CN112853225B - 690 MPa-level steel plate for high-rise building large heat input welding and preparation method thereof - Google Patents

690 MPa-level steel plate for high-rise building large heat input welding and preparation method thereof Download PDF

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CN112853225B
CN112853225B CN202110020973.1A CN202110020973A CN112853225B CN 112853225 B CN112853225 B CN 112853225B CN 202110020973 A CN202110020973 A CN 202110020973A CN 112853225 B CN112853225 B CN 112853225B
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steel plate
heat input
temperature
mpa
input welding
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CN112853225A (en
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师仲然
王东明
潘涛
赵和明
罗小兵
杨海峰
柴锋
王树国
杨才福
曲之国
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Central Iron and Steel Research Institute
Rizhao Steel Yingkou Medium Plate Co Ltd
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Minmetals Yingkou Medium Plate Co ltd
Central Iron and Steel Research Institute
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
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    • C21—METALLURGY OF IRON
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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
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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
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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
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • 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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • 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
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    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C21D2211/008—Martensite

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Abstract

The invention relates to a 690 MPa-grade steel plate for high-rise building high heat input welding and a preparation method thereof, belongs to the technical field of high-rise building steel, and solves the problem that the prior art cannot simultaneously meet the thickness specification, strength grade and welding heat input wire quantity of the steel plate, so that the requirement of the high-rise building steel cannot be met. The 690 MPa-grade steel plate for high-rise building high heat input welding is characterized by comprising the following chemical components in percentage by mass: 0.08-0.12%, Mn: 1.0-1.6%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als is more than or equal to 0.015%, Cu is more than or equal to 0.18%, Ni: 1.0-2.0 percent of Ti/N, 0.4-0.6 percent of Cr, 0.4-0.6 percent of Mo and 0.03-0.06 percent of V, wherein the ratio of Ti to N is 0.67-0.8. The problem of satisfying the steel requirement for high-rise buildings of steel sheet thickness specification, intensity level and welding heat input linear volume simultaneously is realized.

Description

690 MPa-level steel plate for high-rise building large heat input welding and preparation method thereof
Technical Field
The invention relates to the technical field of steel for high-rise buildings, in particular to a 690 MPa-level steel plate for high heat input welding for high-rise buildings and a preparation method thereof.
Background
The high-speed development of modern economy puts higher demands on high-rise, super high-rise, large-span and light steel light plate buildings. Under the condition of high heat input welding, particularly under the condition that the welding heat input is more than 50kJ/cm, along with the increase of the welding heat input, the high-temperature retention time of the welding HAZ is prolonged, the original austenite grains are grown seriously, the cooling speed after welding is slow, coarse side lath ferrite, Wei-Wei tissues, upper bainite, M-A components and other tissues which are unfavorable for toughness are easily formed in a welding heat affected zone after phase transformation, the toughness of the welding heat affected zone is obviously reduced, a local brittle zone is formed, welding defects such as cracks and the like are possibly generated, the safety of a welded component is reduced, and the service use requirement cannot be met. Therefore, how to ensure the low-temperature toughness of the heat affected zone under the condition of high heat input welding is a difficult point for developing the heat affected zone.
The research work is less for the high-strength high heat input welding steel plate for the high-rise building. Such as: patent CN10128972B discloses a low yield ratio high heat input weldable high strength high toughness steel plate and a manufacturing method thereof, wherein a low carbon-high Mn-Nb + Ti micro alloying design is adopted to control C/Mn: 25-55, Ti/N: 3.0-4.0, Ti/Nb: 0.3-1.0, Ca treated and Ca/S between 0.8-3.0, steel plate yield strength 500-: 670 and 680MPa, the thickness specification is less than or equal to 40mm, and the impact energy of the welding joint is more than or equal to 100J when t8/5 is 120 s. Due to the alloy design idea, the thickness specification and the strength level of the steel plate are lower, and the steel plate is not suitable for the requirement of high-strength steel plates with the strength of more than 550MPa for high-rise buildings. Similarly, patent CN109321817A discloses a steel plate suitable for welding with extra large heat input and a manufacturing method thereof, wherein oxygen level in the steel is selectively controlled to be 20-200ppm by controlling a deoxidizer in the smelting process, then Ti and V elements are added, REM is added when oxygen is further determined to be 90ppm, Mg is added when oxygen is determined to be 50ppm, and the Ti, V, Mg and REM are added by adopting a wire feeding mode, so that the size of inclusions in the steel is ensured to be 0.5-5 μm, the number of Ti-Mg-REM-O composite inclusions accounts for 45%, the yield strength of the prepared steel plate is 365MPa, and the thickness of the prepared steel plate is 100 mm. However, the method needs to accurately control the oxygen content of the smelting process and adopt a wire feeding mode to feed wires, which can prolong the smelting period and adversely affect the low-temperature toughness of the steel plate when the size of the inclusions is controlled incorrectly; in addition, the steel plate has lower strength grade, and is not suitable for the requirement of high-strength thick steel plates for high-rise buildings.
Disclosure of Invention
In view of the above analysis, the invention aims to provide a 690 MPa-grade steel plate for high-rise building large heat input welding and a preparation method thereof, so as to solve the problem that the prior art cannot simultaneously meet the thickness specification, strength grade and welding heat input linear quantity of the steel plate, so that the requirement of the steel for the high-rise building cannot be met.
The invention provides a 690 MPa-grade steel plate for high-rise building large heat input welding, which comprises the following chemical components in percentage by mass: 0.08-0.12%, Mn: 1.0-1.6%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als is more than or equal to 0.015%, Cu is more than or equal to 0.18%, Ni: 1.0-2.0 percent of Ti/N, 0.4-0.6 percent of Cr, 0.4-0.6 percent of Mo and 0.03-0.06 percent of V, wherein the ratio of Ti to N is 0.67-0.8.
Further, the steel plate comprises the following chemical components in percentage by mass: 0.10 to 0.12%, Mn: 1.0-1.2%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als: 0.015% -0.018%, Cu: 0.18% -0.25%, Ni: 1.0 to 1.2 percent of Ti, 0.4 to 0.6 percent of Cr, 0.4 to 0.6 percent of Mo and 0.03 to 0.06 percent of V, wherein the ratio of Ti to N is 0.7 to 0.75.
Further, the maximum thickness specification of the steel plate is 60 mm.
Further, the structure of the welding heat affected zone of the steel plate is characterized by martensite + lath bainite + granular bainite structure + M-A islands.
Furthermore, the volume percentage of the lath bainite and martensite structures is more than or equal to 80%, the volume percentage of the granular bainite is less than or equal to 20%, and the volume percentage of the M-A welding heat affected zone of the steel plate is less than or equal to 5%.
Furthermore, the volume percentage of the large-angle crystal boundary of the steel plate is more than or equal to 60 percent, and the large-angle crystal boundary is crystal grains with an orientation difference angle of more than 15 degrees.
On the other hand, the invention provides a preparation method of the steel plate for 690 MPa-level high heat input welding for high-rise buildings, which is used for preparing the steel plate for 690 MPa-level high heat input welding for high-rise buildings and comprises the following rolling and cooling control processes: the steel plate is rolled in two stages of high-temperature stage rolling and low-temperature stage rolling.
Further, the high-temperature section adopts high temperature and high pressure, and the finishing temperature is more than or equal to 950 ℃.
Further, the low-temperature section is rolled at low temperature and high pressure, the development temperature is not higher than 850 ℃, the finish rolling temperature is not lower than 800 ℃, then water cooling is carried out, and the temperature of the steel plate for returning red is controlled to be not lower than 650 ℃.
Further, the method comprises the following steps: the off-line quenching and tempering treatment is carried out on the rolled steel plate, the quenching temperature range is 840-880 ℃, and the tempering temperature range is 550-650 ℃.
Compared with the prior art, the invention can realize at least one of the following beneficial effects:
(1) the alloy composition design is reasonable, the content of nitrogen element is controlled, and the Ti/N is controlled to be between 0.67 and 0.8, so that the Ti/N ratio requirement is met, the 690 MPa-level steel plate for large heat input welding for high-rise buildings, which has the structure characteristics of martensite, lath bainite and granular bainite structures in the welding heat affected zone of the steel plate and an M-A island, is obtained, the volume percentage of the lath bainite and martensite structures in the structure of the welding heat affected zone of the steel plate is more than or equal to 80 percent, the volume percentage of the granular bainite is less than or equal to 20 percent, the volume percentage of the M-A island is less than or equal to 5 percent, the yield strength of the steel plate is more than 690MPa, and the tensile strength of the steel plate can reach 760 minus 930 MPa.
(2) The invention adopts two-stage rolling by a controlled rolling and controlled cooling process, wherein the high-temperature section adopts high temperature and high pressure, the final rolling temperature is more than or equal to 950 ℃, and the accumulated deformation is not lower than 40 percent; the low-temperature section is rolled at low temperature and high pressure, the initial rolling temperature is not higher than 850 ℃, the final rolling temperature is not lower than 800 ℃, the accumulated deformation is not lower than 50%, then water cooling is carried out, the steel plate reddening temperature is controlled to be not lower than 650 ℃, simultaneously a tempering process is adopted, offline quenching (water quenching) and tempering treatment are carried out on the rolled steel plate, the quenching temperature range is 840-880 ℃, the tempering temperature range is 550-650 ℃, and the outstanding performance indexes that the welding line energy is not lower than 200kJ/cm and the 0 ℃ impact energy of a welding joint is not lower than 100J are realized on the condition that the yield strength of the steel is not lower than 690MPa and the tensile strength is 760-930MPa for the steel plate with the thickness of 60mm for high-rise buildings.
(3) According to the preparation method of the 690MPa grade high-strength thick steel plate for high heat input welding for the high-rise building, the hardenability of the steel plate can be improved by optimizing the content of alloy elements, and the yield strength, the tensile strength and the impact toughness of the steel plate are greatly improved by adopting two-stage rolling and quenching and tempering processes; the steel plate has good uniformity, meets the requirement of thick-specification high heat input welding steel plates, and solves the problem that the low-temperature toughness of the steel plate for the high-rise building is poor after high heat input welding.
In the invention, the technical schemes can be combined with each other to realize more preferable combination schemes. 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 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 drawings.
Drawings
The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, wherein like reference numerals are used to designate like parts throughout.
FIG. 1 is a microstructure of a weld heat affected zone of example steel.
Detailed Description
The invention provides a preparation method of a 690MPa grade high-strength steel plate for high-rise building high-heat input welding, which controls the microstructure and fracture characteristics of the steel plate by controlling the steel plate component composition and smelting and rolling process, so that the steel plate meets the following requirements that the yield strength is more than or equal to 690MPa and the tensile strength is as follows: 760 plus 930MPa, the-40 ℃ impact energy of the base material is more than or equal to 200J, the 0 ℃ impact energy of the welding joint is more than or equal to 100J and the like.
The invention provides a preparation method of a 690 MPa-grade high-strength steel plate for high heat input welding for a high-rise building, which specifically comprises the following steps:
(1) smelting by adopting a converter according to the component proportion of the invention;
(2) LF and RH refining for 15-25min, controlling the superheat degree of the tundish to be less than or equal to 20 ℃, and adopting protective pouring in the whole process;
(3) continuously casting to obtain a continuous casting billet, heating the continuous casting billet to 1150-1250 ℃, and preserving heat;
(4) controlled rolling and controlled cooling process: the steel plate is rolled in two stages of high-temperature rolling and low-temperature rolling,
the high-temperature section rolling adopts high temperature and high pressure, the finishing temperature is more than or equal to 950 ℃, and the accumulated deformation is not less than 40 percent;
the low-temperature section rolling adopts low-temperature high-pressure rolling, the initial rolling temperature is not higher than 850 ℃, the final rolling temperature is not lower than 800 ℃, the accumulated deformation is not lower than 50%, and then water cooling is carried out, and the temperature of the steel plate for returning red is not lower than 650 ℃;
(5) and (3) quenching and tempering: off-line quenching and tempering are carried out on the rolled steel plate, the quenching temperature range is 840-880 ℃, and the tempering temperature range is 550-650 ℃.
It should be noted that, because the element composition of the invention has special requirements, especially Ti/N is required to be between 0.67 and 0.8, in order to prevent the austenite grains of the continuous casting slab from obviously growing up, according to the component characteristics of the invention, the continuous casting slab is heated to 1150 to 1250 ℃, and at the moment, the solid solution of the alloy elements and the refinement of the austenite grains can be ensured.
The steel plate is obtained through the process flow, the thickness specification is less than or equal to 60mm, the yield strength is more than or equal to 690MPa, and the tensile strength is as follows: 760 and 930MPa, and the impact energy of the base material at-40 ℃ is more than or equal to 200J.
The structure characteristics of the obtained steel plate welding heat affected zone are martensite, lath bainite, granular bainite structure and M-A islands, wherein the volume percentage of the lath bainite and the martensite structure is more than or equal to 80%, the volume percentage of the granular bainite is less than or equal to 20%, the volume percentage of the M-A islands is less than or equal to 5%, and the volume percentage of the large-angle grain boundary is more than or equal to 60%.
The steel plate is obtained by the process flow, the welding line energy is more than or equal to 200kJ/cm, the impact energy at 0 ℃ is more than or equal to 100J, the unit size of cleavage fracture is less than or equal to 20 mu m, and the fiber rate of fracture is more than or equal to 80%.
The invention provides a 690MPa grade high-strength steel plate for high heat input welding for a high-rise building, which comprises the following chemical components in percentage by mass: 0.08-0.12%, Mn: 1.0-1.6%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als is more than or equal to 0.015%, Cu is more than or equal to 0.18%, Ni: 1.0-2.0 percent of Ti/N, 0.4-0.6 percent of Cr, 0.4-0.6 percent of Mo and 0.03-0.06 percent of V, wherein the ratio of Ti to N is between 0.67 and 0.8.
Preferably, the steel plate comprises the following chemical components in percentage by mass: 0.10 to 0.12%, Mn: 1.0-1.2%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als: 0.015% -0.018%, Cu: 0.18% -0.25%, Ni: 1.0 to 1.2 percent of Ti, 0.4 to 0.6 percent of Cr, 0.4 to 0.6 percent of Mo and 0.03 to 0.06 percent of V, wherein the ratio of Ti to N is 0.7 to 0.75.
The effect of the above alloy elements, wherein the percentage symbol% represents the mass percentage:
(1) c: carbon is an element that secures the strength of the steel sheet, and will significantly affect the weldability of the material. The content of C is lower than 0.05 percent, the strength of the quenched and tempered steel plate is insufficient, and the quenched and tempered steel plate is particularly thick; when the content of C is too high, the low-temperature toughness of the base metal and the welded joint is obviously reduced. Therefore, the C content is controlled to be 0.08-0.12%.
(2) Mn: the solid solution of Mn can improve the strength of the steel, and the Mn content is controlled to be more than 1.0 percent to ensure the strength of the steel. When the Mn content exceeds 1.6%, on the one hand, center segregation occurs, which causes a hardened structure to be formed in the cooling process of the steel sheet, and reduces the low-temperature toughness of the base metal. Therefore, the Mn content is controlled to 1.0 to 1.6%.
(3) Si: when the silicon content is less than 0.1%, the molten steel is easily oxidized. Si is also an element that affects solid solution strengthening and weldability, and the Si content should be controlled to less than 0.15%. Therefore, the Si content is controlled to 0.1 to 0.15%.
(4) S and P: s and P are impurity elements in steel, and seriously damage the toughness of a base metal and a welding heat affected zone. Therefore, the contents of sulfur and phosphorus should be controlled to be less than 0.005% and less than 0.005%, respectively.
(5) N: n can form TiN particles with Ti, and austenite grains and a welding heat affected zone in the slab reheating process are inhibited from growing large; if the N content in the steel is too high, solid-solution nitrogen will be formed in the welding heat affected zone, reducing the low-temperature toughness of the welding heat affected zone, so the nitrogen content is controlled in the range of 0.0100-0.0150%.
(6) Ti: the TiN is formed by combining with the N, so that the growth of austenite grains of the plate blank in a heating and welding heat affected zone is inhibited, the Ti content is lower than 0.005 percent, and the effect is not easy to be exerted; excessive Ti causes the precipitation time of TiN to be reduced, the temperature to be increased and the pinning effect on austenite grains to be reduced. Therefore, the content of Ti is controlled to be 0.008-0.010%.
(7) And Als: als is an important deoxidizing element in the steelmaking process, and when the content of Als is less than 0.02%, the content of oxygen is difficult to control below 0.004%, so that the content of Als is required to be controlled to be more than or equal to 0.015%.
(8) Cu and Ni: cu and Ni elements are usually added compositely. The uniformity of the section strength of a large-thickness steel plate can be improved by utilizing Cu precipitated particles, and the low-temperature toughness of the center of the steel plate and a heat affected zone of a welding joint is improved by utilizing Ni element, so that the addition amount of Cu is controlled to be more than or equal to 0.18 percent, and the ratio of Ni: 1.0-2.0%.
(9) Cr: cr can improve the hardenability of the material and the strength of the material in the form of carbide, and if the Cr content is less than 0.4%, the effect is difficult to be exerted, but if the Cr content exceeds 0.6%, the low-temperature toughness of the base material and the welding heat affected zone is reduced, and the manufacturing cost of the material is increased, so that the Cr content is controlled to be 0.4-0.6%.
(10) Mo: mo can improve the hardenability of the material, promote the transformation of a low-temperature structure and improve the strength of the material, and meanwhile, Mo promotes the formation of an acicular ferrite structure under the condition of no recrystallization rolling; if the Mo content is less than 0.4%, the Mo action is low; if the Mo content exceeds 0.6%, not only the production cost is increased but also the weldability of the steel sheet, particularly the low-temperature toughness under high heat input welding, is impaired. Therefore, Mo is controlled to be 0.4-0.6%.
(11) V: v can improve the strength of the material through solid solution and VN precipitation, and when the content of V is lower than 0.03%, the strengthening effect is difficult to play; when the V content is more than 0.06%, the manufacturing cost of the material is significantly increased. Therefore, V is controlled to be 0.03-0.06%.
It should be noted that, the invention should control Ti/N between 0.67-0.8, in order to promote the precipitation of fine dispersion of TiN particles; in the welding process, TiN can effectively pin the coarsening of austenite grains, and the low-temperature toughness of a welding heat affected zone is obviously improved. If Ti/N is less than 0.67 or TiN is more than 0.8, the dissolving temperature of TiN is not favorably improved, so that austenite grains are obviously grown in the welding process, and the microstructure type of the steel is influenced, and the welding performance and the low-temperature toughness of the steel are also influenced. Therefore, it is necessary to control the temperature to be between 0.67 and 0.8.
The accompanying drawings, which are incorporated in and constitute a part of this application, illustrate preferred embodiments of the invention and together with the description, serve to explain the principles of the invention and not to limit the scope of the invention.
Example one
The invention discloses a preparation method of a 690MPa grade high-strength steel plate for high heat input welding for a high-rise building.
The converter is adopted for smelting according to the component proportion of the invention, and the adopted process route is converter → LF → RH-continuous casting-controlled rolling controlled cooling.
In the smelting process, the refining treatment time of LF and RH is 15min, the superheat degree of the tundish is controlled to be 20 ℃, and protective pouring is adopted in the whole process.
Heating the continuous casting slab to 1150 ℃;
controlled rolling and controlled cooling process: the steel plate is rolled in two stages, the high-temperature stage adopts high temperature and high pressure, the finish rolling temperature is 950 ℃, and the accumulated deformation is 45 percent; rolling at a low temperature section by adopting low temperature and high pressure, wherein the initial rolling temperature is 850 ℃, the final rolling temperature is 800 ℃, the accumulated deformation is 52 percent, then water cooling is carried out, and the temperature for controlling the steel plate to return to red is 650 ℃;
and (3) quenching and tempering: off-line quenching and tempering are carried out on the rolled steel plate, the quenching temperature range is 840 ℃, and the tempering temperature range is 550 ℃.
Example two
The invention discloses a preparation method of a 690MPa grade high-strength steel plate for high heat input welding for a high-rise building.
The converter is adopted for smelting according to the component proportion of the invention, and the adopted process route is converter → LF → RH-continuous casting-controlled rolling controlled cooling.
In the smelting process, the refining treatment time of LF and RH is 25min, the superheat degree of the tundish is controlled to be 10 ℃, and protective pouring is adopted in the whole process.
Heating the continuous casting slab to 1250 ℃;
controlled rolling and controlled cooling process: the steel plate is rolled in two stages, the high-temperature stage adopts high temperature and high pressure, the finish rolling temperature is 1050 ℃, and the accumulated deformation is 40%; rolling at a low temperature section by adopting low temperature and high pressure, wherein the initial rolling temperature is 800 ℃, the final rolling temperature is 880 ℃, the accumulated deformation is 50%, then, performing water cooling, and controlling the temperature of the steel plate to return to red to 710 ℃;
and (3) quenching and tempering: and (3) carrying out off-line quenching and tempering treatment on the rolled steel plate, wherein the quenching temperature range is 880 ℃, and the tempering temperature range is 650 ℃.
The microstructure of the weld heat affected zone of the steel of this example is shown in FIG. 1.
EXAMPLE III
A690 MPa grade high-strength steel plate for high-rise building high-heat input welding is provided, which is prepared into a steel plate with the plate thickness of 60mm by adopting 120 tons of converter smelting, and the composition components are shown in Table 1. The preparation method is adopted for preparation.
Example four
A690 MPa grade high-strength steel plate for high-rise building high-heat input welding is provided, which is prepared into a steel plate with the plate thickness of 60mm by adopting 120 tons of converter smelting, and the composition components are shown in Table 1. It was prepared using the preparation method provided in example two.
Comparative example
The compositions of comparative examples 1 and 2 are shown in Table 1, and steel sheets having a thickness of 60mm were produced by using 120-ton converter, and were produced by the production methods provided in example two.
Table 1 chemical composition of steel (wt.%)
Figure BDA0002886158640000101
The steel plates of the examples and the steel plates of the comparative examples were sampled, and the tensile properties in the longitudinal direction were measured by drawing the steel plates at a constant chuck moving rate of 3mm/min using an MTSNEW810 tensile tester in accordance with GB/T13239-2006 standard, with the sampling position being at 1/2 of the steel plate, and the test results being the average of the two samples. According to GB/T229-. The mechanical properties of the steel sheet are shown in Table 2.
TABLE 2 mechanical Properties and mechanical Properties of the Steel sheets
Figure BDA0002886158640000102
Figure BDA0002886158640000111
Therefore, the yield strength of the steel plate of the test steel prepared according to the invention reaches more than 690MPa, and the mechanical properties of the steel plate are obviously higher than those of the comparative example compared with the low-temperature toughness of the steel plate.
TABLE 3 texture characteristics of heat-affected zone of weld joint
Figure BDA0002886158640000112
The steel plates were subjected to 200kJ/cm submerged arc welding tests, respectively. The V-notch impact energy at-40 ℃ of the welded joint was then measured using an NCS series 500J instrumented pendulum impact tester according to GB/T229-1994, and the results are shown in Table 4.
As can be seen from Table 4, the impact work at 0 ℃ in the weld heat-affected zone of the example steel sheets was 100J higher.
TABLE 4 weld heat affected zone impact work
Figure BDA0002886158640000113
Figure BDA0002886158640000121
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 (9)

1. The 690 MPa-grade steel plate for high-rise building high heat input welding is characterized by comprising the following chemical components in percentage by mass: 0.10 to 0.12%, Mn: 1.0-1.2%, Si: 0.1-0.15%, S is less than or equal to 0.005%, P is less than or equal to 0.005%, N: 0.010-0.015%, Ti: 0.008-0.010%, Als: 0.015% -0.018%, Cu: 0.18% -0.25%, Ni: 1.0 to 1.2 percent of Ti, 0.4 to 0.6 percent of Cr, 0.4 to 0.6 percent of Mo and 0.03 to 0.06 percent of V, wherein the ratio of Ti to N is 0.7 to 0.75.
2. The steel plate for 690 MPa-grade high heat input welding for high-rise buildings according to claim 1, wherein the maximum thickness specification of the steel plate is 60 mm.
3. The steel plate for 690 MPa-grade high heat input welding for high-rise buildings according to claim 1, wherein the structure characteristic of the weld heat affected zone of the steel plate is martensite + lath bainite + granular bainite structure + M-A island.
4. The steel plate for 690 MPa-grade high heat input welding for high-rise buildings according to claim 3, wherein the volume percentage of lath bainite + martensite structure is not less than 80%, the volume percentage of granular bainite is not more than 20%, and the volume percentage of M-A island is not more than 5%.
5. The steel plate for 690 MPa-grade high heat input welding for high-rise buildings according to claim 1, wherein the volume percentage content of the large angle grain boundary of the steel plate is not less than 60%, and the large angle grain boundary is a crystal grain with an orientation difference angle of more than 15 °.
6. A preparation method of a steel plate for 690 MPa-level high heat input welding for high-rise buildings is characterized by being used for preparing the steel plate for 690 MPa-level high heat input welding for high-rise buildings according to any one of claims 1 to 5, and comprising the following steps of: the steel plate is rolled in two stages of high-temperature stage rolling and low-temperature stage rolling.
7. The preparation method of the steel plate for 690 MPa-level high heat input welding for the high-rise building according to claim 6, wherein the high-temperature section adopts high temperature and high pressure, the finishing temperature is not less than 950 ℃, and the accumulated deformation is not less than 40%.
8. The preparation method of the steel plate for 690 MPa-grade high heat input welding for the high-rise building according to claim 6, wherein the low-temperature section is rolled at low temperature and high pressure, the initial rolling temperature is not higher than 850 ℃, the final rolling temperature is not lower than 800 ℃, the accumulated deformation is not lower than 50%, and then water cooling is performed, and the temperature of the steel plate for returning red is controlled to be not lower than 650 ℃.
9. The preparation method of the steel plate for 690MPa grade high heat input welding for the high-rise building according to claim 6, wherein the rolled steel plate is subjected to quenching and tempering, and the quenching and tempering process comprises the following steps: the off-line quenching and tempering treatment is carried out on the rolled steel plate, the quenching temperature range is 840-880 ℃, and the tempering temperature range is 550-650 ℃.
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