CN116200652A - Production and preparation method of Q390GJC hot rolled H-shaped steel for high-performance building - Google Patents
Production and preparation method of Q390GJC hot rolled H-shaped steel for high-performance building Download PDFInfo
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- 239000010959 steel Substances 0.000 title claims abstract description 70
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- 238000005096 rolling process Methods 0.000 claims abstract description 29
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 238000009749 continuous casting Methods 0.000 claims abstract description 14
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 9
- 239000000956 alloy Substances 0.000 claims abstract description 9
- 238000009628 steelmaking Methods 0.000 claims abstract description 5
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- 238000004321 preservation Methods 0.000 claims abstract description 3
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 9
- 239000011572 manganese Substances 0.000 description 8
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- 150000001875 compounds Chemical class 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
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- 239000013535 sea water Substances 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
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Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- 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
- B21B1/08—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 structural sections, i.e. work of special cross-section, e.g. angle steel
- B21B1/088—H- or I-sections
-
- 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
- B21B1/463—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 continuous process, i.e. the cast not being cut before rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
-
- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a production and preparation method of high-performance Q390GJC hot rolled H-shaped steel for buildings, which comprises the following technical parameters controlled in a steelmaking process: VN alloy is adopted to prepare V, and the percentage content of N elements is more than or equal to 0.01 percent; vacuum breaking VD, adding VN alloy, and controlling the temperature of molten steel to be more than or equal to 1630 ℃; the superheat degree of continuous casting is less than or equal to 40 ℃; the pulling speed of the casting machine is more than or equal to 0.9m/min; the temperature of cooling water of the crystallizer is more than or equal to 26 ℃; the technical parameters controlled in the rolling process are as follows: the heating temperature is 1150-1200 ℃, and the heat preservation time is more than or equal to 2.5 hours; the initial rolling temperature is less than or equal to 1050 ℃; the finishing temperature is less than or equal to 890 ℃. The H-shaped steel prepared by the method has the performance indexes that the yield strength Rel is more than or equal to 390MPa, the tensile strength Rm is more than or equal to 490MPa, the elongation A is more than or equal to 20%, the low-temperature impact at 0 ℃ is more than or equal to 34J, the yield ratio is less than or equal to 0.83, the CEV is less than or equal to 0.45%, and the Pcm is less than or equal to 0.29%.
Description
Technical Field
The invention relates to a production and preparation method of high-performance Q390GJC hot rolled H-shaped steel for buildings.
Background
The hot rolled H-shaped steel is a high-efficiency saving type building steel, has the advantages of good comprehensive mechanical property, reasonable section design, metal material saving and the like, and is wide in application range. In recent years, as steel structure buildings gradually develop to high-rise, super high-rise and large-span, the quality requirements on steel materials are higher and higher, and the steel materials are required to have better strength, hardness, plasticity, toughness, fatigue strength and welding performance.
At present, the hot rolled H-shaped steel for the high-grade building structure is not issued by specific standards, and the production and preparation method of the Q390GJC hot rolled H-shaped steel for the high-grade building structure is produced according to the standard requirements of the Q390GJC hot rolled steel plate for the high-grade building structure.
Disclosure of Invention
The invention aims to provide a production and preparation method of high-performance Q390GJC hot rolled H-shaped steel for buildings, wherein the performance index of the prepared H-shaped steel is satisfied, the yield strength Rel is more than or equal to 390MPa, the tensile strength Rm is more than or equal to 490MPa, the elongation A is more than or equal to 20%, the low-temperature impact at 0 ℃ is more than or equal to 34J, the yield ratio is less than or equal to 0.83, the CEV is less than or equal to 0.45%, and the Pcm is less than or equal to 0.29%.
In order to solve the technical problems, the invention adopts the following technical scheme:
the invention relates to a production and preparation method of high-performance Q390GJC hot rolled H-shaped steel for buildings, which comprises the following steelmaking process flow: converter-external refining-VD-special-shaped blank continuous casting; the steel rolling process flow comprises the following steps: step-by-step heating furnace-high pressure water dephosphorization-BD blooming-CCS finish rolling-cooling-straightening, its characterized in that:
the technical parameters controlled in the steelmaking process are as follows: VN alloy is adopted to prepare V, and the percentage content of N elements is more than or equal to 0.01 percent; vacuum breaking VD, adding VN alloy, and controlling the temperature of molten steel to be more than or equal to 1630 ℃; the superheat degree of continuous casting is less than or equal to 40 ℃; the pulling speed of the casting machine is more than or equal to 0.9m/min; the temperature of cooling water of the crystallizer is more than or equal to 26 ℃;
the technical parameters controlled in the rolling process are as follows: the heating temperature is 1150-1200 ℃, and the heat preservation time is more than or equal to 2.5 hours; the initial rolling temperature is less than or equal to 1050 ℃; the finishing temperature is less than or equal to 890 ℃.
Further, the chemical components of the paint are as follows in percentage by weight: c:0.13 to 0.16 percent; si:0.20 to 0.30 percent; mn:1.30 to 1.40 percent; p: less than or equal to 0.012%; s: less than or equal to 0.010 percent; v:0.05 to 0.07 percent, and the balance of Fe and unavoidable trace impurities.
Further, the chemical components of the paint are as follows in percentage by weight: c:0.15%; si:0.22%; mn:1.38%; p:0.012%; s:0.005%; v:0.06%, the balance of Fe and unavoidable trace impurities.
Further, the chemical components of the paint are as follows in percentage by weight: c:0.15%; si:0.24%; mn:1.35%; p:0.010%; s:0.003%; v:0.05%, the balance of Fe and unavoidable trace impurities.
Further, the mechanical properties of the prepared H-shaped steel are as follows: the yield strength Rel is more than or equal to 390MPa, the tensile strength Rm is more than or equal to 490MPa, the elongation A is more than or equal to 20%, the low-temperature impact at 0 ℃ is more than or equal to 34J, the yield ratio is less than or equal to 0.83, the CEV is less than or equal to 0.45%, and the Pcm is less than or equal to 0.29%.
The design principle of the chemical components is as follows:
c: c is the most effective element for improving the strength of the steel, the tensile strength and the yield strength of the steel are improved along with the increase of the content of C, but the elongation and the impact toughness are reduced, the corrosion resistance is also reduced, and the hardening phenomenon also occurs in a welding heat affected zone of the steel, so that welding cold cracks are generated. In order to ensure that the material obtains good comprehensive performance, the content of the C element in the steel is designed to be 0.13-0.16%.
Mn: mn is an important toughening element, the components are low, the strength of the steel is obviously improved along with the increase of the manganese content, the processing performance of the steel is improved, and the ductile-brittle transition temperature is hardly changed. However, too high manganese content can inhibit ferrite transformation, affect the yield strength of steel, and is unfavorable for the control of yield ratio. The Mn element content of the material is designed as Mn:1.30 to 1.40 percent.
Si: si can improve the corrosion resistance of steel, and is often added into stainless steel, low alloy steel and corrosion resistant alloy to improve the corrosion resistance of the alloy, so that the alloy has the performances of resisting chloride stress corrosion cracking, pitting corrosion, hot concentrated nitric acid corrosion, oxidation resistance, seawater corrosion resistance and the like. Research shows that in the hot and humid atmosphere environment, si can obviously improve the atmospheric corrosion resistance of carbon steel and low alloy steel, and in addition, si can also improve the corrosion resistance of the splash zone of the low alloy steel in seawater. The Si element content of the material is designed to be 0.20-0.30%.
P, S: p, S are impurity elements in steel. P has a certain effect of improving corrosion resistance, but P is an element easy to segregate, serious segregation is generated on the local part of steel, plasticity and toughness are reduced, and the P is extremely harmful to low-temperature toughness. The S element is easy to segregate and concentrate in steel, and is an element harmful to corrosion resistance. The steel of the invention strictly controls the sulfur and phosphorus content level in terms of metallurgical quality, namely P: less than or equal to 0.015 percent; s: less than or equal to 0.010 percent.
V: v and C, O, N have strong binding capacity and form extremely stable compounds with the V, C, O, N, so that grains can be refined, and the heat sensitivity and tempering brittleness of the steel are reduced. Can obviously improve the welding performance of common low alloy steel. The V element content of the steel is designed to be 0.06-0.08%.
Compared with the prior art, the invention has the beneficial technical effects that:
the low-carbon microalloying chemical composition design is adopted, so that the material has good anti-seismic performance and is suitable for high-grade building structures.
With VN microalloying, V and C, O, N both have strong binding ability and form extremely stable compounds therewith, refining the grains of the material.
The H-shaped steel prepared by the method has the performance indexes that the yield strength Rel is more than or equal to 390MPa, the tensile strength Rm is more than or equal to 490MPa, the elongation A is more than or equal to 20%, the low-temperature impact at 0 ℃ is more than or equal to 34J, the yield ratio is less than or equal to 0.83, the CEV is less than or equal to 0.45%, and the Pcm is less than or equal to 0.29%.
Drawings
The invention is further described with reference to the following description of the drawings.
Fig. 1 is a photograph of a metallographic structure of example 1, the structure is a ferrite and pearlite structure, the ferrite proportion is large, and the toughness is good.
Detailed Description
The following describes the invention in detail by way of specific examples, which are intended to aid in understanding the invention and are not intended to limit the invention.
Example 1: production of Q345GJC/D hot-rolled H-shaped steel for high-grade building structure
This example is directed to the production of a Q345GJC/D hot rolled H-section steel for high-grade building construction, the chemical composition and content of which are shown in table 1 below, the production process comprising in particular the following steps:
molten iron pretreatment, converter smelting, external refining, VD vacuum treatment, special-shaped blank continuous casting, heating, high-pressure water descaling, BD blooming, CCS finish rolling, cooling and straightening; wherein:
the tapping temperature of the converter is 1600 ℃;
heating time in the external refining process is 30min, and refining time is 35min;
argon blowing time of the VD furnace is not less than 10min in the VD vacuum treatment process;
the pulling speed range of a continuous casting machine in the special-shaped blank continuous casting process is 0.90m/min, and the degree of superheat of steel grades is less than 30 ℃;
the heating temperature in the heating process is 1220 ℃, and the heating time is 3 hours;
in the BD initial rolling and CCS finish rolling processes, the initial rolling temperature is 1160 ℃ and the final rolling temperature is 880 ℃.
The metallographic structure of the Q345GJC/D hot rolled H-shaped steel for the high-grade building structure, which is produced in the embodiment, is detected, and as shown in the figure 1, the metallographic structure is a ferrite structure and a pearlite structure, the ferrite proportion is larger, and the Q345GJC/D hot rolled H-shaped steel for the high-grade building structure has higher toughness. The mechanical properties of the produced Q345GJC/D hot rolled H-shaped steel for the high-grade building structure were also tested, and the results are shown in the following Table 2.
Example 2: production of Q345GJC/D hot-rolled H-shaped steel for high-grade building structure
This example is directed to the production of a Q345GJC/D hot rolled H-section steel for high-grade building construction, the chemical composition and content of which are shown in table 1 below, the production process comprising in particular the following steps:
molten iron pretreatment, converter smelting, external refining, VD vacuum treatment, special-shaped blank continuous casting, heating, high-pressure water descaling, BD blooming, CCS finish rolling, cooling and straightening; wherein:
the tapping temperature of the converter is 1550 ℃;
heating time in the external refining process is 30min, and refining time is 35min;
argon blowing time of the VD furnace is not less than 10min in the VD vacuum treatment process;
the pulling speed range of a continuous casting machine in the special-shaped blank continuous casting process is 0.90m/min, and the degree of superheat of steel grades is less than 30 ℃;
the heating temperature in the heating process is 1218 ℃, and the heating time is 3 hours;
in the BD initial rolling and CCS finish rolling processes, the initial rolling temperature is 1170 ℃, and the final rolling temperature is 870 ℃.
The mechanical properties of the high-grade building structure Q345GJC/D hot rolled H-shaped steel produced in this example were examined, and the results are shown in Table 2 below.
Example 3: production of Q345GJC/D hot-rolled H-shaped steel for high-grade building structure
This example is directed to the production of a Q345GJC/D hot rolled H-section steel for high-grade building construction, the chemical composition and content of which are shown in table 1 below, the production process comprising in particular the following steps:
molten iron pretreatment, converter smelting, external refining, VD vacuum treatment, special-shaped blank continuous casting, heating, high-pressure water descaling, BD blooming, CCS finish rolling, cooling and straightening; wherein:
the tapping temperature of the converter is 1550 ℃;
heating time in the external refining process is 30min, and refining time is 35min;
argon blowing time of the VD furnace is not less than 10min in the VD vacuum treatment process;
the pulling speed range of a continuous casting machine in the special-shaped blank continuous casting process is 0.90m/min, and the degree of superheat of steel grades is less than 30 ℃;
the heating temperature in the heating process is 1230 ℃, and the heating time is 3 hours;
in the BD initial rolling and CCS finish rolling processes, the initial rolling temperature is 1165 ℃, and the final rolling temperature is 880 ℃.
The mechanical properties of the high-grade building structure Q345GJC/D hot rolled H-shaped steel produced in this example were examined, and the results are shown in Table 2 below.
Comparative examples 1 to 3
Comparative examples 1 to 3 were conducted in the same manner as in example 1 except that the chemical component content of the hot rolled H-steel was different or the process parameters of the production method were different, specifically:
the chemical composition contents of the hot rolled H-steel produced in comparative examples 1-2 were different from those of example 1, and are specifically shown in Table 1 below;
comparative example 3 was different in the start rolling temperature and the finish rolling temperature at the time of producing the hot rolled H-section steel, wherein the start rolling temperature was 1140 ℃ and the finish rolling temperature was 890 ℃.
The mechanical properties of the high-grade building structures produced in comparative examples 1 to 3 were measured with Q345GJC/D hot rolled H-shaped steel, and the results are shown in Table 2 below.
Table 1: the chemical components and weight percentage content of the examples and comparative examples
| C | Si | Mn | P | S | V | |
| Example 1 | 0.13 | 0.22 | 1.35 | 0.012 | 0.005 | 0.04 |
| Example 2 | 0.14 | 0.24 | 1.32 | 0.010 | 0.003 | 0.05 |
| Example 3 | 0.12 | 0.23 | 1.33 | 0.010 | 0.005 | 0.05 |
| Comparative example 1 | 0.13 | 0.22 | 1.27 | 0.010 | 0.005 | 0.05 |
| Comparative example 2 | 0.13 | 0.22 | 1.40 | 0.010 | 0.004 | 0.05 |
| Comparative example 3 | 0.13 | 0.22 | 1.35 | 0.012 | 0.005 | 0.04 |
Table 2: mechanical property test results of steels produced in examples and comparative examples
As is clear from the contents shown in tables 1 and 2, the Q345GJC/D hot rolled H-shaped steel for high-grade building structure produced in examples 1-3 has excellent comprehensive mechanical properties, and satisfies the following conditions: the yield strength Rel is more than or equal to 411MPa, the tensile strength Rm is more than or equal to 587MPa, the elongation A is more than or equal to 25%, the low-temperature impact at minus 20 ℃ is more than or equal to 115J, and the yield ratio is less than or equal to 0.71. The steel produced in comparative example 1 has a reduced Mn content compared with example 1, which results in a reduced strength and impact toughness of the produced steel at-20 ℃; the steel produced in comparative example 2 has an increased Mn content as compared with example 1, and the strength (particularly yield strength) of the steel obtained by the production is greatly improved, but the impact toughness of the steel at 20 ℃ is seriously deteriorated; in comparison with example 1, comparative example 3, which controls a relatively low start rolling temperature and a relatively high finish rolling temperature, produced a steel having better strength properties, but not good for the impact toughness of the steel at 20 ℃ and only reaching 72.3J.
The above embodiments are only illustrative of the preferred embodiments of the present invention and are not intended to limit the scope of the present invention, and various modifications and improvements made by those skilled in the art to the technical solutions of the present invention should fall within the protection scope defined by the claims of the present invention without departing from the design spirit of the present invention.
Claims (5)
1. A production and preparation method of Q390GJC hot rolled H-shaped steel for high-performance buildings comprises the following steelmaking process flow: converter-external refining-VD-special-shaped blank continuous casting; the steel rolling process flow comprises the following steps: step-by-step heating furnace-high pressure water dephosphorization-BD blooming-CCS finish rolling-cooling-straightening, its characterized in that:
the technical parameters controlled in the steelmaking process are as follows: VN alloy is adopted to prepare V, and the percentage content of N elements is more than or equal to 0.01 percent; vacuum breaking VD, adding VN alloy, and controlling the temperature of molten steel to be more than or equal to 1630 ℃; the superheat degree of continuous casting is less than or equal to 40 ℃; the pulling speed of the casting machine is more than or equal to 0.9m/min; the temperature of cooling water of the crystallizer is more than or equal to 26 ℃;
the technical parameters controlled in the rolling process are as follows: the heating temperature is 1150-1200 ℃, and the heat preservation time is more than or equal to 2.5 hours; the initial rolling temperature is less than or equal to 1050 ℃; the finishing temperature is less than or equal to 890 ℃.
2. The method for producing and preparing the high-performance Q390GJC hot rolled H-shaped steel for buildings according to claim 1, which is characterized by comprising the following chemical components in percentage by weight: c:0.13 to 0.16 percent; si:0.20 to 0.30 percent; mn:1.30 to 1.40 percent; p: less than or equal to 0.012%; s: less than or equal to 0.010 percent; v:0.05 to 0.07 percent, and the balance of Fe and unavoidable trace impurities.
3. The method for producing and preparing the high-performance Q390GJC hot rolled H-shaped steel for buildings according to claim 2, which is characterized by comprising the following chemical components in percentage by weight: c:0.15%; si:0.22%; mn:1.38%; p:0.012%; s:0.005%; v:0.06%, the balance of Fe and unavoidable trace impurities.
4. The method for producing and preparing the high-performance Q390GJC hot rolled H-shaped steel for buildings according to claim 2, which is characterized by comprising the following chemical components in percentage by weight: c:0.15%; si:0.24%; mn:1.35%; p:0.010%; s:0.003%; v:0.05%, the balance of Fe and unavoidable trace impurities.
5. The method for producing and preparing the high-performance Q390GJC hot rolled H-shaped steel for construction according to claim 2, wherein the mechanical properties of the prepared H-shaped steel are as follows: the yield strength Rel is more than or equal to 390MPa, the tensile strength Rm is more than or equal to 490MPa, the elongation A is more than or equal to 20%, the low-temperature impact at 0 ℃ is more than or equal to 34J, the yield ratio is less than or equal to 0.83, the CEV is less than or equal to 0.45%, and the Pcm is less than or equal to 0.29%.
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