CN114107612B - Tempering heat treatment design method for H-shaped steel, hot-rolled H-shaped steel for anti-seismic and fireproof building structure and tempering heat treatment method for hot-rolled H-shaped steel - Google Patents

Tempering heat treatment design method for H-shaped steel, hot-rolled H-shaped steel for anti-seismic and fireproof building structure and tempering heat treatment method for hot-rolled H-shaped steel Download PDF

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CN114107612B
CN114107612B CN202111441392.1A CN202111441392A CN114107612B CN 114107612 B CN114107612 B CN 114107612B CN 202111441392 A CN202111441392 A CN 202111441392A CN 114107612 B CN114107612 B CN 114107612B
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shaped steel
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陈辉
夏勐
吴保桥
何军委
吴湄庄
沈千成
黄琦
汪杰
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Maanshan Iron and Steel Co Ltd
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    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • 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
    • C21D11/00—Process control or regulation for heat treatments
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
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Abstract

The invention provides a tempering heat treatment design method for H-shaped steel, hot-rolled H-shaped steel for an earthquake-resistant and fire-resistant building structure and a tempering heat treatment method thereof, wherein the tempering heat treatment design method comprises the following steps: through metallographic structure observation, the ratio A of ferrite in the original material structure of the H-shaped steel and the size range B of ferrite grains are determined 1 ‑B 2 And an average grain size C; calculating the holding time T of the tempering process, wherein T =60/A +2.5 × (C-B) 1 ) (ii) a Calculating tempering temperature T: t =550 ℃ +2 × (B) 2 -C). The tempering heat treatment method of the hot-rolled H-shaped steel for the anti-seismic and fire-resistant building structure, which is designed by utilizing the tempering heat treatment design method of the H-shaped steel, is used for obtaining a product structure of ferrite, pearlite and a small amount of sorbite; the strength index is improved, the high-temperature softening resistance is good, and the product has good shock resistance and fire resistance.

Description

Tempering heat treatment design method for H-shaped steel, hot-rolled H-shaped steel for anti-seismic and fireproof building structure and tempering heat treatment method for hot-rolled H-shaped steel
Technical Field
The invention belongs to the field of H-shaped steel production, and particularly relates to a tempering heat treatment design method of H-shaped steel, hot-rolled H-shaped steel for an earthquake-resistant and fire-resistant building structure and a tempering heat treatment method thereof.
Background
With the rapid development of building structures, the construction steel has higher and higher requirements. In particular to H-shaped steel for high-rise building structures, the structural weight is reduced, and the requirement of the performance service of the material under the conditions of earthquake and fire is also considered. Under the conditions of earthquake sudden strain and concentrated stress, the material can absorb larger energy in a short time, and the yield strength and the tensile strength of the material are required to be not more than 0.8; and in case of fire, the material still keeps larger strength under high temperature, and the yield strength of the material reaches two thirds of the yield strength of the material at the room temperature at the high temperature of 600 ℃. At present, the H-shaped steel for the building in China generally adopts the grade of Q345, and along with the high-rise and large-span development of the building, the H-shaped steel for the structure must use a high-strength series so as to improve the requirement of the stability of the building structure.
At present, MGFR490B steel is taken as a representative steel grade, and is widely applied to the fields of common buildings and structures. However, with the development of high-rise buildings, the ordinary 345MPa level cannot meet the requirements of large buildings and structures. Therefore, the development of the high-strength, anti-seismic and fire-resistant hot-rolled H-shaped steel has important significance for the development of future building application.
In the prior art, less H-shaped steel with the production strength level of 460MPa is produced, and particularly, a hot rolling method is singly adopted, so that not only is the capability of rolling mill equipment required to meet the condition of deformation compression, but also strict requirements on a controlled rolling process are met. The process window of the product in the aspects of earthquake resistance, corrosion resistance and fire resistance is narrow.
Disclosure of Invention
The invention aims to provide a design method for H-shaped steel tempering heat treatment, which is a method for designing the H-shaped steel tempering heat treatment process according to the structure, so that the original structure of the H-shaped steel is austenitized in the high-temperature tempering process, and the structure transformation is carried out in the tempering process range through the redissolution of ferrite, pearlite and a small amount of bainite or martensite structures, thereby improving the product performance and meeting higher use requirements.
The invention also aims to provide hot-rolled H-shaped steel for earthquake-resistant and fire-resistant building structures and a tempering heat treatment method thereof, and the 460MPa earthquake-resistant and fire-resistant hot-rolled H-shaped steel with good earthquake resistance and fire resistance is obtained by utilizing the H-shaped steel tempering heat treatment design method and designing a specific heat treatment method according to the specific structure of the H-shaped steel.
The specific technical scheme of the invention is as follows:
1) Through observation and measurement of H-shaped room temperature metallographic structure, the area ratio A of ferrite in the H-shaped steel raw material structure and the size range B of ferrite grains are determined 1 -B 2 And an average grain size C; b is 1 、B 2 And C is in the unit of μm; b 1 Minimum ferrite grain size, B 2 Is the maximum ferrite grain size; c is the average size of ferrite grains;
2) Calculating the holding time t of the tempering process, wherein t =60/A +2.5 × (C-B) 1 ) T is in units of min;
3) Calculating tempering temperature T: t =550 ℃ +2 × (B) 2 -C), T is in units;
4) According to the technical result, the tempering heat treatment method of the H-shaped steel comprises the following steps: heating to T +/-5 ℃, keeping the temperature for T +/-5 min, and then carrying out furnace cooling to room temperature.
The invention relates to a design method for tempering heat treatment of H-shaped steel, which is mainly based on the following steps: martensite and bainite structures formed in hot-rolled structures are utilized, distribution characteristics of ferrite structures are combined, recrystallization of matrix structures is promoted through a certain heat treatment tempering process, granular carbides are separated out at ferrite grain boundaries and island boundaries, tempered sorbite structures with excellent strength and toughness are formed, and mechanical properties of products after heat treatment are improved.
The tempering heat treatment method for the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure, which is designed by utilizing the tempering heat treatment design method for the H-shaped steel, comprises the following steps: the heating temperature is 570-650 deg.C, and the heat preservation time is 120-180min.
The hot-rolled H-shaped steel for the anti-seismic and fire-resistant building structure produced by the tempering heat treatment method comprises the following components in percentage by mass:
c:0.06% -0.12%, si:0.20% -0.45%, mn:0.60% -1.00%, P: less than or equal to 0.015 percent, S: less than or equal to 0.015 percent, cr:0.020% -0.080%, ni:0.50% -1.00%, cu: 0.20-0.60%, nb 0-0.045%, V:0.040% -0.080%, mo:0.10% -0.30%, al: 0.010-0.025%, and the balance of Fe and trace residual elements.
Wherein Cr + Ni + Cu is more than or equal to 1.2%; ni/Cu is more than or equal to 1.5; mo is more than or equal to 5Nb +15V;
specifically, the principle of the action and the proportion design of each element is as follows:
carbon (C): the carbon element has a very remarkable effect on improving the strength of steel, and the lower limit is set to be 0.06wt% in order to meet the requirement of high strength grade; considering that the carbon content is too high, which easily affects the plasticity of the material, and the composition of the alloy elements is too large, and the carbon content is too high, which easily causes the high temperature performance fluctuation of the material, the upper limit is set to 0.12wt%.
Silicon (Si): exists in a solid solution form in steel, has stronger solid solution strengthening effect, can obviously strengthen ferrite, and sets the lower limit to be 0.20wt% for obtaining higher strength; however, when the Si content is too high, the toughness and ductility of the steel are significantly reduced, and the upper limit is set to 0.45wt%.
Manganese (Mn): the transformation from ferrite to pearlite is effectively inhibited, the transformation temperature can be reduced, the transformation of austenite under the low-temperature condition is facilitated, the toughness of the material is greatly improved, and the lower limit is set to be 0.60wt%; however, when the manganese content is too high, segregation defects are generated in the casting slab, and the upper limit is set to 1.0wt%
Phosphorus (P): segregation is easy to occur in steel grades, the ductility and toughness of steel are greatly reduced, the surface quality of steel is influenced to a certain extent, and the upper limit is set to be 0.015wt% in consideration of the P removal difficulty in the steelmaking process.
Sulfur (S): the steel has large influence on the toughness of steel, and is easy to generate enrichment and segregation in the crystal grain and at the boundary, and particularly MnS inclusion is easy to form with manganese element, so that the matrix structure of the material is easy to form the boundary origin of cracks, and meanwhile, the upper limit is set to be 0.015wt% in consideration of the S removal difficulty in the steelmaking process.
Chromium (Cr): the strength is obviously improved, the yield ratio is reduced, the fire resistance and corrosion resistance of steel can be simultaneously improved, the stability of precipitated phases is improved by matching with Mo, nb and V, and in order to obtain good corrosion resistance, a compact rust layer is formed by matching with Ni and Cu, and the lower limit is set to be 0.02wt% in consideration of the corrosion resistance of the material; in case of addition of other alloying elements, chromium will deteriorate the weldability of the steel, setting the upper limit to 0.08wt%.
Nickel (Ni): the plasticity and toughness of the steel are obviously improved, the compactness of a rust layer can be improved, a stable rust layer is formed to improve the corrosion resistance and solve the surface quality problem caused by Cu brittleness, and the lower limit is set to be 0.50wt%; however, too high a content may result in incomplete descaling before rolling, with an upper limit of 1.00wt% being set.
Copper (Cu): easily enrich in rust layer, oxidation position or crack position, obviously improve the corrosion resistance of steel. The low-temperature-resistant alloy can obtain good corrosion resistance by being matched with Cr and Ni, and the lower limit is set to be 0.20wt% in consideration of small solubility in a matrix structure and improvement of high-temperature strength of steel; however, the content is too high, so that cracks or liquation defects are easily formed on the surface of the casting blank, and the upper limit is set to be 0.60wt%.
Wherein, in order to ensure the corrosion resistance of the product, a formula is calculated according to the weather resistance index
I＝26.01(Cu％)+3.88(Ni％)+1.20(Cr％)+1.49(Si％)+17.28(P％)-7.29(Cu％)(Ni％)-9.10(Ni％)(P％)-33.39(Cu％) 2 The material has good corrosion resistance and can ensure that I is more than or equal to 6.0, and in order to meet the requirement that the weather resistance index I of the product is more than or equal to 6.5, cr + Ni + Cu is more than or equal to 1.2% under the existing steelmaking level; meanwhile, considering that the addition of a large amount of alloy elements such as Cu and the like easily causes blank cracks, the surface quality of a casting blank and a finished product is improved by increasing the Ni content, and the Ni/Cu ratio is ensured to be more than or equal to 1.5.
Niobium (Nb): the strength of the product is improved by a mode of refining grains through precipitation and solution refining of important elements of austenite grains, and the product can reduce the overheating sensitivity of the Mo element in steel and obviously improve the high-temperature performance of the material by matching with the Mo element; considering the compression ratio capability of the product in the method, the high-temperature performance can be realized by combining a single Mo element with a large compression ratio for thin-specification products (the flange thickness is less than 40 mm), but the content of Mo is too high, so that the impact toughness is easily reduced and the fillet is easily cracked, so that the Nb in the invention is set to be in the range of 0-0.045wt%.
Vanadium (V): v is one of the most main microalloy elements in steel, and has obvious functions of fine-grain strengthening, precipitation strengthening and precipitation strengthening. Vanadium element is easy to form carbon-nitrogen compound with nitrogen element, thereby effectively preventing the crystal grains from growing excessively, promoting the transformation of austenite to ferrite and being beneficial to the precipitation of soft and tough phase, in addition, in the cooling process after rolling, the precipitation of the carbon-nitrogen compound plays a certain strengthening role, the upper limit is set to be 0.040wt%, but the plasticity is easy to reduce due to the high content of the vanadium element, the cost is high, and the lower limit is set to be 0.080wt%.
Molybdenum (Mo): the refractory property of the steel is obviously improved, the matrix is directly reinforced through solid solution strengthening, so that the high-temperature strength is improved, meanwhile, the thermal stability of the structure is enhanced at the defects such as a matrix interface and the like through segregation, MC phase nano particles are precipitated and refined in cooperation with Nb, V and the like, the defects such as an interface and dislocation are pinned, the thermal stability of the structure is improved, and the high-temperature strength is indirectly improved, wherein the lower limit is set to be 0.10wt%; however, too high a content lowers the toughness of the material, and the upper limit is set to 0.30wt%.
In consideration of the strength improvement of the V element, the strength performance of the product in the high-temperature deformation process can be ensured only by combining a certain content of Mo element when single V element is adopted to realize grain refinement, so that the content of the Mo element is required to be more than 1.5V; aiming at a thick product with the flange thickness of more than 40mm, the deformation compression is considered to be small, the grain refining effect is limited, precipitation strengthening is realized by adding V, nb composite element, the strength of the product is improved, and meanwhile, in order to realize the effect of reducing the high-temperature sensitivity of Mo by Nb element and increase the Mo content to improve the high-temperature resistance of the product, mo is required to be more than or equal to 5Nb +1.5V.
Aluminum (Al): the aluminum-based alloy is a strong oxidant and an important deoxidizing element, can be combined with a nitrogen element in steel to form AlN precipitates to play a role in refining austenite grains, so the lower limit is set to be 0.010wt%, but the aluminum content is too high, blank nodulation and component inclusion are easily caused in the steelmaking process, the blank quality is influenced, and the upper line is set to be 0.025wt%.
The hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure is obtained by hot rolling and cooling rolling, wherein the hot rolling process is required to realize the total section compression ratio of 15-40% below 960 ℃; the cooling process adopts a water cooling mode to realize the temperature of the red returning at 550-650 ℃. After the hot rolling and cooling production, the room temperature structure of the obtained hot rolled H-shaped steel for the anti-seismic and fire-resistant building structure is ferrite, pearlite and a small amount of bainite or martensite, wherein the area structure of the ferrite accounts for 45-70%, and the grain size of the ferrite is 5-50 mu m.
The thickness of the hot-rolled H-shaped steel flange for the earthquake-resistant and fire-resistant building structure is 20-60 mm.
The structure of the tempered hot-rolled H-shaped steel for the anti-seismic and fire-resistant building structure is ferrite, pearlite and a small amount of tempered sorbite; the strength index is improved, the yield strength reaches 520MPa-650MPa, the tensile strength reaches 650MPa-780MPa, the yield ratio is less than 0.78, meanwhile, the yield strength at 600 ℃ reaches 320-426MPa, high-temperature brittleness is effectively avoided, the high-temperature softening resistance is good, and the product has good shock resistance and fire resistance.
The method is limited by the problems of narrow production process window, high equipment capacity requirement and the like at present, and the use requirements of the product on the shock resistance, the weather resistance and the fire resistance are realized by considering the process treatment such as tempering and the like of the actual production product by adopting a heat treatment process. The invention provides a design method of a tempering treatment process of H-shaped steel, and the H-shaped steel is treated according to the tempering treatment process designed by the design method, so that the performance of the H-shaped steel can be improved, and the use requirements of earthquake resistance and fire resistance can be met. Moreover, the invention also provides 460MPa anti-seismic fire-resistant hot-rolled H-shaped steel treated by the tempering process obtained according to the design method, so that an original tissue is austenitized in the high-temperature tempering process, carbides are separated out in ferrite grain boundaries and island boundaries through matrix tissue recrystallization, and tissue transformation is carried out in the tempering process range, and finally a tempered sorbite tissue with good obdurability is formed, the product strength is higher than that before the tempering process, the yield ratio is less than 0.78, and the H-shaped steel has good anti-seismic property and fire resistance, and can be widely applied to various large-scale stadiums and high-rise buildings.
Drawings
FIG. 1 is the golden phase diagram (x 500) of the original structure of example 1;
FIG. 2 shows the metallographic structure (. Times.200) after the tempering process in example 1.
FIG. 3 is the metallographic structure (. Times.500) after the tempering process of example 1;
FIG. 4 is the original metallographic structure diagram (magnification × 500) of example 2;
FIG. 5 shows the metallographic structure (. Times.200) after the tempering process in example 2;
FIG. 6 shows the metallographic structure (magnification × 500) after the tempering process in example 2;
FIG. 7 is a metallographic image of the original structure of comparative example 1;
FIG. 8 is a gold phase diagram of the original structure of comparative example 2.
Detailed Description
Example 1
A design method for tempering heat treatment of anti-seismic and fireproof hot-rolled H-shaped steel has the product specification of H630 multiplied by 200 multiplied by 15 multiplied by 20 (height multiplied by width multiplied by web thickness multiplied by flange thickness), and the chemical components (by mass percent) of the product are C:0.08%, si:0.35%, mn:0.64%, P: less than or equal to 0.015 percent, S: less than or equal to 0.015 percent, cr:0.035%, ni:0.85%, cu:0.40%, V:0.071%, mo:0.125%, al:0.025%, and the balance of Fe and trace residual elements, wherein Cr + Ni + Cu =1.285%; ni/Cu =2.125; mo is more than or equal to 5Nb +1.5V;
the production of the anti-seismic and fireproof hot-rolled H-shaped steel comprises hot rolling and cooling rolling, wherein the hot rolling process is required to realize 40% of total section compression ratio below 960 ℃; the cooling process adopts a water cooling mode to realize the temperature of the red returning at 550-570 ℃. The original metallographic structure is shown in FIG. 1.
The specific design method of the tempering heat treatment is as follows:
1) At room temperature, the original material (ferrite + pearlite + a small amount of martensite) is determined by metallographic structure observation) The area ratio A of ferrite in the structure is 58% (ratio 0.58) and the ferrite grain size B 1 -B 2 In the range of 7-34 μm and an average grain size C of 14 μm;
2) According to the ferrite proportion A and the size range B in the original material structure 1 -B 2 And the average grain size C determines the holding time t of the tempering process, wherein t =60/A +2.5 × (C-B) 1 ) =60/0.58+2.5 × (14-7) ≈ 121min; the heating and heat preservation time is 116-126min, and the heat preservation time is 120min.
3) The design method provided by the invention is used for calculating the tempering temperature T: t =550 ℃ +2 × (B) 2 -C) =550+2 x (34-14) =590 ℃. In the embodiment 1 of the invention, the material is heated to 550-680 ℃, heat preservation treatment is carried out according to the heat preservation time t =120min, and then furnace cooling is carried out to the room temperature;
in example 1, different tempering and heat preservation temperatures are adopted for treatment, specifically as shown in table 1, and the performance of the heat-treated product is shown in table 1.
Table 1 shows different tempering temperatures and properties of the H-shaped steel of example 1
Figure BDA0003383476230000081
The serial number 8 is the product performance without tempering process.
Calculating the tempering temperature T according to the design method provided by the invention: t =550 ℃ +2 × (B) 2 -C) =550+2 x (34-14) =590 ℃. According to the different tempering processes, when the heat preservation temperature is 590 ℃, the heat preservation time is 120min, the mechanical property of the material is excellent, the high-temperature mechanical property at 600 ℃ is optimal, the structure after tempering treatment is ferrite, pearlite and a small amount of sorbite, wherein the ferrite accounts for 46%.
Example 2
A design method for tempering heat treatment of anti-seismic and fire-resistant hot-rolled H-shaped steel is disclosed, the product specification is H458X 417X 30X 50 (height X width X web thickness X flange thickness), and the chemical components (by mass percent) of the method are C:0.08%, si:0.35%, mn:0.62%, P: less than or equal to 0.015%, S: less than or equal to 0.015 percent, cr:0.035%, ni:1.0%, cu:0.40%, nb:0.035%, V:0.072%, mo:0.285%, al:0.025 percent, and the balance of Fe and trace residual elements, wherein Cr + Ni + Cu =1.435 percent; ni/Cu =2.5; mo is more than or equal to
5Nb+1.5V；
The production of the anti-seismic fire-resistant hot-rolled H-shaped steel comprises hot rolling and cooling rolling, wherein the hot rolling process is required to realize the total section compression ratio of 30% below 960 ℃; the cooling process adopts a water cooling mode to realize the temperature of the red return at 590-610 ℃. The original metallographic structure is shown in FIG. 4 below.
The specific design method of the tempering heat treatment is as follows:
1) At room temperature, by metallographic structure observation, the percentage A of ferrite in the structure of the original material (ferrite + pearlite + a small amount of bainite) is determined to be 52% (percentage 0.52), the grain size B of the ferrite is determined to be 8-28 μm, and the average grain size C is determined to be 19 μm;
2) Determining the tempering temperature of the tempering process according to the ferrite proportion A, the size range B and the average grain size C in the original material structure: heating the material to T =550 ℃ +2 × (B) 2 -C) =550+2 x (28-19) =568 ℃, the heating and heat preservation temperature is 563-573 ℃, and the heat preservation temperature is 570 ℃ in the invention.
3) The incubation time t is calculated, where t =60/A +2.5 × (C-B) 1 ) =60/0.52+2.5 × (19-8) ≈ 143min, the heating and heat preservation time is 138-148min, and the heat preservation time is 140min.
Example 2 the heat preservation treatment is carried out for 100-200min respectively, and then furnace cooling is carried out to the room temperature.
In example 2, different tempering and heat preservation times are adopted for treatment, specifically shown in table 2, and the product performance after heat treatment is shown in table 2.
Table 2 shows different tempering temperatures and properties of the H-shaped steel of example 1
Figure BDA0003383476230000101
No. 7 shows the product performance without tempering, i.e., the room temperature texture.
According to the different tempering processes, when the heat preservation temperature is 570 ℃ and the heat preservation time is 140min, the mechanical property of the material is excellent, the high-temperature mechanical property at 600 ℃ is optimal, the tempered metallographic structure is ferrite, pearlite and a small amount of sorbite, and the ferrite structure accounts for 41%.
Comparative example 1
A design method for tempering heat treatment of anti-seismic and fireproof hot-rolled H-shaped steel has the product specification of H606 multiplied by 201 multiplied by 12 multiplied by 20mm (height multiplied by width multiplied by web thickness multiplied by flange thickness), and the chemical components (by mass percent) of the product are C:0.09%, si:0.30%, mn:0.84%, P:0.012%, S:0.010%, cr:0.06%, ni:0.65%, cu:0.32%, nb:0,V, 0.062%, mo:0.086%, al:0.018%, the balance of Fe and trace residual elements, wherein Cr + Ni + Cu =1.03%; ni/Cu =2.0; mo < 5Nb +1.5V;
the production of the anti-seismic and fireproof hot-rolled H-shaped steel comprises hot rolling and cooling rolling, wherein the hot rolling process is required to realize 36% of total section compression ratio below 960 ℃; the cooling process adopts a water cooling mode to realize the temperature of the red returning at 555-575 ℃. The original metallographic structure of the steel is ferrite + pearlite + a small amount of martensite, as shown in fig. 7.
The specific design method of the tempering heat treatment is as follows:
1) At room temperature, metallographic observation confirmed that the ferrite content A in the structure of the starting material (ferrite + pearlite + a small amount of martensite) was 45% and the ferrite grain size B 1- B 2 In the range of 6 to 35 μm and an average grain size C of 12 μm;
2) Determining the tempering temperature of the tempering process according to the ferrite proportion A, the size range B and the average grain size C in the original material structure: the material was heated to T =550 ℃ +2 × (B) 2 -C) =550+2 x (35-12) =596 ℃, the heating and heat preservation temperature is 591-601 ℃, and the heat preservation temperature is 600 ℃. The temperature during the heat treatment is 560-640 ℃.
3) The incubation time t is calculated, where t =60/A +2.5 × (C-B) 1 ) =60/0.45+, 2.5 × (12-6) ≈ 148min, the heating and heat preservation time is 143-153 min, and the invention adopts the method for heat preservationThe time is 150min.
The properties of the products after heat treatment are shown in Table 3.
Table 3 shows different tempering temperatures and properties of the H-shaped steel of comparative example 1
Figure BDA0003383476230000111
The metallographic structure of the test steel No. 3 after tempering is ferrite + pearlite + a small amount of sorbite, wherein the ferrite structure accounts for 38%.
It can be seen from the above different tempering processes that if the composition conditions of the present invention are not satisfied, even if the heat treatment is performed according to the method designed by the present invention, the properties still do not satisfy the requirements of the present invention.
Comparative example 2
A design method for tempering heat treatment of anti-seismic and fireproof hot-rolled H-shaped steel has the product specification of HH458 multiplied by 417 multiplied by 30 multiplied by 50 (height multiplied by width multiplied by web thickness multiplied by flange thickness), and the chemical components (by mass percent) of the H-shaped steel are as follows: 0.08%, si:0.35%, mn:0.86%, P:0.013%, S:0.008%, cr:0.061%, ni:0.72%, cu:0.42%, nb 0.026%, V:0.068%, mo:0.218%, al:0.015% and the balance of Fe and trace residual elements, wherein Cr + Ni + Cu =1.201%; ni/Cu =1.7; mo < 5Nb +1.5V;
the production of the anti-seismic and fireproof hot-rolled H-shaped steel comprises hot rolling and cooling rolling, wherein the hot rolling process is required to realize the total section compression ratio of 30 percent below 960 ℃; the cooling process adopts a water cooling mode to realize the temperature of the red return at 590-610 ℃. The original metallographic structure thereof was ferrite + pearlite + a small amount of martensite, as shown in fig. 8.
The specific tempering heat treatment design method is as follows:
1) At room temperature, through metallographic structure observation, the ratio A of ferrite in the original material (ferrite + pearlite + a small amount of martensite) structure is determined to be 45%, the range of ferrite grain size B is 12-58 μm, and the average grain size C is determined to be 36 μm;
2) According to the ratio A of ferrite in the original material tissue, the size range B and the averageThe average grain size C determines the tempering temperature of the tempering process: the material was heated to T =550 ℃ +2 × (B) 2 -C) =550+2 x (58-36) =594 ℃, the heating and heat preservation temperature is 589-599 ℃, and the heat preservation temperature is 590 ℃.
3) The incubation time t was calculated, where t =60/A +2.5 × (C-B) 1 ) =60/0.45+, 2.5 × (36-12) ≈ 193min, the heating and heat preservation time is 188-198 min, and the heat preservation time is 190min. In the experimental process, the heat preservation time is respectively selected to be 130-210min.
The properties of the products after heat treatment are shown in Table 4.
Table 4 shows different tempering temperatures and properties of the H-shaped steel of comparative example 2
Figure BDA0003383476230000131
The metallographic structure of the test steel No. 4 after tempering is ferrite + pearlite + a small amount of sorbite, wherein the ferrite structure accounts for 37%.
According to the different tempering processes, even if the components are in the range of the invention, if the Cr + Ni + Cu content of the invention is not more than or equal to 1.2 percent; ni/Cu is more than or equal to 1.5; under the condition that Mo is more than or equal to 5Nb +1.5V, even if the heat treatment is carried out according to the method designed by the invention, the performance still can not meet the requirements of the invention.

Claims (8)

  1. 5363 a method for designing the tempering heat treatment of 1.H section steel, which is characterized in that the method comprises the following steps:
    1) Through observing and measuring H-shaped room temperature metallographic structure, determining the area ratio A of ferrite in the H-shaped steel raw material structure and the size range B of ferrite grains 1 -B 2 And an average grain size C; b is 1 、B 2 C in μm; b 1 Is the minimum value of ferrite grain size, B 2 Is the maximum ferrite grain size; c is the average size of ferrite grains;
    2) Calculating the holding time t of the tempering process, wherein t =60/A +2.5 × (C-B) 1 ) T is in units of min;
    3) Calculate backFire temperature T: t =550 ℃ +2 × (B) 2 -C), T is in units;
    4) According to the technical result, the tempering heat treatment method of the H-shaped steel comprises the following steps: heating to T +/-5 ℃, keeping the temperature for T +/-5 min, and then carrying out furnace cooling to room temperature;
    the H-shaped steel comprises the following components in percentage by mass: c:0.06% -0.12%, si:0.20% -0.45%, mn:0.60% -1.00%, P: less than or equal to 0.015 percent, S: less than or equal to 0.015 percent, cr:0.020% -0.080%, ni:0.50% -1.00%, cu: 0.20-0.60%, nb 0-0.045%, V:0.040% -0.080%, mo:0.10% -0.30%, al:0.010% -0.025%, and the balance of Fe and trace residual elements;
    wherein, cr + Ni + Cu is more than or equal to 1.2 percent; ni/Cu is more than or equal to 1.5; mo is more than or equal to 5Nb +1.5V.
  2. 2. The tempering heat treatment method of the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure designed by the design method of claim 1 is characterized in that the heating temperature of the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure is 570-650 ℃, and the heat preservation time is 120-180min.
  3. 3. The tempering heat treatment method for the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure according to claim 2, wherein the room temperature structure of the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure is ferrite and pearlite plus a small amount of bainite or martensite, wherein the ferrite structure accounts for 45% -70%, and the grain size of the ferrite ranges from 5 μm to 50 μm.
  4. 4. The hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure produced by the tempering heat treatment method according to claim 2 or 3, wherein the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure comprises the following components in percentage by mass: c:0.06% -0.12%, si:0.20% -0.45%, mn:0.60% -1.00%, P: less than or equal to 0.015%, S: less than or equal to 0.015 percent, cr:0.020% -0.080%, ni:0.50% -1.00%, cu: 0.20-0.60%, nb 0-0.045%, V:0.040% -0.080%, mo:0.10% -0.30%, al: 0.010-0.025%, and the balance of Fe and trace residual elements.
  5. 5. The hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure according to claim 4, wherein Cr + Ni + Cu is more than or equal to 1.2%; ni/Cu is more than or equal to 1.5; mo is more than or equal to 5Nb +1.5V.
  6. 6. The hot-rolled H-shaped steel for earthquake-resistant and fire-resistant building structures according to claim 4 or 5, wherein the structure after the tempering heat treatment of the hot-rolled H-shaped steel for earthquake-resistant and fire-resistant building structures is ferrite, pearlite and a small amount of sorbite.
  7. 7. The hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure according to claim 4, wherein after tempering heat treatment, the yield strength of the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure reaches 520MPa to 650MPa, the tensile strength of the hot-rolled H-shaped steel reaches 650MPa to 780MPa, the yield ratio of the hot-rolled H-shaped steel is less than 0.78, and the yield strength of the hot-rolled H-shaped steel at 600 ℃ reaches 320 MPa to 426MPa.
  8. 8. The hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure according to claim 4, wherein the thickness of the flange of the hot-rolled H-shaped steel for the earthquake-resistant and fire-resistant building structure is 20-60 mm.
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10280088A (en) * 1997-02-06 1998-10-20 Sumitomo Metal Ind Ltd Steel product for building structural use and its production
CN1769510A (en) * 2004-11-05 2006-05-10 马鞍山钢铁股份有限公司 Steel for high strength shock-proof hot-rolled steel bar
CN101861406A (en) * 2007-11-22 2010-10-13 株式会社神户制钢所 High-strength cold-rolled steel sheet
CN104619876A (en) * 2012-09-13 2015-05-13 杰富意钢铁株式会社 Hot-rolled steel sheet and method for manufacturing same
CN109628836A (en) * 2019-01-02 2019-04-16 北京科技大学 A kind of high-strength building structure anti-seismic refractory steel and preparation method thereof
JP2020059881A (en) * 2018-10-09 2020-04-16 日本製鉄株式会社 Steel material and method for manufacturing the same

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10280088A (en) * 1997-02-06 1998-10-20 Sumitomo Metal Ind Ltd Steel product for building structural use and its production
CN1769510A (en) * 2004-11-05 2006-05-10 马鞍山钢铁股份有限公司 Steel for high strength shock-proof hot-rolled steel bar
CN101861406A (en) * 2007-11-22 2010-10-13 株式会社神户制钢所 High-strength cold-rolled steel sheet
CN104619876A (en) * 2012-09-13 2015-05-13 杰富意钢铁株式会社 Hot-rolled steel sheet and method for manufacturing same
JP2020059881A (en) * 2018-10-09 2020-04-16 日本製鉄株式会社 Steel material and method for manufacturing the same
CN109628836A (en) * 2019-01-02 2019-04-16 北京科技大学 A kind of high-strength building structure anti-seismic refractory steel and preparation method thereof

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