CN109023039B - Anti-riot steel plate for 980 MPa-grade ATM and manufacturing method thereof - Google Patents
Anti-riot steel plate for 980 MPa-grade ATM and manufacturing method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- 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
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- 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
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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Abstract
The invention discloses an anti-riot steel plate for a 980 MPa-grade ATM and a manufacturing method thereof, and belongs to the technical field of metal material preparation. The anti-explosion steel plate for the 980MPa grade ATM comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-2.0%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.015 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities. The yield strength of the 980MPa grade anti-explosion steel plate for the ATM and the manufacturing method thereof reaches 800MPa grade, the tensile strength reaches over 980MPa, the elongation A reaches over 13 percent, and meanwhile, the 980MPa grade anti-explosion steel plate has good cold bending and welding performance and low alloy and process cost.
Description
Technical Field
The invention relates to the technical field of metal material preparation, in particular to an explosion-proof steel plate for a 980 MPa-grade ATM and a manufacturing method thereof.
Background
No special grade of steel is available in domestic ATM machine steel, 700MPa grade steel with good cold forming performance is mainly used in ATM machine manufacturing at present, the product specification is 12.5mm, and precipitation strengthening steel plates are mainly used. The series S500MC-S700MC in European Standard En10149, the DOMEX series of SSAB Steel plate Co., Ltd, Sweden, and the series BS550-BS700MC in domestic Bao Steel. With the development of the industry of safe cases and ATMs, in order to improve the impact resistance of iron cabinets, prolong the flame cutting time and meet the safety requirements of fire prevention, prying prevention and the like, the production of safe cases and ATMs by using hot-rolled low-alloy high-strength and ultrahigh-strength steel plates has become a development trend.
The existing high-strength steel with the grade of over 900MPa is generally subjected to hot rolling and then thermal refining, the alloy and process cost is relatively high, and the method has no advantages in the application and popularization of ATM machines.
Disclosure of Invention
The invention provides an anti-riot steel plate for a 980 MPa-grade ATM and a manufacturing method thereof, which solve or partially solve the technical problems that high-strength steel with the grade of over 900MPa in the prior art is generally subjected to hot rolling and then thermal refining, the alloy and process cost is relatively high, and the application and popularization of the ATM are not advantageous.
In order to solve the technical problem, the invention provides an explosion-proof steel plate for a 980 MPa-grade ATM, which comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-2.0%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.015 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities.
Further, the carbon equivalent CE is less than or equal to 0.65.
Based on the same inventive concept, the invention also provides a manufacturing method of the anti-explosion steel plate for the 980 MPa-grade ATM, which comprises the following steps: performing KR desulfurization on a steel billet, wherein the steel billet comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-1.8%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.025 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent, and O is less than or equal to 0.015 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities; carrying out full-three-step converter smelting on the desulfurized steel billet; carrying out LF refining on the smelted steel billet, and then carrying out RH refining; continuously casting the billet after RH refining to obtain a continuous casting billet; sending the continuous casting billet into a heating furnace for heating; carrying out rough rolling and finish rolling on the heated continuous casting billet; carrying out ultra-fast cooling on the finish-rolled continuous casting billet; and coiling the cooled continuous casting slab to obtain a steel plate, and cooling the steel plate to room temperature in a slow cooling pit.
Further, the step of feeding the continuous casting slab into the heating furnace for heating comprises the following steps: the heating temperature of the continuous casting billet entering the heating furnace is 1250-1280 ℃, and the heat preservation is carried out for 3.0-5.0 hours.
Further, the rough rolling and finish rolling of the heated continuous casting slab includes: and the rough rolling is deformed for 6 times, and the accumulated deformation of the continuous casting billet is controlled to be more than 80 percent.
Further, the rough rolling and finish rolling of the heated continuous casting slab includes: and 7-pass rolling is adopted in the finish rolling, and the accumulated deformation of the continuous casting billet is controlled to be more than 75%.
Furthermore, the rolling reduction rate of the last pass of finish rolling is controlled to be more than or equal to 8 percent.
Further, the finish rolling temperature of the finish rolling is 820-860 ℃.
Further, the cooling the finish-rolled continuous casting slab includes: the cooling speed of the continuous casting billet is more than 50 ℃/s.
Further, the cooling the finish-rolled continuous casting slab includes: the continuous casting slab is cooled to 350-450 ℃.
The main alloy elements of the invention have the following function descriptions:
c is the most economic and effective element for improving the strength of the material, and is combined with V in the steel coil to generate a certain precipitation strengthening effect. Meanwhile, the strength of the material after hot forming can be obviously improved by adopting higher C. If the content of C is designed to be lower, the strength is reduced after hot forming; if the C content is designed to be higher, the problems of center segregation, welding cracking and the like are easily caused, so the carbon content set range adopted by the method is determined to be 0.10-0.15%.
Si acts as a solid solution strengthening effect in the steel, promoting bainite formation. Too small content, insufficient strength, and too much rust formation on the surface easily affects the surface quality. Therefore, the content of the added Si is 0.2-0.6%.
Mn has a solid solution strengthening effect and is one of important elements for improving the strength of the material, but when added in an excessively high content, it is liable to cause segregation, which lowers the toughness of the material and deteriorates the performance. Therefore, the content of the added manganese is 1.1-1.8%.
Al is a deoxidizing element and has a certain grain refining effect. The invention limits the range of 0.01-0.06%.
P, S and N are impurity elements and are reduced as much as possible. Too high sulfur and phosphorus elements adversely affect the toughness and plasticity of the material, and too high nitrogen content seriously deteriorates the plasticity and toughness of the material. The invention limits S to be less than or equal to 0.004%, P to be less than or equal to 0.025% and N to be less than or equal to 0.004%.
Cr increases the hardenability of the steel. In addition, Cr is a medium carbide former, and among all the carbides, Cr is the finest one, which is uniformly distributed in the steel volume, and therefore has high strength, hardness, yield point and high wear resistance. Cr is an economical element that improves the strength and hardness of the material. The invention limits the Cr content to 1.0-1.5%.
Nb and Ti are refined grain elements and precipitation strengthening is performed. Too little addition, not obvious effect of refining grains and improving strength, excessive addition, cost increase and little performance increase. The invention limits Ti + Nb to be less than or equal to 0.2 percent.
B is an element having a large tendency to segregate, and can segregate in the grain boundary to reduce the segregation concentration of carbon atoms in the grain boundary. Since the grain boundaries are sites where ferrite preferentially nucleates, when boron is localized at the grain boundaries, these sites of preferential nucleation disappear, and fine borides are formed along the grain boundaries and coherent with the matrix. The invention limits B to 0.0015-0.0020%.
One or more technical solutions provided in the embodiments of the present application have at least the following technical effects or advantages:
the anti-explosion steel plate for the 980MPa grade ATM, which is produced by the invention, comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-2.0%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.015 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities, and a low-alloy-cost component system is adopted: the Cr-Nb-B component system is mainly adopted, and the Cr element is added to improve the strength and hardness of the material, so that the explosion-proof performance of the material is improved; the Nb element is added, the grain is further refined by combining an ultra-fast cooling process, the B element can improve the hardenability of the material, inhibit the precipitation of pro-eutectoid ferrite and promote the formation of lath bainite.
The carbon equivalent CE is controlled to be less than or equal to 0.65, the carbon equivalent CE is an important parameter for judging the welding performance, if the carbon equivalent CE is greater than 0.65, the welding performance is obviously reduced, and the CE is equal to [ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15 ]. 100%.
The production process adopted by the invention has the key points that the smelting process strictly controls all smelting process parameters, and the rolling process strictly controls all rolling and cooling control process parameters.
When the continuous casting billet is heated, the heating temperature is 1250-1280 ℃, and the heat is preserved for 3.0-5.0 hours, so that the Nb and Ti carbon nitrogen oxides are fully dissolved.
Two-stage controlled rolling is adopted, and the finish rolling temperature of the finish rolling needs to be strictly controlled to be 820-860 ℃ according to the thickness specification of a finished product in the finish rolling process; the lower rolling temperature is beneficial to obtaining uniform and fine crystal grains, avoids the occurrence of mixed crystal tissues and improves the strength and the plasticity and toughness of the material. By adopting low-temperature controlled rolling, a refined structure is obtained after relatively uniform and fine austenite grains are subjected to phase transformation, and the structure state of the raw material has inheritance to the final structure state of the hot-formed material, so that various mechanical properties of the final product can be improved.
After the continuous casting billet is finish rolled, ultra-fast cooling is carried out in a front-section cooling mode, the cooling speed is more than 50 ℃/s, and the structure strengthening after phase change is favorably enhanced; the target coiling temperature adopted by the invention is 350-450 ℃, and the lower coiling temperature is adopted to obtain good yield strength, tensile strength, elongation and impact toughness.
In conclusion, the invention adopts low-cost component design, improves the plasticity and the shock resistance of the material on the basis of ensuring the strength of the material, has the yield strength of 800MPa, the tensile strength of 980MPa or above and the elongation A of 13 percent or above, simultaneously has good cold bending and welding properties, has certain shock resistance and can prolong the flame cutting time. The method provided by the invention does not carry out thermal refining after hot rolling, the process is easy to realize, the alloy and process cost is low, and the method has advantages in the application and popularization of ATM machines.
Drawings
FIG. 1 is a schematic flow chart of a method for manufacturing an explosion-proof steel plate for a 980 MPa-grade ATM according to an embodiment of the present invention;
FIG. 2 is a schematic diagram of the metallographic phase of explosion-proof steel for a 980MPa ATM.
Detailed Description
In order to make the present application more clearly understood by those skilled in the art to which the present application pertains, the following detailed description of the present application is made by way of specific embodiments with reference to fig. 1-2.
The invention provides an explosion-proof steel plate for a 980 MPa-grade ATM, which comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-2.0%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.015 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities.
And (3) controlling the carbon equivalent CE to be less than or equal to 0.65, wherein the carbon equivalent CE is an important parameter for judging the welding performance, and if the carbon equivalent CE is greater than 0.65, the welding performance is obviously reduced, and the CE is [ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15 ]. 100%.
In practical application, the steel has different component contents according to different types of steel grades, and please refer to table 1 below, which is a component table of different steel grades.
For a better illustration and explanation of the invention, the components of the inventive examples are listed in table 1.
| Examples | C | Si | Mn | P | S | Als | Cr | Nb | Ti | B | CE |
| A-1 | 0.12 | 0.3 | 1.8 | 0.007 | 0.003 | 0.04 | 1.1 | 0.06 | 0.03 | 0.0018 | 0.640 |
| A-2 | 0.12 | 0.4 | 1.7 | 0.009 | 0.004 | 0.04 | 1.05 | 0.02 | 0.06 | 0.0020 | 0.613 |
| A-3 | 0.13 | 0.3 | 1.6 | 0.008 | 0.004 | 0.04 | 1.05 | 0.05 | 0.08 | 0.0018 | 0.607 |
| A-4 | 0.15 | 0.20 | 1.4 | 0.009 | 0.002 | 0.03 | 1.0 | 0.03 | 0.08 | 0.0020 | 0.583 |
| A-5 | 0.13 | 0.2 | 1.6 | 0.009 | 0.003 | 0.04 | 1.2 | 0.06 | 0.017 | 0.0018 | 0.637 |
| A-6 | 0.11 | 0.4 | 1.8 | 0.008 | 0.004 | 0.03 | 1.3 | 0.07 | 0.05 | 0.0019 | 0.620 |
| A-7 | 0.13 | 0.3 | 1.6 | 0.008 | 0.004 | 0.04 | 1.05 | 0.05 | 0.08 | 0.0018 | 0.607 |
| A-8 | 0.14 | 0.5 | 1.6 | 0.009 | 0.002 | 0.03 | 1.2 | 0.03 | 0.09 | 0.0020 | 0.647 |
| A-9 | 0.12 | 0.3 | 1.8 | 0.007 | 0.003 | 0.04 | 1.1 | 0.06 | 0.03 | 0.0018 | 0.640 |
| A-10 | 0.13 | 0.4 | 1.45 | 0.005 | 0.002 | 0.02 | 1.5 | 0.05 | 0.08 | 0.0019 | 0.632 |
Table 1 main chemical composition of steel billet (%)
The preparation method of the experimental group comprises the following steps:
KR desulfurization is carried out on the steel billets of the experimental group, the steel billets after desulfurization are subjected to full-three-step converter smelting, LF refining is carried out on the steel billets after smelting, RH refining is then carried out, and the steel billets after RH refining are continuously cast to obtain continuous casting billets.
KR desulfurization, namely desulfurization by a mechanical stirring method, is to insert a cross stirring paddle formed by pouring refractory materials into quantitative molten iron to rotate after baking so as to generate a vortex in the molten iron, and then to add a quantitative desulfurizer into the vortex of the molten iron so as to ensure that the desulfurizer and sulfur in the molten iron are subjected to desulfurization reaction in continuous stirring; LF refining is alkaline synthetic slag, submerged arc heating, argon blowing and stirring are carried out, and molten steel is refined in a reducing atmosphere; RH refining is as follows: two circulating pipes communicated with the vacuum chamber are arranged at the lower part of the vacuum chamber, the circulating pipes are inserted into molten steel during degassing treatment, the molten steel enters the vacuum degassing chamber from the circulating pipes by virtue of pressure difference established after the vacuum chamber is vacuumized, meanwhile, driving gas is blown in from one (ascending pipe) of the two circulating pipes, the molten steel is pumped by utilizing the principle of a bubble pump to flow through the degassing chamber and the descending pipe to generate circular motion, and gas is removed in the vacuum chamber.
And (3) conveying the continuous casting slab into a heating furnace for heating, wherein the heating temperature is 1250-1280 ℃, preferably 1260 ℃, and the heat preservation time is 3.0-5.0 hours.
And carrying out rough rolling and finish rolling on the heated continuous casting billet, wherein the rough rolling is deformed for 6 times, and the accumulated deformation of the continuous casting billet is controlled to be more than 80%. The initial rolling temperature of finish rolling is 1020 ℃, the final rolling temperature is 820-860 ℃, 7-pass rolling is adopted for finish rolling, the accumulated deformation of the continuous casting billet is controlled to be more than 75%, and the rolling reduction rate of the last pass of finish rolling is controlled to be more than or equal to 8%.
And carrying out ultra-fast cooling on the finish-rolled continuous casting billet at a cooling speed of 50 ℃/s, and cooling the continuous casting billet to 350-450 ℃.
And coiling the cooled continuous casting billet, wherein the integral coiling temperature is 350-450 ℃, and the coiling temperature is 400-500 ℃ after cooling because the process in the embodiment of the invention is to coil after cooling. And slowly cooling to room temperature, namely 15-25 ℃ in the slow cooling pit to obtain the required 980MPa grade anti-explosion steel plate for the ATM machine.
The three groups of finished samples were subjected to mechanical property measurement, and typical properties are shown in table 2.
TABLE 2 mechanical Properties of the experimental groups
By one or more embodiments of the invention, the invention has the following beneficial effects:
the anti-explosion steel plate for the 980MPa grade ATM, which is produced by the invention, comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-2.0%; 0.01 to 0.06 percent of Al; p is less than or equal to 0.015 percent; s is less than or equal to 0.004 percent; n is less than or equal to 0.004 percent; 1.0-1.5% of Cr; ti + Nb is less than or equal to 0.2 percent; 0.0015 to 0.0020 percent of B; the balance of Fe and inevitable impurities, and a low-alloy-cost component system is adopted: the Cr-Nb-B component system is mainly adopted, and the Cr element is added to improve the strength and hardness of the material, so that the explosion-proof performance of the material is improved; the Nb element is added, the grain is further refined by combining an ultra-fast cooling process, the B element can improve the hardenability of the material, inhibit the precipitation of pro-eutectoid ferrite and promote the formation of lath bainite.
The invention controls the carbon equivalent CE to be less than or equal to 0.65, the carbon equivalent CE is an important parameter for judging the welding performance, if the carbon equivalent CE value is more than 0.65, the welding performance is obviously reduced, and the CE is [ C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15 ]. 100 percent.
The production process adopted by the invention has the key points that the smelting process strictly controls all smelting process parameters, and the rolling process strictly controls all rolling and cooling control process parameters.
When the continuous casting billet is heated, the heating temperature is 1250-1280 ℃, and the heat is preserved for 3.0-5.0 hours, so that the Nb and Ti carbon nitrogen oxides are fully dissolved.
Two-stage controlled rolling is adopted, and the finish rolling temperature of the finish rolling needs to be strictly controlled to be 820-860 ℃ according to the thickness specification of a finished product in the finish rolling process; the lower rolling temperature is beneficial to obtaining uniform and fine crystal grains, avoids the occurrence of mixed crystal tissues and improves the strength and the plasticity and toughness of the material. By adopting low-temperature controlled rolling, a refined structure is obtained after relatively uniform and fine austenite grains are subjected to phase transformation, and the structure state of the raw material has inheritance to the final structure state of the hot-formed material, so that various mechanical properties of the final product can be improved.
After the continuous casting billet is finish rolled, ultra-fast cooling is carried out in a front-section cooling mode, the cooling speed is more than 50 ℃/s, and the structure strengthening after phase change is favorably enhanced; the target coiling temperature adopted by the invention is 350-450 ℃, and the lower coiling temperature is adopted to obtain good yield strength, tensile strength, elongation and impact toughness.
In conclusion, the invention adopts low-cost component design, improves the plasticity and the shock resistance of the material on the basis of ensuring the strength of the material, has the yield strength of 800MPa, the tensile strength of 980MPa or above and the elongation A of 13 percent or above, simultaneously has good cold bending and welding properties, has certain shock resistance and can prolong the flame cutting time. The method provided by the invention does not carry out thermal refining after hot rolling, the process is easy to realize, the alloy and process cost is low, and the method has advantages in the application and popularization of ATM machines.
Finally, it should be noted that the above embodiments are only for illustrating the technical solutions of the present invention and not for limiting, and although the present invention has been described in detail with reference to examples, it should be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, which should be covered by the claims of the present invention.
Claims (4)
1. A manufacturing method of an anti-explosion steel plate for a 980 MPa-grade ATM is characterized by comprising the following steps:
performing KR desulfurization on a steel billet, wherein the steel billet comprises the following chemical components in percentage by mass: c: 0.10-0.15%; si: 0.2-0.6%; mn: 1.10-1.8%; 0.01 to 0.06 percent of Al; less than or equal to 0.025 percent of P, less than or equal to 0.004 percent of S, less than or equal to 0.004 percent of N, less than or equal to 0.015 percent of O, 1.0-1.5 percent of Cr, less than or equal to 0.2 percent of Ti and Nb, 0.0015-0.0020 percent of B, and the balance of Fe and inevitable impurities; the carbon equivalent CE is less than or equal to 0.65; the yield strength of the anti-explosion steel plate for the ATM reaches 800MPa, the tensile strength reaches over 980MPa, and the elongation A reaches over 13 percent;
carrying out full-three-step converter smelting on the desulfurized steel billet;
carrying out LF refining on the smelted steel billet, and then carrying out RH refining;
continuously casting the billet after RH refining to obtain a continuous casting billet;
sending the continuous casting billet into a heating furnace for heating, wherein the heating temperature of the continuous casting billet entering the heating furnace is 1260 plus 1280 ℃, and preserving heat for 3.0-5.0 hours;
carrying out rough rolling and finish rolling on the heated continuous casting billet, wherein the finish rolling temperature of the finish rolling is 820-860 ℃;
carrying out ultra-fast cooling on the finish-rolled continuous casting billet, wherein the cooling speed of the continuous casting billet is more than 50 ℃/s;
and coiling the cooled continuous casting slab to obtain a steel plate, cooling the steel plate to room temperature in a slow cooling pit, and cooling the continuous casting slab to 350-450 ℃.
2. The method for manufacturing the explosion-proof steel plate for the 980 MPa-class ATM machine as recited in claim 1, wherein the rough rolling and finish rolling the heated slab comprises:
and the rough rolling is deformed for 6 times, and the accumulated deformation of the continuous casting billet is controlled to be more than 80 percent.
3. The method for manufacturing the explosion-proof steel plate for the 980 MPa-class ATM machine as recited in claim 1, wherein the rough rolling and finish rolling the heated slab comprises:
and 7-pass rolling is adopted in the finish rolling, and the accumulated deformation of the continuous casting billet is controlled to be more than 75%.
4. The method for manufacturing the explosion-proof steel plate for the 980MPa class ATM according to the claim 3, wherein the method comprises the following steps:
and controlling the rolling reduction rate of the last pass of finish rolling to be more than or equal to 8 percent.
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| JP2005293982A (en) * | 2004-03-31 | 2005-10-20 | Nisshin Steel Co Ltd | Ferritic stainless steel for solid polymer fuel cell separator |
| BRPI0805832B1 (en) * | 2007-10-29 | 2014-11-25 | Nippon Steel & Sumitomo Metal Corp | THERMAL TREATED STEEL FOR USE IN MARTENSITE TYPE HOT FORGING AND HOT THREADED NON-TREATED STEEL PIECE |
| CN103526111B (en) * | 2013-10-17 | 2015-04-08 | 马鞍山市安工大工业技术研究院有限公司 | Hot-rolled plate band steel with yield strength being 900MPa and preparation method thereof |
| CN103993235B (en) * | 2014-05-19 | 2016-04-27 | 首钢总公司 | A kind of manufacture method of high-strength hot-rolled armor plate |
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