CN108546882B - Cu precipitation enhanced high-strength refractory corrosion-resistant steel and manufacturing method thereof - Google Patents
Cu precipitation enhanced high-strength refractory corrosion-resistant steel and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- 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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- 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
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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
- 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
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- 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
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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Abstract
The invention discloses Cu precipitation enhancement type high-strength fireproof corrosion-resistant steel and a manufacturing method thereof, belonging to the technical field of steel for building structures. The composition is as follows: c: 0.01-0.03 wt.%, Si: 0.10-0.30 wt.%, Mn: 0.10-0.50 wt.%, Ni: 3.00-5.00 wt.%, Cu: 0.80-1.50 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities. The manufacturing method adopts converter or electric furnace smelting, and the casting adopts continuous casting or die casting. The high-strength fire-resistant corrosion-resistant steel can be used for steel structure buildings.
Description
Technical Field
The invention belongs to the technical field of steel for building structures, and particularly relates to Cu precipitation enhanced high-strength fire-resistant corrosion-resistant steel and a manufacturing method thereof.
Background
The steel structure building has the advantages of light weight, quick construction, large space, comfort, beauty and the like. However, firstly, the steel for common structural use has poor weather resistance, and often needs to be coated with an anticorrosive coating, especially in severe marine atmospheric corrosion environment along the sea or in islands, and the cost of anticorrosive maintenance of steel structural buildings is high, and even the difficulty is high. Secondly, the fire resistance of the common steel structure is poor, the yield strength drops sharply above 350 ℃, and the high-temperature bearing capacity is insufficient. Fire safety therefore requires the steel structure to be protected by adding a fire protection structure or a fire protection coating in order to obtain a time for escaping from a fire. The addition of the anti-corrosion and fireproof coatings and the fireproof structure not only increases the construction difficulty, prolongs the construction period and increases the construction cost, but also causes pollution to the environment. Therefore, there is a trend toward development of steel for building structures which is a composite of weather-resistant, corrosion-resistant and fire-resistant functions.
Disclosure of Invention
In view of the above analysis, the present invention aims to provide a Cu precipitation-enhanced high-strength refractory corrosion-resistant steel and a manufacturing method thereof, wherein a low-C design is adopted, Ni and Cu corrosion-resistant elements are adopted for alloying, and the refractory property is mainly ensured by the combination of room-temperature bainite structure control and nano Cu particles precipitated at high temperature when encountering fire.
The purpose of the invention is mainly realized by the following technical scheme:
the invention provides Cu precipitation enhanced high-strength refractory corrosion-resistant steel, which comprises the following components: c: 0.01-0.03 wt.%, Si: 0.10-0.30 wt.%, Mn: 0.10-0.50 wt.%, Ni: 3.00-5.00 wt.%, Cu: 0.80-1.50 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Further, the composition is: c: 0.015-0.026 wt.%, Si: 0.24-0.25 wt.%, Mn: 0.28-0.45 wt.%, Ni: 3.55-4.45 wt.%, Cu: 0.92-1.45 wt.%, Ti: 0.021-0.025 wt.%, Al: 0.021-0.023 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Furthermore, in the microstructure of the high-strength refractory corrosion-resistant steel, the volume percentage of bainite is 80-100%.
At room temperature, the tensile strength of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is 500-700MPa, the yield strength is 390-560MPa, the elongation is 21.0-25.0%, and the yield ratio is 0.77-0.82.
At the temperature of 600 ℃, the tensile strength of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is 330-440MPa, the yield strength is 260-360MPa, and the elongation is 19.0-23.0%;
the impact energy Akv at-40 ℃ of the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel is 250-300/J.
The invention also provides a manufacturing method of the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel, which is used for manufacturing the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel and comprises the following steps:
step 1: heating the continuous casting billet or the cast ingot, and soaking to obtain a soaked billet;
step 2: carrying out rough rolling and finish rolling on the uniformly heated billet to obtain a finish rolled billet;
and step 3: and (3) carrying out water spraying rapid laminar cooling on the finish-rolled steel billet, wherein the final cooling re-reddening temperature is below 500 ℃, the laminar cooling speed is more than 10 ℃/s, then, air cooling is carried out to the room temperature, bainite and martensite structures are obtained, the room-temperature steel plate obtains supersaturated solid-dissolved copper, and the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is obtained.
Further, in step 1, the heating temperature is 1150-1200 ℃, and the soaking time is 0.5-3 h.
Further, in the step 2, the initial rolling temperature of the rough rolling is 1160-.
Further, in step 3, the final cooling temperature is 399-483 ℃, and the laminar cooling speed is 20-26 ℃/s.
Compared with the prior art, the invention has the following beneficial effects:
1) the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel provided by the invention adopts a low-C design, adopts Ni and Cu corrosion-resistant elements for alloying, and the proper content of the Ni and the Cu corrosion-resistant elements is coupled, so that the high-strength refractory corrosion-resistant steel has excellent marine atmospheric corrosion resistance. The high-strength refractory corrosion-resistant steel achieves the comprehensive properties that: the composite basic mechanical properties of yield strength (345-500MPa level) and anti-seismic property (low yield ratio is less than 0.83 and elongation is more than 20 percent), the composite material has 600 ℃ fire resistance, and the relative corrosion resistance under the marine atmospheric corrosion environment is more than 6 times of that of the common Q345GJ (0.16C-1.35Mn-0.25Si-0.015Nb-0.015Ti-0.025 Al). Has excellent marine atmospheric corrosion resistance, shock resistance and mechanical properties.
2) According to the manufacturing method of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel, provided by the invention, a room-temperature structure mainly comprising bainite is obtained through water spraying and rapid laminar cooling, the room-temperature structure has better refractory performance than a ferrite structure, and meanwhile, nano Cu particles are precipitated from solid solution copper supersaturated at room temperature when encountering fire at high temperature, so that the refractory property can be enhanced.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by the practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims thereof.
Detailed Description
The preferred embodiments of the present invention are described in detail below.
The invention provides Cu precipitation enhanced high-strength refractory corrosion-resistant steel, which comprises the following components: c: 0.01-0.03 wt.%, Si: 0.10-0.30 wt.%, Mn: 0.10-0.50 wt.%, Ni: 3.00-5.00 wt.%, Cu: 0.80-1.50 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Compared with the prior art, the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel provided by the invention adopts a low-C design, adopts Ni and Cu corrosion-resistant elements for alloying, and the proper content of the Ni and the Cu corrosion-resistant elements is coupled, so that the high-strength refractory corrosion-resistant steel has excellent marine atmospheric corrosion resistance. The high-strength refractory corrosion-resistant steel achieves the comprehensive properties that: the composite basic mechanical properties of yield strength (345-500MPa level) and anti-seismic property (low yield ratio is less than 0.83 and elongation is more than 20 percent), the composite material has 600 ℃ fire resistance, and the relative corrosion resistance under the marine atmospheric corrosion environment is more than 6 times of that of the common Q345GJ (0.16C-1.35Mn-0.25Si-0.015Nb-0.015Ti-0.025 Al). Has excellent marine atmospheric corrosion resistance, shock resistance and mechanical properties.
Specifically, in the Cu precipitation-enhanced high-strength refractory corrosion-resistant steel, the functions and the proportions of the elements are as follows:
carbon (C): can directly influence the mechanical properties of the steel, such as strength, toughness and the like. Has obvious solid solution strengthening effect and improves the hardenability of the steel. At higher alloy contents, the carbon content is controlled at a lower level, which is advantageous for obtaining medium and high strength through simple manufacturing methods and processes. The steel is designed by adopting low-carbon components, and the carbon content ranges from 0.01 wt.% to 0.03 wt.%.
Silicon (Si): one of important reduction and deoxidation elements in the steel-making process, and simultaneously has stronger solid solution strengthening effect, thereby being beneficial to high-temperature strengthening. However, excessive Si accelerates high-temperature delamination, deteriorating toughness and weldability of the steel. The silicon content in the steel is 0.10-0.30 wt.%.
Manganese (Mn): the most common alloying element in steel, the steel of the present invention, is one of the deoxidizing elements. The content of manganese in the steel is 0.10-0.50 wt.%.
Nickel (Ni): the lattice constant of the nickel is close to that of face-centered cubic iron, and the nickel can be continuously dissolved in solid, thereby being beneficial to improving the hardenability of the steel. The method can promote the proceeding of the cross sliding, reduce the resistance of the dislocation movement, relax the stress and improve the plasticity and toughness of the steel. In addition, the carbon equivalent coefficient of nickel is only 1/15, and low-carbon medium-high nickel steel also has good welding performance. The nickel is not easy to oxidize and corrode, and the invention finds that when the nickel content is not less than 3 wt.%, the nickel steel with lower marine atmosphere corrosion resistance is obviously improved; on the basis, the marine atmospheric corrosion resistance is not greatly improved by continuously increasing the nickel content, but the marine atmospheric corrosion resistance is obviously improved after the nickel content is coupled with copper. The content range of nickel in the steel is 3.00-5.00 wt.%.
Copper (Cu): the solid solubility in austenite is larger, the solid solubility in ferrite is relatively smaller, and solid-dissolved copper in bainite or martensite is rapidly separated out in the process of heating in case of fire, so that the high-temperature strength and the fire resistance of the steel are improved. Copper in steel can promote gamma-Fe2O3The transformation of/gamma-FeOOH to a stable rust phase α -FeOOH can enrich at the cracks of the oxidized or corroded rust and prevent the corrosion medium from further contacting with the matrix, therefore, the addition of copper can improve the corrosion resistance of the steel, in addition, the carbon equivalent coefficient of copper is only 1/15, and the low-carbon copper-containing steel also has good welding performance, and the content of copper in the steel is 0.80-1.50 wt.%.
Titanium (Ti): the steel is mainly subjected to micro-titanium treatment, titanium is mainly combined with nitrogen to form nano-sized titanium nitride particles, and austenite grains in the heating process of a casting blank are refined. The nitrogen content in the steel of the invention does not exceed 80 ppm. According to the ideal chemical proportion of the titanium nitride, the content of the titanium is generally not more than 0.030 wt%, and overhigh titanium is easy to form thicker titanium nitride, is not beneficial to refining austenite grains and is harmful to the toughness and the plasticity of the steel. Too low a titanium does not fix nitrogen sufficiently to form an effective amount of titanium nitride. The titanium content in the steel according to the invention ranges from 0.010 to 0.030 wt.%.
Aluminum (Al): aluminum is a strong deoxidizing element and can be combined with nitrogen to form aluminum nitride, so that the function of refining austenite grains can be achieved. The content of aluminum in the steel is 0.015-0.035 wt.%.
Phosphorus (P) and sulfur (S): the content of impurity elements in the steel, which obviously reduces the ductility and the welding performance, is as low as possible without obviously increasing the cost, so that the content is controlled within 0.015 wt.% and 0.010 wt.% respectively.
In order to further improve the comprehensive performance of the Cu precipitation enhanced high-strength fire-resistant corrosion-resistant steel, the composition of the shock-resistant fire-resistant corrosion-resistant steel can be further adjusted. Illustratively, the composition may be: c: 0.015-0.026 wt.%, Si: 0.24-0.25 wt.%, Mn: 0.28-0.45 wt.%, Ni: 3.55-4.45 wt.%, Cu: 0.92-1.45 wt.%, Ti: 0.021-0.025 wt.%, Al: 0.021-0.023 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
The invention also provides a manufacturing method of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel, which adopts converter or electric furnace smelting and adopts continuous casting or die casting for casting, and the manufacturing method comprises the following steps:
step 1: and (3) putting the cogging continuous casting billet or the cogging cast ingot into a heating furnace for heating and soaking to obtain a soaked billet, wherein the heating temperature is 1150-1200 ℃ and the soaking time is 0.5-3 h.
Step 2: and carrying out rough rolling and finish rolling on the soaked steel billet to obtain a finish rolled steel billet, wherein the rough rolling start temperature is 1160-1200 ℃, the rough rolling finish temperature is 1050-1100 ℃, the finish rolling start temperature is 950-960 ℃, the finish rolling temperature is 850-950 ℃, and the finish rolling temperature is 850-950 ℃ on the rolling production line on the basis of the finish rolling temperature of 850-950 ℃ of the finish rolling whether the steel billet is a plate blank or a special-shaped steel billet.
And step 3: and (2) carrying out water spraying rapid laminar cooling on the finish-rolled steel billet, wherein the final cooling re-reddening temperature or the coiling temperature is below 500 ℃ (for example 399-483 ℃), the laminar cooling speed is more than 10 ℃/s (for example 20-26 ℃/s), and then carrying out air cooling to room temperature to obtain the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel, wherein the final main structure of the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel is bainite, the volume percentage is 80-100%, and other structures are martensite.
Compared with the prior art, the method for manufacturing the Cu precipitation enhancement type high-strength refractory corrosion-resistant steel provided by the invention has the advantages that the room-temperature structure mainly comprising bainite is obtained through water spraying and rapid laminar cooling, the structure has better refractory performance than a ferrite structure, and meanwhile, nano Cu particles are precipitated from solid solution copper supersaturated at room temperature at high temperature when encountering fire, so that the refractory property can be enhanced.
The bainite and martensite structures are obtained by rapid laminar cooling, so that the room-temperature steel plate can obtain the purpose of supersaturated solid-dissolved copper, the precipitation is convenient in the ignition and temperature rise process, the high-temperature strength of the steel is enhanced, and the functions of precipitation in case of fire and fire resistance enhancement are realized. By controlling bainite rather than martensite as the main structure, excellent toughness and plasticity can be obtained.
In the above preparation method, the high-strength refractory corrosion-resistant steel may be a steel plate with a thickness of 8-100mm manufactured by a medium plate rolling line, a steel plate with a thickness of 20mm or less manufactured by a continuous hot rolling line, and the H-shaped steel may be manufactured by a section steel rolling line, which requires rapid cooling equipment.
In order to further improve the comprehensive performance of the Cu precipitation-enhanced high-strength refractory corrosion-resistant steel, the method further comprises, after the laminar cooling and before the air cooling in step 3, the following steps: and (3) preserving the heat of the steel billet subjected to laminar cooling in a heat preservation furnace at the temperature of 400-450 ℃ for 0.5-1h, and cooling the furnace to the temperature of 180-220 ℃.
The compositions of the Cu precipitation-enhanced high-strength refractory corrosion-resistant steels of the following examples are shown in table 1, and the process parameters of some of the manufacturing methods are shown in table 2.
Example 1-1: heating the casting blank to 1180 ℃, preserving heat for 2 hours, carrying out 3-pass rough rolling at the rough rolling start rolling temperature of 1180 ℃, carrying out 3-pass rough rolling at the rough rolling finish rolling temperature of 1095 ℃, carrying out finish rolling at the finish rolling start rolling temperature of 953 ℃, carrying out finish rolling at the finish rolling temperature of 883 ℃, and carrying out 5-pass finish rolling to roll the thickness of the steel plate to 20 mm; laminar cooling is carried out on the steel plate at the cooling speed of 20 ℃/s to 483 ℃, and then air cooling is carried out to the room temperature.
Examples 1 to 2: heating the casting blank to 1180 ℃, preserving heat for 2 hours, carrying out 3-pass rough rolling at the rough rolling start rolling temperature of 1180 ℃, carrying out 3-pass rough rolling at the rough rolling finish rolling temperature of 1065 ℃, carrying out fine rolling at the fine rolling start rolling temperature of 955 ℃, carrying out 3-pass fine rolling at 881 ℃, and rolling the thickness of the steel plate to 30 mm; the steel plate was subjected to laminar cooling to 481 ℃ at a cooling rate of 21 ℃/s, and then air-cooled to room temperature.
Example 2-1: heating the casting blank to 1180 ℃, preserving heat for 2 hours, carrying out 3-pass rough rolling at the rough rolling start rolling temperature of 1180 ℃, carrying out 6-pass finish rolling at the rough rolling finish rolling temperature of 1055 ℃, carrying out 952 ℃ at the finish rolling start rolling temperature of 881 ℃, and rolling the steel plate to the thickness of 16 mm; carrying out laminar flow cooling on the steel plate to 447 ℃ at the cooling speed of 26 ℃/s, then sending the steel plate into a heat preservation furnace at 450 ℃, preserving heat for 0.5h, cooling the steel plate to 200 ℃, and finally discharging the steel plate from the furnace and air-cooling the steel plate to room temperature.
Example 2-2: heating the casting blank to 1180 ℃, preserving heat for 2 hours, carrying out 3-pass rough rolling at the rough rolling start rolling temperature of 1180 ℃, carrying out 3-pass rough rolling at the rough rolling finish rolling temperature of 1068 ℃, carrying out the finish rolling start rolling temperature of 952 ℃, carrying out the finish rolling temperature of 883 ℃, carrying out 5-pass finish rolling, and rolling the steel plate to 25mm in thickness; the steel plate was subjected to laminar cooling to 443 ℃ at a cooling rate of 23 ℃/s, and then air-cooled to room temperature.
Example 3-1: heating the casting blank to 1180 ℃, preserving heat for 2 hours, carrying out rough rolling for 4 times at the rough rolling start rolling temperature of 1180 ℃, carrying out rough rolling for 1075 ℃, carrying out finish rolling for 953 ℃, carrying out finish rolling for 882 ℃, carrying out finish rolling for 6 times, and rolling the thickness of the steel plate to 16 mm; carrying out laminar flow cooling on the steel plate to 399 ℃ at the cooling speed of 23 ℃/s, then sending the steel plate into a 400 ℃ heat preservation furnace, carrying out heat preservation for 0.5h, then cooling the steel plate to 200 ℃, and finally discharging the steel plate from the furnace and carrying out air cooling to the room temperature.
Example 3-2: heating the casting blank to 1180 ℃, preserving heat for 2h, carrying out rough rolling for 4 times at the rough rolling start rolling temperature of 1180 ℃, carrying out rough rolling for 4 times at the rough rolling finish rolling temperature of 1050 ℃, carrying out finish rolling at the finish rolling start rolling temperature of 951 ℃, carrying out finish rolling at the finish rolling temperature of 882 ℃, and carrying out finish rolling for 6 times to roll the thickness of the steel plate to 16 mm; the steel plate was subjected to laminar cooling to 405 ℃ at a cooling rate of 26 ℃/s, and then air-cooled to room temperature.
The mechanical property tests of the steel plates are shown in the table 3, and it can be seen from the table that the yield strength at room temperature of the examples 1-1 and 1-2 reaches 345MPa, the yield strength at room temperature of the examples 2-1 and 2-2 reaches 460MPa, the yield strength at room temperature of the examples 3-1 and 3-2 reaches 500MPa, and the yield ratio of the steel plates is not higher than 0.83. The elongation is not lower than 20 percent; the yield strength at 600 ℃ is greater than 2/3 of the yield strength standard at room temperature, which indicates good fire resistance.
In the above embodiment, the tensile strength of the Cu precipitation-enhanced high-strength refractory corrosion-resistant steel is 500-700MPa, the yield strength is 390-560MPa, the elongation is 21.0-25.0%, and the yield ratio is 0.77-0.82 at room temperature. At 600 ℃, the tensile strength of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is 330-440MPa, the yield strength is 260-360MPa, and the elongation is 19.0-23.0%. The impact energy Akv at-40 ℃ is 250-300/J.
Then, the steel plate in the above example is subjected to a corrosion resistance test under the following experimental conditions: at room temperature, the steel is soaked in a 2% NaCl solution for a period (the parameters are shown in Table 4), common Q345GJ steel (0.16C-1.35Mn-0.25Si-0.015Nb-0.015Ti-0.025Al) is used as a comparison steel plate, the corrosion results are shown in Table 5, the corrosion result of the Q345GJ steel plate is 1, and the corrosion result of the embodiment of the invention is not higher than 20% of the corrosion result of the Q345GJ steel plate, which shows that the Cu precipitation enhanced high-strength refractory corrosion-resistant steel has good corrosion resistance.
TABLE 1 composition of Cu precipitation-strengthened high-strength refractory corrosion-resistant steel (wt%)
| C | Si | Mn | Ni | Cu | Ti | Al | P | S | |
| Examples 1 to 1 | 0.015 | 0.25 | 0.45 | 3.55 | 0.92 | 0.023 | 0.021 | 0.008 | 0.002 |
| Examples 1 to 2 | 0.015 | 0.25 | 0.45 | 3.55 | 0.92 | 0.023 | 0.021 | 0.008 | 0.002 |
| Example 2-1 | 0.019 | 0.24 | 0.30 | 4.06 | 1.20 | 0.025 | 0.023 | 0.009 | 0.003 |
| Examples 2 to 2 | 0.019 | 0.24 | 0.30 | 4.06 | 1.20 | 0.025 | 0.023 | 0.009 | 0.003 |
| Example 3-1 | 0.026 | 0.25 | 0.28 | 4.45 | 1.45 | 0.021 | 0.023 | 0.008 | 0.002 |
| Examples 3 to 2 | 0.026 | 0.25 | 0.28 | 4.45 | 1.45 | 0.021 | 0.023 | 0.008 | 0.002 |
TABLE 2Cu precipitation-strengthened high-strength refractory corrosion-resistant steel manufacturing method
TABLE 3 mechanical properties of Cu precipitation-enhanced high-strength refractory corrosion-resistant steel
TABLE 4 periimmersion corrosion test parameters for Cu precipitation-enhanced high-strength refractory corrosion-resistant steels
| Item | Parameter(s) |
| Temperature of | 45±2℃ |
| PH | 6.5-7.5 |
| Relative humidity | 70±5％ |
| Time per cycle | 60±2min |
| Immersion time per cycle | 12±2min |
| Peri-leaching solution | 2wt％NaCl |
TABLE 5 relative Corrosion resistance of Cu precipitation-enhanced high-strength refractory corrosion-resistant steels
| Q345GJ | Examples 1 to 1 | Example 2-1 | Example 3-1 | |
| Relative corrosion rate | 100％ | 15.3％ | 13.5％ | 12.6％ |
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention.
Claims (5)
1. The Cu precipitation enhancement type high-strength refractory corrosion-resistant steel is characterized by comprising the following components: c: 0.015-0.026 wt.%, Si: 0.24-0.25 wt.%, Mn: 0.28-0.45 wt.%, Ni: 4.06-4.45 wt.%, Cu: 0.92-1.45 wt.%, Ti: 0.021-0.025 wt.%, Al: 0.021-0.023 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities; the Cu precipitation enhancement type high-strength fire-resistant corrosion-resistant steel has supersaturated solid dissolved copper at room temperature, the supersaturated solid dissolved copper precipitates nano Cu particles at high temperature when encountering fire, and the high-temperature strength and fire resistance of the Cu precipitation enhancement type high-strength fire-resistant corrosion-resistant steel are enhanced;
in the microstructure of the high-strength refractory corrosion-resistant steel, the volume percentage of bainite is 80-100%;
at the temperature of 600 ℃, the tensile strength of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is 330-440MPa, the yield strength is 260-360MPa, and the elongation is 19.0-23.0%;
the manufacturing method of the Cu precipitation enhanced high-strength refractory corrosion-resistant steel comprises the following steps:
step 1: heating the continuous casting billet or the cast ingot, and soaking to obtain a soaked billet;
step 2: carrying out rough rolling and finish rolling on the uniformly heated billet to obtain a finish rolled billet;
and step 3: carrying out water spraying rapid laminar cooling on the finish-rolled steel billet, wherein the final cooling temperature is 399-483 ℃, the furnace cooling is carried out to 180-220 ℃, and then the air cooling is carried out to the room temperature, so as to obtain bainite and martensite structures, obtain supersaturated solid-dissolved copper on the room-temperature steel plate and obtain Cu precipitation enhanced high-strength refractory corrosion-resistant steel;
in the step 2, the initial rolling temperature of the rough rolling is 1160-;
in the step 3, the laminar cooling speed is 20-26 ℃/s.
2. The Cu precipitation-enhanced high-strength refractory corrosion-resistant steel as recited in claim 1, wherein said Cu precipitation-enhanced high-strength refractory corrosion-resistant steel has a tensile strength of 500-700MPa, a yield strength of 390-560MPa, an elongation of 21.0-25.0%, and a yield ratio of 0.77-0.82 at room temperature.
3. The Cu precipitation-enhanced high-strength refractory corrosion-resistant steel according to claim 1, wherein the impact energy Akv at-40 ℃ of the Cu precipitation-enhanced high-strength refractory corrosion-resistant steel is 250-300J.
4. A method for producing a Cu precipitation-enhanced high-strength refractory corrosion-resistant steel, characterized by comprising the steps of:
step 1: heating the continuous casting billet or the cast ingot, and soaking to obtain a soaked billet;
step 2: carrying out rough rolling and finish rolling on the uniformly heated billet to obtain a finish rolled billet;
and step 3: carrying out water spraying rapid laminar cooling on the finish-rolled steel billet, wherein the final cooling re-reddening temperature is 399-483 ℃, and then carrying out air cooling to room temperature to obtain bainite and martensite structures, so that the room-temperature steel plate obtains supersaturated solid-dissolved copper, and the Cu precipitation enhanced high-strength refractory corrosion-resistant steel is obtained;
in the step 2, the initial rolling temperature of the rough rolling is 1160-;
in the step 3, the laminar cooling speed is 20-26 ℃/s.
5. The method for manufacturing the Cu precipitation-enhanced high-strength refractory corrosion-resistant steel as recited in claim 4, wherein in the step 1, the heating temperature is 1150-1200 ℃ and the soaking time is 0.5-3 h.
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