CN108823504B - 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel and preparation process thereof - Google Patents
500 MPa-grade wear-resistant impact-resistant fracture-resistant steel and preparation process thereof Download PDFInfo
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Abstract
The invention discloses 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel which comprises the following components in percentage by mass: 0.041 to 0.106 percent of C, 0.10 to 0.45 percent of Si, 0.82 to 1.85 percent of Mn, less than or equal to 0.010 percent of P, less than or equal to 0.004 percent of S, 0.045 to 0.095 percent of Als, 0.030 to 0.060 percent of Nb, 0.038 to 0.060 percent of V, 0.030 to 0.105 percent of Ti, 1.35 to 2.61 percent of Ni, 0.31 to 0.80 percent of Mo and 0.30 to 0.60 percent of Cr; in addition, one or two of Zr and RE are contained. The steel obtained by the invention has high strength, impact fracture resistance and wear resistance; the ship is particularly suitable for extreme environments such as arctic ice regions and the like, and the safe use performance of the ship body is improved; and the related preparation method is simple, low in cost and suitable for popularization and application.
Description
Technical Field
The invention belongs to the technical field of steel materials, and particularly relates to 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel and a preparation process thereof.
Background
The ocean contains abundant resources, the opening of the arctic channel saves a large amount of ocean transportation resources for various countries, promotes the development of new concept ships such as arctic shuttle oil tankers, icebreakers and the like, and simultaneously also provides new requirements for the steel for the high-grade ships: on the one hand, these marine steels are required to have high strength and excellent toughness, especially impact fracture resistance (e.g., NDT properties); on the other hand, the steel material is required to have a certain wear resistance even when the ship body is in contact with an ice surface for a long time.
The Chinese patent application No. CN201210067794.4 discloses an extra-thick high-strength excellent low-temperature toughness steel plate for an ocean platform and a manufacturing method thereof, wherein a C, Ni-Cr-Mo alloying and Nb-V-Ti microalloying component system is adopted, and the weight percentage of the components is as follows: 0.10-0.24% of C, 0.05-0.35% of Si, 0.60-1.15% of Mn, less than or equal to 0.015% of P, less than or equal to 0.005% of S, 0.01-0.030% of Ti, 1.45-1.75% of Cr, 0.15-0.44% of Mo, 0.80-2.50% of Ni, 0.010-0.070% of Nb0.020-0.080% of V, 0.02-0.06% of Alt, 0.001-0.004% of Ca, less than or equal to 0.006% of N and 0.0007-0.0030% of B; the process conditions comprise: heating the plate blank at 1150-1300 ℃ and finishing at 900-1100 ℃, cooling after rolling, and cooling the plate blank to a pit temperature below 400 ℃; stress relief annealing temperature: cooling the mixture to below 200 ℃ along with the furnace at 450-600 ℃; slab reheating temperature: 1050-1200 ℃, the finishing temperature is 900-1000 ℃, cooling is carried out after rolling, and the pit is cooled to below 400 ℃; quenching at the heating temperature of 900-980 ℃ by water; the tempering and heating temperature is 580-680 ℃. By adopting the component process, the tempered steel with different thickness specifications has tempered sorbite and martensite structures, high strength and excellent low-temperature toughness are ensured, the yield strength of the obtained steel is more than or equal to 690MPa, the tensile strength is more than or equal to 770MPa, the charpy V-notch impact energy at-40 ℃ is more than or equal to 69J, NDT and less than or equal to-35 ℃, Z is more than or equal to 35 percent, and the maximum thickness reaches more than 200mm, so that the rack can be used for manufacturing racks for ocean platforms. But the NDT drop hammer temperature of the steel is only-35 ℃, which is not beneficial to large-scale oil-carrying vessels and container ships to run in cold and icy areas in polar regions; in addition, the steel grade needs to be subjected to stress relief annealing process, and the production flow is long.
The Chinese patent application No. CN201710719496.1 discloses a corrosion-resistant wear-resistant steel plate and a production method thereof, and the steel plate comprises the following chemical components in percentage by mass: 0.18-0.23% of C, 0.60-0.80% of Si, 1.20-1.60% of Mn1.010%, less than or equal to 0.010% of P, less than or equal to 0.002% of S, 0.85-1.15% of Cr, 0.25-0.35% of Mo, 0.60-0.80% of Al, 0.20-0.30% of Ni, 0.04-0.06% of V, and the balance of Fe and inevitable impurities; the steel plate production method comprises the working procedures of smelting, continuous casting, electroslag remelting, heating, rolling, hydrogen diffusion, quenching and tempering. The steel plate produced by the method has excellent mechanical properties and remarkably improved corrosion resistance by adjusting the chemical components of the steel plate and combining proper process technologies such as smelting, heating, rolling, heat treatment and the like; however, the toughness of the steel is relatively low, which is not beneficial to improving the running safety of large-scale heavy-duty oil tanker, container ship and icebreaker in polar regions with high and cold water, and the steel plate production method comprises the working procedures of smelting and continuous casting, electroslag remelting, heating, rolling, hydrogen diffusion, quenching and tempering, and has long production flow and high cost.
Disclosure of Invention
The invention mainly aims to provide 500 MPa-grade wear-resistant impact-resistant fracture steel aiming at the problems of requirements on high strength, impact-resistant fracture performance (NDT performance) and wear resistance in the fields of extreme environments and the like, wherein the steel has excellent strength, impact-resistant fracture performance and weather resistance, and can keep excellent service performance particularly under the low-temperature extreme condition; and the related preparation process is simple, the preparation cost is low, and the method is suitable for popularization and application.
In order to realize the scheme, the technical scheme adopted by the invention is as follows:
500 MPa-grade wear-resistant impact-resistant fracture-resistant steel comprises the following components in percentage by mass: 0.041-0.106 percent of C, 0.10-0.45 percent of Si, 0.82-1.85 percent of Mn, less than or equal to 0.010 percent of P, less than or equal to 0.004 percent of S, 0.045-0.095 percent of Als, 0.030-0.060 percent of Nb0.030, 0.038-0.060 percent of V, 0.030-0.105 percent of Ti, 1.35-2.61 percent of Ni, 0.31-0.80 percent of Mo and 0.30-0.60 percent of Cr0.30; further, one or both of Zr and RE (rare earth element) are contained.
In the scheme, in the 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel, Zr and RE account for the following mass percent respectively: 0.02-0.08% of Zr and 0.15-0.20% of RE.
Preferably, in the 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel, the components and the mass percentages thereof comprise: 0.061-0.086% of C, 0.30-0.40% of Si, 1.52-1.85% of Mn, less than or equal to 0.010% of P, less than or equal to 0.003% of S, 0.075-0.095% of Als, 0.038-0.060% of Nb, 0.048-0.060% of V, 0.080-0.105% of Ti, 1.95-2.61% of Ni, 0.51-0.80% of Mo, 0.40-0.60% of Cr0.05-0.08% of Zr, 0.15-0.20% of RE, and the balance of Fe and inevitable impurities.
The preparation method of the 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel comprises the following steps:
1) desulfurizing molten iron, and controlling S in the molten iron to be less than or equal to 0.001 wt%;
2) performing converter smelting, and controlling the content of C in the molten steel to be 0.041-0.106 wt% and P to be less than or equal to 0.010 wt%;
3) carrying out conventional continuous casting and heating the casting blank, wherein the heating temperature is controlled to be 1205-1290 ℃;
4) carrying out sectional rolling, wherein the initial rolling temperature of rough rolling is 1085-1198 ℃, and the rough rolling pass is controlled not to be higher than 5 passes; and controlling the starting temperature of finish rolling to be not higher than 988 ℃, controlling the finish rolling temperature to be 810-875 ℃, controlling the pass of finish rolling to be not higher than 5 passes, and controlling the cumulative reduction rate of the last three passes to be not less than 34%.
5) Carrying out quenching heat treatment, wherein the quenching process comprises the following steps: heating at 905-925 ℃, keeping the temperature for (plate thickness +40) min, and cooling: water cooling;
6) carrying out tempering heat treatment, wherein the tempering process comprises the following steps: heating at 480-550 ℃, keeping the temperature for (plate thickness +60) min, and cooling: and air cooling.
The principle of the invention is as follows:
design of first, component
C is an essential element for improving the comprehensive performance of steel, the strength of the steel can be effectively improved, the yield and the tensile strength are respectively improved by about 50MPa and 90MPa when the carbon content is increased by 0.1%, the C element is combined with Nb, V, Ti, Mo and other elements in the steel and is precipitated in the form of carbide or carbonitride, the structure is refined, the strength and the toughness are improved, and the welding performance is improved; however, as the C content increases, Fe will increase3C content, hardenability, carbon segregation, M-A island contentAnd welding cold crack sensitivity coefficient, thereby deteriorating ductility, welding performance and cold and hot workability, and aggravating the tendency of generating cold cracks during welding; in order to ensure that the steel plate obtains good comprehensive performance, the carbon element content of the steel is designed to be 0.041-0.106%.
Si element does not form carbide in steel, but exists in the steel in the form of solid solution, and can obviously improve the strength of the solid solution in the steel, but also reduces the toughness and plasticity to a certain extent; the Si content of the invention is limited to 0.10-0.45%.
Mn is an important strengthening and toughening element, the strength of steel is obviously increased along with the increase of Mn content, and the tensile strength can be improved by about 100MPa by containing 1% of Mn; mn is an indispensable element for ensuring the obdurability of steel and the low-temperature toughness of a welding heat affected zone, and a proper amount of Mn can refine the structure, improve the strength and improve the low-temperature toughness; excessive Mn promotes austenite grains to grow during heating, and the structure size of a final coarsened product is not favorable for low-temperature toughness and welding performance; therefore, the Mn content of the steel is limited to 0.82-1.85%.
P, S is an impurity element in steel, P is an element easy to segregate, and the element can seriously segregate in the local part of the steel, reduce the plasticity and the toughness and is extremely harmful to the low-temperature toughness; s and P are easy to segregate and enrich in steel, S and Mn are easy to form coarse MnS inclusions, low-temperature toughness and performance in the thickness direction are damaged, and the coarse MnS inclusions are easy to become crack sources for forming cracks; the invention strictly controls the content levels of sulfur and phosphorus in the aspect of metallurgical quality, namely P is less than or equal to 0.010 percent and S is less than or equal to 0.004 percent, so as to meet the requirements of steel grades on purity and toughness.
Al is a main deoxidizing element in steel, the melting point of Al is high, Al and N in the steel can form AlN in production, and the AlN can prevent high-temperature austenite from growing and plays a role in refining grains; the preferred Als content of the invention is 0.045-0.095%.
Nb and Ti are two strong carbide and nitride forming elements, have strong affinity with nitrogen and carbon, and can form extremely stable carbonitride with the nitrogen and the carbon; the distribution of the dispersed Nb carbonitride second phase particles along the austenite grain boundary can greatly improve the coarsening temperature of original austenite grains, the Nb carbonitride precipitate can be used as the nucleation core of the austenite grains in the austenite recrystallization temperature region in the rolling process, and the dispersed Nb carbonitride precipitate can effectively pin the austenite grain boundary in the non-recrystallization temperature range to prevent the austenite grains from further growing up, thereby refining ferrite grains and achieving the purpose of improving the strength and the impact toughness; the Ti nitride can effectively pin the austenite grain boundary, is beneficial to controlling the growth of austenite grains and greatly improves the low-temperature toughness of a welding heat affected zone; the steel plate can obtain excellent strength and toughness through the fine-grain strengthening and precipitation strengthening effects of Nb and Ti microalloy elements; the Nb content is designed to be 0.030-0.060%, and the Ti content is designed to be 0.030-0.105%.
The element V and the carbon have extremely strong affinity, and form an extremely stable compound with the carbon, so that the structure and the crystal grains of the steel can be refined, and the strength and the wear resistance of the steel are obviously improved; meanwhile, V can increase the hardenability of steel, enhance the secondary hardening effect of the steel and improve the wear resistance; when V and Nb are added in a compounding way, the transverse crack phenomenon can be obviously improved, and the recrystallization temperature is obviously increased; the V content is limited to 0.038-0.060%.
Ni can strengthen a ferrite matrix in steel, inhibit coarse proeutectoid ferrite, obviously improve the toughness of steel, reduce the ductile-brittle transition temperature of the steel and improve the low-temperature impact toughness of the steel; the content of Ni is designed to be 1.35-2.61%.
The main function of Mo element in steel is solid solution strengthening, a small amount of Mo can form refractory carbide, thereby preventing austenite grains from growing during heating, refining product structure, and improving strength, hardness and wear resistance; mo can improve hardenability, reduce or eliminate temper brittleness caused by other alloy elements, is greatly beneficial to toughness of steel, improves temper stability, and effectively eliminates or reduces residual stress in the steel, but too high Mo is easy to obtain coarse martensite in the processes of rapid cooling and welding cooling, and reduces low-temperature toughness of a base material and deteriorates welding performance, so that the content of Mo is controlled to be 0.31-0.80%.
The Cr element is an element which effectively improves the strength and the hardenability, and when Cr, Ni and the like are added in a proper proportion, the hardenability is improved more obviously; the steel is added with a certain amount of Cr to improve the strength and the hardness (wear resistance), and the content of Cr in the steel is limited to 0.30-0.60%.
Zr element can be matched with Ti to further refine grains, so that the low-temperature toughness of steel is effectively improved, the strain timeliness of the steel is reduced, and the Zr content is limited to 0.02-0.08%.
RE (rare earth element) can obviously improve the plasticity and impact toughness of the quenched and tempered steel, improve the form and distribution of inclusions, purify the steel, deoxidize and desulfurize, effectively remove harmful impurities and gases in the steel and improve the anisotropy of the steel; the RE content of the invention is 0.15-0.20%.
Second, the process improvement
By the composition design and the combination of the sectional rolling, quenching and tempering heat treatment processes, the invention is beneficial to fully refining and homogenizing the structure in the steel, eliminating the internal stress of the steel plate and improving the wear resistance and the low-temperature toughness of the obtained steel; the related process is simple, the condition is mild, the treatment processes such as electroslag remelting and hydrogen diffusion are not needed, and the economic and environmental benefits are remarkable.
Compared with the prior art, the invention has the beneficial effects that:
1) the low-temperature toughness can be effectively improved by combining component design and process improvement, Ti and Nb modification, subsequent rolling and heat treatment processes, and the wear resistance can be improved by regulating V, Mo, C and Cr modification, subsequent quenching and tempering processes; the obtained steel has high strength (yield strength is more than or equal to 500MPa), excellent shock fracture resistance (NDT temperature is less than or equal to-75 ℃, low-temperature toughness) and wear resistance (wear loss is less than or equal to 0.06 mg/cm)2)。
2) The preparation method provided by the invention is simple and easy to operate, has obvious environmental and economic benefits, and is suitable for popularization and application.
3) The steel obtained by the method has excellent wear resistance and impact and fracture resistance on the basis of ensuring high strength, especially has excellent low-temperature toughness, can be used for novel ships such as oil tankers, icebreakers and icebreaker container ships shuttling in arctic ice regions, reduces the abrasion of ship bodies, ice surfaces and gravels, and improves the safety use performance of the ship bodies by means of the high strength and high impact and fracture resistance of steel.
Detailed Description
In order to better understand the present invention, the following examples are further provided to illustrate the present invention, but the present invention is not limited to the following examples.
Examples 1 to 8
The chemical components of the 500 MPa-grade wear-resistant impact-resistant fracture-resistant steels in the embodiments 1-8 are respectively shown in Table 1, and the process parameters are respectively shown in Table 2; the preparation method comprises the following steps:
1) desulfurizing the molten iron, and controlling the S in the molten iron to be less than or equal to 0.001 percent;
2) carrying out converter smelting, and controlling the ratio of C in molten steel: 0.041-0.106 percent and P is less than or equal to 0.010 percent;
3) carrying out conventional continuous casting and heating the casting blank, wherein the heating temperature is controlled to be 1205-1290 ℃;
4) carrying out sectional rolling, wherein the initial rolling temperature of rough rolling is 1085-1198 ℃, and the rough rolling pass is controlled not to be higher than 5 passes; and controlling the starting temperature of finish rolling to be not higher than 988 ℃, controlling the finish rolling temperature to be 810-875 ℃, controlling the pass of finish rolling to be not higher than 5 passes, and controlling the cumulative reduction rate of the last three passes to be not less than 34%.
5) Carrying out quenching heat treatment, wherein the quenching process comprises the following steps: heating at 905-925 ℃, keeping the temperature for (plate thickness +40) min, and cooling: water cooling;
6) carrying out tempering heat treatment, wherein the tempering process comprises the following steps: heating at 480-550 ℃, keeping the temperature for (plate thickness +60) min, and cooling: and air cooling.
Comparative examples 1 to 2
The preparation process of the steel materials in the comparative examples 1-2 is almost the same as that in the examples, and the specific components and process parameter differences are shown in tables 1 and 2 respectively.
TABLE 1 chemical Components and content information (wt%) of examples of the present invention and comparative examples
TABLE 2 Main Process parameters of examples of the invention and comparative examples
The steel obtained in examples 1-8 and comparative examples 1 and 2 are respectively subjected to strength, impact fracture resistance and wear resistance tests, and the test results are respectively shown in Table 3; wherein the wear resistance comparative test conditions are as follows: the inventive steel and the comparative steel are made into sample pieces with the size of 20 multiplied by 40mm, and then the abrasion loss of the sample pieces is measured after the sample pieces are polished back and forth for 50 times by 1200-mesh sand paper under the pressure of 1kg, and the sample pieces are used as the basis for the abrasion resistance comparison.
TABLE 3 comprehensive performance test results of steels obtained in examples and comparative examples of the present invention
| Steel grade | Yield strength/MPa | NDT temperature/. degree.C | Abrasion loss mg/cm2 |
| Example 1 | 534 | -75 | 0.06 |
| Example 2 | 556 | -75 | 0.05 |
| Example 3 | 568 | -80 | 0.02 |
| Example 4 | 549 | -75 | 0.05 |
| Example 5 | 550 | -75 | 0.06 |
| Example 6 | 527 | -75 | 0.03 |
| Example 7 | 547 | -80 | 0.05 |
| Example 8 | 564 | -75 | 0.04 |
| Comparative example 1 | 700 | -40 | 0.17 |
| Comparative example 2 | 1030 | -30 | 0.09 |
As can be seen from table 3: the steel obtained by the invention has the impact and fracture resistance NDT temperature of less than or equal to-75 ℃, is obviously superior to that of comparative examples 1 and 2, and is especially suitable for low-temperature conditions; and has good wear resistance.
In summary, the steel obtained by the method has excellent wear resistance and impact fracture resistance on the basis of ensuring high strength, especially has excellent low-temperature toughness, can be used for novel ships such as oil tankers, icebreakers and icebreaker container ships shuttling at arctic ice regions, reduces the abrasion of the ship body, ice surface and gravel, and improves the safety use performance of the ship body by means of the high strength and high impact fracture resistance of steel.
It is apparent that the above embodiments are only examples for clearly illustrating and do not limit the embodiments. Other variations and modifications will be apparent to persons skilled in the art in light of the above description. And are neither required nor exhaustive of all embodiments. And obvious variations or modifications are therefore intended to be included within the scope of the invention as claimed.
Claims (2)
1. 500 MPa-grade wear-resistant impact-resistant fracture-resistant steel comprises the following components in percentage by mass: 0.061-0.086% of C, 0.30-0.40% of Si, 1.52-1.85% of Mn, less than or equal to 0.010% of P, less than or equal to 0.003% of S, 0.075-0.095% of Als, 0.040-0.060% of Nb0.048-0.060% of V, 0.080-0.105% of Ti, 1.95-2.61% of Ni, 0.51-0.80% of Mo, 0.40-0.60% of Cr0.05-0.08% of Zr and 0.15-0.20% of RE; the balance of Fe and inevitable impurities;
the preparation process comprises the following steps:
1) desulfurizing the molten iron, and controlling the S in the molten iron to be less than or equal to 0.001 percent;
2) performing converter smelting, and controlling the content of C in the molten steel to be 0.041-0.106% and P to be less than or equal to 0.010%;
3) carrying out conventional continuous casting and heating the casting blank, wherein the heating temperature is controlled to be 1205-1290 ℃;
4) carrying out sectional rolling, wherein the initial rolling temperature of rough rolling is 1085-1198 ℃, and the rough rolling pass is controlled not to be higher than 5 passes; controlling the starting temperature of finish rolling to be not higher than 988 ℃, controlling the finish rolling temperature to be 810-875 ℃, controlling the pass of finish rolling to be not higher than 5 passes, and controlling the cumulative reduction rate of the last three passes to be not less than 34%;
5) carrying out quenching heat treatment, wherein the quenching process comprises the following steps: heating at 905-925 ℃, keeping the temperature for (plate thickness +40) min, and cooling: water cooling;
6) carrying out tempering heat treatment, wherein the tempering process comprises the following steps: heating at 480-550 ℃, keeping the temperature for (plate thickness +60) min, and cooling: and air cooling.
2. The process for preparing the 500MPa grade abrasion-resistant impact-resistant fracture-resistant steel as claimed in claim 1, is characterized by comprising the following steps:
1) desulfurizing the molten iron, and controlling the S in the molten iron to be less than or equal to 0.001 percent;
2) performing converter smelting, and controlling the content of C in the molten steel to be 0.041-0.106% and P to be less than or equal to 0.010%;
3) carrying out conventional continuous casting and heating the casting blank, wherein the heating temperature is controlled to be 1205-1290 ℃;
4) carrying out sectional rolling, wherein the initial rolling temperature of rough rolling is 1085-1198 ℃, and the rough rolling pass is controlled not to be higher than 5 passes; controlling the starting temperature of finish rolling to be not higher than 988 ℃, controlling the finish rolling temperature to be 810-875 ℃, controlling the pass of finish rolling to be not higher than 5 passes, and controlling the cumulative reduction rate of the last three passes to be not less than 34%;
5) carrying out quenching heat treatment, wherein the quenching process comprises the following steps: heating at 905-925 ℃, keeping the temperature for (plate thickness +40) min, and cooling: water cooling;
6) carrying out tempering heat treatment, wherein the tempering process comprises the following steps: heating at 480-550 ℃, keeping the temperature for (plate thickness +60) min, and cooling: and air cooling.
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