980MPa levels dual phase steel and its processing method |
| CN111607736A (en) * | 2020-06-28 | 2020-09-01 | 武汉钢铁有限公司 | Wear-resistant steel with excellent welding performance and production method thereof |
| CN113637894A (en) * | 2021-06-30 | 2021-11-12 | 武汉钢铁有限公司 | Leveling-free and tempering-free HB 450-grade wear-resistant steel and production method thereof |
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