CN112575252A - Economical high-crack-sensitivity high-strength steel plate and preparation method thereof - Google Patents
Economical high-crack-sensitivity high-strength steel plate and preparation method thereof Download PDFInfo
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- CN112575252A CN112575252A CN202011299678.6A CN202011299678A CN112575252A CN 112575252 A CN112575252 A CN 112575252A CN 202011299678 A CN202011299678 A CN 202011299678A CN 112575252 A CN112575252 A CN 112575252A
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/46—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting
- B21B1/466—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling metal immediately subsequent to continuous casting in a non-continuous process, i.e. the cast being cut before 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
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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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- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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Abstract
The invention discloses an economical high-crack-sensitivity high-strength steel plate and a preparation method thereof, wherein a component system of high Mn, high Ti, high Cr and a proper amount of Nb is adopted, and simultaneously, the requirements of (3Ti + Cr)/10Nb which is more than or equal to 1.12 and less than or equal to 2.90 are met, the tensile strength of the steel plate is more than or equal to 900MPa, the yield ratio is more than or equal to 0.92, the steel plate has good forming performance, and the quenching and tempering production is not needed. The composition has the advantages of low production cost, but the content of alloy elements such as Mn, Cr and the like which reduce the toughness of the plate blank material is high due to the activity of Ti element, so that cracks are easy to appear in the cooling and heating processes of the plate blank, the problems of rolling cracking and even blank breaking are common, and the tissue production is difficult. Therefore, in the preparation process, the charging temperature is controlled to be 570-750 ℃, so that the area with low reduction of area can be avoided in the casting blank cooling process, the internal stress of the casting blank is reduced, the casting blank is prevented from cracking, and the key points of controlling the crack sensitivity of the steel and ensuring stable production are achieved.
Description
Technical Field
The invention belongs to the technical field of hot continuous rolling steel plate manufacturing, and particularly relates to an economical high-crack-sensitivity high-strength steel plate and a preparation method thereof.
Background
With the continuous development of industries such as engineering machinery, mining vehicle manufacturing and the like, the high strength, the thinning and the wear resistance of steel plate materials become the current mainstream development trend, the high strength and the thinning can reduce the weight of equipment, improve the capacity of the equipment, and effectively prolong the service life of the equipment due to the wear resistance. Meanwhile, with the increasing competition of the industries on the upstream and downstream, the economic steel materials with low cost have become the main development direction of steel products with similar performance indexes.
At present, in order to obtain the hot-rolled high-strength steel plate for the industries of engineering machinery, mining vehicle manufacturing and the like with the yield strength reaching 700-900MPa, a quenching and tempering production scheme designed by high alloy cost or a direct rolling production scheme designed by economic alloy cost containing Ti components are mainly adopted. In comparison, the production process of the quenching and tempering production scheme is stable, but the cost is relatively high. The smelting cost can be greatly reduced by adopting the economic alloy cost design containing the Ti component. However, as Ti element is active, the alloy content is high, the steel plate has high strength requirement and high cooling strength, cracks are very easy to appear in the plate blank cooling and heating processes, the production problems of rolling cracking, even blank breaking and the like generally exist, the steel belongs to high-crack sensitivity steel, and the production process is difficult to control. At present, the cracking problem of common high crack sensitivity steel is mainly solved at home and abroad by adopting a slow cooling pit slow cooling method or a cover-covering slow cooling method, the effect is good, but the rolling cracking problem still often occurs on the varieties with high part crack sensitivity, and the complete avoidance is difficult. Therefore, when an economical high-strength steel plate with excellent performances is manufactured by a reasonable production method, the adverse effect of high crack sensitivity on the rolling production process is thoroughly eliminated, and the important direction of the current urgent research is provided.
Disclosure of Invention
The invention aims to provide an economical high-crack-sensitivity high-strength steel plate which avoids cracking and ensures smooth production and a preparation method thereof aiming at the defects of the prior art.
In order to achieve the purpose, the economical high-crack-sensitivity high-strength steel plate designed by the invention comprises the following chemical elements in percentage by weight: 0.01 to 0.15%, Si: 0.03 to 0.40%, Mn: 1.5-2.5%, P: less than or equal to 0.020%, S: less than or equal to 0.008 percent, Ti: 0.12-0.22%, Nb: 0.04-0.07%, Cr: 0.15-0.80%, and the balance of Fe and impurities, wherein (3Ti + Cr)/10Nb is not less than 1.12 and not more than 2.90.
Selectively adding trace V, B and other elements under the condition of ensuring the mechanical property of the steel plate, such as V: 0-0.015%, B: 0-0.0006 percent of the steel wire used for refining grains, improving toughness and uniformity of structural components.
Furthermore, the thickness of the steel plate is 2-12 mm, the tensile strength is 900-1050 MPa, and the yield ratio is 0.92-0.94.
C: the content is controlled within the range of 0.01-0.15%. Carbon is a main element for improving strength and wear resistance, and the strength of the steel sheet can be ensured only if it is contained in an amount of 0.01% or more. However, too high C lowers the ductility and weldability of the steel, and is preferably 0.08 to 0.11%.
Si: the content is controlled within the range of 0.03-0.40%. Silicon is an essential element for steelmaking deoxidization, the strength of steel is improved in a solid solution strengthening mode, the deoxidization effect is poor when the content is too low, low-melting-point silicate can be generated when the content is too high in subsequent straight seam resistance welding, the fluidity of slag and molten metal is increased, the quality of a welding seam is reduced, and the welding performance is reduced, and the preferable content is 0.13-0.38%.
Mn: the content is controlled to be 1.5-2.5%. The proper amount of manganese can effectively eliminate the influence of sulfur and oxygen on the hot brittleness of the steel plate and improve the hot workability of the steel. Mn and iron form a solid solution, so that the hardness and strength of ferrite and austenite in the steel are improved, and a matrix is strengthened; meanwhile, Mn is a carbide forming element and enters cementite to replace part of iron atoms to generate Mn3C, it is mixed with Fe3C can be dissolved in each other and formed in the steel (Fe Mn)3The C-type compound improves the strength and hardness of the steel and improves the wear resistance of the steel plate. Therefore, in order to ensure the performance of the steel plate, the manganese content is controlled to be more than 1.5 wt%. However, too high manganese causes severe center segregation and decreases toughness, and is preferably 1.76 to 1.82%.
Ti: the content is controlled to be 0.12-0.22%. Ti is an economical microalloy element, and can greatly reduce the alloy cost. The addition of a certain amount of Ti can improve the strength and the welding performance of the steel through solid solution strengthening and precipitation strengthening while reducing the carbon equivalent. Proper amount of titanium generates dispersed TiN particles under the condition of continuous casting and cooling, and because the melting point of the titanium is very high, the coarsening of crystal grains in a heat affected zone can be prevented, the toughness of the heat affected zone is improved, and the welding performance of steel is improved. However, Ti element is very active, and the high addition amount causes the low-temperature toughness of the steel to be difficult to control, and the crack sensitivity of the steel is greatly increased. Meets the requirements that (3Ti + Cr)/10Nb is more than or equal to 1.12 and less than or equal to 2.90 so as to ensure the economical efficiency and the yield ratio of the steel plate.
Nb: the content is controlled to be 0.04-0.070%. Niobium can refine crystal grains and enhance the strength and the hardness by dispersion strengthening, and the niobium can refine the crystal grains and enhance the dispersion strengthening by less than 0.10 wt%. Meanwhile, in order to improve the economy of the steel plate, the requirement that (3Ti + Cr)/10Nb is more than or equal to 1.12 and less than or equal to 2.90 is met so as to ensure the economy and yield ratio of the steel plate.
Cr: the content is controlled to be 0.15-0.80%. The proper amount of Cr can effectively improve the strength of the steel plate, the low-temperature toughness and the elongation of the steel plate are obviously reduced due to the overhigh amount of Cr, and meanwhile, in order to ensure the economy and the mechanical property, the requirement that (3Ti + Cr)/10Nb is more than or equal to 1.12 and less than or equal to 2.90 is met so as to ensure the economy and the yield ratio of the steel plate.
Further, the range of (3Ti + Cr)/10Nb is 2.02-2.85.
The preparation method of the economical high-crack-sensitivity high-strength steel plate comprises the following production process flows: blast furnace molten iron → molten iron pre-desulfurization → converter smelting → LF + RH refining → slab continuous casting → slab heating → hot continuous rolling → laminar cooling → coiling;
directly charging and heating the plate blank in a furnace without discharging after continuous casting and cutting, and strictly controlling the charging temperature to be 570-750 ℃ so as to ensure the quality of the plate blank and ensure the rolling stability; discharging at 1250-1330 ℃, heating for 140-300 min, descaling after discharging, and then rolling in a hot continuous rolling mill;
the rough rolling temperature of the plate blank is 980-1140 ℃, the finish rolling temperature is 800-920 ℃, and the coiling temperature is 580-700 ℃.
The method adopts a component system of high Mn, high Ti, Cr and a proper amount of Nb, does not basically add high-cost alloy elements such as Mo, Ni, V, Cu and the like, and simultaneously satisfies the conditions that (3Ti + Cr)/10Nb is less than or equal to 2.90, and adopts a proper rolling process to obtain an economical high-strength steel plate, wherein the tensile strength of the steel plate is more than or equal to 900MPa, the yield ratio is more than or equal to 0.92, and the steel plate has good formability and does not need tempering production. The composition has the advantages of low production cost, but the content of alloy elements such as Mn, Cr and the like which reduce the toughness of the plate blank material is high due to the activity of Ti element, so that cracks are easy to appear in the cooling and heating processes of the plate blank, the problems of rolling cracking and even blank breaking are common, and the tissue production is difficult. Therefore, in the preparation process, the charging temperature is controlled to be 570-750 ℃, so that the area with low reduction of area can be avoided in the casting blank cooling process, the internal stress of the casting blank is reduced, the casting blank is prevented from cracking, and the key points of controlling the crack sensitivity of the steel and ensuring stable production are achieved.
Further, the charging temperature is 575-692 ℃, and the discharging temperature is 1278-1326 ℃.
Further, the rough rolling temperature of the plate blank is 1130-1140 ℃, the finish rolling temperature of the plate blank is 890-910 ℃, and the coiling temperature of the plate blank is 660-680 ℃.
Compared with the prior art, the invention has the following advantages: the tensile strength of the steel plate is more than or equal to 900MPa, the yield ratio is more than or equal to 0.92, and the steel plate has good forming performance and does not need quenching and tempering production. (ii) a By controlling the charging temperature, the casting blank can be ensured to avoid a region with lower reduction of area in the cooling process, the internal stress of the casting blank is reduced, and the casting blank is prevented from generating cracks, so that the method is the key for controlling the crack sensitivity of the steel and ensuring stable production.
Detailed Description
The present invention will be described in further detail with reference to specific examples.
TABLE 1 chemical composition (wt%) of inventive examples 1 to 6 and comparative examples 1 to 3
Example 1
The chemical compositions of the economical high-crack-sensitivity high-strength steel sheet of the present invention are shown in table 1. Smelting according to the chemical components shown in Table 1, charging the continuously cast billets or steel ingots at 583 ℃, heating to 1297 ℃, the rough rolling and final rolling temperature of 1110 ℃, the finish rolling temperature of 870 ℃ and the coiling temperature of 610 ℃.
Example 2
The process is carried out as in example 1, wherein the slab or ingot is charged at 605 ℃ after the smelting, heated to 1313 ℃, a rough rolling finishing temperature of 1120 ℃, a finish rolling finishing temperature of 860 ℃ and a coiling temperature of 620 ℃.
Example 3
The embodiment is as in example 1, wherein the continuously cast slab or ingot after smelting is charged at 647 ℃, heated to 1321 ℃, rough rolling and final rolling temperature is 1100 ℃, finish rolling temperature is 850 ℃ and coiling temperature is 600 ℃.
Example 4
The process is carried out as in example 1, wherein the strand or ingot is charged at 706 ℃ after the smelting, heated to 1303 ℃, a rough rolling finishing temperature of 1110 ℃, a finish rolling finishing temperature of 880 ℃ and a coiling temperature of 650 ℃.
Example 5
The embodiment is as in example 1, wherein the continuously cast slab or ingot is charged at 575 ℃ after smelting, heated to 1326 ℃, the rough rolling finishing temperature is 1130 ℃, the finish rolling finishing temperature is 890 ℃ and the coiling temperature is 660 ℃.
Example 6
The embodiment is as in example 1, wherein the slab or ingot is charged at 692 ℃ after smelting, heated to 1278 ℃, rough rolling finishing temperature 1140 ℃, finish rolling finishing temperature 910 ℃, and coiling temperature 680 ℃.
Comparative example 1
The process is carried out as in example 1, wherein the slab or ingot is charged at 541 ℃ after the smelting, heated to 1286 ℃, the rough rolling finishing temperature 1130 ℃, the finish rolling finishing temperature 890 ℃ and the coiling temperature 650 ℃.
Comparative example 2
The process is carried out as in example 1, wherein the slab or ingot is charged at 176 ℃ after the smelting, heated to 1297 ℃, a rough rolling finishing temperature of 1120 ℃, a finish rolling finishing temperature of 890 ℃ and a coiling temperature of 660 ℃.
Comparative example 3
The process is carried out as in example 1, wherein the slab or ingot is charged after the smelting at 582 ℃, heated to 1306 ℃, rough rolling finishing temperature 1110 ℃, finish rolling finishing temperature 870 ℃ and coiling temperature 620 ℃.
The rolling production conditions and the mechanical property test results of the finished products of each example and each comparative example are shown in table 2, and the examples can meet the design requirements of the invention, and have stable rolling process and good mechanical property. In the comparative example which can not meet the requirements of the invention, when the charging temperature is not strictly controlled and the alloy elements can not meet the requirements of (3Ti + Cr)/10Nb less than or equal to 1.12 and 2.90, the performances of the steel such as rolling stability, yield ratio and the like can not meet the requirements of the invention.
Table 2 properties and rolling stability of examples 1 to 6 of the present invention and comparative examples 1 to 3.
Claims (10)
1. An economical high-crack-sensitivity high-strength steel plate is characterized in that: the chemical elements comprise C: 0.01 to 0.15%, Si: 0.03 to 0.40%, Mn: 1.5-2.5%, P: less than or equal to 0.020%, S: less than or equal to 0.008 percent, Ti: 0.12-0.22%, Nb: 0.04-0.07%, Cr: 0.15-0.80%, and the balance of Fe and impurities, wherein (3Ti + Cr)/10Nb is not less than 1.12 and not more than 2.90.
2. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the chemical elements further comprise V in percentage by weight: 0-0.015%, B: 0 to 0.0006%.
3. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the thickness of the steel plate is 2-12 mm, the tensile strength is 900-1050 MPa, and the yield ratio is 0.92-0.94.
4. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the weight percentage of C is 0.08-0.11%.
5. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the weight percentage of the Si is 0.13-0.38%.
6. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the weight percentage of Mn is 1.76-1.82%.
7. The economical high crack-sensitive high-strength steel sheet as set forth in claim 1, wherein: the range of (3Ti + Cr)/10Nb is 2.02-2.85.
8. The method for preparing the economical high-crack-sensitivity high-strength steel plate as claimed in claim 1 comprises the following production process flows: blast furnace molten iron → molten iron pre-desulfurization → converter smelting → LF + RH refining → slab continuous casting → slab heating → hot continuous rolling → laminar cooling → coiling; the method is characterized in that:
directly charging and heating a plate blank in a furnace without taking off the line after continuous casting and cutting, wherein the charging temperature is 570-750 ℃, the discharging temperature is 1250-1330 ℃, the heating time is 140-300 min, descaling after discharging, and then rolling in a hot continuous rolling mill;
the rough rolling temperature of the plate blank is 980-1140 ℃, the finish rolling temperature is 800-920 ℃, and the coiling temperature is 580-700 ℃.
9. The method for manufacturing an economical high crack-sensitivity high strength steel sheet according to claim 8, wherein: the charging temperature is 575-692 ℃, and the discharging temperature is 1278-1326 ℃.
10. The method for manufacturing an economical high crack-sensitivity high strength steel sheet according to claim 8, wherein: the rough rolling temperature of the plate blank is 1130-1140 ℃, the finish rolling temperature of the plate blank is 890-910 ℃, and the coiling temperature of the plate blank is 660-680 ℃.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115351094A (en) * | 2022-06-28 | 2022-11-18 | 武安市裕华钢铁有限公司 | Production method of carbon structural steel for pipe making with low welding crack sensitivity |
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2020
- 2020-11-19 CN CN202011299678.6A patent/CN112575252A/en active Pending
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| JP2007254797A (en) * | 2006-03-22 | 2007-10-04 | Jfe Steel Kk | Thick electric resistance welded pipe having excellent toughness in base metal part and electric resistance weld zone and its production method |
| CN101736199A (en) * | 2008-11-18 | 2010-06-16 | 鞍钢股份有限公司 | Hot-rolled strip steel for high-strength cold-formed welded structure and manufacturing method thereof |
| CN101497972A (en) * | 2009-03-13 | 2009-08-05 | 武汉钢铁(集团)公司 | High strength low yield ratio welding structure steel and production method thereof |
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